NUREG/CR-7103 Vol. 4

Pacific Northwest National 

Laboratory Investigation of 

Stress Corrosion Cracking in 

Nickel-Base Alloys: Behavior 

of Alloy 152 And 52 Welds

Office of Nuclear Regulatory Research
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NUREG/CR-7103 Vol. 4

Pacific Northwest National 

Laboratory Investigation of 

Stress Corrosion Cracking in 

Nickel-Base Alloys: Behavior 

of Alloy 152 And 52 Welds

Office of Nuclear Regulatory Research

Manuscript Completed: December 2017

Date Published: April 2019

Prepared by: 

S. M. Bruemmer

M. J. Olszta

R.J. Seffens

R.A. Bouffioux

N.R. Overman

M. B. Toloczko

Pacific Northwest National Laboratory

Richland, WA 99352

Margaret Audrain, NRC Project Manager

iii

ABSTRACT

This report summarizes experimental results evaluating the primary water stress corrosion 

cracking (PWSCC) susceptibility of high-chromium, nickel-base weld metals and interface 

regions in more complex dissimilar metal welds. The primary research objectives were to 

establish quantitative measurements of SCC growth rates and determine relationships among 

cracking susceptibility, metallurgical characteristics and environmental conditions. Crackgrowth rates have been determined under cyclic loading and at constant stress intensity (K) in 

simulated PWR primary water environments for 21 weld metal specimens including tests on 

nine alloy 152, one alloy 152M, three alloy 52, seven alloy 52M and one alloy 52MSS 

specimens. In addition, SCC response was investigated from alloy 182/82 into alloy 52M for 4 

alloy 52M/182 overlay weld specimens and 2 alloy 52M/82 inlay weld specimens. Finally, 

crack-growth behavior was evaluated at various regions in dissimilar metal (DM) welds including 

9 tests at DM interfaces covering those between two alloy 152 and low alloy steel, one alloy 

52M and low alloy steel, two alloy 152M and carbon steel, two alloy 52M and carbon steel, and 

two alloy 152 and stainless steel interfaces. Most test specimens were machined from industry 

mockups to provide plant-representative materials, while a few were produced at laboratories 

using industry recommended procedures. In all cases, crack extension was monitored in situ by 

direct current potential drop (DCPD) with an estimated length resolution of about +1 μm making 

it possible to measure extremely low growth rates approaching 5x10-10 mm/s. Most SCC tests 

were performed at 360°C with a dissolved hydrogen concentration of 25 cc/kg to establish an 

electrochemical potential (ECP) at the Ni/NiO stability line where many nickel-base alloys are 

most susceptible to SCC; however, environmental conditions were modified during a few 

experiments to evaluate the influence of temperature, water chemistry or ECP on propagation 

rates. Extensive characterizations have been performed on material microstructures and 

stress-corrosion cracks by optical and electron microscopy techniques and linked to crackgrowth test results to help define material and environmental parameters controlling SCC 

susceptibility.

v 

FOREWORD

This report describes a study sponsored by the NRC Office of Nuclear Regulatory Research 

(RES) to investigate the stress corrosion cracking (SCC) susceptibility of alloy 690 weld metals 

including alloys 152, 52 and its many variants. SCC of nickel-based weld metals, such as those 

used for reactor vessel head penetration nozzles and reactor coolant system nozzles, is a 

degradation mechanism that can affect the operational safety of pressurized water reactors 

(PWRs). For instance, through-wall cracking was detected in an Alloy 82 and 182 hot leg 

nozzle weld at the V.C. Summer plant in 2000. Alloys 52 and 152 are thought to be more 

resistant to SCC than Alloys 82 and 182 because of higher chromium content, and there is no 

operational experience of their cracking in service. In light of the positive service history and 

low crack growth rates measured in laboratory testing sponsored by the industry, utilities have 

submitted requests to the Office of Nuclear Reactor Regulation (NRR) for relief from the 

inspection requirements found in Title 10 of the Code of Federal Regulations, Part 50.55a, 

including a 10 year interval for volumetric examination of pressure vessel head nozzles.

In the course of reviewing the relief requests and test results from industry-sponsored research, 

RES and NRR staff raised questions with respect to the potential for SCC due to higher strains 

associated with the welds and the weld metal’s complex microstructure. These higher 

chromium weld metals are also more susceptible to segregation and weld cracking including 

solidification cracking and ductility dip cracking. Very little testing has been performed on 

dissimilar metal (DM) welds where complex compositions and microstructure can be produced 

at interfaces between Fe-bases alloys (e.g., low allow steel, carbon steel and stainless steels) 

and the high-Cr, Ni-base weld metal.

This report has documented SCC results on a large number of industry-made alloy 152, 152M, 

52, 52M and 52MSS weld mockups revealing low CGRs in 360°C simulated PWR primary 

water. Specialized tests performed on alloy 52M overlay and inlay mockups supported very low 

SCC CGRs in the alloy 52M weld metal. The main conclusion from these experiments on alloy 

152, 152M, 52, 52M and 52MSS weld metals with typical Cr bulk concentrations (28-30 wt%) is 

that they are resistant to SCC crack growth. Some differences were observed for alloy 152 and 

52M welds in regions where the local Cr concentration was found to equal to or below ~24 wt%. 

SCC propagation rates up to ~1.4x10-8 mm/s were measured in an alloy 52M weld pass for the 

Ringhals overlay (CT035) and within DM weld alloy 152 dilution zones adjacent to the LAS 

interface. The presence of aligned grain boundaries along the crack path were a key 

requirement for significant SCC growth in the dilution zone specimens and limited the extent of 

observed IGSCC to local areas. Overall, these results support the excellent SCC resistance of 

the high Cr welds in the as-welded condition.

The application of the test results to plant components is particularly challenging given the large 

number of potential variations in weld designs and configurations that are found in service. 

These tests are ongoing and will continue to inform the evaluations by NRR to determine 

whether inspection requirement for components with Alloy 52 and 152 welds provide a 

reasonable assurance of safety.

vii

TABLE OF CONTENTS

ABSTRACT ................................................................................................................... iii

FOREWORD................................................................................................................... v

LIST OF FIGURES......................................................................................................... ix

LIST OF TABLES ...................................................................................................... xxix

EXECUTIVE SUMMARY ........................................................................................... xxxi

ACKNOWLEDGMENTS .......................................................................................... xxxiii

ABBREVIATIONS AND ACRONYMS...................................................................... xxxv

1 INTRODUCTION ..................................................................................................... 1-1

2 SCC CRACK-GROWTH TEST SYSTEMS, TESTING APPROACH, AND 

MATERIALS SELECTION....................................................................................... 2-1

2.1 Overview of SCC Crack-Growth Test Systems.............................................................2-1

2.2 General SCC Crack-Growth Testing Approach and Issues...........................................2-5

2.3 Specific SCC Crack-Growth Testing Approach.............................................................2-8

2.4 Materials Selection .......................................................................................................2-9

3 ALLOY 152/52/52m WELDS................................................................................... 3-1

3.1 Alloy 152 Welds............................................................................................................3-1

3.1.1 Early Tests on MHI Alloy 152 U-Groove Mockup Welds (CT013, CT017 

and CT018)....................................................................................................3-1

3.1.2 More Recent Tests on MHI Alloy 152 U-Groove Mockup Welds (CT052, 

CT135)......................................................................................................... 3-17

3.1.3 ANL 152V2 DM Weld (CT049, CT080)......................................................... 3-25

3.1.4 Analysis of Multi-Lab SCC Tests Results on the ANL Alloy 152v2 Weld....... 3-46

3.2 Alloy 52/52/52MSS Welds .......................................................................................... 3-61

3.2.1 Areva 52 Butt Weld and MHI 52 U Groove Weld .......................................... 3-61

3.2.2 Alloy 52 Weld Samples (CT024, CT025, CT032 and CT033) ....................... 3-61

3.2.3 KAPL Alloy 52M Welds................................................................................. 3-77

3.2.4 Special Metals Alloy 52MSS Weld (CT050)................................................ 3-105

3.3 Summary of SCC Behavior in High Cr, Ni Alloy Welds ............................................. 3-110

4 ALLOY 52M OVERLAYS/INLAYS.......................................................................... 4-1

4.1 Ringhals Alloy 52M/182 Overlay Welds........................................................................4-1

4.1.1 Alloy 52M/182 Overlay Weld Sample Pair #1 (CT028 & CT029).....................4-1

4.1.2 Alloy 52M/182 Overlay Sample Pair #2 (CT034 and CT035) ........................ 4-11

4.2 Ringhals Alloy 52M/82 Inlay Mockup (CT030 & CT031) ............................................. 4-25

4.3 Summary of SCC Tests on Alloy 52M Overlay and Inlay Mockups ............................. 4-35
viii

5 INTERFACES AND DILUTION ZONES IN DM WELDS......................................... 5-1

5.1 Dissimilar Metal Welds: Materials and Specimens........................................................5-1

5.2 MHI Alloy 152-SS DM Weld Interface Specimens (CT075 and CT076) ...................... 5-16

5.3 Alloy 152/52-LAS/CS Interfaces ................................................................................. 5-24

5.3.1 KAPL 52M/152M-CS DM Weld Interface (CT065 and CT66)........................ 5-24

5.3.2 Characterization of ANL 152/LAS Interface DM Weld Specimen (N152-

LAS-11)........................................................................................................ 5-39

5.3.3 ANL 152v2 DM Weld: Specimen CT117 - 152/LAS Interface........................ 5-49

5.3.4 ANL 152v2 DM Weld: Specimen CT119 – Alloy 152/LAS Interface .............. 5-74

5.3.5 EPRI Temper Bead DM Repair Weld: Specimen CT136 – Alloy 

52M/LAS Interface ....................................................................................... 5-87

5.4 Summary of Testing at Alloy 152/152M/52M DM Weld Interfaces .............................. 5-99

6 SUMMARY AND FUTURE RESEARCH NEEDS.................................................... 6-1

7 REFERENCES ........................................................................................................ 7-1
ix

LIST OF FIGURES

Figure 2-1 General Water Flow Diagram for PNNL SCC Crack-Growth Test Systems.......2-2

Figure 2-2 Typical Crack-Growth-Rate Test Frame Loading System Used at PNNL ..........2-3

Figure 2-3 Schematic Diagram Illustrating the DCPD System to Measure Crack 

Length in Situ....................................................................................................2-4

Figure 2-4 Schematic Drawing of a 0.5T CT Specimen. Dimensions for 1T CT 

Specimens Are Approximately Double..............................................................2-6

Figure 2-5 Example of Large Uncracked Ligament Detected in the Wake of a Crack.........2-8

Figure 3-1 Optical Image of the MHI Alloy 152 Mockup Showing U-Groove Weld in 

Cross-Section ...................................................................................................3-1

Figure 3-2 Sectioning Diagram for the Alloy 152 Welded Block. End Sections X and 

G Are 1.3 cm Thick and Were Used for Metallographic Observations 

While Sections A-F Are 1.9 cm Thick and Were Used for CT Samples. 

There Is ~7.6 cm of Welded Block in Front of Section “X”.................................3-2

Figure 3-3 Optical Micrograph of Section C Showing the Location of the Machined 

Notch. This Same Weld Pass Was Selected in Section D, While the One 

Just Above and to the Left Was Selected in Section E......................................3-2

Figure 3-4 SEM (BSE (a), SE (b,c)) Images Are Shown from the Alloy 152 Weld 

Metal.................................................................................................................3-3

Figure 3-5 SEM-EBSD Micrographs of CT052 Showing the Inverse Pole Figure 

(IPF)-X, IPF-Y, IPF-Z and Local Misorientation Map of the General 

Microstructure in the MHI Alloy 152 Weld..........................................................3-4

Figure 3-6 SEM-SE Micrograph Is Shown Along with Composition Maps for Mn, Nb 

and Al. The Mn Map Indicates a Slight Degree of Coring and the Other 

Two Maps Show the Locations of the Large NbC and the Ti-Al Particles in 

the Microstructure .............................................................................................3-5

Figure 3-7 An Example of a SGB That Shows a Single Large Cr-Carbide, with 

Numerous Smaller Nb Carbides Along the Boundary. In This Case, Ti 

Was Not Found Associated with the Nb Carbides.............................................3-6

Figure 3-8 Compositional Maps Taken in STEM Mode Revealed That Both Cr- and 

Nb-Rich Carbides Are Present on SSGBs. The Bottom Image Reveals 

That the Two Carbide Phases Can Sometimes Be Superimposed with 

Each Other. In This Example, Nb and Ti Were Associated with the Same 

Particles............................................................................................................3-6

Figure 3-9 Image of MHI Alloy 152 Weld Showing Positioning of 0.5T CT Specimens.......3-7

Figure 3-10 Crack Growth Response of MHI Alloy 152 Specimen CT013 During 

Transitioning and Constant K Steps..................................................................3-8

Figure 3-11 Side Surface Profile of MHI Alloy 152 Sample CT013 Showing Alignment 

of Crack Relative to Dendrite Structure.............................................................3-9
x 

Figure 3-12 Crack Growth Surface of MHI Alloy 152 Specimen CT013. Optical Image 

on Left Reveals Local Areas of SCC Propagation and SEM Images on 

Right Illustrate IG Morphology...........................................................................3-9

Figure 3-13 Overall Crack Growth Response of MHI Alloy 152 Specimens CT017 & 

CT018............................................................................................................. 3-10

Figure 3-14 Constant K Crack Growth Response of MHI Alloy 152 Specimens CT017 

& CT018 at 30 MPa√m.................................................................................... 3-11

Figure 3-15 Crack Growth Response During Cyclic Loading Conditions of MHI Alloy 

152 Specimens CT017 & CT018 in the Second Microstructural Region 

Examined........................................................................................................ 3-12

Figure 3-16 Constant K Crack Growth Response of MHI Alloy 152 Specimens CT017 

& CT018 at ~48 MPa√m ................................................................................. 3-12

Figure 3-17 Crack Growth Response of MHI Alloy 152 Specimens CT017 & CT018 at 

50°C in Simulated PWR Primary Water .......................................................... 3-14

Figure 3-18 Detailed Plot Showing DCPD Measured Crack Growth Response During 

Cycle + Hold Loading Conditions at 50°C in MHI Alloy 152 Specimen 

CT017............................................................................................................. 3-14

Figure 3-19 Optical Image of High Temperature Crack Growth Surface of the MHI 

Alloy 152 Specimen CT017............................................................................. 3-15

Figure 3-20 SEM Images of 350°C and 50°C Crack Growth Surfaces in MHI Alloy 152 

Specimen CT018 ............................................................................................ 3-17

Figure 3-21 Crack Growth Response During Constant K Loading for Specimen CT052 .... 3-19

Figure 3-22 Optical (top) and SEM-EBSD (bottom) Micrographs of CT052 CrossSection Showing the IPF-Y and Local Misorientation Map of the Crack 

from the Specimen Notch (left edge in top image, top center in bottom 

images)........................................................................................................... 3-19

Figure 3-23 SEM-BSE Images from the CT052 Cross-Section Highlighting the TG 

Crack-Tip Region and Illustrating Oxidation at the Crack Walls to the Final 

Tip .................................................................................................................. 3-20

Figure 3-24 Optical Image of the Crack-Growth Surface on MHI Alloy 152 Specimen 

CT052............................................................................................................. 3-21

Figure 3-25 MHI Alloy 152 U-Groove Weld Showing the Standard T-S CT Specimen 

Orientation and Alternate L-S Orientation. For Both, the Target Crack 

Patch Is Aligned to the Long Axis of the Grains .............................................. 3-22

Figure 3-26 Measured Crack Growth During Cycle + 24h Hold Loading for CT135............ 3-22

Figure 3-27 Measured SCC Growth Rates During Constant K Loading for CT135 at 

Two K Levels: 33 MPa√m (Upper) and 38.5 MPa√m (Lower).......................... 3-24

Figure 3-28 Weld Buildup Plan for the ANL Alloy 152v2 Weldment Fabricated Using 

Alloy 152 Heat WC04F6. PNNL Has Been Using the Name "Alloy 152 

V2" for This Weldment .................................................................................... 3-26

Figure 3-29 Optical Macro Image of a Weld Slice Taken from the ANL Alloy 152v2 

Weldment. Note That the Weld Orientation Is Flipped from Drawing in 

Figure 3-28 ..................................................................................................... 3-26
xi

Figure 3-30 Microhardness Indent Pattern and Resulting Hardness Map for the Macro 

Slice of the WC04F6 Weld Region.................................................................. 3-27

Figure 3-31 Comparison of SGB and SSGB Structures of the Alloy 152 V2 Weldment 

Using Optical Imaging (top), SEM-BSE Imaging (middle), and EBSD 

Pattern Quality Map (bottom).......................................................................... 3-27

Figure 3-32 Low Magnification SEM-EDS Maps Provide an Overview of Composition 

Variations in the ANL Alloy 152 V2 Weldment. SEM-BSE Image in the 

Upper Left Shows the Grain and Dendrite Structure ....................................... 3-28

Figure 3-33 a) SEM-BSE Image Where Heavier Elements Produce Higher Brightness. 

Bright Precipitates Decorating SGBs and SSGBs Are NbC. Black Dot 

Contrast Is Polishing Debris. b) Higher Magnification SEM-BSE and EDS 

Images Showing NbC and Cr23C6 Carbides Decorating a Grain 

Boundary ........................................................................................................ 3-29

Figure 3-34 Locations of the 0.5T CT Specimens Extracted from Two Different Slices 

of the Alloy 152 V2 Weldment. Image on the Left Is for the First Test 

(CT049), While the Image on the Right Is for the Second Test (CT080). 

Both Specimens Were Oriented to Align the Elongated Grain Boundaries 

with the Geometric Crack Path and Within a Region of Higher Hardness 

Indicated in Figure 3-30 .................................................................................. 3-30

Figure 3-35 EBSD Inverse Pole Figures Illustrating the Grain Structure in the Alloy 

152 V2 Specimen CT049 Specimen as Viewed from the Face of the 

Specimen........................................................................................................ 3-30

Figure 3-36 EBSD Inverse Pole Figures Illustrating the 3D Grain Structure in the ANL 

Alloy 152 V2 Specimen CT049 Specimen as Viewed from the End of the 

Specimen (Test Plane A) or on the Geometric Crack Plane (Test Plane 

B). The Z-Axis Is Normal to the Face of the Specimen................................... 3-31

Figure 3-37 Optical Images of the Polished and Etched Side Grooves for the First 

Specimen (CT049) Cut from the ANL Alloy 152 V2 Weldment. Grain 

Shape Is Highly Variable, but Based on These Side-Groove Observations 

the Geometric Crack Path Is Well Aligned with the Grain Boundaries of 

the Elongated Grains ...................................................................................... 3-32

Figure 3-38 Optical Images of the Polished and Etched Side Grooves for the First 

Specimen (CT049) Cut from the ANL Alloy 152 V2 Weldment. Grain 

Shape Is Highly Variable, but Based on These Side-Groove Observations 

the Geometric Crack Path Is Well Aligned with the Grain Boundaries of 

the Elongated Grains ...................................................................................... 3-32

Figure 3-39 Overview of the Entire Test of the First ANL Alloy 152v2 Weld Specimen 

(CT049) Performed in 360°C Simulated PWR Primary Water. Dashed 

Red Line Indicates the Percent IG Engagement ............................................. 3-35

Figure 3-40 Crack Growth Response During the Second Constant K Evaluation of 

CT049 in 360°C Simulated PWR Primary Water. Stress Intensity Was 

~33 MPa√m .................................................................................................... 3-35

Figure 3-41 Measured Crack-Growth Response During the Fifth and Final Constant K 

Evaluation of CT049 in 360°C Simulated PWR Primary Water. Stress 

Intensity Was ~39 MPa√m .............................................................................. 3-36
xii

Figure 3-42 Crack-Growth Surface Optical Image of the 8-mm Wide Section of the 

CT049 Specimen. Yellow Arrows Indicate Examples of IG Protrusions 

Along the Final Crack Front. Blue Boxes Indicate Regions of SEM 

Examinations Presented in Figure 3-43 .......................................................... 3-38

Figure 3-43 SEM-SE Images of Regions Within the Blue Boxes in the Optical Image 

of the Entire Crack-Growth Surface for the CT049 Specimen (Figure 

3-42) ............................................................................................................... 3-38

Figure 3-44 Higher Magnification SEM-SE Image Illustrating the IG Crack Surface 

Appearance in CT049 ..................................................................................... 3-39

Figure 3-45 SEM-BSE (upper) and SE (lower) Images Showing IG Regions (blue tint) 

Along the Final ~1.5 mm of the SCC Test of CT049. Yellow Line Denotes 

the Final Crack Front at the Conclusion of the Test......................................... 3-39

Figure 3-46 Compilation of SEM-BSE, Optical, and EBSD Images Showing the Crack 

Path in Profile from Notch to Final Crack Front in a Side-Surface Cross 

Section from the CT049 Specimen ................................................................. 3-40

Figure 3-47 SEM-BSE and EDS Maps Showing Elemental Compositions Along the 

Final ~150 μM of the CT049 Crack Profile ...................................................... 3-40

Figure 3-48 Illustration of Postulated Constant K IG Extension Along the Final Crack 

Front of CT049................................................................................................ 3-41

Figure 3-49 Overview of CGR Test on the Second Alloy 152 V2 Specimen (CT080) 

Performed in 360°C (0-3800 hours) and 320°C (3800-8000 Hours) 

Simulated PWR Primary Water. Terminal Constant K CGRs Are Listed ........ 3-43

Figure 3-50 Constant K Crack Growth Response Following the First Transitioning 

Sequence on the Alloy 152 V2 Specimen CT080 in 360°C Simulated 

PWR Primary Water........................................................................................ 3-43

Figure 3-51 Env/air Ratio During the First Three Transitioning Sequences (two at 

360°C and one at 320°C) for the Second Test on the Alloy 152 V2 

Weldment (CT080).......................................................................................... 3-44

Figure 3-52 Third Constant Load Observation on the Alloy 152 V2 Specimen CT080. 

This Portion of the Test Was Conducted in 320°C Simulated PWR 

Primary Water................................................................................................. 3-45

Figure 3-53 Optical Image of the 8-mm-Wide Section of the Crack-Growth Surface of 

the Second Alloy 152 V2 Specimen (CT080) Tested in 360°C and 320°C 

Simulated PWR Primary Water....................................................................... 3-46

Figure 3-54 SEM BSE Image of the Final ~1 Mm of Crack Growth of the Second Alloy 

152 V2 Specimen (CT080). This Portion of the Test Was at 320°C ............... 3-46

Figure 3-55 Optical Image of the Side-Surface Cross Section Taken from the Second 

Alloy 152 V2 Specimen (CT080) After SCC Testing........................................ 3-46

Figure 3-56 Ratio of CGR in High Temperature Water to Estimate Air Fatigue CGR for 

PNNL Test #1 on ANL Alloy 152v2 (CT049) Tested in 360°C Water............... 3-48

Figure 3-57 Optical Image of the Crack Surface from the First Test (CT049) by PNNL 

on ANL Alloy 152v2. Arrows Indicate Examples of Significant IG 

Protrusions Along the Final Crack Front.......................................................... 3-49
xiii

Figure 3-58 Overview of the Entire First Test (C541) by GEG on the ANL 152v2 

Weldment Supplied by Peter Andresen. Percent IG Estimate Was 

Determined by PNNL ...................................................................................... 3-52

Figure 3-59 Ratio of Measured CGR in 360°C Simulated PWR Primary Water to 

Estimated Air Fatigue CGR for GEG Test C541 on ANL Alloy 152v2.............. 3-53

Figure 3-60 SEM Secondary Image Obtained by PNNL of the GEG C541 Showing 

Various Features of the Crack Growth Surface ............................................... 3-54

Figure 3-61 1T CT Specimen That ANL Used for Their Test (N152-TS-1) on the ANL 

152v2 Weldment............................................................................................. 3-56

Figure 3-62 Ratio of CGR in High Temperature Water to Estimate Air Fatigue CGR for 

ANL Test on ANL Alloy 152v2 (N152-TS-1) Tested in 320°C Water ............... 3-57

Figure 3-63 ANL Optical Image of the Crack Growth Surface of N152-TS-1. ANL's 

SEM Images Are Overlaid onto the Surface to Show Locations of IG 

Cracking Relative to the Entire Crack Surface and Indicated Crack 

Lengths at Constant Load............................................................................... 3-58

Figure 3-64 Image of the MHI Alloy 52 and AREVA Alloy 52 Welds Showing 

Positioning of the 0.5T CT Specimens ............................................................ 3-62

Figure 3-65 Overview of the Crack Growth Response of Two Alloy 52 Welds, One 

Made by AREVA (CT024) and One Made by MHI (CT025)............................. 3-62

Figure 3-66 Cycle + Hold and Constant K Response of the AREVA and MHI Alloy 52 

Specimens (CT024 & CT025) in the Second Phase of Each Specimen 

That Was Examined........................................................................................ 3-63

Figure 3-67 Overview of the Crack Growth Response of the AREVA and MHI Alloy 52 

Specimens (CT024 & CT025) During Cyclic Loading Conditions at 50°C ....... 3-64

Figure 3-68 Constant K Crack Growth Response of the MHI and AREVA Alloy 52 

Specimens (CT024 & CT025) at 350°C After Cyclic Loading Crack 

Extension at 50°C ........................................................................................... 3-65

Figure 3-69 Optical Image of the Crack Growth Surface of the AREVA Alloy 52 

Specimen (CT024).......................................................................................... 3-67

Figure 3-70 Optical Image of the Crack Growth Surface of the MHI Alloy 52 Specimen 

(CT025). Yellow Boxes Indicate Regions of IG Growth and the Blue Box 

Identifies the Area of the SEM Image Shown in Figure 3-71 ........................... 3-67

Figure 3-71 SEM Images Illustrating IG Regions on the Crack Growth Surface for the 

Alloy 52 Specimens: (left) Isolated IG Finger-like Area in AREVA Sample 

and (right) Typical IG Area in MHI Sample...................................................... 3-68

Figure 3-72 White Lines Indicate Where Crack Growth Surfaces Were Sectioned to 

Expose and Polish Crack Side Surfaces ......................................................... 3-69

Figure 3-73 Side Surface Image of the AREVA Alloy 52 Specimen CT024........................ 3-69

Figure 3-74 Side Surface Image of the MHI Alloy 52 Specimen CT025 ............................. 3-70

Figure 3-75 Overall Response for the Second Test on the AREVA and MHI Alloy 52 

Specimens CT032 and CT033........................................................................ 3-70
xiv

Figure 3-76 Similar CGRs Were Seen During Early Transitioning Between First Test 

(a) CT024/25 and Second Test (b) CT032/33 on the AREVA and MHI

Materials ......................................................................................................... 3-71

Figure 3-77 Cyclic Loading Response at 50°C of AREVA (CT032) and MHI Alloy 52 

(CT033) .......................................................................................................... 3-72

Figure 3-78 Crack Growth Response of a Second Set of AREVA and MHI 52 

Specimens (CT032 & CT033) Tested at 350°C Following Crack Extension 

at 50°C............................................................................................................ 3-72

Figure 3-79 AREVA and MHI Alloy 52 Crack Growth Response at 40 MPa√m .................. 3-73

Figure 3-80 Optical Image of the Crack Growth Surface of the AREVA Alloy 52 

Specimen CT032 (left) and the MHI Alloy 52 Specimen CT033 (right)............ 3-75

Figure 3-81 Side Surface Optical Image (top) and SEM-BSE Image (bottom) of 

Cracking in the AREVA Alloy 52 Specimen CT032 Showing Both TG and 

IG Growth ....................................................................................................... 3-75

Figure 3-82 Side Surface Optical Image (top) and SEM-BSE Image (bottom) of 

Cracking in the MHI Alloy 52 Specimen CT033 Showing Both TG and IG 

Growth............................................................................................................ 3-76

Figure 3-83 SEM-BSE of the Side Surface of the Leading Crack Growth Front of 

CT033 Showing Both IG and TG Cracking...................................................... 3-76

Figure 3-84 SEM-BSE of a Leading Crack Tip in CT033 Highlighting IG Cracking............. 3-77

Figure 3-85 Alloy 52M Welds from KAPL: (a) Dissimilar Metal V-Groove Weld of Alloy 

EN52M Joining 304 SS and Carbon Steel and (b) Alloy EN52M Narrow 

Gap Weld Joining Alloy 690 ............................................................................ 3-78

Figure 3-86 Photos of KAPL Alloy 52M Narrow Gap Weld Blank “A” and CT040 

Specimen Machined from the Blank................................................................ 3-79

Figure 3-87 Photos of KAPL Alloy 52M V-Groove Weld Blank “A” and CT041 

Specimen Machined from the Blank................................................................ 3-79

Figure 3-88 Overview of Defects in the KAPL Alloy 52M Weld with Known Weld 

Cracks ............................................................................................................ 3-80

Figure 3-89 Photos of Specimens Cut from KAPL Alloy 52M Narrow Gap Weld 

Containing Hot Cracks. Blank a (CT042) Is Positioned Off-Center and 

near the Bottom of the Weldment to Insect a High Density of Weld 

Cracks, While Blank B (CT043) Is Positioned near the Center of the Weld 

Where No Weld Cracks Were Observed......................................................... 3-80

Figure 3-90 Overview of the Entire Test on the KAPL Alloy 52M Narrow Gap (CT040) 

and V-Groove (CT041) Specimens ................................................................. 3-81

Figure 3-91 Response During Initial Cycle + Hold Transitioning Steps on the KAPL 

Alloy 52M Narrow Gap (CT040) and V-Groove (CT041) Specimens............... 3-82

Figure 3-92 Response During Initial Constant K Step on the KAPL Alloy 52M Narrow 

Gap (CT040) and V-Groove (CT041) Specimens............................................ 3-82

Figure 3-93 Crack-Growth Response During the K Increase by dK/da for KAPL Alloy 

52M Specimens CT040 and CT041 ................................................................ 3-83
xv 

Figure 3-94 Crack-Growth Response from Cycle + Hold to Constant K for CT040 and 

CT041............................................................................................................. 3-84

Figure 3-95 Crack Growth Response During Constant K at 360°C for the KAPL Alloy 

52M Narrow Gap (CT040) and V-Groove (CT041) Weld Specimens .............. 3-84

Figure 3-96 Crack Growth Surface of the KAPL Alloy 52M Narrow Gap Specimen 

CT040: (a) Optical Image of the Overall Crack Growth Surface and (b) 

SEM-BSE Image of the Area Highlighted in (a)............................................... 3-86

Figure 3-97 Crack Growth Surface of the KAPL Alloy 52M V-Groove Specimen 

CT041: (b) Optical Image of the Overall Crack Growth Surface and (b) 

SEM-BSE Image of the Area Highlighted in (a)............................................... 3-87

Figure 3-98 Crack Profile of the KAPL Alloy 52M Narrow Gap Specimen CT040............... 3-87

Figure 3-99 Crack Profile of the KAPL Alloy 52M V-Groove Specimen CT041................... 3-88

Figure 3-100 SEM-BSE of the Leading Crack Tip in the CT040 Cross-Section Sample. 

Dashed Yellow Box Highlights the Region of Interest for EBSD Analysis in 

Figure 3-102 ................................................................................................... 3-89

Figure 3-101 SEM-BSE High Magnification Micrograph of the Leading TG SCC Crack 

Tip in CT040 (higher magnification of the dashed yellow box shown in 

bottom figures). Note the Sample Is Rotated 90° from the Previous 

Figure ............................................................................................................. 3-90

Figure 3-102 EBSD of CT040 (IPF, misorientation, and image quality maps) from the 

Yellow Dashed Box in Figure 3-100. The Yellow Line in the Pattern 

Quality Map Shows the Approximate SCC Crack............................................ 3-91

Figure 3-103 EBSD of CT040 (IPF maps and a misorientation map) from ~1-2 mm 

Ahead of the Yellow Dashed Box in Figure 3-100 ........................................... 3-92

Figure 3-104 EBSD (IPF and misorientation density) of the Leading SCC Tip of CT041. 

Portions of the SCC Test Were Observed to Be IG, but the Leading Crack 

Tip Ended Transgranularly.............................................................................. 3-93

Figure 3-105 EBSD (IPF and misorientation density) ~1-2 mm Ahead of the Leading 

SCC Tip in CT041. Note That the Analysis Orientation Is Rotated 90 

Degrees from the Previous Figure (i.e., the crack would be running top to 

bottom) ........................................................................................................... 3-93

Figure 3-106 SEM Images of a Secondary Crack in CT041. A FIB-TEM Foil Was 

Prepared from This Region That Showed the IG Crack Split off into a TG 

Crack Before the End (identical orientation as Figure 3-99) ............................ 3-94

Figure 3-107 STEM (BF) and EDS Elemental Maps of the Secondary SCC Tip of 

CT041 Shown in Figure 3-106. Note That the Analysis Orientation of the 

SCC Tip Was Rotated from That Which Is Shown in Figure 3-106.................. 3-95

Figure 3-108 Overview of the Entire Test on the KAPL Alloy 52M Narrow Gap Weld 

Specimens (CT042 and CT043) with Preexisting Weld Cracks....................... 3-96

Figure 3-109 In Situ Precracking and Transitioning of the KAPL Alloy 52M Narrow Gap 

Weld Specimens (CT042 & CT043) with Known Hot Cracks........................... 3-97

Figure 3-110 Continued Transitioning Steps Performed on the KAPL Alloy 52M Narrow 

Gap Weld Specimens (CT042 and CT043) with Weld Cracks......................... 3-97
xvi

Figure 3-111 First Observation of Constant K Crack Growth Response on the KAPL 

Alloy 52M Narrow Gap Weld Specimens (CT042 & CT043) with Known 

Hot Cracks. Slightly Lower CGR in the Specimen Aligned to Intersect Hot 

Cracks ............................................................................................................ 3-98

Figure 3-112 Second and Final Observation of Constant K Crack Growth Response of 

the KAPL Alloy 52M Narrow Gap Weld Specimens (CT042 & CT043) with 

Known Hot Cracks .......................................................................................... 3-99

Figure 3-113 Post-Test Serial Sectioning Plan for KAPL Alloy 52M NG Weld 

Specimens with Weld Cracks (CT042 and CT043) ....................................... 3-100

Figure 3-114 Crack Profile of Images from CT042, the Weld Specimen Aligned with Hot 

Cracks .......................................................................................................... 3-101

Figure 3-115 Crack Profile of Images from CT043, the Weld Specimen Not Aligned with 

IG Weld Cracks. The Profile Images Show Hot Cracks Below the SCC 

Test Plane..................................................................................................... 3-101

Figure 3-116 Crack Growth Surface from CT042, the Weld Specimen Aligned with Hot 

Cracks .......................................................................................................... 3-102

Figure 3-117 Crack Growth Surface from CT043, the Weld Specimen Not Aligned with 

Hot Cracks.................................................................................................... 3-103

Figure 3-118 SEM-BSE Image of the Side Surface of the Leading Crack Growth Tip of 

CT043........................................................................................................... 3-104

Figure 3-119 SEM-BSE Image of a TEM FIB Sample of a Weld Crack in CT043 Taken 

from the Dashed Yellow Box Region of Figure 3-115. The Solid Green 

Box in the Top Image Shows the Region of Interest in the Higher 

Magnification Image at the Bottom................................................................ 3-104

Figure 3-120 STEM BF Image and EDS Elemental Maps of the IG Weld Crack Region 

in CT043. A Higher Magnification Examination Was Taken of the Dashed 

Yellow Box and Is Shown in Figure 3-121. No O-K Signal Was Detected 

in These Cracks and Grain Boundary Precipitates Are Enriched in Cr and 

Ti .................................................................................................................. 3-105

Figure 3-121 STEM-BF Image and EDS Elemental Maps of the Weld Crack in CT043 

from the Yellow Dashed Box in Figure 3-120. At Higher Magnification, 

Small (100 nm) Nb-Rich Precipitates Are Observed on the Grain 

Boundary ...................................................................................................... 3-105

Figure 3-122 Overview of the Crack Growth Response of the Alloy 52MSS Specimen 

CT050........................................................................................................... 3-107

Figure 3-123 Second Observation of Constant K Crack Growth Response on the Alloy 

52MSS Specimen CT050.............................................................................. 3-108

Figure 3-124 Fifth and Final Observation of Constant K Crack Growth Response on the 

Alloy 52MSS Specimen CT050..................................................................... 3-109

Figure 3-125 Optical Micrograph of the CT050 Crack Growth Surface Showing 

Primarily TG Cracking. Small Partially IG Protrusions Can Be Seen at the 

Crack Front................................................................................................... 3-109

Figure 3-126 SEM-SE of the Cross-Section of CT050 Showing the First Part of the 

Crack Growth Test Being TG and the Last 250 μM of the Test Being IG....... 3-110
xvii

Figure 3-127 SEM-SE of the Cross-Section of CT050 Showing the Final 250 μm of the 

Crack Growth Test Being IG ......................................................................... 3-110

Figure 3-128 Summary of PNNL-Measured Constant K SCC CGRs for Alloy 

152/152M/52/52M Weld Metal Specimens as a Function of Stress 

Intensity ........................................................................................................ 3-111

Figure 3-129 PNNL Measured Constant K SCC CGRs for Alloy 152/42/52M Weld 

Metal Specimens as a IG Cracking Observed on the Post-Test Crack 

Growth Surface............................................................................................. 3-113

Figure 3-130 Summary of PNNL- and GEG-Measured Constant K SCC Crack-Growth 

Rates for Alloy 152/152M/52/52M Weld Metals as a Function of Stress 

Intensity ........................................................................................................ 3-114

Figure 3-131 Summary of PNNL- and ANL-Measured SCC Crack-Growth Rates for 

Alloy 152/152M/52/52M Weld Metals as a Function of Stress Intensity......... 3-115

Figure 3-132 Summary of PNNL-, GEG-, ANL- and CIEMAT-Measured SCC 

Crack-Growth Rates for Alloy 152/152M/52/52M Weld Metals as a 

Function of Stress Intensity........................................................................... 3-116

Figure 4-1 Overview of the Ringhals Alloy 52M Overlay (a) and Inlay (b) Mockups............4-1

Figure 4-2 Photographs Showing Location of Specimens to Be Taken from Alloy 

182/52/690 Overlay Received from Ringhals. Machined Notch Was 

~3 mm from the Alloy 182 – Alloy 52M Boundary..............................................4-2

Figure 4-3 Compositional Profile #1 Across the Bottom of an Alloy 182 Weld Puddle 

and into the Alloy 52M of the Ringhals Alloy 52M/182 Overlay Material ............4-2

Figure 4-4 Compositional Profile #2 Across an Alloy 182 Weld Trough and into the 

Alloy 52M of the Ringhals Alloy 52M/182 Overlay Material ...............................4-3

Figure 4-5 Initial Cycle + Hold Steps in the Alloy 182 Portion of the Ringhals Alloy 

52M/182 Overlay Material .................................................................................4-4

Figure 4-6 First Constant K Response of the Ringhals Alloy 52M/182 Weld Showing 

Very Low CGRs in the Alloy 182 Material .........................................................4-4

Figure 4-7 Crack Extension into New Microstructural Region and Growth Response 

During Cycle + Hold Loading with R = 0.7 and R = 0.5 .....................................4-5

Figure 4-8 Repeat Observation of Constant K and Cycle + Hold Response at 350°C 

in the Ringhals Alloy 52M/182 Overlay. Very Low CGRs Suggest the 

Crack Had Entered into the Alloy 52M Weld .....................................................4-6

Figure 4-9 Crack Extension in Alloy 52M During Cycling at 50°C in the Ringhals 

Alloy 52M/182 Overlay......................................................................................4-7

Figure 4-10 Constant K Crack-Growth Response in the Alloy 52M Weld Material After 

Temperature Increase from 50°C to 350°C.......................................................4-8

Figure 4-11 Optical Images Showing Crack in the Side Groove (top) and Fracture 

Morphology on the Crack-Growth Surface (bottom) for the Alloy 182/52 

Overlay Specimen #1 (CT028)........................................................................ 4-10

Figure 4-12 Transitioning Steps to Constant K Response Under BWR Oxidizing 

Conditions of the Second Pair of Ringhals Alloy 52M/182 Overlay 

Specimens (CT034 & CT035) ......................................................................... 4-11
xviii

Figure 4-13 Crack Growth Response on Switching from BWR Oxidizing to 

Hydrogenated Water in the Second Pair of Ringhals Alloy 52M/182 

Specimens (CT034 & CT035) ......................................................................... 4-12

Figure 4-14 Response During the Second Transitioning Phase in BWR Oxidizing 

Water of the Second Pair of Ringhals Alloy 52M/182 Specimens (CT034 

& CT035) ........................................................................................................ 4-13

Figure 4-15 The Second Observation of Constant K Response for the Second Pair of 

Ringhals Alloy 52M/182 Specimens in BWR Oxidizing Water with Sulfate...... 4-14

Figure 4-16 Final Cycle + Hold Loading Response of Ringhals Alloy 52M/182 

Specimen CT035 Showing a Relatively High Rate of 3.2x10-8 mm/s.............. 4-15

Figure 4-17 Final Constant K Response of Ringhals Alloy 52M/182 Specimen CT035 

with Final Propagation in the Alloy 52M .......................................................... 4-15

Figure 4-18 Optical Micrograph of the Crack Growth Surface of CT035............................. 4-17

Figure 4-19 Optical Micrographs (low and high magnification with solid yellow box 

showing high mag region of interest) of the Side Surface of CT035. The 

Dashed Green Box Shows the Location of EBSD Analysis. Two FIB 

Samples (Regions 1 and 2) Were Prepared from This Cross-Section and 

Are Highlighted by the Solid Red Boxes.......................................................... 4-18

Figure 4-20 SEM-BSE Image and EDS Elemental Maps of the CT035 Cross-Section 

Following the SCC Crack Path from the Alloy 182 Through Several Weld 

Passes of the Alloy 52M (approximately the same region as solid yellow 

box in Figure 4-19a). The Crack Ends in an Alloy 52M Region of 

Distinctly Different Composition (higher Ni, lower Cr and Fe).......................... 4-19

Figure 4-21 SEM-BSE Image with an Overlaid Composite EDS Elemental Maps for 

the CT035 Cross-Section Following the SCC Crack Path from the Alloy 

182 Through Several Weld Passes of the Alloy 52M. EDS Line Scans 

Are Shown Illustrating the Composition Changes from the Alloy 182 to 

Alloy 52M and into the Ni-Rich Pass ............................................................... 4-20

Figure 4-22 SEM-EBSD Pattern Quality Map, IPF Images and Local Misorientation 

Maps for the Final Length of the SCC Crack on the Side Surface of 

Specimen CT035. The Pattern Quality Map Is Shown for the Leading 

SCC Crack Tip (with a red line overlay to show approximate location of 

the crack)........................................................................................................ 4-21

Figure 4-23 SEM-BSE Micrographs of the Leading SCC Crack in CT035 

Corresponding to FIB Region 1 in Figures 4-19 and 4-22. The Solid 

Yellow Box in a) Shows the Location of b), and the Dashed Yellow Box in 

b) Indicates the Location of the Plan View FIB Sample ................................... 4-22

Figure 4-24 SEM-BSE Images of the Leading IGSCC Crack Tip in the Alloy 52M Pass 

of Altered Composition.................................................................................... 4-22

Figure 4-25 STEM/EDS Elemental Maps of an IG Crack Tip from the Dashed Yellow 

Box in Figure 4-24........................................................................................... 4-23
xix

Figure 4-26 SEM-BSE Image of Secondary IGCSCC Cracks in the Alloy 182 Weld 

Metal for CT035. Solid Yellow Box in a) Provides the Location of b), and 

the Dashed Yellow Box in b) Illustrates the Location of the Plan View FIB 

Sample. Note the Orientation of These Images Is Identical to Those 

Shown Earlier in This Section ......................................................................... 4-24

Figure 4-27 SEM-BSE Images of Secondary IGSCC Cracks (FIB region 2 in Figures 

4-19 and 4-22) In the Alloy 182 Weld Metal for Specimen CT035. Note 

the FIB Orientation of the Sample Has Changed (crack orientation is now 

left to right instead of bottom to top) From the Previous Figures ..................... 4-24

Figure 4-28 STEM/EDS Elemental Maps of a Secondary IGSCC Crack Tip in the 

A182 Region of the CT035 Sample................................................................. 4-25

Figure 4-29 Profile of Ringhals Alloy 52M Inlay Mockup Weld Received from 

Westinghouse. Alloy 52M Inlay Is 10 mm Thick ............................................. 4-26

Figure 4-30 Optical Images of the Alloy 52M/82 Inlay Sample CT031................................ 4-26

Figure 4-31 Test Overview for the Ringhals Alloy 52M/82 Inlay Mockups (CT030 & 

CT031)............................................................................................................ 4-27

Figure 4-32 Initial Cycle + Hold and Constant K Response in PWR Primary Water of 

the Ringhals Alloy 52M/82 Inlay Mockup (CT030 & CT031)............................ 4-28

Figure 4-33 Constant K and Cyclic Loading Response of the Ringhals Alloy 52M/82 

Inlay Mockup (CT030 & CT031) After Switching from PWR Primary Water 

to BWR Oxidizing Water ................................................................................. 4-29

Figure 4-34 Alloy 52M Response During Cycle and Cycle + Hold Loading at R=0.5 in 

the Ringhals Alloy 52M/82 Inlay Mockup Specimens (CT030 & CT031) ......... 4-30

Figure 4-35 Alloy 52M Response During Constant K Loading in the Ringhals Alloy 

52M/82 Inlay Mockup Specimens (CT030 & CT031)....................................... 4-30

Figure 4-36 dK/da Response Going from 30 to 40 MPa√m of the Ringhals Alloy 

52M/82 Inlay Mockup Specimens (CT030 & CT031)....................................... 4-31

Figure 4-37 Constant K Response at 40 MPa√m of the Ringhals Alloy 52M/82 Inlay 

Mockup Specimens (CT030 & CT031)............................................................ 4-32

Figure 4-38 Crack Growth Surface of Ringhals Alloy 52M/82 Specimen CT030 ................ 4-34

Figure 4-39 Optical Image of Side Surface of Crack Growing into Alloy 52M in the 

Ringhals Alloy 52M/82 Specimen CT031 ........................................................ 4-34

Figure 4-40 SEM Image of Side Surface of Crack Growing into Alloy 52M in the 

Ringhals Alloy 52M/82 Specimen CT031 ........................................................ 4-35

Figure 5-1 Photograph Showing the Target Orientation of the Two Alloy 152/304SS 

DM Weld Fusion Line Specimens (CT075 and CT076).....................................5-3

Figure 5-2 Polished and Etched Side Grooves of the MHI Alloy 152/304SS DM Weld 

Fusion Line Specimen #1 (CT075). Notch Can Be Seen on the Left Edge 

of the Optical Image..........................................................................................5-3

Figure 5-3 Polished and Etched Side Grooves of the MHI Alloy 152/304SS DM Weld 

Fusion Line Specimen #2 (CT076). Notch Can Be Seen on the Left Edge 

of the Optical Image..........................................................................................5-3
xx 

Figure 5-4 Optical Images Showing the Target Location of the Alloy 52M and Alloy 

152M Dilution Zone CT Specimens (CT065 and CT066) ..................................5-4

Figure 5-5 Polished and Etched Side Grooves of the Alloy 52M/CS Dilution Zone 

Specimen (CT065) Showing That the Crack Growth Plane Is ~0.5 mm 

into the Alloy 52M .............................................................................................5-4

Figure 5-6 Polished and Etched Side Grooves of the Alloy 152M/CS Dilution Zone 

Specimen (CT066) Showing That the Crack Growth Plane Is ~0.5-1.5 mm 

into the Alloy 152M ...........................................................................................5-5

Figure 5-7 Polished and Etched Side-Grooves of the Alloy 152M/CS Fusion Line 

Specimen (CT082) Showing That the Crack Growth Plane Is ~0.5-1 mm 

into the A516 CS...............................................................................................5-5

Figure 5-8 Polished and Etched Side-Grooves of the Alloy 52M/CS Fusion Line 

Specimen (CT083) Showing That the Geometric Crack Growth Plane 

Starts on the Fusion Line and Drifts ~0.4 mm into the A516 CS........................5-6

Figure 5-9 SEM-BSE Image Highlighting the Microstructure in the Alloy 152 – LAS 

Dilution Zone of the ANL V2 Alloy 152 DM Weld...............................................5-6

Figure 5-10 SEM-EDS Composition Maps from the Area near Aligned Grain Boundary 

#1 .....................................................................................................................5-7

Figure 5-11 SEM-EDS Composition Maps from the Area near Aligned Grain Boundary 

#2 .....................................................................................................................5-7

Figure 5-12 Optical Image Showing the Location of the Alloy 152 - LAS Dilution Zone 

CT Specimens (CT117 and CT119). Alloy 152 Weld Metal in Upper 

Portion Is Heat WC04F6 and in Lower Portion Is Heat 146444.........................5-8

Figure 5-13 Macro Images of the Alloy 152v2 DZ CT117 Specimen ....................................5-9

Figure 5-14 Macro Images of the Alloy 152v2 DZ CT119 Specimen ....................................5-9

Figure 5-15 Polished and Etched Side-Grooves of the ANL 152v2 Specimen CT119........ 5-10

Figure 5-16 SEM-EDS Elemental Maps of Fe-K on Side-Grooves of the ANL 152v2 

Specimen CT119 ............................................................................................ 5-10

Figure 5-17 Polished and Etched Side-Grooves of the ANL 152v2 Specimen CT117........ 5-11

Figure 5-18 Etched Cross-Section Slice from the EPRI Temper Bead DM Repair 

Weld, Measured Hardness Maps and CT Specimen Layout Positions Are 

Superimposed in the Bottom Image. The Alloy 52M – LAS Dilution Zone 

Specimen CT136 Is on the Right .................................................................... 5-12

Figure 5-19 Polished and Etched Side-Grooves of the EPRI Temper Bead DM Repair 

Weld Specimen CT136 ................................................................................... 5-13

Figure 5-20 Highlighted Area of Fe Enrichment (and Cr depletion) Region 

Corresponding to the Presence of Two Aligned Grain Boundaries in the 

First Weld Pass of Side A for the EPRI Temper Bead DM Repair Weld 

Specimen CT136 ............................................................................................ 5-14

Figure 5-21 SEM-BSE Images and EDS Elemental Maps Showing the 52M/LAS 

Interface Ahead of the Notch in the Side A Side Groove for the CT136 

Specimen. Bottom Images Highlight the Local LOF Cracks ........................... 5-15
xxi

Figure 5-22 SEM-BSE Images and EDS Elemental Maps Showing the 52M/LAS 

Interface Ahead of the Notch in the Side B Side Groove for the CT136 

Specimen. Bottom Images Highlight the Local LOF Cracks ........................... 5-16

Figure 5-23 Overview of the Entire Test on the Two Alloy 152/304SS Fusion Line 

Specimens...................................................................................................... 5-17

Figure 5-24 Crack Growth During the First and Second Constant K Assessments of 

the Alloy 152/304SS Fusion Line Specimens (CT075 and CT076) ................. 5-19

Figure 5-25 Post-Test Optical Images of the Polished and Etched Side Grooves for 

the First Alloy 152/304SS Fusion Line Specimen (CT075). Approximate 

Locations for the Constant K or Constant Load Exposures Are Indicated 

by the Arrows.................................................................................................. 5-20

Figure 5-26 Post-Test Optical Images of the Polished and Etched Side Grooves for 

the Second Alloy 152/304SS Fusion Line Specimen (CT076). 

Approximate Locations During Constant K or Constant Load Exposures 

Are Indicated by the Arrows ............................................................................ 5-21

Figure 5-27 Optical Image of the Interior Crack Profile of the Alloy 152/304SS 

Specimen #1 (CT075)..................................................................................... 5-22

Figure 5-28 SEM-SE and EDS Elemental Maps of the Interior Crack Profile of the 

Alloy 152/304SS Specimen #2 (CT076).......................................................... 5-22

Figure 5-29 Optical Image of the Crack Surface of Alloy 152/304SS Fusion Line 

Specimen #1 (CT075)..................................................................................... 5-23

Figure 5-30 Optical Image of the Crack Surface of Alloy 152/304SS Fusion Line 

Specimen #2 (CT076)..................................................................................... 5-23

Figure 5-31 SEM-SE Montage of the Crack Surface of Alloy 152/304SS Fusion Line 

Specimen #2 (CT076) Illustrating TG Cracking Morphology............................ 5-24

Figure 5-32 SEM-SE Images of the Typical Crack Surface Regions of Alloy 

152/304SS Fusion Line Specimen #2 (CT076) Illustrating TG Cracking 

Morphology..................................................................................................... 5-24

Figure 5-33 Overview of the Entire SCC Test on the Alloy 52M/152M-CS Dilution 

Zone Specimens (CT065 and CT066)............................................................. 5-25

Figure 5-34 Crack Growth of the Alloy 52M/152M-CS Dilution Zone Specimens 

CT065 and CT066 During the Second SCC Assessment................................ 5-27

Figure 5-35 Post-Test Specimen Sectioning Plan for the Alloy 52M/152M-CS Dilution 

Zone Specimens CT065 and CT066............................................................... 5-27

Figure 5-36 SEM-BSE Images of the Side Grooves for the Alloy 52M-CS Dilution 

Zone Specimen (CT065) After SCC Testing ................................................... 5-28

Figure 5-37 SEM-EDS Fe Map of the Alloy 52M-CS Dilution Zone Specimen (CT065) 

Crack Profile Slice #5 Showing Composition in the Region Around the 

Crack .............................................................................................................. 5-28

Figure 5-38 SEM-BSE Image of the Inner Most Slice (#5) Cut from the Alloy 152M-CS 

Dilution Zone Specimen (CT066).................................................................... 5-29
xxii

Figure 5-39 Corresponding SEM-EDS Fe-K Map for the SEM-BSE Image in Figure 

5-38 of the Alloy 152M-CS Specimen (CT066). Locations of Constant K

or Constant Load Evaluations Are Indicated by the Arrows............................. 5-29

Figure 5-40 SEM-BSE Images of Slices #2 and #3 from the Alloy 152M-CS DZ 

Specimen. The Crack Can Be Seen to Intersect and Remain on the 

Fusion Line for a Short Distance in Both Slices............................................... 5-30

Figure 5-41 Optical Image of a ~6 mm Width of the Crack Growth Surface for the 

Alloy 152M-CS Specimen CT066. A Reconstruction of the Other Half Is 

Included Based on Crack Profile Exams ......................................................... 5-31

Figure 5-42 SEM-EBSD Analysis of the Alloy 152M-CS Specimen CT066 in the 

Region of the Fusion Line ............................................................................... 5-31

Figure 5-43 Map of Microhardness Measurements Across the CS – Alloy 152M 

Interface Region in Slice #5 from the Alloy 152-CS DM Weld Specimen 

CT066.KAPL 52M/152M-CS DM Weld Interface (CT082 and CT083)............. 5-32

Figure 5-44 Overview Crack Growth Plot of the Entire Test on the Alloy 152M/52M-CS 

Fusion Line Specimens (CT082 and CT083) .................................................. 5-33

Figure 5-45 Constant K Crack Growth Response at 36-40 MPa√m of the Alloy 

152M/52M-CS Fusion Line Specimens Before Application of a Prototypic 

PWHT............................................................................................................. 5-35

Figure 5-46 Constant K Crack Growth Response at 36-40 MPa√m of the Alloy 

152M/52M-CS Fusion Line Specimens After Application of a Prototypic 

PWHT............................................................................................................. 5-35

Figure 5-47 Optical (upper four) and SEM-BSE (bottom) Images Showing Cracking in 

the Alloy 152M-CS Specimen (CT082) That Is Primarily in the Alloy 152M..... 5-36

Figure 5-48 Collage of Optical Images of the Cracking in the Alloy 52M-CS Specimen 

(CT083) Revealing Cracking Either in the CS HAZ or on the Fusion Line ....... 5-37

Figure 5-49 Collage of SEM-BSE Images Comparing Microstructural Differences 

Between the PWHT alloy152M-CS CT082 Specimen and the Non-Heat 

Treated CT066 Specimen............................................................................... 5-38

Figure 5-50 Crack-Growth Response Reported for the Alloy 152/LAS Dilution Zone 

Specimen N152-LAS-11 with SCC Propagation Averaging ~1.4x10-10 m/s 

(1.4x10-7 mm/s) ............................................................................................... 5-40

Figure 5-51 Schematic Illustrating the Cross-Section of Face A of the ANL N152-LAS11 Dilution Zone CT. The Inner Portions of Section 11 and Section 22 

Were Analyzed by PNNL ................................................................................ 5-40

Figure 5-52 SEM-SE Micrographs of the Face A Crack-Growth Surface for the ANL 

N152-LAS-11 Specimen ................................................................................. 5-41

Figure 5-53 Crack-Growth Surface for the Alloy 152/LAS Dilution Zone Specimen 

N152-LAS-11.................................................................................................. 5-42

Figure 5-54 Higher Magnification SEM BSE Image of N152-LAS-11 Face A near 

Section 11 Showing the Cracking Morphology on or near the Fusion Line...... 5-42
xxiii

Figure 5-55 Comparison Between the SEM-BSE Crack Appearance on Face A and 

the Corresponding Cross Section View of the Crack on Section 11 (from 

Piece B). Cracking on or near the Fusion Line Is Between the Two Blue 

Arrows ............................................................................................................ 5-43

Figure 5-56 SEM-BSE Micrograph of Face A with Dotted Box Showing Where Higher 

Magnification Imaging Was Performed. The Dotted Line Is a Reminder of 

the Location of the Section 22 Cut .................................................................. 5-43

Figure 5-57 SEM-SE Micrographs of the Primary IGSCC Region on Face A Shown in 

Figure 5-56. Dashed Box Shows Where the Higher Magnification Image 

Was Taken in the Figure on the Right. Dashed Lines in the Figure on the 

Right Illustrate Examples of Grain Boundaries ................................................ 5-44

Figure 5-58 SEM (SE and BSE pairs) of Regions on the Face A Crack Growth Face 

Corresponding to Figures 5-56 and 5-57 Where IGSCC Cracking 

Occurred ......................................................................................................... 5-45

Figure 5-59 SEM-SE Image and Elemental Maps of an IGSCC Region on Face A 

Similar to That Shown in Figure 5-58 .............................................................. 5-46

Figure 5-60 SEM-BSE of a Cross-Section Through Crack-Growth Surface for the 

Alloy 152/LAS Dilution Zone Specimen N152-LAS-11 Revealing Etched 

Microstructure of the Dilution Zone. Lighter Regions in the Alloy 152 

Dilution Zone Indicate Fe-Rich, Cr-Depleted Areas......................................... 5-47

Figure 5-61 SEM-SE and Elemental Maps of EDS Region 1 in Figure 5-60. Dashed 

Lines Show the Extent of the Cross-Section. Elemental Indications 

Beyond the Dotted Lines Are Due to X-Ray Signals Detected from the 

Crack Growth Face Rather than the Cross Section......................................... 5-47

Figure 5-62 SEM EDS Composition Maps in the N152-LAS-11 Cross-Section in 

Figure 5-60 ..................................................................................................... 5-48

Figure 5-63 SEM-SE and SEM-EBSD IPF-Z Map Revealing Grain Structure in the 

Alloy 152 Dilution Zone and the Presence of Grain Boundaries Aligned 

with the Crack Growth Direction in the ANL N152-LAS-11 Specimen 

Cross-Section (see Figure 5-62) ..................................................................... 5-49

Figure 5-64 Overview Crack Growth Plot of the First Part for Test on the ANL Alloy 

152 - LAS Dilution Zone Specimen (CT117) ................................................... 5-50

Figure 5-65 First Evaluation of SCC Response at Constant K for Specimen CT117 .......... 5-52

Figure 5-66 Crack-Growth Response at Cycle + 24h Hold Loading for Specimen 

CT117............................................................................................................. 5-52

Figure 5-67 Fourth Evaluation of SCC Response at Constant K for Specimen CT117....... 5-53

Figure 5-68 Crack-Growth Response at Cycle + 24h Hold Loading for Specimen 

CT117............................................................................................................. 5-53

Figure 5-69 SEM-BSE Low Magnification Montage of the Crack in Side Groove A at 

mid Test.......................................................................................................... 5-56

Figure 5-70 SEM-BSE Higher Magnification Image of Leading Crack Region in Side 

Groove A (area from dashed yellow box in Figure 5-69). Considerable 

Secondary Cracking Can Be Seen in Pass #2 as Highlighted by Dashed 

Red Box.......................................................................................................... 5-56
xxiv

Figure 5-71 SEM-BSE Montage from Figure 5-70 and Corresponding EDS Elemental 

Maps of the Leading Crack Region in Side Groove A ..................................... 5-57

Figure 5-72 SEM-BSE Montage and Corresponding EDS Elemental Maps near the 

Weld Pass Boundary Behind the Leading Crack Region in Side Groove A..... 5-57

Figure 5-73 SEM-BSE Micrograph and Corresponding EDS Elemental Maps at a 

Region of Secondary Cracking Just Behind the Leading Crack Tip on 

Side A............................................................................................................. 5-58

Figure 5-74 SEM-EDS Fe-K Map of the Leading Crack and Crack-Tip Region from the 

Side Groove on Side A ................................................................................... 5-58

Figure 5-75 SEM-BSE Low Magnification Montage of the CT117 Side Groove on 

Side B............................................................................................................. 5-60

Figure 5-76 SEM-BSE High Magnification Montage Showing the Microstructural 

Feature Immediately Ahead of Crack Tip in Side Groove B ............................ 5-60

Figure 5-77 SEM-BSE Montage and Corresponding EDS Elemental Maps of the 

CT117 Leading Crack Region on Side B......................................................... 5-61

Figure 5-78 SEM-EDS Fe-K Map of the Leading Crack Region for CT117 Side B

(Figure 5-77)................................................................................................... 5-62

Figure 5-79 Overview Crack Growth Plot of Second Part for Test on the ANL Alloy

152 - LAS Dilution Zone Specimen CT117...................................................... 5-63

Figure 5-80 Evaluation of SCC Response After Specimen CT117 Restart and 

Transitioning ................................................................................................... 5-65

Figure 5-81 Crack-Growth Response at Cycle + 24 H Hold Loading Showing Distinct 

Jumps During Cycle and Decrease in Crack Length During Hold Time........... 5-65

Figure 5-82 Evaluation of SCC Response for Specimen CT117 Showing No Growth at 

Constant K...................................................................................................... 5-66

Figure 5-83 Crack-Growth Response at Cycle + 24 H Hold Loading at Higher K Level...... 5-66

Figure 5-84 Tenth and Final Evaluation of SCC Response at Higher K for Specimen 

CT117............................................................................................................. 5-67

Figure 5-85 Side Groove SEM-BSE Montages Showing the Overall Crack Path on 

Side A (top) and Side B (bottom) .................................................................... 5-69

Figure 5-86 Higher Magnification SEM/BSE Image from Side B Showing Crack Has 

Propagated into Weld Pass #2........................................................................ 5-69

Figure 5-87 Upper Image Is a SEM-BSE Montage Showing the Entire Crack Growth 

Surface and Lower Image Is a SEM-SE Montage Revealing the Cracking 

Morphology in the Dashed Red Box. Darker Contrast in the CrackGrowth Surface BSE Image Identifies Region Exposed to HighTemperature Water with Lighter Upper Area Opened by Fatigue in Air 

After the SCC Test.......................................................................................... 5-70
xxv 

Figure 5-88 SEM-BSE Images from Left to Right: (a) Side Groove A, (b) Side Surface 

Cross-Section, (c) Crack-Growth Surface Montage and (d) Right Side 

Groove B. The Dashed Line in the CGF Image Illustrates Approximate 

Location of the Boundary Between the Two Weld Passes. Darker 

Contrast in the Crack-Growth Surface Image Identifies Region Exposed 

to High-Temperature Water with Lighter Upper Area Opened by Fatigue 

in Air After the SCC Test................................................................................. 5-71

Figure 5-89 Upper SEM-SE Montage Maps the Entire Crack-Growth Surface Area 

and Identifies IG Regions That Are Surrounded by the Fine Dashed 

Yellow Lines. Two Typical IG Regions Are Highlighted by Orange and 

Light Blue Boxes in the Montage and Shown at Higher Magnification in 

the Lower Images ........................................................................................... 5-72

Figure 5-90 Characterization of the Cross-Section Sample off Side A of the Specimen 

CT117 Showing the Overall Crack Produced in Water (top image) and the 

Final Crack Path After It Propagated into Weld Pass #2 (below)..................... 5-73

Figure 5-91 SEM-BSE Image and EDS Elemental Maps of the Cross-Section Sample 

off Side A of the Specimen CT117 .................................................................. 5-74

Figure 5-92 Overview Crack Growth Plot of First Part for Test on the ANL Alloy 152 - 

LAS Dilution Zone Specimen (CT119) ............................................................ 5-75

Figure 5-93 Second Evaluation of SCC Response at Constant K Showing Slowing 

Growth with Time over 1200 Hours. Evidence for Ligament Formation 

and Unmeasured Crack Extension by DCPD Indicating Higher SCC 

Propagation Rate............................................................................................ 5-75

Figure 5-94 Crack Growth Response During Cycle + 24 h Hold Loading ........................... 5-77

Figure 5-95 Crack Growth Response During Cycle + 48 h Hold Loading ........................... 5-78

Figure 5-96 Crack Growth Response During Cycle + 12 h Hold Loading ........................... 5-78

Figure 5-97 Crack Growth Response for the 3rd Constant K Evaluation Showing Little 

or No Growth .................................................................................................. 5-79

Figure 5-98 SEM-BSE Images of Side Groove A (top) and Side Groove B (bottom) for 

Specimen CT119 After 6555 Hours of Testing ................................................ 5-80

Figure 5-99 Higher Magnification SEM-BSE Image of the Leading Crack Region in 

Side Groove A with Crack Tips Highlighted in Small Circles ........................... 5-81

Figure 5-100 Fine Cracks and Leading Crack Tips for the Side Groove B. Cracks Are 

Shown in Yellow with Apparent Grain Boundaries in Dashed Green 

Based on the Nb Composition Map................................................................. 5-81

Figure 5-101 Overview Crack Growth Plot of Second Part for CT119 Specimen Test.......... 5-83

Figure 5-102 Cyclic and Cycle + 2.5 h Hold Response After Restarting Specimen 

CT119............................................................................................................. 5-83

Figure 5-103 Post-Test Side Groove Images for Specimen CT119...................................... 5-84

Figure 5-104 Final Crack Tips in the LAS for CT119 in Side Grooves A (top) and B 

(bottom) .......................................................................................................... 5-84
xxvi 

Figure 5-105 Crack Path in Side Groove A Through Weld Pass #2 During Second Part 

of the Test on CT119 Along with EDS Composition Maps Showing No 

Significant Dilution in This Region................................................................... 5-85

Figure 5-106 Crack Path in Side Groove B Through Weld Pass #2 During Second Part 

of the Test on CT119 Along with EDS Composition Maps Showing No

Significant Dilution in This Region................................................................... 5-85

Figure 5-107 SEM-SE Montage Maps the Entire Crack-Growth Surface Area and 

Identifies IG Regions Outlined in Yellow ......................................................... 5-86

Figure 5-108 A Typical IG Region from Figure 5-107 (blue box), Bumpy Appearance 

Results from the Termination of Dendrite Packets at the Surface ................... 5-87

Figure 5-109 Overview Crack Growth Plot for Test on the EPRI Alloy 52M - LAS 

Interface and Dilution Zone Specimen (CT136) .............................................. 5-89

Figure 5-110 First Constant K Evaluation of SCC Response in the CT136 Specimen.......... 5-89

Figure 5-111 Cycle + 24 h Hold CGR Response in the CT136 Specimen............................ 5-90

Figure 5-112 Third Constant K Evaluation of SCC Response in the CT136 Specimen ........ 5-90

Figure 5-113 Optical Images Showing Cracking in CT136 Side Grooves After a Test 

Time of 5900 Hours. Crack Front Has Reached the LOF Defects (black 

arrows) at the LAS Interface on Both Sides and Small Cracks Appear to 

Extend to the End of the LAS Plateau............................................................. 5-91

Figure 5-114 Fourth Constant K Evaluation of SCC Response in the CT136 Specimen 

Immediately After Restart. Problems with Water Flow and Chemistry

Impacted DCPD Measurements and Corrective Action Was Taken at 

~6325 Hours ................................................................................................... 5-92

Figure 5-115 Fifth and Final Constant K Evaluation of SCC Response in the CT136 

Specimen........................................................................................................ 5-92

Figure 5-116 SEM-EBSD Pattern Quality Image Showing Crack Path Through the 

Weld Metal Microstructure (a) and the Corresponding SEM-BSE Image 

and EDS Compositional Maps (b) from This Region ....................................... 5-93

Figure 5-117 EBSD IPF Image of the Alloy 52M Microstructure Along the Crack Path in 

CT136............................................................................................................. 5-94

Figure 5-118 EBSD IPF Image and Local Misorientation Map of a Region Along the 

Crack Path. A Higher Magnification IPF Image of the Plateau Region Is 

Presented in Figure 5-119 Along with an EBSD Local Misorientation Map...... 5-94

Figure 5-119 EBSD IPF Image and Local Misorientation Map at the LOF Region in 

CT136............................................................................................................. 5-95

Figure 5-120 SEM-BSE Image of the Crack Path in CT136 with Regions Identified for 

Exams............................................................................................................. 5-96

Figure 5-121 SEM-BSE Images Showing the Crack Region 1 from Figure 5-120 at 

Increasing Magnifications Revealing Short Propagation Along a Grain 

Boundary off the Main TG Crack Tip............................................................... 5-96

Figure 5-122 SEM-BSE Images Showing the Crack Region 2 from Figure 5-120 Where 

the Crack Intersected the First Preexisting LOF Defect at the LAS 

Interface.......................................................................................................... 5-97
xxvii 

Figure 5-123 SEM-BSE Images Showing the Crack Region 3 from Figure 5-120 at 

Higher Magnifications Revealing Cracks in the Alloy 52M near the LAS 

Interface. Two Cracks Are Seen to Reach the Interface and Form Pit-like 

Corrosion into the LAS.................................................................................... 5-97

Figure 5-124 SEM-SE Image Montage Revealing the Crack Growth Surface Produced 

in Water for Specimen CT136. Two Islands of Primarily IG Cracking 

Were Observed in Pass #1 ............................................................................. 5-98

Figure 5-125 SEM-SE Image Highlighting One of the Two IG Islands Present on the 

CT136 Crack Growth Surface ......................................................................... 5-99

xxix

LIST OF TABLES

Table 2-1 Alloy 152, 152M, 52, 52M and 52MSS Weldments at PNNL ........................... 2-10

Table 2-2 Summary of PNNL SCC Tests on Alloy 152, 52 and 52M Weldments ............ 2-11

Table 3-1 Test Conditions and Corrected Specimen Response for MHI Alloy 152 

Specimen CT013 ..............................................................................................3-8

Table 3-2 Test Conditions and Corrected Response of MHI Specimens CT017 & 

CT018............................................................................................................. 3-16

Table 3-3 Data Summary for MHI 152 U-Groove Weld Specimen CT052....................... 3-18

Table 3-4 Data Summary for MHI 152 U-Groove Weld Specimen CT135....................... 3-23

Table 3-5 Composition of the Alloy 152 Heat WC04F6 Weld Filler Metal Used by 

ANL in Their Original (V1) and New (V2) Alloy 152 Weldments. Values 

Are in wt%....................................................................................................... 3-25

Table 3-6 SEM-EDS Measurements of ANL Weld Metal Composition, Values Are in 

wt%................................................................................................................. 3-26

Table 3-7 Summary of Test Conditions and Corrected Response for the ANL Alloy 

152v2 Weld Specimens CT049....................................................................... 3-34

Table 3-8 Summary of Measured Constant K CGRs for the CT049 Specimen................ 3-36

Table 3-9 Summary of CGR Indicators for the Test on CT049 at 360°C ......................... 3-50

Table 3-10 Estimated CGR During the Hold Phase of Cycle + Hold Loading 

Conditions for CT049 Tested at PNNL............................................................ 3-51

Table 3-11 Summary of CGR Indicators for the First GEG Test (C541) on ANL 152v2 

at 360°C.......................................................................................................... 3-55

Table 3-12 Estimated CGR During the Hold Phase of Cycle + Hold Loading 

Conditions of C541 Tested at GEG................................................................. 3-55

Table 3-13 Summary of CGR Indicators for the First ANL Test (N152-TS-1) on ANL 

152v2 at 320°C............................................................................................... 3-59

Table 3-14 Estimated CGR During the Hold Phase of Cycle + Hold Loading 

Conditions of N152-TS-1 Tested at ANL ......................................................... 3-59

Table 3-15 Summary of Test Conditions and Corrected Response for AREVA and 

MHI Alloy 52 Specimens CT024 & CT025 ...................................................... 3-66

Table 3-16 Summary of Test Conditions and Corrected Response for AREVA and 

MHI Alloy 52 Specimens CT032 & CT033 ...................................................... 3-74

Table 3-17 Corrected Data Summary for KAPL Alloy 52M Narrow Gap Weld 

Specimens CT042 and CT043 with Preexisting Weld Cracks ......................... 3-99

Table 3-18 Corrected Data Summary for SM Alloy 52MSS Narrow Weld Specimen 

CT050........................................................................................................... 3-106

Table 3-19 SCC Crack Growth Test Conditions for CT050 Showing the CGRs for 

Each Constant K Evaluation ......................................................................... 3-107
xxx 

Table 3-20 Weld and Specimen Information for Data Presented in Figures 3-128 to 

3-132 ............................................................................................................ 3-112

Table 4-1 Corrected Data Summary for Ringhals Alloy 52M/182 Overlay Specimens 

CT028 & CT029................................................................................................4-9

Table 4-2 Data Summary for Ringhals Alloy 52M/182 Overlay Specimens CT034 & 

CT035............................................................................................................. 4-16

Table 4-3 Corrected Data Summary for Ringhals Alloy 52M/82 Inlay Specimens #1 

and #2 (CT030 & CT031)................................................................................ 4-33

Table 5-1 Composition of the Alloy 152/152M/52M Used for the DM Welds .....................5-2

Table 5-2 Test Summary for MHI Alloy 152/304SS Weld Fusion Line Specimens 

CT075 and CT076 .......................................................................................... 5-18

Table 5-3 Test Summary for KAPL Alloy 52M/CS and Alloy 152M/CS Dilution Zone 

Specimens CT065 and CT066........................................................................ 5-26

Table 5-4 Test Summary for KAPL Alloy 152M/CS and Alloy 52M/CS Dilution Zone 

Specimens CT082 and CT083........................................................................ 5-34

Table 5-5 SEM EDS Area Scan Composition (wt%) Measurements from Figure 5-62 .... 5-48

Table 5-6 Data Summary for the First Part of the Test on the ANL Alloy 152 - LAS

Dilution Zone Specimen CT117 ...................................................................... 5-51

Table 5-7 Estimated Constant K SCC CGR for CT117 from Cycle+Hold Loading 

Data Using a 980s/20s Load Cycle ................................................................. 5-55

Table 5-8 Composition of Regions Near Crack Front (wt%) in Figure 5-74 ..................... 5-59

Table 5-9 Composition (wt%) near the Leading Crack Region on Side B (Figure 

5-78) ............................................................................................................... 5-62

Table 5-10 Data Summary for the Second Part of the Test on the ANL Alloy 152 - 

LAS Dilution Zone Specimen CT117............................................................... 5-64

Table 5-11 Estimated Constant K SCC CGR from Cycle + Hold Loading Data Using a 

980s/20s Load Cycle for the Second Part of the Test on CT117..................... 5-68

Table 5-12 Data Summary for the First Part of the Test on the ANL Alloy 152 - LAS 

Dilution Zone Specimen CT119 ...................................................................... 5-76

Table 5-13 Data Summary for the Second Part of the Test on the ANL Alloy 152 - 

LAS Dilution Zone Specimen CT119............................................................... 5-82

Table 5-14 Data Summary for the Test on the EPRI DM Repair Weld Specimen 

CT136............................................................................................................. 5-88
xxxi 

EXECUTIVE SUMMARY

Primary water stress-corrosion cracking (PWSCC) is a degradation mechanism that can affect 

pressure boundary components made of nickel-base alloys and their welds in pressurized water 

reactors (PWR). Fabrication and welding processes and especially weld repairs leave residual 

stresses that promote cracking in susceptible materials. Undetected PWSCC has led to reactor 

pressure boundary leaks and boric acid corrosion in nuclear power plants worldwide. 

PWSCC of high-chromium, nickel-base alloys has been evaluated in simulated pressurized 

water reactor environments. This report focuses on material characterizations and test results

for alloy 690 weld metals (alloy 152, 52 and 52M) conducted at PNNL over the last decade for 

NRC projects JCN N6007 and JCN N6925 as well as recent work under the EWA agreement 

NRC-HQ-25-14-D-0001, Task Order NRC-HQ-60-15-T-0008. Stress-corrosion crack-growth 

rates have been determined for 11 alloy 152/52/52M weld metal specimens, 4 alloy 52M/182 

overlay specimens, 2 alloy 52M/82 inlay specimens and 9 alloy 152/52M dissimilar metal (DM) 

weld specimens in simulated PWR primary water environments. Weld metal, overlay/inlay and 

DM dilution zone specimens were machined from industry mock ups to provide plantrepresentative materials for testing. Specimens have been tested for one alloy 152 weld, two 

alloy 52 welds and three alloy 52M welds. The overlay and the inlay specimens were prepared 

to propagate stress-corrosion cracks from the alloy 182 or 82 material into the more resistant 

alloy 52M. In all cases, crack extension was monitored in-situ by direct current potential drop 

(DCPD) with length resolution of about +1 μm making it possible to measure extremely low 

growth rates approaching 5x10-10 mm/s. Most SCC tests were performed at 360°C with a 

dissolved hydrogen concentration of 25 cc/kg, while environmental conditions were modified 

during a few experiments to evaluate the influence of temperature, water chemistry or 

electrochemical potential on propagation rates. In addition, low-temperature (~50°C) cracking 

behavior was examined for selected weld metal specimens.

This project has completed some of the first SCC crack-growth tests on alloys 152, 52 and 52M 

weld metals in PWR primary water and helped establish a basis for their SCC propagation 

behavior. Similar to the previous PNNL test results for the as-received alloy 690 materials, the 

high-chromium weld metals have consistently shown a high resistance to SCC. Several 

different weld mockup types have been tested including U-groove, V-groove, butt weld, and 

narrow gap welds. Unlike the thermally treated alloy 690 base metal, a higher degree of 

intergranular (IG) engagement is typically seen, but measured propagation rates have been 

≤1x10-8 mm with most being less than 2x10-9 mm at test temperatures from 325 to 360°C. 

Despite the higher degree of engagement, transitioning to SCC can be more challenging due to 

the interdendritic weld metal microstructure and large grain sizes making uniform IG 

engagement across the crack front difficult. Only a few weld metal specimens have exhibited 

significant crack propagation along grain boundaries during long-term tests suggesting an 

overall good resistance to IGSCC for the high-chromium weld metals. 

In an effort to improve IG engagement, limited testing has also been conducted at 50°C in PWR 

primary water. Hydrogen-induced IG crack growth and higher growth rates were promoted 

during cycling steps for an alloy 152 weld, but much smaller effects were seen for alloy 52 

welds. The environment-induced cracking at low temperature is believed to occur during 

dynamic straining, and much more experimentation is needed to properly assess this behavior. 

The influence of preexisting ductility-dip cracks on SCC response has also been evaluated in 

alloy 52M with preliminary results showing no enhancement of crack growth due to a low 

density of these preexisting defects. SCC tests were also performed on industry mockups for 
xxxii 

an alloy 52M/182 overlay and an alloy 52M/82 inlay. For both, initial SCC propagation rates in 

the lower-chromium layer (alloy 182 or 82) were less than expected with only partial IG 

engagement. Although the growth decreased significantly as the alloy 52M interface was 

reached, this was due to isolated IGSCC fingers intersecting the interface. A simple 

assessment of chromium concentration on growth rates through the interface region was not 

possible without a straight crack front.

Additional SCC data was generated for alloy 52M from the overlay and the inlay welds with the 

highest crack growth rate at constant stress intensity (K) in weld metals detected for the alloy 

52M overlay material. Final activities have focused on characterizations and SCC experiments 

on various DM welds including stainless steel to alloy 152, carbon steel to alloy 152/52 and low 

alloy steel to alloy 152/52M interface regions. Unique microstructures and microchemistries 

were developed in the weld metal dilution zones and local areas of IGSCC were detected within 

selected weld passes. However, overall sustained crack growth under constant K was not 

observed in the weld or along the interface for any of the DM weld specimens evaluated.

This report documents SCC results on a large number of alloy 690 weld metal mockups 

revealing low crack growth rates in 360°C simulated PWR primary water. In addition, 

specialized tests performed on alloy 52M overlay and inlay mockups supported very low SCC 

CGRs in the alloy 52M weld metal. Overall, these results support the excellent SCC resistance 

of the high Cr welds in the as-welded condition at PWR operating conditions.
xxxiii 

ACKNOWLEDGMENTS

The authors recognize support from PNNL staff for the research performed including Clyde 

Chamberlin and Anthony Guzman for optical metallography, and Ziqing Zhai for SCC 

discussions. The work was sponsored by the Office of Nuclear Regulatory Research, U.S. 

Nuclear Regulatory Commission (NRC) under EWA NRC-HQ-25-14-D-0001 entitled “Technical 

Assistance in Support of Agency Environmental and Reactor Programs” with Pacific Northwest 

National Laboratory. The specific task order for this work in the EWA is NRC-HQ-60-15-T-0008 

entitled “Technical Assistance for Primary Water Stress Corrosion Testing of Nickel-Base Alloys 

and Welds” with Margaret Audrain as the current project manager. In addition, some research 

conducted using prior NRC job codes is also included in this report. Many helpful discussions 

with NRC staff are recognized including Greg Oberson, Jay Collins, David Alley, Robert 

Tregoning, Eric Reichelt and Margaret Audrain. Pacific Northwest National Laboratory is 

operated by Battelle Memorial Institute for the U.S. Department of Energy.

xxxv 

ABBREVIATIONS AND ACRONYMS

ANL Argonne National Laboratory

APT atom probe tomography

ASTM American Society for Testing and Materials

ATEM analytical transmission electron microscopy

AW as welded

BSE backscatter electron

BWR boiling-water reactor

CIEMAT Energy Environmental and Technological Investigations Centre

CF cold forged

CGR crack-growth rate

CM carbide modified

CR cold rolled

CRDM control rod drive mechanism

CS carbon steel

CT compact tension

CW cold worked

DCPD direct current potential drop

DH dissolved hydrogen

DM dissimilar metal

DOE Department of Energy

DZ dilution zone

EBSD electron backscatter diffraction

ECP electrochemical potential

EDS energy-dispersive x-ray spectroscopy

ENSA Equipos Nucleares S.A.

EPRI Electric Power Research Institute

FIB focused ion beam

GEG General Electric Global

GTAW gas tungsten arc weld

H hydrogen

HAZ heat affected zone

HWC hydrogen water chemistry

IG intergranular

IGSCC intergranular stress corrosion cracking

INSS Institute of Nuclear Safety Systems, Incorporated

IPF inverse pole figure

K stress intensity factor

KAPL Knolls Atomic Power Laboratory

LAS low alloy steel
xxxvi 

LOCA loss of coolant accident

LOF lack of fusion

LWR light water reactor

MA mill annealed

MHI Mitsubishi Heavy Industries

MRP Materials Reliability Program

NG narrow groove

NRC U.S. Nuclear Regulatory Commission

PEELS parallel detection electron energy loss spectrometer

PNNL Pacific Northwest National Laboratory

PWR pressurized water reactor

PWHT post weld heat treatment

PWSCC primary water stress corrosion cracking

R load ratio (minimum/maximum)

RCS reactor coolant system

RPV reactor pressure vessel

SA solution annealed

SCC stress corrosion cracking

SE secondary electron

SEM scanning electron microscopy

SGB solidification grain boundary

SMAW shielded metal arc weld

SS stainless steel

SSGB sub-solidification grain boundary

STEM scanning transmission electron microscopy

TEM transmission electron microscopy

TG transgranular

TT thermally treated

TTZ transformation toughened zirconia

VG V-groove
1-1 

1 INTRODUCTION

Primary water stress corrosion cracking (PWSCC) is a degradation mechanism that can affect 

pressure boundary components made of nickel-base alloys and their welds in pressurized water 

reactors (PWRs). PWSCC preferentially occurs in components that operate at high 

temperatures and pressures. Fabrication and welding processes and especially weld repairs 

leave residual stresses that promote cracking in susceptible materials. The narrow cracks, 

which are often located in complex structures either within or adjacent to welds, are difficult to 

detect and characterize during in-service inspections. PWSCC that went undetected has led to 

reactor pressure boundary leaks and subsequent boric acid corrosion of low alloy steels at 

Arkansas Nuclear One-1 in 2001 and Davis-Besse in 2002. Extensive wastage of the DavisBesse reactor head could have resulted in a loss of coolant accident (LOCA) had reactor 

operation continued and the damage gone undetected. Circumferential cracks discovered in 

the V.C. Summer reactor coolant system (RCS) piping welds in 2000 and in pressurizer nozzle 

welds at Wolf Creek in 2006 have raised concerns that PWSCC in PWR piping also could result 

in a LOCA.

Increasingly, industry has utilized alloy 690 and associated weld metals alloys 52 and 152 in 

both replacement components and in mitigation methods including weld inlays and overlays. 

Alloy 690 has been used in steam generators since 1989 and more than 30 PWR replacement 

heads using alloys 690/152/52 have been placed into service. The high chromium nickel-base 

alloys have also been used in RCS piping, nozzles, and instrument penetrations. While the 

service history has been favorable, significant industry and international efforts are underway to 

characterize the PWSCC susceptibility of alloys 690/152/52. Initial results have been reported 

in document MRP-237 Rev. 1 [1] and Rev. 2 [2]. Although the issue of PWSCC susceptibility is 

being addressed by industry, the U.S. Nuclear Regulatory Commission (NRC) has sought to 

obtain PWSCC growth rates of these crack resistant alloys and assess mitigation methods to 

determine the validity and acceptability of licensee flaw analyses and to support regulatory 

inspection requirements. In order to be successful, an improved understanding of the complex 

interrelations between stresses in the affected components, material microstructure, and the 

aggressive nature of the PWR environment is necessary.

In the original testing program (JCN N6007), three test systems were assembled. Initial testing 

was conducted on 300-series stainless steels, alloy 600 and alloy 182 in BWR and PWR 

simulated water chemistries. The effect of cold work, electrochemical potential, stress intensity 

and temperature were examined, and the results obtained were in good agreement with 

previously reported data. While limited tests were also conducted on alloy 690 and its weld 

metals, testing of the higher chromium alloys was the focus of the follow-up project (JCN 

N6782) at PNNL and two additional test systems were constructed. At the beginning of this 

project, very few quantitative SCC growth rate measurements had been reported on alloy 690 

and even less on its weld metals. Additional SCC propagation data was (and still is) needed to 

define improvement factors for these materials when compared with alloy 600 and its 

weldments. One of the biggest challenges for quantitative measurements has been the difficulty 

in promoting and measuring SCC growth in the nickel-base, high-chromium materials. 

However, modern test systems, proper transitioning and considerable patience makes this 

possible for most alloys. 

The effects of material microstructure, cold work, stress intensity, water chemistry, temperature 

and electrochemical potential on PWSCC growth rates were investigated in the first two 

NUREG/CR reports (Volume 1 [3] and Volume 2 [4]) from this project. This was followed by a 
1-2

focused NUREG/CR report (Volume 3 [5]) dealing with SCC of cold-worked alloy 690. Crackgrowth rates were measured in 37 different alloy 690 specimens exposed to simulated PWR 

primary water environments and detailed relationships were established among the degree of 

cold work, hardness, strain distributions, material microstructure and SCC response. 

Quantifying the influence of cold work and material strength on PWSCC growth rates was an 

important aspect of this NUREG/CR along with an assessment of many different alloy 690 

product forms such as CRDM tubing, plate and bar materials.

The current Volume 4 report summarizes PNNL testing results completed by the end of 2016 on 

alloy 690 weld metals including alloys 152, 52 and its many variants. The higher strains 

associated with the welds and the weld metal complex microstructure provides more issues of 

concern. These higher chromium weld metals are also more susceptible to segregation and 

weld cracking including solidification cracking and ductility dip cracking. Finally, very little 

testing has been performed on dissimilar metal (DM) welds where complex compositions and 

microstructure can be produced at interfaces between Fe-bases alloys (e.g., low allow steel, 

carbon steel and stainless steels) and the high-Cr, Ni-base weld metal. Individual chapters will 

describe characterizations and SCC crack growth experiments for each of these interest areas: 

alloy 152/152M/52/52M/52MSS weld metals (Chapter 3), alloy 52M overlay and inlay welds 

(Chapter 4), and the interface regions in DM welds (Chapter 5). Results from 26 crack-growth 

tests on specimens from 16 different mockup welds are described in some detail and 

conclusions are made with respect to SCC susceptibility in these weldments. 
2-1 

2 SCC CRACK-GROWTH TEST SYSTEMS, TESTING APPROACH,

AND MATERIALS SELECTION 

The purposes of the crack-growth systems are to develop, control, and measure stress 

corrosion cracks under well-defined material and environmental conditions, and to ensure that 

the SCC growth rate response is reproducible and characteristic of the test conditions. 

Features expected in a good crack-growth system include active constant K load control, active 

temperature control, a sensitive crack length measurement apparatus, a recirculating hightemperature water system, control over all aspects of water chemistry, and continuous 

monitoring of all pertinent test parameters. The options for PNNL in creating a crack growth 

capability were for PNNL to design crack growth test systems, buy commercial systems, or copy 

a system at another research institute. It was determined very early in the previous program 

that the most advanced and reliable crack-growth systems in the world have been designed, 

developed, and run by Peter Andresen at General Electric Global Research (GEG). His crackgrowth systems have been copied to various degrees by research institutes and commercial 

companies throughout the world. The decision was made to work closely with Peter Andresen 

and GEG staff on a crack growth system design. In the process of building the systems, some 

design aspects were improved, and more up-to-date parts were chosen when advantageous. 

GEG has incorporated some of these improvements and newer parts into their systems.

2.1 Overview of SCC Crack-Growth Test Systems

The key components of these systems are: (1) a servo-electric load control system capable of 

holding constant load for very long periods of time, (2) a high-pressure piston pump to 

pressurize and flow water through the high-temperature loop, (3) an autoclave, (4) a custommade water board for water chemistry control, (5) a reversing DCPD system for crack length 

estimation, and (6) a continuous data acquisition system. Careful consideration went into the 

selection of each piece of equipment to optimize either test system control or test environment. 

Some of the most important optimizations were to: (1) make sure that all wetted components 

release no contamination into the water, (2) have a high water flow rate through the autoclave, 

(3) have uniform temperature through a large volume of the autoclave, (4) have consistent water 

pressure, (5) have highly accurate measurements of test environment (temperature, 

conductivity, pH, load, dissolved gas content), and (6) have a sensitive DCPD measurement 

system. Each of the subsystems will be discussed in further detail below.

The water flow design of the system is a loop within a loop as shown in Figure 2-1. One loop is 

at low pressure, and its purpose is to flow water through a water column where selected gases 

and ionic impurities are dissolved or injected into the water. A side stream is taken off this lowpressure loop and fed into a high-pressure piston pump. The large pressure pulses and flow 

surges created by the piston pump are dampened by the use of pulsation dampers both at the 

inlet and outlet of the pump. The high-pressure water flows into a regenerative heat exchanger 

where hot water leaving the autoclave is used to heat the incoming water. Just prior to the 

water entering the autoclave, the partially heated water is brought up to test temperature using a 

preheater. After the water flows through the heated autoclave, it goes back through the 

regenerative heat exchanger and then through a water cooler that brings the water back down 

to room temperature. The cooled water then passes through a back-pressure regulator and 

emerges at ~0.07 MPa (10 psi) of pressure. The water flows through a flow meter, a 

conductivity sensor, a mixed resin bed demineralizer, and is finally dumped back into the lowpressure chemistry control loop.
2-2

Figure 2-1 General Water Flow Diagram for PNNL SCC Crack-Growth Test Systems

Boron (B) and lithium (Li) levels for PWR water testing are controlled by pre-saturating the 

mixed resin bed demineralizer with boric acid and lithium hydroxide to specific levels that will 

result in tailored near-constant B and Li content in the water. There is some drift in the Li level 

in the water because it is singly ionized and is easily displaced from the demineralizer by more 

highly positively ionized species coming off the autoclave such as chromate. The displaced Li is 

removed by periodic partial replacement of water in the mixing loop with water having little or no 

Li (and some B). Boron and Li levels in the mixing loop are determined from measurements of 

water conductivity, pH, and temperature using pHSC4 software (obtained from Rick Eaker of 

Duke Power). Autoclave flow rate is held to at least 125 cc/min (approximately two autoclave 

exchanges per hour) to provide a consistent chemistry environment within the autoclave.
2-3 

Load is applied to a sample using a servo-electric motor attached to the test frame. The servoelectric motor is controlled using proprietary software from GEG. The servo-electric motor can 

provide a smooth cyclic loading sine wave up to about 3 Hz, allowing in-situ pre-cracking of a 

test sample. Using DCPD data, the GEG software can continuously adjust the servo-electric 

motor to provide constant K loading conditions. As shown in Figure 2-2, the load from the 

servo-electric motor is transmitted into the autoclave with a pullrod, and the sample is braced 

from above by a top plate and 4-bar linkage that transmits load to the baseplate of the autoclave 

which is bolted to the test frame.

Crack length is estimated using a reversing DCPD system developed by Peter Andresen of 

GEG. A sketch of the system is shown in Figure 2-3. As with all DC potential drop 

measurement systems a constant current is run though the sample, and the voltage across the 

crack plane is measured and converted into a crack length by means of an empirically derived

formula relating voltage to crack length. A referenced DCPD resistivity is monitored directly on 

the test specimen using a “back face” potential method developed at GEG. Using a solid-state 

polarity-reversing switch built into the current path, potential drop is measured in both a forward 

and reverse current flow condition. By measuring in both directions, the system eliminates 

contact voltages from the measurement.

Figure 2-2 Typical Crack-Growth-Rate Test Frame Loading System Used at PNNL
2-4

Figure 2-3 Schematic Diagram Illustrating the DCPD System to Measure Crack Length 

in Situ

The GEG software also controls the operation of the DCPD system and aggregates the data. 

Platinum wire is used for current and voltage feeds into the autoclave. For PWR water testing, 

segmented transformation toughened zirconia (TTZ) tubing is used to help prevent shorting of 

the Pt wires against other wires or any metal surfaces in the autoclave. Some crosstalk in the 

voltage wires occurs and is minimized by keeping the wires separated as far as reasonably 

possible from each other. In addition, the current wires are kept away from the voltage 

measurement wires. The sample is electrically insulated from the load train through a 

combination of ceramic spacers and sleeves. Spot welding is used to attach the platinum wires 

to a specimen. The spot weld locations are marked on the sample prior to inserting the sample 

into the load train.

The PNNL systems have the capability to monitor autoclave water outlet conductivity, mixing 

loop water conductivity, autoclave temperature, autoclave water flow rate, sample corrosion 

potential (via a ZrO2 insulated Cu/Cu2O reference electrode in the autoclave), dissolved oxygen, 

water pressure, DCPD current, and DCPD voltage. With the exception of water pressure and 

flow rate, these parameters are recorded in the test data file. Statistical information on 

temperature and current fluctuations are also recorded. Additionally, messages describing 

changes in test conditions and other issues are a permanent part of the data record.
2-5 

2.2 General SCC Crack-Growth Testing Approach and Issues

Although systems have been designed for both 1T and 0.5T CT specimens, the primary 

specimen geometry used in this project is the 0.5T CT with side grooves. The details of the 

specimen geometry are shown in Figure 2-4. Prior to loading a specimen in the autoclave, the 

sample thickness, notch depth and width values are all measured and recorded into the data 

record for the test. Using the sample dimensions and the yield strength of the specimen at the 

test temperature, in accordance with American Society for Testing and Materials (ASTM) E1681, an upper limit on the value of the stress intensity (K) is calculated using the formula:

 KK = σσyyyy�DD/11. 2222 (2.1)

where σys is the yield strength at the test temperature and D is the smallest of the specimen 

thickness, the remaining uncracked specimen width and the crack length. In the case of 

materials with large amounts of work hardening (defined as σUTS/σys > 1.3) such as annealed 

300-series stainless steels and nickel-base alloys, the average of the yield and ultimate stress is 

used in place of the yield stress as per ASTM guidelines.

After the sample dimensions are measured and spot-weld locations are marked on the sample, 

it is cleaned and inserted into a test system. Pre-cracking of a sample is done in-situ at the test 

temperature when a single specimen is being tested. Initial pre-cracking of two or more 

specimens mounted in-series is not possible in-situ because the length of time needed to 

nucleate a pre-crack is not consistent, so precracking two specimens in series would likely lead 

to specimens with different precrack lengths. The differing precrack lengths would make it 

impossible to maintain and control the K level in both specimens during and after pre-cracking. 

Thus, the approach for testing at PNNL is to nucleate a crack individually on each of the two 

specimens under fatigue in air1

, followed by continued precracking of the two samples loaded 

together in-situ. Crack transitioning steps are carefully selected to grow the pre-crack in hightemperature water using the following stages: (1) fatigue, (2) corrosion fatigue and (3) SCC. 

Typically, this means producing initial precracks of ~1 mm in air followed by an additional ~1 mm 

by cycling in-situ before transitioning to slow cyclic loading plus hold times to promote SCC. An 

Instron servohydraulic test frame is used to precrack CT specimens in air, and the same DCPD

electronics and system control software used for the crack-growth systems is also used for the 

Instron test frame.

 

1 Practically speaking, CT samples slated for testing in series could be individually precracked in-situ. However, this

would result in a significant increase in system set-up requirements, sample modifications, test time and expense. 

The initial precracking in air is now done without impacting the current operation of the available PNNL SCC test 

systems. This precracking is done under well-controlled conditions, and care is taken to make sure that samples, 

grips and other components are cleaned before testing.
2-6

Figure 2-4 Schematic Drawing of a 0.5T CT Specimen. Dimensions for 1T CT 

Specimens Are Approximately Double

The first step in pre-cracking is to cycle the sample at a relatively high frequency (1–20 Hz) with 

a large load ratio and Kmax less than the K level chosen for constant K. As the crack begins to 

grow from the notch, the load ratio and frequency are reduced while the Kmax value is increased.

By pre-cracking in this way, each pre-crack segment can grow beyond the plastic zone created 

by the previous segment. For all samples, cyclic loading steps at frequencies of 0.1 Hz down to 

0.001 Hz are performed in high-temperature water. The final phase involves crack transitioning 

by very slow cycling with a hold time ranging from 1 h to 24 h. This grows the crack beyond the 

pre-cracking plastic zone and allows the crack to transition from transgranular (TG) fatigue to 

the crack growth mechanism that occurs for that material under constant K conditions.

For materials such as cold-worked (CW) 316SS that crack readily in LWR environments, 

obtaining a steady crack growth rate (CGR) after transitioning to constant K can easily be 

accomplished by following a standard procedure. However, determining a constant K CGR in 

highly SCC-resistant materials such as alloy 690 and its welds is more challenging with the 

main focus on giving the crack adequate opportunity to become an engaged IG crack. For 

these materials, the use of alternate cyclic and cycle + hold loading conditions, including various 

load ratio (R) values and modified rise/fall times, are often employed prior to reaching constant 

K. Tests conducted at PNNL have shown that an R of 0.5 usually produces the best

engagement response, and in base metal materials, efforts are made to run the specimen under

slow continuous cycling for several grain dimensions prior to the onset of cycle + hold loading.

The much larger grain dimensions and more irregular shape of the grain boundaries in weld

metals makes transitioning to an engaged crack front even more challenging. If extremely slow

or inconsistent CGRs are observed, cyclic loading is typically restarted to move the crack

forward (ten microns to several hundred microns) and then retransition to constant K. This

retransitioning procedure may be performed several times. The constant K SCC response is
2-7 

judged on the response of the material to these multiple observations at constant K. 

Observation of the propagation rate under selected cyclic loading and hold time conditions is 

also used to judge the crack growth resistance of the material.

The ideal increment of crack length over which to measure a steady CGR would be several 

grain diameters. However in alloy 690 and its weld metals, this is often an extremely impractical 

goal that could take more than two years to achieve and so it is necessary to choose an 

increment based on factors related to accuracy and resolution in the DCPD crack length data 

trend. The most easily quantifiable factor is noise or scatter in the DCPD crack length data. 

Each PNNL crack growth system has slightly different noise levels. The best system at PNNL 

has a noise level of 1.0 μm peak-to-peak while the “worst” system has ~3 μm peak-to-peak 

noise. Noise creates uncertainty in the measurement. Uncertainty is greatest when only a few 

measurements are performed, but as the number of measurements is increased, an average 

value can be resolved along with statistics on the goodness of fit. This is equivalent to fitting a 

trend line through the data. As long as the noise remains random (e.g., the residuals in the 

curve fit remain random), trends in the data down to the noise level can be resolved. Other 

factors contributing to the uncertainty in trends in the data are related to environment, crack 

morphology effects, and resistivity drift of the material. Environmental parameters such as 

water temperature, water conductivity, and dissolved hydrogen have been found to affect crack 

length, and it is important to limit deviations in these parameters. All environmental parameters 

on PNNL crack growth systems that can lead to phantom changes in crack length are monitored 

and tightly controlled. The factor affecting crack length accuracy and resolution that is most 

difficult to control is crack morphology. DCPD is based on the notion that there is no electrical 

current conduction behind the crack front. In stress corrosion crack-growth testing (especially in 

PWSCC testing), it has been found that there is almost always some feature in the crack 

morphology that allows current conduction behind the crack front. The most easily identifiable 

feature is an uncracked ligament in the wake of a crack as shown in Figure 2-5. Electric current 

bridging across very closely spaced crack walls is also thought to contribute to conduction 

behind the crack front. These features cause underprediction of DCPD-measured crack length 

and reduce the sensitivity of the DCPD system to detecting movement of the crack front. Crack 

ligaments can also cause large steps in crack extension when they break. Uneven growth 

along the crack front also causes crack length underprediction and reduced sensitivity in the 

same way as ligaments behind the crack front. It is important to recognize that all these 

morphology effects do not cause falsely high CGRs, but instead lead to underprediction of crack 

extension. The only phenomenon that leads to a falsely high CGR is resistivity change that 

occurs in Ni-base alloys such as alloy 600 and alloy 690. It is a well-known phenomenon that 

the resistivity of these alloys will slowly increase with time when testing at PWSCC 

temperatures. Without compensation, resistivity drift will give the appearance of a slowly 

increasing crack length. It is typical to compensate for resistivity drift by monitoring the resistivity 

of a piece of unstressed reference coupon placed in the autoclave environment. The resistivity 

change of the test specimen is normalized to the resistivity of the reference coupon. Looking at 

all these factors in aggregate, the test systems at PNNL are designed with a sufficiently high 

data acquisition rate to allow trends in crack extension to be detected down to the noise level of 

the DCPD system as long as test conditions are tightly controlled and resistivity drift is properly 

factored into the crack length measurement. Effects of current conduction behind the crack 

front and uneven crack extension will produce CGRs that are lower than what are actually 

occurring, so any CGR that is detectable by DCPD is expected to be an underprediction of the 

actual rate. There has yet to be a test where CGR has been overpredicted.
2-8

Figure 2-5 Example of Large Uncracked Ligament Detected in the Wake of a Crack

2.3 Specific SCC Crack-Growth Testing Approach

Unless noted otherwise, experiments were conducted in simulated PWR primary water with 

2000 ppm B and 2 ppm Li. A prototypic simulated PWR primary water environment is 

considered to be 325°C with 29 cc/kg H2. Tests conducted early in the program were often 

done at this temperature and hydrogen concentration, however as the program progressed, the 

desire to better understand the crack growth response of alloy 690 and its welds eventually led 

to testing at 350°C, and then later at 360°C. Testing now is typically conducted at 360°C. 

Dissolved hydrogen (DH) concentration also evolved over the course of the program with most 

testing now done at DH concentrations that place the corrosion potential of the material on the 

Ni/NiO stability line where crack growth response is known to be greatest in alloy 600 and its 

weld metals. Limited testing was also performed at 50°C under primary water conditions. The 

K was controlled to a value of 30 MPa√m under most conditions, however high K values were 

often evaluated up to ~40 MPa√m near the end of many SCC CGR tests. Crack growth tests 

were performed with two specimens in series allowing a greater range of material conditions to 

be examined in a shorter period of time.

Specimens were first precracked in air and followed by further crack extension using aggressive 

cycling in high temperature water. A variety of loading conditions were used to attempt to 

transition from the TG precrack to an IGSCC crack front. Loading conditions included R values 

ranging from 0.5 to 0.9, the addition of hold times up to 24 h, and various “periodic unload” 

schemes with a symmetric or a sawtooth wave form (e.g., rapid unload followed by a slow 

reload). Based on the current work and tests on alloy 690, a final cycling step at 0.001 Hz with 

R = 0.5-0.7 was often used and followed by the addition of hold times before determining CGRs 

at constant K.

The response of the material during transitioning was assessed continuously by comparing 

current propagation rates to results from earlier tests. As the database of observed CGRs and 

accompanying crack surface morphologies from previous tests grew, higher propagation rates 

during transitioning (particularly during cycle + hold loading) could be identified. If a CGR during 
2-9 

transitioning was indicative of a non-engaged crack front, then the crack would often be retransitioned in an attempt to improve SCC engagement. For these SCC resistant alloys, several 

transitioning attempts were typically made before documenting constant K CGR response.

The general philosophy for assessing CGRs of alloy 690 and its weld metals is to first obtain 

baseline SCC behavior with the material in the expected plant thermomechanical treatment and 

then follow with tests on material in off-normal conditions. Testing typically begins in simulated 

PWR primary water environment, but at an elevated temperature and DH concentration at the

Ni/NiO stability line). In some tests, these conditions would eventually be followed by systematic 

variations in environmental conditions to assess the effects of parameters such as temperature, 

stress intensity and DH on the SCC response of these materials.

Most weld metals were tested in the as-welded condition with the crack plane aligned along the 

dendrite growth direction (often referred to as the T-S orientation in weldments). For one case, 

the influence of a post weld heat treatment was evaluated and testing is also underway on 4 

welds in the cold-forged condition with a reduction of 15% in thickness. The standard 

environmental condition for all tests has been 360°C simulated PWR primary water, however 

test temperature and hydrogen content has been varied to assess effects on crack growth 

response. With only five NRC test systems and test times ranging from 6 to 12 months, it has 

been challenging to study a wide range of welds even when testing two specimens in series.

From a testing perspective, several factors make determination of the IGSCC susceptibility of 

weldments particularly challenging. The first factor is that a relatively large amount of crack 

extension is required during transitioning to effectively sample the grain boundaries of the very 

large and elongated grains in these materials. A second factor is that these high-Cr welds 

appear to be resistant to IG growth in PWR primary water. This leads to a simultaneous need 

for aggressive cycling to sample grain boundaries in a reasonable time and gentle cycling to 

provide the best conditions for IG engagement. Our approach to dealing with these opposing 

requirements has been to frequently retransition and maintain gentle cycling conditions for long 

times. Another issue is that ligaments or contacts can form in these weld metals even when 

aggressive cycling is used during transitioning sequences. Not only can crack growth 

sometimes be slowed in the vicinity of these ligaments, but ligaments also affect the DCPDbased measurement of crack extension. The effect of ligament or contact formation during 

constant K crack growth has been assessed by observing the immediate crack growth response 

during cycling after constant K exposures. Ligaments or contacts that break will produce an 

initially high CGR for the given loading condition.

2.4 Materials Selection

Various alloy 152, 52 and 52M weld mockups have been obtained for SCC testing as part of this 

project. All of these materials were supplied by industry sources and were selected to represent 

industry practices of direct relevance to PWR service. In most cases, these mockups were 

produced specifically to qualify a welding approach to be used for plant replacement or repair. 

Alloy 152 and 52 U-groove welds produced by Mitsubishi Heavy Industries (MHI) were obtained 

from EPRI and were mockups for the pressure vessel head replacement at the Kewaunee plant. 

In addition, an alloy 52 butt weld was obtained from AREVA NP that was produced as part of a 

testing program. Alloy 52M and 152M welds were obtained from George Young at KAPL and 

supplied as part of an international cooperative program on alloy 690 led by EPRI and the NRC. 

Finally, alloy 52M/182 overlay and alloy 52M/82 inlay weld mockups produced by RinghalsVatenfall were obtained with the help of Pal Efsing. A brief description of the welds, their heat 
2-10

numbers, and compositions are listed in Table 2-1. Weld fabrication method differed for each of 

the weldments and available information will be provided in the following sections. 

Twenty-six SCC crack-growth tests on alloy 152/52/52M weldments were completed. Table 2-2

summarizes the various welds, specimen numbers and general test conditions for each of the 

weld metal tests. SCC results for these crack-growth tests will be described in detail along with 

characterizations of the welds.

Table 2-1 Alloy 152, 152M, 52, 52M and 52MSS Weldments at PNNL

Material - Source Heat Number and Description Weld Metal Composition, wt%

Alloy 152 – MHI Heat 307380, U-groove mock-up 

weld for Kewanee, 304SS plate

Ni-28.7Cr-9.1Fe-0.03C-3.6Mn-0.33Si0.15Al-0.12Ti-0.003S

(independent analysis)

Alloy 152-ANL V2 Dissimilar Metal Weld

ANL 152-IHI Butt Weld

Alloy 152M - KAPL

Heat WC83F8, V-groove dissimilar 

metal weld, carbon steel (CS) and 

316SS plate, no butter used on the 

CS and no PWHT applied

Ni-30.2Cr-8.7Fe-<0.005C-3.0Mn0.22Si-<0.01Al-0.03Ti-1.176Nb0.002S-0.03V (mill test report)

Alloy 52 – MHI

NX2686JK, MHI U-groove weld to 

304SS plate, mock-up for 

Kewaunee plant

Ni-29.1Cr-10.0Fe-0.024C-0.25Mn0.13Si-0.71Al-0.52Ti-0.01N2 

(standard comp)

Alloy 52M – KAPL Heat NX5285TK, High constraint, 

narrow groove weld, alloy 690 plate

Ni-30.0Cr-7.9Fe-0.026C-0.19Mn0.12Si-0.07Al-0.19Ti-3.83Mo-2.57Nb

(mill test report)

Alloy 52M – KAPL V groove weld

Alloy 52M- ENSA DPM 52M Butter

Alloy 52MSS-Special 

Metals

NX77W3UK, V-groove weld, alloy 

690 plate

Ni-29.9Cr-8.3Fe-0.014C-0.75Mn0.13Si-0.11Al-0.21Ti-0.81Nb+Ta

Alloy 52 – AREVA NP NX3926JK, Mockup butt weld, alloy 

690 plate

Ni-29.1Cr-10.0Fe-0.024C-0.25Mn0.13Si-0.71Al-0.52Ti-0.01N2

(standard comp.)

Alloy 52M – KAPL

Heat NX5285TK, V-groove 

dissimilar metal weld, carbon steel 

and 316SS plate

Ni-30.0Cr-7.9Fe-0.014C-0.75Mn0.13Si-0.11Al-0.21Ti-0.81Nb+Ta

(mill test report)

Alloy 52M - KAPL

Heat NX5285TK, Narrow groove 

weld with modified weld conditions 

to create hot cracks

Ni-30.0Cr-7.9Fe-0.014C-0.75Mn0.13Si-0.11Al-0.21Ti-0.81Nb+Ta

(mill test report)

52M - EPRI 52M Temper Bead Repair Weld

Alloy 52 - MHI U groove weld

Alloy 52M/182 Overlay 

- Ringhals

Mockup alloy 52M overlay on alloy 

690 plate with alloy 182 overlay

(heat numbers not available)

Ni-30.0Cr-8.4Fe-0.020C-0.81Mn0.03Si-0.10Al-0.21Ti-0.85Nb+Ta

(mill test report)

Alloy 52M/82 Inlay - 

Ringhals

Mockup alloy 52M inlay on alloy 82 

weld and A533 pipe

(heat numbers not available)

not available
2-11

Table 2-2 Summary of PNNL SCC Tests on Alloy 152, 52 and 52M Weldments

Specimen Material Test Description

Completion 

Date

CT013 Alloy 152 - MHI PWR Primary Water, alloy 152 4/07

CT017 Alloy 152 – MHI, as welded PWR Primary Water,

Temp effects, alloy 152 6/08

CT018 Alloy 152 – MHI, stress relieved PWR Primary Water,

Stress relief effects, alloy 152 6/08

CT024 Alloy 52 – AREVA, as welded PWR Primary Water, alloy 52 1/09

CT025 Alloy 52 – MHI, as welded PWR Primary Water, alloy 52 1/09

CT028 Alloy 52M on Alloy 182 overlay –

Ringhals

PWR Primary Water, alloy 182 

into 52M, alloy 52M 4/09

CT029 Alloy 52M on Alloy 182 overlay –

Ringhals

PWR Primary Water, alloy 182 

into 52M, alloy 52M 4/09

CT030 Alloy 52M on Alloy 82 inlay -

Ringhals

PWR Primary Water, alloy 82 

into 52M, alloy 52M 10/09

CT031 Alloy 52M on Alloy 82 inlay -

Ringhals

PWR Primary Water, alloy 82 

into 52M, alloy 52M 10/09

CT032 Alloy 52 – AREVA as welded PWR Primary Water, low temp 

on high temp CGR

10/09

CT033 Alloy 52 – MHI as welded PWR Primary Water, low temp 

on high temp CGR

10/09

CT034 Alloy 52M on Alloy 182 overlay –

Ringhals

PWR Primary Water, alloy 182 

into 52M, alloy 52M

10/09

CT035 Alloy 52M on Alloy 182 overlay –

Ringhals

PWR Primary Water, alloy 182 

into 52M, alloy 52M

2/10

CT040 Alloy 52M narrow gap weld -

KAPL PWR Primary water, alloy 52M 7/10

CT041 Alloy 52M V-groove weld - KAPL PWR Primary water, alloy 52M 7/10

CT042 Alloy 52M KAPL narrow gap 

weld with aligned hot cracks

PWR Primary Water, weld 

defects/cracks on SCC 7/10

CT043 Alloy 52M KAPL narrow gap 

weld with non-aligned hot cracks

PWR Primary Water, weld 

defects/cracks on SCC 7/10

CT049 Alloy 152 – As welded PWR Primary Water, alloy 152 1/11-11/11

CT050 Alloy 52MSS – As welded PWR Primary Water, 52MSS 1/11-11/11

CT051 Alloy 152 – AW+ 20%CF PWR Primary Water, effect of 

cold work 1/11-8/11

CT052 Alloy 152 – As welded PWR Primary Water, alloy 152 1/11-8/11

CT065 Alloy 52M/CS Interface dilution 

zone (no PWHT)

PWR Primary Water, CS 

interface 5/12

CT066 Alloy 152M/CS Interface dilution 

zone (no PWHT)

PWR Primary Water, CS 

interface 5/12

CT075 Alloy 152/SS Interface region PWR Primary Water, SS 

interface 1/12-1/13

CT076 Alloy 152/SS Interface region PWR Primary Water, SS 

interface 1/12-9/12

CT080 Alloy 152 – As welded PWR Primary Water, alloy 152 6/12-6/13

CT081 Alloy 52M – As welded PWR Primary Water, alloy 52M 6/12-6/13
2-12

Specimen Material Test Description

Completion 

Date

CT082 Alloy 152M/CS Interface dilution 

zone + PWHT

PWR Primary Water, CS 

interface 6/12-3/13

CT083 Alloy 52M/CS Interface dilution 

zone + PWHT

PWR Primary Water, CS 

interface 6/12-3/13

CT117 ANL Alloy 152/LAS interface PWR Primary Water, LAS 

interface 8/14-4/16

CT119 ANL Alloy 152/LAS interface PWR Primary Water, LAS 

interface 8/14-11/15

CT120 Alloy 52 – As welded PWR Primary Water, alloy 52 8/14-6/15

CT134 Alloy 52M repair weld PWR Primary Water, repair 

weld 9/15-11/16

CT135 Alloy 152 – As welded PWR Primary Water, alloy 152 9/15-5/16

CT136 Temper bead repair weld, 

52M/LAS interface

PWR Primary Water, LAS 

interface 11/15-11/16

CT137 Alloy 52M butter – As welded PWR Primary Water, alloy 52M 11/15-11/16

CT138 Alloy 52M butter – AW + 

15%CW

PWR Primary Water, effect of 

cold work 5/16-Ongoing

CT139 Alloy 52 – AW + 15%CF PWR Primary Water, effect of 

cold work 5/16-Ongoing

CT140 Alloy 152M – AW + 15%CF PWR Primary Water, effect of 

cold work 7/16-Ongoing

CT141 Alloy 152 – AW+15%CF PWR Primary Water, effect of 

cold work 7/16-Ongoing
3-1 

3 ALLOY 152/52/52M WELDS

3.1 Alloy 152 Welds

3.1.1 Early Tests on MHI Alloy 152 U-Groove Mockup Welds (CT013, CT017 and CT018) 

Initial weld metal SCC testing started with the alloy 152 mockup weld obtained from EPRI, 

which was produced for the Kewaunee reactor pressure vessel head replacement by MHI. It 

was made using 6.1 mm (2.4 in.) thick plates of 304SS butted together with a U-groove as 

shown in Figure 3-1. Alloy 152 (heat 307380) butter passes were applied to each half of the Ugroove (the ends of buttering were machined flat), and then the plates were welded together 

with alloy 152 (heat 307380). Both the buttering and the filler were applied by shielded metal 

arc welding (SMAW), of which the welding parameters for the alloy 152 SMAW filler material 

consisted of a deposition speed of 4-25 cm/min and a current of 95-145 A.

A portion of the weldment was sectioned at PNNL into 1.9 cm (0.75-in.) thick blocks (Figure 

3-2), and metallographically prepared to reveal the individual weld passes and the butter zone 

as shown, for example, in Figure 3-1. Sections C, D, and E indicated in Figure 3-2 were 

selected for fabricating CT samples. After polishing, these blanks were marked for machining 

so as to locate the end of the pre-crack in a single weld pass and enable >1 mm of growth in 

that weld pass. A close examination was made to select a weld pass where the dendrites would 

be as parallel as possible to the pre-crack. The machined notch from section C is shown in 

Figure 3-3. Crack growth testing was performed in the weld pass below the pass where the 

machined notch is located. The precrack was located in the same weld pass for sections C and 

D, but the slight microstructural variability in the weld along the length of the mockup meant that 

it was necessary to use a different weld pass for crack growth testing (moving one up) for

section E.

Figure 3-1 Optical Image of the MHI Alloy 152 Mockup Showing U-Groove Weld in 

Cross-Section

304SS 

plate

crack 

extending 

into 152 weld butt joint
3-2

Figure 3-2 Sectioning Diagram for the Alloy 152 Welded Block. End Sections X and G 

Are 1.3 cm Thick and Were Used for Metallographic Observations While 

Sections A-F Are 1.9 cm Thick and Were Used for CT Samples. There Is 

~7.6 cm of Welded Block in Front of Section “X”

Figure 3-3 Optical Micrograph of Section C Showing the Location of the Machined 

Notch. This Same Weld Pass Was Selected in Section D, While the One 

Just Above and to the Left Was Selected in Section E

Scanning electron microscopy (SEM) examinations were carried out in section X and revealed a 

standard solidification and sub-solidification grain boundaries (SGB and SSGB, respectively). 

Examples of these are seen in Figures 3-4 and 3-5. Based on SEM examination of the 

microstructure of the alloy 152 weld, the weld is composed of a mixture of a cellular and 

columnar dendritic structure with heavy precipitation on both the SGB and SSGBs. The 

backscatter electron (BSE) images of the dendrites in Figure 3-4 reveal a mottled contrast that 

Weld pass for SCC 

testing C, D

Weld pass for SCC 

testing E 
3-3 

is presumed to arise due to strain in the matrix. Carbides scattered throughout the dendrites 

show up as dark particles in the BSE images, whereas in the secondary electron (SE) images, 

the particles typically show up as bright particles because they are sticking out from the 

specimen surface. Some of the dendritic boundaries etched differently than the surrounding 

matrix, possibly due to either compositional changes or from precipitation on the boundaries. 

Perhaps the best method to illustrate the weld microstructure is by electron backscatter 

diffraction (EBSD) shown in Figure 3-5. Grain-to-grain orientation differences are highlighted 

identifying the elongated solidification grain boundaries.

Figure 3-4 SEM (BSE (a), SE (b,c)) Images Are Shown from the Alloy 152 Weld Metal 
3-4

Figure 3-5 SEM-EBSD Micrographs of CT052 Showing the Inverse Pole Figure (IPF)-X, 

IPF-Y, IPF-Z and Local Misorientation Map of the General Microstructure in 

the MHI Alloy 152 Weld

Additionally, electron dispersive spectroscopy (EDS) composition maps were made to elucidate 

compositional inhomogeneities in the structure, and identify the major second-phase particles. 

As seen in Figure 3-6, there is a slight amount of coring indicated in the Mn map. Coring 

profiles in the Fe map (not shown) were complementary to the Mn map. The primary particles 

identified were rich in Nb (likely NbC) and Ti-Al-rich particles (likely a Ti-Al-O). TEM sample 
3-5 

preparation of a SGB (Figure 3-7) and SSGBs (Figure 3-8) was performed, and subsequent 

STEM/EDS maps were collected of each. Analysis of SGBs (Figure 3-7) indicates small (15-25 

nm), semi-continuous Nb rich particles on the SGB as well as larger (100 nm), discontinuous Cr 

rich precipitates. Ti was not observed to be associated with the Nb carbides. On the SSGBs 

(Figure 3-8) large (100 nm), discontinuous Cr and Nb rich precipitates were observed on the 

boundaries. In this instance, Ti was observed to be associated with the Nb rich precipitation.

Figure 3-6 SEM-SE Micrograph Is Shown Along with Composition Maps for Mn, Nb 

and Al. The Mn Map Indicates a Slight Degree of Coring and the Other Two 

Maps Show the Locations of the Large NbC and the Ti-Al Particles in the 

Microstructure
3-6

Figure 3-7 An Example of a SGB That Shows a Single Large Cr-Carbide, with 

Numerous Smaller Nb Carbides Along the Boundary. In This Case, Ti Was 

Not Found Associated with the Nb Carbides

Figure 3-8 Compositional Maps Taken in STEM Mode Revealed That Both Cr- and NbRich Carbides Are Present on SSGBs. The Bottom Image Reveals That the 

Two Carbide Phases Can Sometimes Be Superimposed with Each Other. In 

This Example, Nb and Ti Were Associated with the Same Particles
3-7 

The welds were tested in the as-welded (AW) condition with the exception of one test that was 

performed on an MHI alloy 152 weld that had been given a low-alloy steel (LAS) stress relief

heat treatment of 610°C for 12 h followed by air cooling. High-resolution SEM examinations did 

not indicate any significant effect of the heat treatment on the precipitate microstructures. 

Orientation of the specimens relative to the weld is shown in Figure 3-9. Specimens were 

machined from the blanks to target the desired crack growth path aligned with the elongated 

solidification grain boundaries shown in Figure 3-5. 

Figure 3-9 Image of MHI Alloy 152 Weld Showing Positioning of 0.5T CT Specimens

The first SCC crack-growth test was performed on a single CT specimen (CT013) of the MHI 

alloy 152 in the as-welded condition. Crack extension and transitioning were done in 325°C 

PWR primary water by cyclic loading at decreasing frequencies, with an R value of 0.7 and a K 

of 30 MPa√m. After >500 h cycling at 0.001 Hz, hold times of 2.5 h and then 24 h were added 

as shown in Figure 3-10. Extremely low, but stable CGRs were observed under these 

conditions decreasing to 3x10-9 mm/s after ~1000 h for the 24 h hold. Constant K was 

established and the measured propagation rate gradually decreased to <5x10-10 mm/s over the 

next few months. After ~2200 h (3 months) at constant K, the test was ended. A summary 

table of test conditions and corrected specimen response for each test phase is shown in Table 

3-1. Post-test examination started by sectioning of the specimen to obtain a crack side surface 

profile and then fatiguing the other piece of the CT specimen to expose the crack growth 

surface. The crack profile in Figure 3-11 shows that the crack growth direction was not as well 

aligned with the dendrites as appeared when marking the blank to cut the CT specimen. 

Nevertheless, regions of IG growth were found on the crack growth surface shown in Figure 

3-12 during post-test examination. The SEM images indicate that the IG cracking is SGB. The 

IG growth appeared to begin during the cycle + hold steps and the final crack front was ~35% 

IG. Based on this degree of IG engagement, area-averaged propagation rates were determined 

and are reported in Figure 3-10. If only the maximum IG crack extension was considered, 

estimated local rates would be ~5X higher or ~1.5x10-9 mm/s at constant K.
3-8

Figure 3-10 Crack Growth Response of MHI Alloy 152 Specimen CT013 During 

Transitioning and Constant K Steps

Table 3-1 Test Conditions and Corrected Specimen Response for MHI Alloy 152 

Specimen CT013

Test 

Phase

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax 

(MPa√m)

Avg. 

CGR 

(mm/s)

Approx. 

Crack 

Extension 

(mm)

1 8.1 0.3 1 0 29 cc/kg H2 325 26 4.8E-05 0.936

2 4.4 0.5 1 0 29 cc/kg H2 325 30 3.3E-05 0.526

3 4.6 0.6 1 0 29 cc/kg H2 325 33 2.3E-05 0.361

4 6.8 0.7 1 0 29 cc/kg H2 325 33 1.4E-05 0.335

5 26 0.7 0.1 0 29 cc/kg H2 325 33 2.8E-06 0.289

6 161 0.7 0.01 0 29 cc/kg H2 325 34 6.0E-07 0.353

7 552 0.7 0.001 0 29 cc/kg H2 325 34 9.4E-08 0.171

8 520 0.7 0.001 2.5 29 cc/kg H2 325 34 2.0E-08 0.032

9 855 0.7 0.001 24 29 cc/kg H2 325 34 3.0E-09 0.010

10 2413 --- const --- 29 cc/kg H2 325 34 3E-10 0.004
3-9 

Figure 3-11 Side Surface Profile of MHI Alloy 152 Sample CT013 Showing Alignment of 

Crack Relative to Dendrite Structure

 

Figure 3-12 Crack Growth Surface of MHI Alloy 152 Specimen CT013. Optical Image on 

Left Reveals Local Areas of SCC Propagation and SEM Images on Right 

Illustrate IG Morphology
3-10

The next two alloy 152 specimens were tested in series with one in the as-welded condition 

(CT018) and one given a low alloy steel (LAS) stress-relief heat treatment (CT017). Overall 

crack growth response is shown in Figure 3-13 with testing performed both at 350°C and at 

50°C. Unlike the CT013 test, shorter transitioning intervals were used with more emphasis on 

sampling the response of the material at several different regions in each specimen and on 

trying different methods to obtain a more engaged IG crack front. The transitioning conditions 

used in the first region of the specimen were identical to those in the first test on the MHI alloy 

152 (CT013) with the exception of shorter duration. The initial crack growth during cycle + hold 

and constant K steps was essentially identical to that observed in the previous test (specimen 

CT013) as shown in Figure 3-14. Stable propagation rates were measured, and slowed to 

extremely low values under constant K conditions (<5x10-10 mm/s). A second region of the 

alloy 152 microstructure was then evaluated by extending the crack ~0.4 mm in both samples 

by moderate cycling.

Figure 3-13 Overall Crack Growth Response of MHI Alloy 152 Specimens CT017 & 

CT018
3-11

Figure 3-14 Constant K Crack Growth Response of MHI Alloy 152 Specimens CT017 & 

CT018 at 30 MPa√m.

An alternate SCC transitioning approach was then used with sawtooth waveforms during cycling 

with R = 0.5, a 12 s unload, and increasingly longer reload time ranging from 300 s to 1000 s. 

After ~100 μm of growth with the 1000 s reload time, the R value was then changed to 0.7 and a 

2.5 h hold was added. Over ~200 h, the CGR was observed to slowly decrease to a rate below 

1x10-8 mm/s as shown in Figure 3-15. The load cycle was then converted from a sawtooth 

waveform to a 0.001 Hz symmetric waveform while maintaining the same 2.5 h hold time and R 

value of 0.7. As shown in Figure 3-15, no change in propagation rate occurred upon converting 

to the symmetric waveform, and the CGR of ~6x10-9 mm/s was slightly less than that observed 

when this same cycle + hold condition was used earlier in the test. Since no SCC enhancement 

was indicated during the cycle + hold loading, it was decided to investigate the crack growth 

response at a higher K of 40 MPa√m. This was done for both specimens by extending the 

crack 0.4 mm using cyclic loading (0.01 Hz, R=0.6) and a dK/da value of 100 MPa√m/mm. 

Based on post-test correction of the crack length, the actual K value was ~48 MPa√m after the 

dK/da transition. After switching to 0.001 Hz (symmetric waveform) and an R of 0.7, 

propagation rates were evaluated after adding a 2.5 h hold and finally during constant K as 

shown in Figure 3-16. CGRs were 3-4X higher than seen at lower K levels with values of 1.7- 

2.1x10-8 mm/s and 1.0-1.7x10-9 mm/s for the cycle + hold and constant K conditions, 

respectively.
3-12

Figure 3-15 Crack Growth Response During Cyclic Loading Conditions of MHI Alloy 

152 Specimens CT017 & CT018 in the Second Microstructural Region 

Examined

Figure 3-16 Constant K Crack Growth Response of MHI Alloy 152 Specimens CT017 & 

CT018 at ~48 MPa√m
3-13

The final stage of the test examined crack-growth response at 50°C while maintaining PWR 

primary water chemistry conditions, including a dissolved hydrogen content of 29 cc/kg. After 

extending the crack ~1 mm by cycling at 0.01 Hz, transitioning and constant K steps were 

performed as shown in Figure 3-17. The CGRs during cyclic and cycle + hold loading were 

found to be ~2-3X greater than rates observed at 350°C at the same K value and cycling 

conditions. However when the test was converted to constant K, the crack in both specimens 

ceased growing entirely, and when cyclic loading conditions were re-established, crack growth 

resumed. The test was later converted to constant K again with no crack advance. This 

suggests that dynamic strain during cycling is required for environment-assisted propagation at 

this low temperature.

One of the characteristic features of the crack growth response at 50°C was a relatively large 

systematic variation in the DCPD-measured crack length during low frequency cyclic loading. 

To better assess the cause of this, the DCPD response was examined in detail during cycle + 

hold loading conditions as shown in Figure 3-18. Large spikes in the DCPD-measured crack 

length were found to occur at the onset of each load cycle with the crack length decaying rapidly 

to a value slightly higher than existed prior to the load cycle. The spikes in the crack extension 

are clearly not a real phenomenon, but each load cycle does produce a small increment in crack 

length. The lack of growth during the hold time is consistent with the constant K response. It is 

thought that the spikes in crack length are due to the formation (during constant K loading) and 

destruction (during cycling) of “conducting” bridges behind the crack front. These bridges may 

form in the crack wake due to the electrochemical conditions of the PWR primary water at 50°C 

where Ni metal is stable. Enhanced electronic conduction across the crack will result in DCPD 

underestimating the actual crack length. Dynamic deformation during load cycling is apparently 

sufficient to break the bridges resulting in an immediate increase in DCPD-measured crack 

length. However, the bridges across the crack quickly re-form once the cycle is complete.

As a final phase of the test, the air fatigue CGR at 50°C of these specimens was measured and 

found to be 3-4X lower than in PWR primary water at the same temperature, further 

demonstrating that propagation at 50°C was an environment-assisted process. A summary of 

test conditions and corrected response of both specimens for each phase of the entire test is 

shown in Table 3-2. The specimens were then fatigue fractured in air to expose the crack 

growth surfaces. An optical image highlighting the crack growth surface created during high 

temperature testing is shown in Figure 3-19. Lines on the surface separate different phases of 

the tests. Regions of IGSCC are apparent, especially at the final high temperature crack front 

with the higher K level. SEM images in Figure 3-20 better illustrate the degree of IG 

engagement with the final crack front at 350°C having about 40% IG engagement. Somewhat 

surprisingly, more than 90% IG engagement was found to occur during the crack growth testing 

at 50°C. This IG growth is consistent with the higher CGRs observed during cycling loading of 

the specimens at 50°C in water.
3-14

Figure 3-17 Crack Growth Response of MHI Alloy 152 Specimens CT017 & CT018 at 

50°C in Simulated PWR Primary Water

Figure 3-18 Detailed Plot Showing DCPD Measured Crack Growth Response During 

Cycle + Hold Loading Conditions at 50°C in MHI Alloy 152 Specimen CT017
3-15

Figure 3-19 Optical Image of High Temperature Crack Growth Surface of the MHI Alloy 

152 Specimen CT017
3-16

Table 3-2 Test Conditions and Corrected Response of MHI Specimens CT017 & 

CT018

CT017 MHI Alloy 152

Blank D - LAS Stress Relief

CT018 MHI Alloy 152

Blank E - As Welded

Test 

Phase

Duration

(h) R Freq (Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax

(MPa√m)

CGR 

(mm/s)

Approx. 

Crack 

Ext. 

(mm)

Kmax

(MPa√m)

CGR 

(mm/s)

Approx. 

Crack 

Ext. 

(mm)

1 ~3 0.3 3 0 air precrack RT 25 9.3E-05 0.40 25 8.4E-05 0.40

2 ~2 0.5 3 0 air precrack RT 28 7.3E-05 0.35 29 6.1E-05 0.35

3 ~2 0.6 3 0 air precrack RT 30 5.2E-05 0.35 31 4.3E-05 0.35

4 ~3 0.7 3 0 air precrack RT 31 2.7E-05 0.20 31 2.0E-05 0.20

5 79 0.7 0.1 0 29 cc/kg H2 325 31 1.6E-06 0.398 32 2.4E-06 0.589

6 227 0.7 0.01 0 29 cc/kg H2 325 31 3.0E-07 0.264 33 4.3E-07 0.346

7 795 0.7 0.001 0 29 cc/kg H2 325 31 5.8E-08 0.155 33 5.7E-08 0.169

8a 822 0.7 0.001 2.5 29 cc/kg H2 325 31 7.0E-09 0.021 33 7.0E-09 0.023

8b 686 0.7 0.001 2.5 29 cc/kg H2 350 31 6.2E-09 0.017 33 7.6E-09 0.019

9 633 0.7 0.001 24 29 cc/kg H2 350 31 1.4E-09 0.006 33 1.5E-09 0.007

10 726 --- const K --- 29 cc/kg H2 350 31 4E-10 0.001 33 3E-10 <0.001

11 15 0.5 0.1 0 29 cc/kg H2 350 32 9.2E-06 0.337 34 1.1E-05 0.396

12 66 0.5 0.01 0 29 cc/kg H2 350 32 1.6E-06 0.414 35 1.8E-06 0.464

13 55 0.5 300s/12s 0 29 cc/kg H2 350 33 8.5E-07 0.167 35 8.3E-07 0.162

14 112 0.5 600s/12s 0 29 cc/kg H2 350 33 4.7E-07 0.175 35 4.1E-07 0.160

15 97 0.5 1000s/12s 0 29 cc/kg H2 350 33 2.9E-07 0.106 36 3.0E-07 0.103

16 190 0.7 1000s/12s 2.5 29 cc/kg H2 350 33 7.9E-09 0.007 36 8.4E-09 0.008

17 225 0.7 0.001 2.5 29 cc/kg H2 350 33 7.9E-09 0.006 36 8.4E-09 0.008

18 80 0.6 0.01 0 29 cc/kg H2 350 33->46 1.4E-06 0.562 36->49 1.3E-06 0.466

19 84 0.65 0.001 0 29 cc/kg H2 350 46 2.8E-07 0.090 49 2.4E-07 0.074

20 69 0.7 0.001 0 29 cc/kg H2 350 46 1.8E-07 0.048 49 1.8E-07 0.046

21 200 0.7 0.001 2.5 29 cc/kg H2 350 46 2.4E-08 0.015 49 3.1E-08 0.021

22 923 --- const K --- 29 cc/kg H2 350 46 1.4E-09 0.004 49 1.0E-09 0.006

23 89 --- const K --- 29 cc/kg H2 100 37 no growth --- 39 no growth ---

24 151 --- const K --- 29 cc/kg H2 50 37 no growth --- 39 no growth ---

25 39 0.5 0.01 0 29 cc/kg H2 50 49 5.7E-06 0.711 53 6.5E-06 0.865

26 59 0.5 0.001 0 29 cc/kg H2 50 50 6.5E-07 0.139 55 8.8E-07 0.189

27 116 0.5 0.001 2.5 29 cc/kg H2 50 50 1.3E-07 0.009 55 1.2E-07 0.016

28 100 0.7 0.001 2.5 29 cc/kg H2 50 50 1.3E-07 0.031 55 1.2E-07 0.026

29 142 --- const K --- 29 cc/kg H2 50 50 no growth --- 55 no growth ---

30 337 0.7 0.001 2.5 29 cc/kg H2 50 50 5.4E-08 0.110 55 5.1E-08 0.108

31 339 0.9 0.001 2.5 29 cc/kg H2 50 50 1.2E-08 0.018 56 6.0E-09 0.015

32 208 0.7 0.001 2.5 29 cc/kg H2 50 51 2.0E-08 0.011 56 1.6E-08 0.017

33 197 0.7 0.001 2.5 air 50 51 1.1E-08 0.028 56 6.3E-09 0.015

34 122 0.5 0.01 0 air 50 51 8.0E-07 0.381 57 8.5E-07 0.402

35 191 0.5 0.001 0 air 50 52 8.3E-08 0.064 57 8.9E-08 0.065

36 146 0.5 0.001 2.5 air 50 52 8.2E-09 0.006 57 9.2E-09 0.005

37 112 0.7 0.001 2.5 air 50 52 1.2E-08 0.002 57 1.3E-09 0.001
3-17

Figure 3-20 SEM Images of 350°C and 50°C Crack Growth Surfaces in MHI Alloy 152 

Specimen CT018

3.1.2 More Recent Tests on MHI Alloy 152 U-Groove Mockup Welds (CT052, CT135) 

Two additional specimens have been tested from the MHI alloy 152 U-groove weld with both as 

companions to more important controlling specimens. The first specimen CT052 was tested in 

series with a 20%CF alloy 152 specimen (CT051, reviewed in Chapter 5) where high CGRs 

were observed and limited the detailed evaluation of the as-welded CT052. The overall test 

summary for CT052 is listed in Table 3-3 and a slightly decreasing K value was obtained during 

the test driven by the faster crack growth in the cold-worked companion specimen. 

Transitioning was performed based on the CT051 specimen response and SCC response was 

assessed in step 15 under constant K loading. Crack growth behavior is documented in Figure 

3-21 with a relatively stable (albeit a bit noisy) CGR of 2.6x10-9 mm/s. This is consistent with 

previous observations for the MHI alloy 152 weld metal described above.

The decision was made to remove this specimen and continue testing on the 20%CF specimen 

alone. Post-test characterizations were limited due to the short exposure of this specimen. An 

optical image in Figure 3-22 shows the initial air precrack (~1.3 mm) angled slightly upward 

followed by the crack growth in water (~0.5 mm). In addition, this region was examined by 

EBSD (lower images in Figure 3-22) and reveals TG cracking at the cross-section location. This 

TG crack is documented by SEM at higher magnifications as presented in Figure 3-23. 

~40% IGSCC

engagement at 350°C

>90% IG

engagement at 

50°C
3-18

Penetrative oxidation off the crack walls can be seen to the crack tip. Finally, the crack-growth 

surface is presented in Figure 3-24 showing the short crack extension in water from the air 

precrack. No detailed analysis was performed to determine if any significant IG cracking was 

present.

Table 3-3 Data Summary for MHI 152 U-Groove Weld Specimen CT052

Test 

Phase

Start 

(h)

Duration

(h) R 

Freq 

(Hz)

Hold 

(h)

Water 

Chem. (cc 

H2 / kg)

Temp 

(°C)

Kmax 

(MPa√m)

CGR 

(mm/s)

Approx. 

Crack 

Extension 

(mm)

1 --- ~3 0.3 5 0 air 

precrack RT 21 --- 0.40

2 --- ~2 0.5 5 0 air 

precrack RT 23 --- 0.35

3 --- ~2 0.6 5 0 air 

precrack RT 25 --- 0.35

4 --- ~3 0.7 5 0 air 

precrack RT 25 --- 0.20

5 0 6 0.5 0.1 0 25 360 29 6.8E-06 0.121

6 6 50 0.5 0.01 0 25 360 29 1.3E-06 0.214

7 56 201 0.5 0.001 0 25 360 29 1.8E-07 0.117

8 257 45 0.5 0.01 0 25 360 28 4.1E-07 0.075

9 302 3 0.5 0.1 0 25 360 28 3.1E-06 0.027

10 306 12 0.5 0.01 0 25 360 28 4.2E-07 0.019

11 318 113 0.5 0.001 0 25 360 27 5.0E-08 0.022

12 431 160 0.5 0.001 2.5 25 360 27 9.3E-09 0.010

13 590 153 0.5 0.001 1 25 360 27 7.8E-09 0.002

14 743 158 0.5 0.001 2.5 25 360 27 3.7E-09 0.004

15 901 362 --- const K --- 25 360 27 2.6E-09 0.004

16 1263 297 0.5 0.001 1 25 360 27 3.9E-09 0.001

17 1560 208 0.5 0.001 2.5 25 360 27 2.1E-09 0.001
3-19

Figure 3-21 Crack Growth Response During Constant K Loading for Specimen CT052

Figure 3-22 Optical (top) and SEM-EBSD (bottom) Micrographs of CT052 Cross-Section 

Showing the IPF-Y and Local Misorientation Map of the Crack from the 

Specimen Notch (left edge in top image, top center in bottom images)
3-20

Figure 3-23 SEM-BSE Images from the CT052 Cross-Section Highlighting the TG CrackTip Region and Illustrating Oxidation at the Crack Walls to the Final Tip
3-21

Figure 3-24 Optical Image of the Crack-Growth Surface on MHI Alloy 152 Specimen 

CT052

A final specimen (CT135) from the MHI alloy 152 U-groove weld was more recently tested in 

series with the EPRI alloy 52M repair weld specimen (CT134). Once again, the companion 

CT134 was the controlling specimen and testing steps were determined based on its response. 

The key difference for the CT135 specimen is that SCC response was investigated in the L-S 

orientation, while all the prior tests (CT013, CT017, CT018 and CT052) were performed in the 

T-S orientation. This modified orientation is illustrated in Figure 3-25 and it is important to note 

that the crack path is again aligned with the elongated solidification grain boundaries.

The testing sequence and response is summarized in Table 3-4, revealing that constant K 

behavior was evaluated twice along with a variety of cycle + hold loadings during transitioning. 

An early indication of limited SCC engagement was discovered during a 24h hold time as 

illustrated in Figure 3-26. Subsequent cycle + hold CGRs suggested an improved SCC 

response and constant K behavior was evaluated at two different K levels (33 and 38 MPa√m) 

as shown in Figure 3-27. In both attempts, the SCC propagation rate slowed with time at 

constant K and reached a value of 2-3x10-9 mm/s. 
3-22

Figure 3-25 MHI Alloy 152 U-Groove Weld Showing the Standard T-S CT Specimen 

Orientation and Alternate L-S Orientation. For Both, the Target Crack Patch 

Is Aligned to the Long Axis of the Grains

Figure 3-26 Measured Crack Growth During Cycle + 24h Hold Loading for CT135
3-23

Table 3-4 Data Summary for MHI 152 U-Groove Weld Specimen CT135

Test 

Step 

Start 

(h) 

Duration

(h) R 

Freq 

(Hz)

Hold 

(h) 

Water 

Chem. 

(cc H2 / 

kg)

Temp 

(°C) 

Kmax 

(MPa√m)

CGR 

(mm/s)

Approx. 

Crack 

Extension 

(mm)

1 0 6 0.5 0.1 0 25 360 31 9.5E-06 0.236

2 6 28 0.5 0.01 0 25 360 31 2.0E-06 0.220

3 34 306 0.5 980s/20s 0 25 360 32 2.9E-07 0.323

4 340 668 0.5 980s/20s 2.5 25 360 32 3.2E-08 0.084

5 1008 635 0.5 980s/20s 24 25 360 32 4.6E-09 0.013

6 1643 182 0.5 980s/20s 2.5 25 360 32 2.2E-08 0.011

7 1825 394 0.5 980s/20s 0 25 360 33 3.1E-07 0.452

8 2219 137 0.5 980s/20s 2.5 25 360 33 4.5E-08 0.033

9 2356 618 --- const K --- 25 360 33 3.2E-09 0.008

10 2974 227 0.5 980s/20s 2.5 25 360 33 3.2E-08 0.027

11 3201 87 0.5 980s/20s 0 25 360 34 2.8E-07 0.084

12 3288 151 0.5 280/20s 0 25 360 35 9.8E-07 0.580

13 3439 190 0.5 980s/20s 2.5 25 360 36 4.2E-07 0.265

14 3629 210 0 980s/20s 2.5 25 360 36 6.5E-08 0.057

15 3839 264 0.5 980s/20s 24 25 360 36 1.1E-08 0.009

16 4103 159 0.5 980s/20s 0 25 360 38 7.5E-07 0.390

17 4262 95 0.5 980s/20s 2.5 25 360 38 8.0E-08 0.028

18a 4357 123 --- const K --- 25 360 38 4.4E-09 0.002

18b 4480 453 --- const K --- 25 360 38 2.3E-09 0.003

19 4930 120 0.5 980s/20s 2.5 25 360 38 6.5E-08 0.025
3-24

Figure 3-27 Measured SCC Growth Rates During Constant K Loading for CT135 at Two 

K Levels: 33 MPa√m (Upper) and 38.5 MPa√m (Lower)
3-25

3.1.3 ANL 152V2 DM Weld (CT049, CT080)

Material and Specimens

The composition of the alloy 152 heat WC04F6 weld filler metal used by ANL in their original, as 

well as in their new, alloy 152 weldment is listed in Table 3-5. PNNL received slices from the 

new (second) weldment, and it is referred here as the alloy 152 v2 weld. A diagram provided by 

ANL of the intended weldment geometry and weld-pass buildup plan is shown in Figure 3-28. It 

is a double bevel weld that joins alloy 690 to A533 steel. In preparation for the joint weld, the 

A533 steel plate was buttered with three layers of alloy 152 (not heat WC04F6), and this 

buttered A533 plate was given a post-weld heat treatment at 621°C for 3 hours. Due to limited 

quantities of heat WC04F6 weld filler metal, only a portion of the joint was fabricated using this 

filler metal. The remaining weld passes were made from two other heats of alloy 152. SCC 

testing at PNNL was confined to weld passes made from heat WC04F6.

As part of test preparation and during post-test analysis of the specimens, a variety of 

characterizations were carried out in the region of the WC04F6 weld passes. A rough polish 

and etch was first applied to the entire weldment as shown in 

Figure 3-29. Since SCC susceptibility often scales with material strength, microhardness 

mapping was performed on the weldment. As shown in Figure 3-30, Vickers hardness was 

found to vary from ~200-260 kg/mm2

. In comparison, microhardness measurements on nonCW alloy 690TT, 17%CR alloy 690TT and 31%CR alloy 690TT yielded average values of 175, 

240 and 300 kg/mm2

, respectively. Next, a variety of optical and SEM examinations were 

performed to characterize boundary structures and compositional variations within the 

weldment. Measured compositions by SEM-EDS are listed in Table 3-6 and were similar 

between the two welds using the WC04F6 filler. 

Figure 3-31 shows grain boundaries and dendrite boundaries using optical differential imaging 

contrast, BSE imaging and EBSD. Both high angle and low angle grain boundaries were 

apparent and exhibited different contrast in EBSD imaging while optical imaging tended to 

detect only SGBs. SEM-BSE imaging did not clearly distinguish between high and low angle 

grain boundaries, but tended to most clearly show the SSGBs. 

Table 3-5 Composition of the Alloy 152 Heat WC04F6 Weld Filler Metal Used by ANL 

in Their Original (V1) and New (V2) Alloy 152 Weldments. Values Are in 

wt%

Heat Cr Fe Mn C Si Nb+Ti Al Ti P S 

WC04F6 28.7 10.4 3.5 0.048 0.41 1.54 0.06 0.09 0.003 0.003
3-26

Table 3-6 SEM-EDS Measurements of ANL Weld Metal Composition, Values Are in 

wt%

Sample/Region Ni Cr Fe Mn Nb Si Al Ti Mo Cu

Large Area Scan

(0.75 x 0.5 mm2) 

New V2 Weld

53.40 29.21 9.88 4.32 2.06 0.61 0.21 0.10 0.11 0.09

Large Area Scan

Old V1 Weld 53.95 28.86 9.88 4.15 1.95 0.61 0.32 0.09 0.11 0.09

Average Grains

New V2 Weld 53.38 29.04 9.87 4.35 2.13 0.63 0.23 0.11 0.15 0.13

Average Grains

Old V1 Weld 53.85 28.94 9.72 4.20 2.16 0.63 0.24 0.11 0.11 0.03

Figure 3-28 Weld Buildup Plan for the ANL Alloy 152v2 Weldment Fabricated Using 

Alloy 152 Heat WC04F6. PNNL Has Been Using the Name "Alloy 152 V2" 

for This Weldment

Figure 3-29 Optical Macro Image of a Weld Slice Taken from the ANL Alloy 152v2 

Weldment. Note That the Weld Orientation Is Flipped from Drawing in 

Figure 3-28

A533 steel alloy 690 
3-27

 

Figure 3-30 Microhardness Indent Pattern and Resulting Hardness Map for the Macro 

Slice of the WC04F6 Weld Region

Figure 3-31 Comparison of SGB and SSGB Structures of the Alloy 152 V2 Weldment 

Using Optical Imaging (top), SEM-BSE Imaging (middle), and EBSD Pattern 

Quality Map (bottom)

Both lower (Figure 3-32) and higher (Figure 3-33) magnification SEM-EDS imaging of spatial 

elemental distributions was performed. The low magnification images indicate variations in Mn 

and Nb content consistent with the size and shape of the dendritic fingers. These EDS maps 

also showed a low density of Al- and Ti-containing particles dispersed throughout the matrix. 
3-28

Higher magnification images revealed Nb- and Cr-rich carbides of the order of 50-100 nm 

decorating high-angle grain boundaries, while only NbC was found on the dendritic boundaries. 

These elemental distributions are similar to other alloy 152 weldments that have been 

characterized at PNNL.

Figure 3-32 Low Magnification SEM-EDS Maps Provide an Overview of Composition 

Variations in the ANL Alloy 152 V2 Weldment. SEM-BSE Image in the 

Upper Left Shows the Grain and Dendrite Structure
3-29

Figure 3-33 a) SEM-BSE Image Where Heavier Elements Produce Higher Brightness. 

Bright Precipitates Decorating SGBs and SSGBs Are NbC. Black Dot 

Contrast Is Polishing Debris. b) Higher Magnification SEM-BSE and EDS 

Images Showing NbC and Cr23C6 Carbides Decorating a Grain Boundary

Stress-corrosion crack growth tests were performed on 0.5T compact tension (CT) specimens 

with the orientation of the two specimens relative to the weld slices shown in Figure 3-34. Care 

was taken to position the geometric crack plane of each specimen parallel to the long axis of the 

weld grain boundaries because this was perceived to be the most susceptible crack path. The 

first specimen (CT049) was oriented to assess the SCC susceptibility of the third layer of weld 

passes from the alloy 152 butter on the LAS, while the second specimen (CT080) was 

positioned to assess the second layer of weld passes from the butter. The notch and precrack 

were positioned so that SCC evaluations would be made on weld pass regions of higher 

hardness (220-260 kg/mm2 as shown in Figure 3-30). Detailed three-dimensional EBSD 

characterization of the grain structure was performed on specimen CT049 after testing. These 

results are shown here in Figures 3-35 and 3-36, and reveal that the grains have an overall 

acicular shape with an aspect ratio of roughly 5:1. The Test Plane A images in Figure 3-36

show ~200 μm sized grains with complex grain boundary shapes while the other images 

indicate that the long grain dimensions range from ~500 μm to >2000 μm. Many grains have 

been observed to run continuously from one weld pass to a neighboring weld pass. This 

combination of relatively large grains and complex grain shape is thought to represent a very 

tortuous IG cracking mode that cannot be easily maintained under crack-growth testing 

conditions. 

After specimen fabrication, the specimen side grooves were polished and etched to indicate the 

level of success in specimen positioning within the weldment and also to give an idea of the 

microstructure sampled during SCC testing. Images of the side grooves for the two specimens 

are shown in Figure 3-37 (CT049) and Figure 3-38 (CT080). In both cases, the specimens 

appear to be well aligned with the grain boundaries.

GB

SEM-BSE

NbC

a b

SEM-BSE

Cr23C6

GB
3-30

Figure 3-34 Locations of the 0.5T CT Specimens Extracted from Two Different Slices of 

the Alloy 152 V2 Weldment. Image on the Left Is for the First Test (CT049), 

While the Image on the Right Is for the Second Test (CT080). Both 

Specimens Were Oriented to Align the Elongated Grain Boundaries with 

the Geometric Crack Path and Within a Region of Higher Hardness 

Indicated in Figure 3-30

Figure 3-35 EBSD Inverse Pole Figures Illustrating the Grain Structure in the Alloy 152 

V2 Specimen CT049 Specimen as Viewed from the Face of the Specimen
3-31

Figure 3-36 EBSD Inverse Pole Figures Illustrating the 3D Grain Structure in the ANL 

Alloy 152 V2 Specimen CT049 Specimen as Viewed from the End of the 

Specimen (Test Plane A) or on the Geometric Crack Plane (Test Plane B). 

The Z-Axis Is Normal to the Face of the Specimen

Y

X

Y

X
3-32

Figure 3-37 Optical Images of the Polished and Etched Side Grooves for the First 

Specimen (CT049) Cut from the ANL Alloy 152 V2 Weldment. Grain Shape 

Is Highly Variable, but Based on These Side-Groove Observations the 

Geometric Crack Path Is Well Aligned with the Grain Boundaries of the 

Elongated Grains

Figure 3-38 Optical Images of the Polished and Etched Side Grooves for the First 

Specimen (CT049) Cut from the ANL Alloy 152 V2 Weldment. Grain Shape 

Is Highly Variable, but Based on These Side-Groove Observations the 

Geometric Crack Path Is Well Aligned with the Grain Boundaries of the 

Elongated Grains

PWSCC Testing of Alloy 152 v2 Weld Specimen #1 (CT049)

An overview of the entire SCC test is summarized in Table 3-8 and in Figure 3-39. This test 

was conducted in 360°C primary water with a target K of 30 MPa√m, and five constant K 
3-33

evaluations were performed. DCPD underestimated the actual crack length in this test resulting 

in actual K values that were up to 30% higher than the target value. The approach to this test 

was to evaluate SCC response in five separated microstructural regions. In each transitioning 

sequence, a different set of transitioning conditions (cyclic and cycle + hold loading) was used 

to attempt to promote IG engagement along the crack front prior to converting the test to 

constant K. The degree of IG engagement was determined from optical and SEM images of the 

crack growth surface after the test was completed (shown later), and the estimated percent 

engagement values are reported in Figure 3-39 where it can be compared to the crack position. 

Approximately 50% IG engagement was achieved at the onset of gentle cycling (estimated to be 

at 0.001 Hz) during the first transitioning sequence and was maintained over ~0.5 mm of crack 

extension during the first and second transitioning sequences. More aggressive cyclic loading 

conditions at the onset of the third transitioning sequence (at 2500 h) reduced engagement to 

~20% IG, and this fraction increased during the fourth and fifth transitioning sequences to 

~60%. The transitioning approaches for CT049 can be roughly grouped into two categories. 

Transitioning sequences #1-4 attempted to produce IG engagement using cyclic loading 

frequencies of ~0.001 Hz (using rise/fall times of 500s/500s, 980s/20s, 600s/12s, or 1000s/12s) 

at R = 0.5 with the addition of hold times, while transitioning sequence #5 attempts to produce 

IG engagement through slower continuous cycling down to much lower frequencies (5000s/12s 

and 25000s/12s) but at a more aggressive R value of 0.35. The highest amount of IG 

engagement (60%) was achieved in the final transitioning sequence where low frequency 

continuous cycling at an R of 0.35 was used, however as much as 50% IG engagement was 

measured where more typical frequencies of ~0.001 Hz (R = 0.5) were used.

Initial constant K CGRs can be grouped into the two categories of <1x10-9 mm/s or 2-6x10-

9 mm/s. Examples of these behaviors can be found in Figures 3-40 and 3-41. All constant K 

CGRs eventually dropped to <1x10-9 mm/s. No clear correlation exists between constant K 

CGRs and the degree of IG engagement with very little (if any) SCC growth observed during the 

final constant K exposure (Figure 3-40). Response for the five SCC evaluations is summarized 

in Table 3-8. The possibility of contacts behind the crack front or fingered crack advance were 

masking the DCPD measurement during constant K testing was often assessed by applying 

gentle cyclic loading after constant K. In cases of significant masking of DCPD response during 

constant K, gentle cycling will immediately produce a CGR that is temporarily an order of 

magnitude higher than expected rates. Testing of the ANL 152 v2 material showed no such 

response with CGRs immediately matching the expected values, thus reinforcing the notion that 

little or no crack advance occurred during loading at constant K.
3-34

Table 3-7 Summary of Test Conditions and Corrected Response for the ANL Alloy 

152v2 Weld Specimens CT049

Test 

Phase

Duration

(h) R Freq (Hz) Hold 

(h)

Water Chem. 

Conditions

Temp 

(°C)

Kmax 

(MPa√m)

CGR 

(mm/s)

Approx. 

Crack Ext 

(mm)

1 ~3 0.3 5 0 air precrack RT 21 9.6E-05 0.40

2 ~2 0.5 5 0 air precrack RT 24 7.1E-05 0.35

3 ~2 0.6 5 0 air precrack RT 26 5.6E-05 0.35

4 ~3 0.7 5 0 air precrack RT 26 2.8E-05 0.20

5 8 0.5 0.1 0 25 cc/kg H2 360 32 1.2E-05 0.279

6 85 0.5 0.01 0 25 cc/kg H2 360 32 1.7E-06 0.540

7 258 0.5 0.001 0 25 cc/kg H2 360 33 3.2E-07 0.287

8 119 0.5 980/20 0 25 cc/kg H2 360 33 3.2E-07 0.129

9 480 0.5 0.001 2.5 25 cc/kg H2 360 33 4.2E-08 0.072

10 310 --- const K --- 25 cc/kg H2 360 33 4.3E-09 0.001

11 53 0.5 0.001 2.5 25 cc/kg H2 360 33 - - - 0.004

12 114 0.5 600/12 0 25 cc/kg H2 360 33 6.4E-07 0.222

13 220 0.5 600/12 1 25 cc/kg H2 360 33 8.6E-08 0.075

14 93 0.5 600/12 2 25 cc/kg H2 360 33 4.7E-08 0.020

15 367 0.5 600/12 1 25 cc/kg H2 360 33 9.2E-08 0.126

16 134 0.5 600/12 2 25 cc/kg H2 360 33 4.9E-08 0.020

17 267 --- const K --- 25 cc/kg H2 360 33 <5E-10 0.001

18 156 0.5 0.01 0 25 cc/kg H2 360 35 2.1E-06 1.095

19 65 0.5 0.001 0 25 cc/kg H2 360 35 2.8E-07 0.067

20 93 0.5 600/12 0 25 cc/kg H2 360 36 5.4E-07 0.168

21 76 --- const K --- 25 cc/kg H2 360 36 <5E-10 0.012

22 115 0.5 600/12 0 25 cc/kg H2 360 36 5.2E-07 0.203

23 172 0.5 1000/12 0 25 cc/kg H2 360 37 3.5E-07 0.218

24 213 0.5 1000/12 2 25 cc/kg H2 360 37 7.1E-08 0.048

25 380 0.5 1000/12 10 25 cc/kg H2 360 37 1.4E-08 0.019

26 611 --- const K --- 25 cc/kg H2 360 37 1.8E-09 0.004

27 116 0.5 600/12 0 25 cc/kg H2 360 37 4.6E-07 0.220

28 70 0.35 600/12 0 25 cc/kg H2 360 38 9.8E-07 0.248

29 95 0.35 1000/12 0 25 cc/kg H2 360 39 6.6E-07 0.221

30 240 0.35 5000/12 0 25 cc/kg H2 360 39 1.7E-07 0.150

31 348 0.35 25000/12 0 25 cc/kg H2 360 39 4.9E-08 0.058

32 240 0.35 25000/12 3.5 25 cc/kg H2 360 39 2.8E-08 0.026

33 849 --- const K --- 25 cc/kg H2 360 39 4.6E-10 0.002
3-35

Figure 3-39 Overview of the Entire Test of the First ANL Alloy 152v2 Weld Specimen 

(CT049) Performed in 360°C Simulated PWR Primary Water. Dashed Red 

Line Indicates the Percent IG Engagement

Figure 3-40 Crack Growth Response During the Second Constant K Evaluation of 

CT049 in 360°C Simulated PWR Primary Water. Stress Intensity Was ~33 

MPa√m
3-36

Figure 3-41 Measured Crack-Growth Response During the Fifth and Final Constant K 

Evaluation of CT049 in 360°C Simulated PWR Primary Water. Stress 

Intensity Was ~39 MPa√m

Table 3-8 Summary of Measured Constant K CGRs for the CT049 Specimen

Trans.

Sequence

Stress 

Intensity 

(MPa√m) % IG

Initial Const K 

CGR (mm/s)

Final Const 

K CGR 

(mm/s)

1 33 ~50 2.8x10-9 <1x10-9

2 33 ~50 5.6x10-9 <1x10-9

3 36 ~20 <1x10-9 <1x10-9

4 37 ~40 2.2x10-9 <1x10-9

5 39 ~60 <1x10-9 <1x10-9

After SCC testing, the specimen was first sliced into two, producing slices that were 4 and 8 mm 

thick. The thicker piece was fatigued open for crack growth surface examinations, while the 

thinner piece was used for crack profile examinations. An optical image of the crack surface 

from the thicker piece is shown in Figure 3-42. Yellow lines were drawn where distinct changes 

in crack surface appearance were observed. In this optical image, areas of higher IG 

engagement have a rougher appearance than TG regions. IG cracking is responsible for the 

protrusions along the final crack front.

Detailed mapping of the IG/TG cracking morphology was performed using SEM imaging. SEMSE images of regions within the four blue boxes in Figure 3-42 are shown in Figure 3-43. 

Significant amounts of IG cracking are present. The crenulated appearance clearly 
3-37

distinguishes IG from TG cracking (see also Figure 3-44). Comparison of such images to the 

optical images permitted measurement of the degree of IG engagement throughout the test. 

However, additional efforts were put into analysis of the final ~1.5 mm of crack extension by 

analyzing SEM-BSE and SE montages across the width of the surface as shown in Figure 3-45. 

Observations of the crack profile from the 4-mm-wide piece of CT049 are shown in Figures 3-46

and 3-47. In Figure 3-46, the air precrack can be clearly distinguished from the in-situ portion of 

the test. In this crack profile slice, the crack was entirely TG until the last ~1.4 mm, where it 

encountered and remained on a grain boundary. EBSD imaging shows that it is a high-angle 

grain boundary. The small branching cracks that formed near the final crack front are likely due 

to stresses driving the crack back down towards the geometric crack growth plane of the 

specimen. The final ~150 μm of IG crack extension shows nothing compositionally unique from 

SEM-EDS examinations (Figure 3-47). Major and minor elemental constituents appear 

compositionally similar to neighboring dendritic grain boundaries. 

A key aspect of the crack growth morphology is very long sections of IG extension, often 

exceeding 1.5 mm. These long amounts of IG extension were probably made possible by 

having the geometric crack growth plane of the specimen well aligned to the long grain 

boundaries of the weld metal microstructure. IG extensions of this length clearly indicate that 

some grain boundaries in this weld are susceptible to environment-assisted cracking under a 

variety of cyclic loading conditions. The loading conditions during the last 1.5 mm of testing 

ranged from constant K to somewhat aggressive cycling at 600s/12s (R = 0.5) and 1000s/12s 

(R = 0.35) showing that IG cracking will occur in this weld metal even under continuous cyclic 

loading. However, these observations also show that despite “easy” IG cracking along some 

grain boundaries, full IG engagement across the crack front was not achieved despite the 

application of a variety of gentle cyclic loading conditions over very long crack extensions. This 

suggests that grain shape and boundary orientation to the crack path play a significant role in IG 

propagation along with possible variations in grain boundary susceptibility.
3-38

Figure 3-42 Crack-Growth Surface Optical Image of the 8-mm Wide Section of the 

CT049 Specimen. Yellow Arrows Indicate Examples of IG Protrusions 

Along the Final Crack Front. Blue Boxes Indicate Regions of SEM 

Examinations Presented in Figure 3-43

Figure 3-43 SEM-SE Images of Regions Within the Blue Boxes in the Optical Image of 

the Entire Crack-Growth Surface for the CT049 Specimen (Figure 3-42)

A B

C

D
3-39

Figure 3-44 Higher Magnification SEM-SE Image Illustrating the IG Crack Surface 

Appearance in CT049

Figure 3-45 SEM-BSE (upper) and SE (lower) Images Showing IG Regions (blue tint) 

Along the Final ~1.5 mm of the SCC Test of CT049. Yellow Line Denotes 

the Final Crack Front at the Conclusion of the Test
3-40

Figure 3-46 Compilation of SEM-BSE, Optical, and EBSD Images Showing the Crack 

Path in Profile from Notch to Final Crack Front in a Side-Surface Cross 

Section from the CT049 Specimen

Figure 3-47 SEM-BSE and EDS Maps Showing Elemental Compositions Along the Final 

~150 μM of the CT049 Crack Profile

SEM BSE
3-41

With such long amounts of IG extension occurring over a wide range of testing conditions, a 

major challenge in assessing the SCC response of this material is determining what amount of 

crack advance occurred during constant K loading. DCPD clearly shows crack advance during 

cyclic and cycle + hold loading, but indicates very little (few μm) or no growth during constant K 

testing. The crack surface of this specimen contains extensive IG cracking and localized IG 

protrusions at the final crack front. At this point in time, a method to accurately isolate IG growth 

that occurs during constant K loading from what occurs during cyclic or cycle + hold loading has 

not been determined. On the possibility that some IGSCC is occurring during constant K that 

DCPD did not accurately capture, constant K CGRs were estimated from the IG protrusions 

along the final crack front. For this analysis, it was assumed that constant K IG extension is 

what occurred beyond TG tearing on either side of the IG cracking. This is illustrated in Figure 

3-48 for two extreme examples (these are two of the same images in Figure 3-43) where the 

white dashed line indicates the postulated start of constant K IG growth, and the white arrows 

indicate the maximum extension. Following this method on all the protrusions along the final 

crack front in Figure 3-45, engaged constant K CGRs were calculated to be as high as ~1x10-7

mm/s, however the majority of the measurements gave values closer to ~2x10-8 mm/s.

Figure 3-48 Illustration of Postulated Constant K IG Extension Along the Final Crack 

Front of CT049

It is important to recognize that while this analysis of the final crack front gives average constant 

K CGRs in the engaged regions of ~1-3x10-8 mm/s, the shape of the final crack front shows no 

indication of a tendency for the crack to become progressively more IG during constant K 

loading. The only constant K IG cracking that may have occurred was from regions that were 

already engaged prior to setting the test to constant K. In addition, the morphology of the 

engaged regions of the final crack front shows no indication of IG expansion or ballooning. 

Instead, the IG regions typically have a pointed shape suggesting that the degree of IG 

engagement was decreasing as time progressed. The same resistance to achieving very high 

degrees of IG engagement was also observed during crack transitioning. While 60% 

engagement is higher than any other alloy 152/52 weld metal specimen tested at PNNL, there is 

no indication that full engagement would have been achieved if the transitioning had continued 

for much longer periods of time. The torturous grain boundary shape of this material favors the 

assessment that only limited engagement is likely.

The inability to obtain >60% IG engagement during transitioning or obtain an increase in IG 

cracking during constant K loading is somewhat in contrast to the ease at which portions of the 

specimen transitioned to (and maintained) IG growth for several millimeters at mildly aggressive 
3-42

fatigue cycling conditions. The overall assessment of this specimen is that while significant IG 

crack advance is clearly possible, widespread sustained IGSCC is not.

PWSCC Testing of Alloy 152 v2 Weld Specimen #2 (CT080)

The observation of significant IG engagement, but with apparent low CGRs in the CT049 

specimen prompted the decision to run a second test on this weldment. As described in the 

experimental section, this specimen was located in a slightly different position. The CT080 

specimen was also rotated 180 degrees relative to CT049 so that cracking would progress 

towards the weld root rather than towards the crown. As with the first specimen, this one was 

again aligned parallel to the grain boundaries as best as possible (Figures 3-34 and 3-38). An 

overview of the entire DCPD-based crack growth response is shown in Figure 3-49. The first 

portion of the test was conducted under the same environmental conditions as the prior CT049 

test (360°C at the Ni/NiO oxide stability). Similar transitioning techniques were also applied in 

this first part of this test, i.e., progressively more gentle cycling leading to gentle cycle + hold 

loading before assessing constant K response. The first constant K assessment that was 

started at ~1950 h produced very low CGRs of <1x10-9 mm/s as shown in Figure 3-50. After 

~600 h at constant K, gentle cyclic loading was applied and produced typical CGRs for this 

loading condition, indicating that DCPD had not been masked by contact formation or fingered 

crack advance during constant K. The crack was then aggressively advanced to a new region 

where re-transitioning steps were started. CGRs during these transitioning steps were found to 

be identical to earlier in the test and similar to that in the prior test (CT049).

Having duplicated the crack-growth response during transitioning and constant K of the first test 

(360°C) based on in-situ DCPD, the environmental conditions and crack transitioning methods 

were altered to approximate those used by ANL on the two alloy 152 welds using the WC04F6 

weld filler metal. Thus, test temperature was reduced to 320°C and the dissolved hydrogen 

concentration shifted to 29 cc/kg in the Ni-metal stability regime. Common ANL transitioning 

methods use progressively more-gentle cyclic loading steps and hold times just like PNNL and 

many other SCC testing laboratories, however the particular cyclic waveforms are slightly 

different. ANL tends to favor a 600s/12s (R = 0.5) load cycle for their most gentle continuous 

cyclic loading condition for this material and test temperature, and the most common hold time 

is 2 hours. As part of their crack-growth assessment, ANL also occasionally uses a periodic 

partial unloading step that consists of a 12s/12s (R = 0.5) load cycle every 1 or 2 hours. Since 

in-situ constant K correction is not done at ANL, this feature was turned off as well, and K was 

allowed to increase with crack length and SCC was evaluated under constant load conditions. 

Lastly, ANL assesses CGR response during transitioning by comparing the in-situ 

environmental CGR to a calculated air CGR that is an empirical fit to air fatigue tests on alloy 

600, 182, and 690. Inputs into the air fatigue formula include K, load ratio and temperature. 

The ratio of the environment CGR to the calculated air fatigue CGR is used as a gauge for 

estimating the SCC engagement during transitioning. All these aspects of SCC testing were 

adopted for the second half of this test.
3-43

Figure 3-49 Overview of CGR Test on the Second Alloy 152 V2 Specimen (CT080) 

Performed in 360°C (0-3800 hours) and 320°C (3800-8000 Hours) Simulated 

PWR Primary Water. Terminal Constant K CGRs Are Listed

Figure 3-50 Constant K Crack Growth Response Following the First Transitioning 

Sequence on the Alloy 152 V2 Specimen CT080 in 360°C Simulated PWR 

Primary Water
3-44

During testing at 320°C, the CGR at 600s/12s (R = 0.5) cycling was frequently measured as 

suggested by the many small ramps in 320°C portion of the overview test plot (Figure 3-49). 

The env/air CGR ratio consistently hovered between 2-3 for 600s/12s continuous cycling 

transitioning steps, and the addition of a hold time tended to increase this ratio by ~10%. The 

env/air CGR ratios for the first transitioning sequence at 320°C are shown in Figure 3-51, where 

they are compared to env/air ratios measured during the two transitioning sequences at 360°C. 

These ratios at the first 320°C transitioning sequence are typical of those in later transitioning 

sequences at 320°C, and they are similar or slightly lower than the values determined at 360°C. 

Constant load SCC evaluations were made three times at 320°C with all evaluations producing 

CGRs that quickly dropped below 1x10-9 mm/s, as illustrated by the last attempt shown in Figure 

3-52. As with testing at 360°C, application of gentle cycling always showed no indication that

DCPD was being masked during constant load exposures.

Figure 3-51 Env/air Ratio During the First Three Transitioning Sequences (two at 360°C 

and one at 320°C) for the Second Test on the Alloy 152 V2 Weldment 

(CT080)
3-45

Figure 3-52 Third Constant Load Observation on the Alloy 152 V2 Specimen CT080. 

This Portion of the Test Was Conducted in 320°C Simulated PWR Primary 

Water

Post-test examinations were conducted in a similar fashion to the prior test on the CT049 

specimen. The CT080 specimen was sectioned into an 8-mm-wide slice for crack-growth 

surface observations and a 4-mm-wide slice for crack profile observations. Optical imaging of 

the crack-growth surface (Figure 3-53) revealed differing appearances for the portions of the 

test at 360°C and 320°C. The degree of IG engagement was examined in detail along the final 

crack front using SEM-BSE imaging as shown in Figure 3-54 where regions of IG cracking are 

highlighted in blue. Complimentary SEM-SE images were also taken to confirm crack 

morphologies. The degree of IG engagement along the final crack front was estimated to be 

~33%. Assessment of the remainder of the surface using the optical image produced a value of 

~45% during the first constant load assessment at 320°C, while 50-60% peak IG engagement 

was measured at 360°C, consistent with the first test on this weldment. The crack profile image 

in Figure 3-55 (left side of the specimen in Figure 3-53) was found to have primarily TG cracking 

for this cross-section location.

The general conclusion for the test on this second alloy 152 v2 specimen (CT080) is that similar 

response was seen at 360°C, i.e., 50-60% IG engagement and terminal constant K CGRs were 

<1x10-9 mm/s. When the test temperature was lowered to 320°C, the degree of IG engagement 

decreased and constant load CGRs were again <1x10-9 mm/s.
3-46

Figure 3-53 Optical Image of the 8-mm-Wide Section of the Crack-Growth Surface of the 

Second Alloy 152 V2 Specimen (CT080) Tested in 360°C and 320°C 

Simulated PWR Primary Water

Figure 3-54 SEM BSE Image of the Final ~1 Mm of Crack Growth of the Second Alloy 

152 V2 Specimen (CT080). This Portion of the Test Was at 320°C

Figure 3-55 Optical Image of the Side-Surface Cross Section Taken from the Second 

Alloy 152 V2 Specimen (CT080) After SCC Testing

3.1.4 Analysis of Multi-Lab SCC Tests Results on the ANL Alloy 152v2 Weld

Discussions among NRC, ANL and PNNL staff focused on multi-lab test results on the ANL 

alloy 152v2 weld (designated N152, double J, heat WC04F6) produced at ANL. A primary goal 

was to compare the testing approaches and measured crack growth responses during 

transitioning and under constant load or K conditions. The key issue is the observation by ANL 

of sustained crack growth during several of their constant load exposures versus the results at 

PNNL where sustained crack growth at constant stress intensity was not obtained. Peter 
3-47

Andresen at GEG had also completed a test on this same weld with results similar to those 

found at PNNL. This section repeats some description of the two PNNL tests above then 

provides further analysis for the comparison of tests at all three laboratories.

PNNL Test #1 (CT049) on ANL Alloy 152v2 Weld

An overview of the entire SCC test curve was shown in Figure 3-39. This test was conducted in 

360°C primary water with a target K of 30 MPa√m, and five constant K evaluations were 

performed. The approach to this test was to evaluate the constant K SCC response in five 

separated microstructural regions. In each transitioning sequence a different set of transitioning 

conditions (cyclic and cycle + hold loading) were used to attempt to promote IG engagement 

along the crack front prior to converting the test to constant K. The degree of IG engagement 

was determined from optical and SEM images of the crack growth surface after the test was 

completed and estimated values are reported as a function of test time and can be compared to 

the crack position also shown in Figure 3-39. Approximately 50% IG engagement was achieved 

at the onset of gentle cycling (estimated to be 0.001 Hz) during the first transitioning sequence 

and was maintained over ~0.5 mm of crack extension during the first and second transitioning 

sequences by gentle cycling. More aggressive cyclic loading conditions at the onset of the third 

transitioning sequence drove the crack down to 20% IG, and during gentle cycling in the fourth 

and fifth transitioning sequences, IG engagement increased to 60%. Initial constant K CGRs 

can be grouped into two categories of either ≤1x10-9 mm/s or 2-6x10-9 mm/s. Final CGRs all 

dropped to ≤1x10-9 mm/s. No clear correlation exists between constant K CGRs and the degree 

of IG engagement with the constant K CGR at 60% IG engagement remaining below 1x10-9

mm/s from the onset.

The ratio of the CGR in high temperature water to the estimated air CGR is presented in Figure 

3-56. The dependency of the air fatigue formula on ∆K and R is identical to that used by ANL, 

but due to the wide scatter of the small amount of ANL air fatigue data at 360°C, the formula is 

normalized to produce an env/air ratio of ~1 at the relatively aggressive cyclic loading condition 

of 0.1 Hz where air fatigue response is expected to dominate in both air and water. Because 

the air values are simply estimates from a formula that has very little alloy 152 data to support it, 

not too much should be read into the values produced as a function of cyclic loading condition, 

however the env/air ratio does provide a means to compare response throughout a test for a 

particular loading condition. In concept, high env/air ratios are expected to correlate to a high 

degree of IG engagement and indicate the possibility of higher SCC growth rates when 

converting to constant K or load. In particular, the change in env/air ratio with the addition of a 

hold time may be an indicator of constant K CGRs. 
3-48

Figure 3-56 Ratio of CGR in High Temperature Water to Estimate Air Fatigue CGR for 

PNNL Test #1 on ANL Alloy 152v2 (CT049) Tested in 360°C Water

The transitioning approaches for the PNNL specimen CT049 can be roughly grouped into two 

categories. Transitioning sequences 1-4 attempt to produce IG engagement using minimum 

cycles of 500s/500s, 600s/12s, or 1000s/12s at R = 0.5 with the addition of hold times, while 

transitioning sequence #5 attempts to produce IG engagement through continuous cycling down 

to much lower frequencies (5000s/12s and 25000s/12s) but at a more aggressive R value of 

0.35. As would be expected, the general trend during any one transitioning sequence is that 

lower cyclic loading frequencies where environmental effects are expected to play a bigger role 

in crack extension produced higher env/air ratios. The addition of a hold time was seen to either 

increase, decrease or have no effect on the env/air ratio. Peak env/air values remain at 3-4 

throughout most of the test, but the env/air ratio for the 600s/12s cycle that was applied several 

times throughout the test continually decreases as the test progressed.

Transitioning sequences 1 and 2 where the addition of a hold time either increased or didn't 

lower the env/air ratio produced initial constant K CGRs that were in a higher category of 2-

6x10-9 mm/s, and these sequences had approximately 50% IG engagement. Transitioning 

sequence #3 was applied after significant crack extension (~1 mm) at 0.01 Hz. The env/air 

ratios were ≤ 2 and a low initial constant K CGR along with low IG engagement were observed. 

Transitioning sequence #4 has relatively high final env/air ratios, but the addition of a hold 

lowered the env/air ratio slightly. This sequence produced initial constant K CGR in the higher 
3-49

category of 2-6x10-9 mm/s and had ~40% IG engagement. Transitioning sequence #5 had a 

peak env/air ratio of ~3, but the ratio decreased with the addition of a hold time. Constant K 

CGR was ≤1x10-9 mm/s, but ~60% IG engagement was achieved.

An optical image of the crack surface (~8 mm of the width of the CT specimen, other 4 mm is 

used for crack profile exams) is shown in Figure 3-57. As indicated by the yellow lines mapped 

from variations in oxide appearance of the surface before it was sonicated, a relatively straight 

crack front was maintained throughout the test. Areas of higher IG engagement have a rougher 

appearance than TG regions. IG cracking is also responsible for the protrusions along the final 

crack front.

Figure 3-57 Optical Image of the Crack Surface from the First Test (CT049) by PNNL on 

ANL Alloy 152v2. Arrows Indicate Examples of Significant IG Protrusions 

Along the Final Crack Front

Detailed mapping of the IG/TG cracking morphology was performed using SEM montages

(using both BSE and SE modes) across the width of the surface as shown earlier in Figure 3-45. 

A key aspect of the crack growth surface is very long sections of IG extension. This is made 

possible by having the geometric crack growth plane of the specimen well aligned to the long 

grain boundaries of the weld metal microstructure. IG extensions of this length (many mm) 

clearly indicate that certain grain boundaries are the preferred cracking path in this weld under a 

variety of cyclic loading conditions. An example would be the final ~1.5 mm of crack extension 

shown in Figure 3-45. This spans loading conditions ranging from constant K all the way down 

to 600s/12s at R = 0.5 and 1000s/12s at R = 0.35 showing that this weld will readily undergo IG 

cracking. However, these observations also show that despite “easy” cracking along certain 

grain boundaries, full IG engagement across the crack front is not achieved despite the 

application of a variety of gentle cycling conditions. This suggests grain shape and boundary 

orientation to the crack path play a significant role in IG propagation along with possible 

variation in grain boundary susceptibility.
3-50

Another challenge in assessing the SCC response of this material is determining what amount 

of crack advance occurred during constant K loading. DCPD clearly shows crack advance 

during cyclic and cycle + hold loading, but DCPD shows very little or no growth during constant 

K testing. The crack surface of this specimen reveals extensive IG cracking and localized IG 

protrusions at the final crack front. At this point in time PNNL has not found a method to isolate 

IG growth that occurs during constant K loading from that which occurs during cyclic or cycle + 

hold loading. It is intuitive to assume that IG protrusions mostly occur during constant K loading 

where fatigue advance is not happening, but it could simply be that during cyclic loading, IG 

cracks advance more readily along properly oriented grain IG boundaries than do TG portions of 

the crack front. Stress concentrations on the lagging TG portions of the crack may eventually 

limit how far the TG portions can lag behind the IG portions.

Comparisons of the various SCC “indicators” are summarized in Table 3-9. Transitioning 

sequences 1, 2 and 4 have the highest SCC indicators and also have initial constant K CGRs in 

the higher category. Transitioning sequence #3 has lower SCC indicators and a low initial 

constant K CGR. These sequences suggest a possible correlation between transitioning 

response, IG engagement and constant K CGR. However, transitioning sequence #5 does not 

have this consistency. The env/air values were reasonable and IG engagement is 60%, but the 

initial SCC CGR was below 1x10-9 mm/s and remains below that value. Post-test observation of 

the crack growth surface did not reveal any ligaments that could have affected the DCPD value.

Overall, while ≥50% IG engagement was achieved and encouraging env/air ratios were 

obtained during several of the transitioning sequences, initial constant K CGRs were no higher 

than 6x10-9 mm/s and always fell below 1x10-9 mm/s within 100 hours.

Table 3-9 Summary of CGR Indicators for the Test on CT049 at 360°C

Trans.

Sequence

Peak Env/Air 

ratio for cont. 

cycling

Env/Air ratio 

with addition 

of hold time % IG

Initial Const K 

CGR (mm/s)

Final Const 

K CGR 

(mm/s)

1 2.8 3.7 ~50 2.8x10-9 ≤1x10-9

2 3.5 3.4 ~50 5.6x10-9 ≤1x10-9

3 2.1 no hold time ~20 ≤1x10-9 ≤1x10-9

4 3.3 2.8 ~40 2.2x10-9 ≤1x10-9

5 2.8 2.4 ~60 ≤1x10-9 ≤1x10-9

One other potential SCC indicator is the estimated CGR during the hold phase of cycle + hold 

loading steps. This is calculated by subtracting off the CGR that occurs during a pure cyclic 

loading condition with the same load cycle period and same R. Table 3-10 shows these results. 

Both positive and negative CGRs were obtained. The presence of both positive and negative 

values of the same order of magnitude suggest that on average, very little growth was occurring 

during the hold times, and this is consistent with CGRs measured during constant K 

assessments. 
3-51

Table 3-10 Estimated CGR During the Hold Phase of Cycle + Hold Loading Conditions 

for CT049 Tested at PNNL

Trans.

Seq.

Test 

Step

Load Cycle 

Period

Hold 

Time 

(s)

Total 

Period 

(s)

CGR

(mm/s)

Estimated 

CGR During 

Hold (mm/s)

1 8 980s/20s 0 1000 3.2x10-7 ---

" 9 " 9000 10000 4.2x10-8 1x10-8

2 600s/12s 0 612 6.4x10-7 ---

" 12 " 3600 4212 8.6x10-8 -8x10-9

" 13 " 7200 7812 4.7x10-8 -3x10-9

" 14 " 3600 4212 9.2x10-8 -1x10-9

" 15 " 7200 7812 4.9x10-8 -1x10-9

" average: -4x10-9

4 23 1000s/12s 0 1012 3.5x10-7 ---

" 24 " 7200 8212 7.1x10-8 3x10-8

" 25 " 36000 37012 1.4x10-8 5x10-9

" average: 2x10-8

5 31 25000s/12s 0 25012 4.9x10-8 ---

" 32 " 12600 37612 2.8x10-8 -1.4x10-8

GEG Test #1 (C541) on ANL Alloy 152v2 Weld

As part of the NRC-EPRI collaboration, GE Global Research (GEG) has provided to PNNL a full 

series of CGR plots and one half of the 0.5T CT specimen used by GEG for their first test 

(C541) on the ANL alloy 152v2 weld. Detailed exams of the crack growth surface have now 

been performed at PNNL enabling comparisons to the GEG measured crack growth response 

and to PNNL results.

An overview of the entire SCC test curve is shown in Figure 3-58. This test was conducted in 

360°C primary water with an initial target K of 33 MPa√m, with three transitioning sequences 

and two constant K evaluations. The approach to this test was to evaluate the SCC response in 

three separated microstructural regions. Similar to the approach used by PNNL, in each 

transitioning sequence a different set of cyclic loading conditions were used to attempt to 

generate an SCC crack front prior to converting the test to constant K. Also shown in the plot is 

the estimated IG engagement as measured by PNNL from SEM and optical images (shown 

later in this section). Peak IG engagement was ~40% during transitioning prior to the first 

constant K assessment. This IG engagement was maintained during the first few steps of crack 

advance of the second transitioning sequence but fell off to ~30% IG by the start of the second 

constant K assessment. The third transitioning sequence appears to have forced the crack to 

predominantly TG fatigue, and IG cracking had increased only slightly prior to ending the test 

despite ~3000 hours of very gentle cycle + hold transitioning. However because of the very 

gentle cycling conditions and low CGRs, a total of only ~100 μm of material was covered during 

this final transitioning.
3-52

Figure 3-58 Overview of the Entire First Test (C541) by GEG on the ANL 152v2 

Weldment Supplied by Peter Andresen. Percent IG Estimate Was 

Determined by PNNL

Figure 3-59 lists the cyclic loading conditions for all three transitioning sequences and plots the 

ratio of environment to estimated air response as a function of test step. Moderate env/air ratios 

(2.6-3.0) were achieved during the first transitioning sequence where the cyclic loading period 

was 1000 s with R=0.6. The second transitioning sequence started at R=0.4 produced an 

env/air ratio of 4.2. The remainder of this transitioning sequence utilized a 1000 s cycle but with 

R=0.5. The addition of increasingly longer hold times during the second transitioning sequence 

had no significant effect on the env/air ratio. Constant K assessment after these two 

transitioning sequences produced initial CGRs of no higher than 2x10-9 mm/s that fell off to 

≤1x10-9 mm/s.

The third transitioning sequence utilized a base cyclic loading period of 475s/25s again at 

R=0.5. This produced an env/air ratio of 1 suggesting no environmental enhancement. 

Increasingly longer hold times were tacked onto this cycle to encourage IG engagement. The 

addition of the hold times had no effect on the env/air ratio. A constant K assessment was not 

performed after this transitioning sequence, but growth rates under cycle + hold loading were 

very low suggesting that constant K CGRs would also be very low.

Optical and SEM imaging performed at PNNL was used to document the GEG C541 crack 

growth surface and is summarized in the SEM secondary electron image shown in Figure 3-60. 

Note that a portion of the air precrack region is not shown in this figure. Blue lines indicate 

either the air precrack boundary or the final crack front produced in water, while yellow 

highlighted regions indicate areas of IG cracking. Two features of this crack growth surface 

worth noting are: 1) crack growth was somewhat uneven across the width of the crack with one 

side having a final length of ~3.9 mm and the other having a final length of ~3.0 mm, and 2) a 
3-53

very long ligament reaching back to the air precrack boundary formed and remained intact

through the entire test. Both of these features have the potential to diminish the accuracy of 

DCPD crack length measurement.

Figure 3-59 Ratio of Measured CGR in 360°C Simulated PWR Primary Water to 

Estimated Air Fatigue CGR for GEG Test C541 on ANL Alloy 152v2

A feature that stands out on this surface is that ~25% of the surface on the right side shows very 

little IG engagement throughout the test. This region is separated from the rest of the surface 

by the ligament mentioned above, and the difference in the degree of IG engagement between 

the two regions of the surface suggests there may have been some differences in the weld 

microstructural characteristics. Additional characterizations may be worthwhile to map weld 

characteristics across the weld in this specimen. Unless otherwise noted, the percentage of IG 

engagement will be quoted as relative to the entire width of the surface.

Focusing now on the left ~75% of the surface, the first ~0.5 mm of growth from the air precrack 

shows very little IG engagement. This corresponds to load cycling at 500s/500s with R = 0.6. 

Somewhat surprisingly, significant IG engagement of ~40% subsequently occurs very rapidly at 

distance of ~0.5 mm from the precrack. Due to the uncertainty in the correlation between 

DCPD crack length and actual crack length, two interpretations of the relationship between 

transitioning and IG engagement are possible. The first is that the step change in IG 

engagement corresponds to the onset of 980s/20s load cycling with either a 0.8 h or 2.5 h hold. 
3-54

If this is the case, 40% IG engagement is then maintained during constant K and during the first 

steps of the second transitioning sequence that included load cycling at 250s/250s with R = 0.4 

where the env/air value was 4.2. The IG engagement then diminishes slightly to ~30% by the 

start of the second constant K assessment.

Figure 3-60 SEM Secondary Image Obtained by PNNL of the GEG C541 Showing 

Various Features of the Crack Growth Surface

The alternative interpretation of the IG engagement during the first and second transitioning 

sequences is that the step change in IG engagement took place at the start of second 

transitioning sequence at 250s/250s with R = 0.4 where the env/air ratio was 4.2. This 

interpretation has some compelling aspects in that 40% IG engagement occurs over a distance 

of roughly 1 mm consistent with the measured crack advance during this loading condition. The 

strong change in loading conditions also provides a palatable explanation for the step change in 

IG engagement. If this scenario is true, the first constant K measurement was conducted with 

0% IG engagement, while the second would again be at ~30% IG engagement. Without clear 

evidence to point to one scenario or the other, it will be assumed that significant IG engagement 

occurred during the first transitioning sequence where gentle cycling is expected to produce IG 

cracking.

By the start of the second constant K assessment, IG cracking had diminished to ~30%. IG 

cracking is almost completely eliminated by the application of a 0.02 Hz cycle with R = 0.5 at the 

start of the third transitioning sequence. A small amount of IG engagement occurred in 

subsequent transitioning steps, reaching only ~5% by the end of the test. Table 3-11

summarizes the SCC indicators for this test. If IG cracking occurred during the final steps of the 

first transitioning sequence, then what is seen is that the env/air ratios are roughly consistent 

with the degree of IG cracking that occurred during cyclic loading. However, higher env/air 

ratios and higher degrees of IG engagement do not correlate to higher constant K CGRs. 

One other SCC indicator that is reviewed here is the estimated CGR during the hold phase of 

cycle + hold loading steps. This is calculated by subtracting off the CGR that occurs during a 

pure cyclic loading condition with the same load cycle period and the same R. Table 3-12

shows these results. The positive and negative values reported here indicate that the CGR 
3-55

during the hold is very low, and averaging the results together produces a CGR that is 

consistent with what GEG measured during constant K assessments.

Table 3-11 Summary of CGR Indicators for the First GEG Test (C541) on ANL 152v2 at 

360°C

Trans.

Seq. % IG

Peak 

Env/Air 

Ratio for 

Continuous 

Cycling

Peak 

Env/Air 

Ratio with 

Addition of 

Hold Time

Initial 

Const K 

CGR 

(mm/s)

Final 

Const K 

CGR 

(mm/s)

1 ~40 2.6 2.7 1.7x10-9 ≤1x10-9

2 ~30 4.2 2.6 ≤1x10-9 ≤1x10-9

3 ~15 1.1 1.1 no constant K

Table 3-12 Estimated CGR During the Hold Phase of Cycle + Hold Loading Conditions 

of C541 Tested at GEG

Trans.

Seq.

Test 

Step

Load Cycle 

Period

Hold 

Time 

(s)

Total 

Period 

(s)

CGR During 

Load Cycle 

(mm/s)

Estimated 

CGR During 

Hold (mm/s)

2 6 500s/500s 0 1000 2.6x10-7 ---

" 7 " 3000 4000 7.2x10-8 9x10-9

" 8 " 9000 10000 2.4x10-8 -2x10-9

" 9 " 85900 86900 3.0x10-9 ~0

" average: 2x10-9

3 12 475s/25s 0 500 4.9x10-7 ---

" 13 " 9500 10000 2.6x10-8 2x10-9

" 14 " 27000 27500 8.0x10-9 -1x10-9

" 15 " 85900 86400 2.8x10-9 -4x10-11

" average: 0.3x10-9

ANL Test #1 (N152-TS-1) on ANL Alloy 152v2 Weld

The measured CGRs, %IG engagement values and crack growth surface images for the N152-

TS-1 specimen (1T CT as shown in Figure 3-61) were obtained from ANL reports. One feature 

of this specimen worth noting is that the geometric crack plane of the specimen is roughly at a 

10-15 degree angle to the long grain boundaries in weldment. The post-test crack growth path 

indicated by the crack profile on the right half of the specimen in Figure 3-61(b) shows that not

unexpectedly, cracking does go off the geometric crack plane in an attempt to follow the long 

grain boundaries.
3-56

Figure 3-61 1T CT Specimen That ANL Used for Their Test (N152-TS-1) on the ANL 

152v2 Weldment

An overview crack growth plot of the entire test is not available to present here. The test can be 

broken up into four transitioning sequences with three taking place at 26-30 MPa√m and the 

fourth taking place at 46 MPa√m. An env/air vs test step plot was constructed based on the 

reported ANL data as shown in Figure 3-62. This plot serves to show the step-by-step response 

of the specimen from an env/air perspective. Transitioning appears to have been performed 

primarily with a 600s/12s waveform sometimes with a 1 or 2 h hold. Periodic partial unloading 

with a hold time of either 1 or 2 h was also used frequently during the testing. The env/air 

values hovered between 0 and 3 for all but two steps where values of 10.2 and 4.0 were 

observed for transitioning sequences #2 and #3b. Constant load SCC assessments 

immediately after these high env/air values produced initial rates of ~2-4x10-8 mm/s, but did not 

produce sustained high CGRs. In particular, the constant load response after the env/air value 

of 10.2 during transitioning quickly dropped from ~4x10-8 mm/s to <1x10-9 mm/s. The two 

highest sustained constant load CGRs (~2.0x10-8 mm/s) were obtained immediately after 

transitioning sequences #3a and #4 with low env/air values (<2).

ANL's optical image of the N152-TS-1 crack growth surface is shown in Figure 3-63 with their 

three SEM images overlaid by PNNL to show the regions of the detailed IG analysis (performed

by ANL). Arrows on the sides of the optical image show the location of constant load 

assessment as taken from an ANL crack growth summary table. The contrast on the SEM 

images was inverted to allow easier determination of the position of these SEM images on the 

optical image. Yellow highlighted regions represent PNNL's attempt to determine the areas of 

IG engagement. This was guided by lines that ANL drew onto the SEM images to indicate 

regions of IG engagement. However, these lines were only drawn on two of the three SEM 

images, so it was necessary to estimate IG engagement on the third image (SEM image on the 

left). During the exams, it was noted that much of the IG cracking appeared to be piece-meal as 

if the crack was alternately growing through grains and then on grain boundaries as it traversed 

the microstructure. This is likely due to the inclined angle of the specimen relative to the grain 

boundary microstructure. It was extremely difficult to independently assess the %IG 

engagement and IG morphology from these images. Higher resolution SEM-SE and -BSE

images covering this region as done for the PNNL and GEG crack growth surfaces are needed 

to enable accurate and consistent determination of the %IG engagement comparable to what is 

shown for CT049 (PNNL) and C541 (GE) in this report.

a) - before b) - after
3-57

Figure 3-62 Ratio of CGR in High Temperature Water to Estimate Air Fatigue CGR for 

ANL Test on ANL Alloy 152v2 (N152-TS-1) Tested in 320°C Water

The red line in Figure 3-63 indicates ANL's method for determining the degree of IG 

engagement. In essence, a band across the surface is considered, and any IG that is found 

within that band adds to the fraction of IG engagement across the width of the specimen. ANL 

reports that 70% IG engagement was observed in the area covering the first four constant load 

assessments. The PNNL approach is somewhat different, the fraction of IG engagement is 

considered by drawing a line that is believed to best represent the crack front location at the 

time of the SCC assessment at constant load and then add up the fraction of the line length that 

intersects regions of IG growth. The blue line in the image represents PNNL's attempt at 

defining the crack front at the time of the third constant load assessment where a CGR of 2x10-8

mm/s was measured by ANL. IG engagement is measured to be <50%. This may be due, in 

part, to inaccuracies in locating regions of IG growth, but it is also due to the difference in the 

methods for calculating IG engagement. ANL's reported values for the %IG engagement (~70% 

early and ~40% at the end of the test) are used for comparison to the PNNL and GEG tests.
3-58

Figure 3-63 ANL Optical Image of the Crack Growth Surface of N152-TS-1. ANL's SEM 

Images Are Overlaid onto the Surface to Show Locations of IG Cracking 

Relative to the Entire Crack Surface and Indicated Crack Lengths at 

Constant Load

Table 3-13 summarizes the available SCC indicators for ANL's test on the alloy 152v2 material. 

The first four constant load assessments took place over ~0.5 mm of crack extension. The low 

CGRs obtained during the first two assessments are attributed by ANL as being due to the 

presence of a ligament that was either holding up crack advance or masking DCPD response. 

The sustained constant load CGR of 2.0x10-8 mm/s after transitioning sequence 3b was 

obtained over a period of ~1400 h and a DCPD indicated crack advance of ~100 μm. This 

assessment was ended by a 3-h power outage. Re-transitioning with a cycle + hold and 

converting back to constant load produced only a 5x10-9 mm/s CGR. Thus, a wide range of 

response was observed over a region that is reported to have 70% IG engagement. The K level

was then increased to ~46 MPa√m while advancing the crack ~8 mm. Final transitioning took 

place through a series of continuous cycling steps with the final step being a 9500s/12s cycle at 

R = 0.3. Despite the low SCC indicators, a constant load CGR of 2.0x10-8 mm/s was obtained 

albeit the exposure time was limited to ~350 h.
3-59

Table 3-13 Summary of CGR Indicators for the First ANL Test (N152-TS-1) on ANL 

152v2 at 320°C

Transitioning

Sequence

Peak Env/Air 

ratio for 

continuous 

cycling

Env/Air ratio 

with addition of 

hold time % IG

Initial 

Const K 

CGR 

(mm/s)

Final 

Const K 

CGR 

(mm/s)

1 2.8 no hold time 70 ≤1x10-9 ≤1x10-9

2 3.0 10.3 70 4.3x10-8 ≤1x10-9

3a 2.6 2.6 70 4.6x10-8 2.0x10-8

3b no cont. cycle 4.0 70 1.7x10-8 5.0x10-9

4 1.5 1.8 40 5.0x10-8 2.0x10-8

The last item to be covered is the estimated CGRs during hold times as shown in Table 3-14. 

Only two instances are present in ANL's testing where the CGR during a hold can be calculated. 

In one instance during the second sequence, a slightly negative CGR is calculated, while the 

second instance produced positive a CGR during a hold of 5x10-8 mm/s. This corresponds to 

the transitioning step that produced an env/air value of 10.3 and was followed by a low CGR at 

constant load.

Table 3-14 Estimated CGR During the Hold Phase of Cycle + Hold Loading Conditions 

of N152-TS-1 Tested at ANL

Trans.

Seq.

Test 

Step

Load Cycle 

Period

Hold 

Time 

(s)

Total 

Period 

(s)

CGR During 

Load Cycle 

(mm/s)

Estimated 

CGR During 

Hold (mm/s)

2 6 600s/12s 0 612 2.6x10-7 ---

" 7 " 7200 7812 7.2x10-8 4x10-9

" 8 " 3600 4212 2.4x10-8 -1x10-8

" average: -3x10-9

2 13 600s/12s 0 612 1.2x10-7 ---

" 14 " 7200 7812 5.2x10-8 5x10-8

Comparison of Results from PNNL, GEG, and ANL

Selected analyses have been performed on SCC growth rate test results for the same ANL alloy 

152v2 weld tested at PNNL, GEG and ANL. It is important to note that no specimen is identical 

to another due to variations within a weld and how a specimen is aligned to the weld metal 

microstructure. Each lab has used some unique approaches in their attempt to generate 

sustained SCC propagation under constant K or load conditions. We believe some trends are 

apparent from the measured material response and the various analyses of SCC indicators.

Material Response

• IG engagement versus load cycling conditions: this weld will readily undergo IG 

cracking during continuous cycling under what could be considered mildly aggressive 

loading conditions with reasonable high growth rates (>10-7 mm/s). Example conditions 
3-60

are 600s/12s with R=0.5, 1000s/12s with R=0.35, and 475s/25s with R=0.4. In addition, 

some of the highest degrees of IG engagement have been observed at the most 

aggressive R values, e.g. 0.4 and 0.35.

• Significant amounts of IG extension can occur without full engagement. Tests at PNNL

and GEG show that 40-60% engagement can take place over fairly short distances and

then persist at that level for as much as ~1.5 mm of crack extension without a further

increase in IG engagement.

• High degrees of IG engagement do not consistently produce high DCPD-measured

CGRs. The two highest sustained CGRs during testing at ANL were produced in

regions of claimed 70% and 40% IG cracking. Testing at ANL in the same region of

claimed 70% IG cracking more frequently produced constant load CGRs of ≤5x10-9

mm/s. Tests at PNNL with 50-60% IG engagement and at GEG with 40% IG

engagement did not produce any sustained DCPD-measured propagation at constant

K.

• There is nothing on the crack growth surface to clearly separate IG growth during

constant K or load from IG growth during the prior transitioning steps.

The analysis of ANL's crack growth surface suggests a different cracking morphology. Whereas 

large amounts of IG crack extension were observed on the PNNL and GEG crack growth 

surfaces, much of the IG cracking that could be determined on the ANL crack growth surface 

was more piecemeal. The IG regions also tended to appear to be inclined to the crack growth 

surface. This suggests that the inclined orientation of the specimens produced interspersed TG 

and IG growth as the crack would alternately grow through a grain and then on grain 

boundaries.

In-Test SCC Indicators

• Cyclic CGRs from all three laboratories typically produced env/air ratios of 2-3. Several

instances of higher values or lower values were not a consistent predictor of high or low

constant K/load CGRs. The transitioning sequences that produced the two highest

sustained CGRs at ANL had env/air ratios below 2.

• CGRs calculated from the hold phase of cycle + hold loading steps tended to have a

high degree of scatter with negative values often being produced. Averaging several

sequences together tended to produce a CGR that was generally consistent with the

constant K response of the material but was not necessarily a representative value, i.e.,

-5x10-9 mm/s to +5x10-9 mm/s seemed to be representative of the average CGRs

calculated from hold times where subsequent constant K or load assessments

produced CGRs of ≤1x10-9 mm/s.

• Env/air ratios during cycling do seem to scale with the degree of IG engagement. There

is some scatter in the trend, but a general trend does exist of higher degrees of IG

engagement being found during portions of tests where higher env/air ratios are

observed. Since it appears that all the IG engagement takes place during cyclic loading

steps, this result perhaps should not be unexpected.
3-61

Conclusions from Analysis of Multi-Lab Tests on the ANL Alloy 152v2 Weld

SCC indicators as provided by ANL on their test on this material do not stand out in any way 

from those observed during tests at PNNL and GEG. However, PNNL's examination of the ANL 

crack growth surface indicates a more piecemeal IG cracking morphology and indicates a lower 

estimated degree of IG engagement than reported by ANL. The lower degree of observed IG 

engagement is due in part to the method used to calculate the fraction of IG engagement. A

better understanding of ANL's result might be obtained if a more detailed SEM exam could be 

performed on the crack growth surface. 

3.2 Alloy 52/52/52MSS Welds

3.2.1 Areva 52 Butt Weld and MHI 52 U Groove Weld

For the MHI alloy 52 weld, alloy 152 (heat 307380) was buttered onto the U-groove surface by 

SMAW, while alloy 52 (heat NX2686JK) was used as the filler and applied by gas tungsten arc 

welding (GTAW). Welding parameters for the MHI alloy 52 GTAW consisted of a deposition 

speed of 4-10 cm/min and a current of 150-300 amps. Welding parameters for the AREVA alloy 

52 butt weld were not provided. 

3.2.2 Alloy 52 Weld Samples (CT024, CT025, CT032 and CT033)

Duplicate tests have been performed on two alloy 52 welds, one made by AREVA (CT024 and 

CT032) and the other made by MHI (CT025 and CT033). Orientations of these specimens

relative to the welds are shown in Figure 3-64. Before machining specimens, the blanks were 

etched to allow viewing the weld morphology, and a desired crack growth path through specific 

weld passes was determined. Specimens were again machined from the blanks to target the 

desired crack growth path, for example, as shown in Figure 3-64. 

Two tests were performed with an AREVA alloy 52 sample paired with an MHI alloy 52 sample 

in both tests. An overview of the first test is shown in Figure 3-65 with CT024 being the AREVA 

material and CT025 being the MHI material. The test can be separated into three main phases. 

The first two phases evaluated crack growth response during transitioning and constant K at 

350°C on two different regions in the specimens, while the third phase of the test examined the 

350°C constant K crack growth response after extending the crack by cyclic loading at 50°C. 

This unusual transitioning method was based on the high degree of IG engagement observed in 

the MHI alloy 152 specimens during cyclic loading at 50°C (section 3.1.1). 
3-62

Figure 3-64 Image of the MHI Alloy 52 and AREVA Alloy 52 Welds Showing Positioning

of the 0.5T CT Specimens

Figure 3-65 Overview of the Crack Growth Response of Two Alloy 52 Welds, One Made 

by AREVA (CT024) and One Made by MHI (CT025)

In the first region that was evaluated, CGRs during cycle + hold loading with R=0.7 were found 

to be a factor of 2-5X lower than transitioning CGRs in the MHI alloy 152 specimens from 

previous tests. Additional transitioning steps were applied using an R=0.5 and CGRs 

increased, however propagation rates in the alloy 52 specimens remained a factor of ~2X lower 

than for the alloy 152 specimens under equivalent gentle load cycling. Cycle + hold and 

constant K response was then determined as presented in Figure 3-66. The CGR during the 

extended time at cycle + hold loading was very linear with no suggestion of any change in the 
3-63

degree of engagement. At approximately 2130 h, the loading conditions were set to constant K 

and no crack advance was measured over a period of approximately 500 hours. Transitioning 

was reinitiated using a series of different hold times and periodic unloading steps, but none 

gave any indication of an increase in engagement, and it was decided to advance the crack in 

the specimens to a new region. Using moderate cyclic loading conditions, the crack in each 

specimen was advanced over 0.5 mm, and transitioning was initiated using symmetric 

waveforms with R = 0.5. Propagation rates during subsequent cycle + hold conditions were 

found to be only slightly higher (40% higher with rates of ~1.4x10-8 mm/s) than the rates 

observed in the previous region suggesting that constant K CGR for the specimens would again 

be well below 1x10-9 mm/s.

For the final phase of the test, transitioning at 50°C was performed. In an attempt to generate 

an engaged IG crack front in the alloy 52 specimens, it was decided to perform similar cycling at 

50°C in PWR primary water as was done for the alloy 152 specimens where extensive IG 

cracking was observed. The crack growth response of the alloy 52 specimens at 350°C is 

shown in Figure 3-65. 

Figure 3-66 Cycle + Hold and Constant K Response of the AREVA and MHI Alloy 52 

Specimens (CT024 & CT025) in the Second Phase of Each Specimen That 

Was Examined

While an increase in propagation rate with time during 0.001 Hz step is suggestive of an 

improvement in engagement, the CGR in each of the three cyclic loading steps was consistently 

lower than the rates observed at 350°C and much lower than measured for the alloy 152 

specimens under equivalent cycling conditions. After ~1000 hours of crack extension at 50°C, 

the loading was converted to constant K, and the test temperature was brought back up to 
3-64

350°C. DCPD fluctuations were allowed to settle out for 24 h before crack length 

measurements were resumed. The resulting crack length with time response at 350°C is shown 

in Figure 3-68. As can be seen, very high initial CGRs in excess of 1x10-7 mm/s were observed. 

Over the next 1400 hours (2 months), the propagation rates slowly decreased reaching levels 

below 1x10-9 mm/s similar to earlier high-temperature constant K response for these specimens. 

The high initial DCPD-measured growth rates is possibly due to the disruption of conducting 

bridges across the cracks formed at low temperatures and during the temperature increase to 

350°C. As noted previously, electrochemical conditions are very Ni-metal stable at 50°C and 

move closer to the Ni/NiO potential as the temperature is increased to 350°C. The increase in 

DCPD-measured crack length may be due to oxidation or creep-induced fracture of these 

bridges in the crack at high temperature. It was not possible to separate this process from 

actual propagation, but it appears likely that the final constant K rates after 2 months are more 

representative of SCC growth rates. A summary of test conditions and corrected specimen 

response for each phase of the test is shown in Table 3-15. 

Figure 3-67 Overview of the Crack Growth Response of the AREVA and MHI Alloy 52 

Specimens (CT024 & CT025) During Cyclic Loading Conditions at 50°C
3-65

Figure 3-68 Constant K Crack Growth Response of the MHI and AREVA Alloy 52 

Specimens (CT024 & CT025) at 350°C After Cyclic Loading Crack Extension 

at 50°C

The test was ended and the specimens were fatigued open in air to document the crack growth 

surfaces. Optical images of the crack growth surfaces for the AREVA and MHI alloy 52 

specimens are shown in Figures 3-69 and 3-70, respectively. Several distinct bands are 

apparent on the surface, and are labeled as A through D in Figure 3-69. Band A corresponds to 

the transitioning and constant K testing in the first region that was examined. Band B 

corresponds to rapid crack extension performed to move the crack front forward to the next 

microstructural region of crack-growth testing while band C corresponds to the transitioning 

steps in this region. Finally, band D corresponds to crack extension at 50°C and during the 

subsequent constant K phase at 350°C. SEM examination determined that the crack-growth 

surface of the AREVA alloy 52 specimen was TG except for two small protrusions of IG growth 

within the yellow boxed region. An SEM example of this IG morphology is presented in Figure 

3-71(left). This IG growth appears to have been initiated and propagated during 50°C cycling 

with no significant IG cracking produced during prior testing at 350°C. A higher fraction of IG 

cracking was discovered for the MHI alloy 52 specimen as indicated by the yellow-boxed 

regions in Figure 3-70. Whereas the AREVA alloy 52 specimen was less than 5% IG at the final 

crack front, the MHI alloy 52 specimen was ~35% IG. The cracking morphology in one of these 

IG regions for the MHI sample is documented in Figure 3-71(right) and again appears to have 

initiated and propagated during 50°C cycling.
3-66

Table 3-15 Summary of Test Conditions and Corrected Response for AREVA and MHI 

Alloy 52 Specimens CT024 & CT025

CT024 AREVA Alloy 52

Butt Weld Blank #1

CT025 MHI Alloy 52

U-groove Weld Blank #1

Test 

Phase

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax

(MPa√m)

CGR

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

Kmax 

(MPa√m)

CGR 

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

1 ~3 0.3 3 0 air precrack RT 25 1.2E-04 0.40 25 7.6E-05 0.40

2 ~2 0.5 3 0 air precrack RT 28 7.6E-05 0.35 28 4.6E-05 0.35

3 ~2 0.6 3 0 air precrack RT 31 5.1E-05 0.35 30 3.1E-05 0.35

4 ~3 0.7 3 0 air precrack RT 31 2.1E-05 0.20 30 1.5E-05 0.20

5 88 0.7 0.1 0 29 cc/kg H2 325 31 8.0E-07 0.257 30 7.5E-07 0.235

6 237 0.7 0.01 0 29 cc/kg H2 325 31 1.6E-07 0.133 30 1.5E-07 0.128

7 323 0.7 0.001 0 29 cc/kg H2 325 31 2.2E-08 0.031 31 2.2E-08 0.033

8 82 0.7 0.001 0 29 cc/kg H2 350 31 3.1E-08 0.011 31 5.3E-08 0.016

9 314 0.7 0.001 2.5 29 cc/kg H2 350 31 1.4E-09 0.004 31 5.7E-09 0.015

10 272 0.5 0.001 0 29 cc/kg H2 350 31 1.0E-07 0.098 31 1.5E-07 0.126

11 806 0.5 0.001 2.5 29 cc/kg H2 350 31 1.2E-08 0.024 31 1.0E-08 0.028

12 365 --- const K --- 29 cc/kg H2 350 31 no growth --- 31 9E-10 0.002

13 500 0.5 0.04 2.5 29 cc/kg H2 350 31 4.3E-09 0.013 31 6.1E-09 0.012

14 343 0.5 0.04 0.5 29 cc/kg H2 350 31 1.9E-08 0.022 31 3.1E-08 0.037

15 313 0.5 0.04 12.5 29 cc/kg H2 350 31 8E-10 0.002 31 2.4E-09 0.004

16 49 0.5 0.1 0 29 cc/kg H2 350 32 5.2E-06 0.718 34 7.2E-06 1.161

17 78 0.5 0.01 0 29 cc/kg H2 350 33 9.7E-07 0.286 34 1.0E-06 0.308

18 225 0.5 0.001 0 29 cc/kg H2 350 33 1.4E-07 0.119 34 1.5E-07 0.115

19 341 0.5 0.001 2.5 29 cc/kg H2 350 33 1.4E-08 0.038 34 1.5E-08 0.042

20 297 0.5 0.01 0 29 cc/kg H2 50 33 3.5E-07 0.306 36 7.7E-07 0.592

21 513 0.5 0.001 0 29 cc/kg H2 50 34 4.3E-08 0.051 36 8.4E-08 0.018

22 250 0.5 0.001 2.5 29 cc/kg H2 50 34 4.0E-09 0.012 36 1.6E-08 0.023

23 1327 --- const K --- 29 cc/kg H2 350 34 1.4E-09 0.053 37 2.8E-09 0.151

24 352 --- const K --- 20 cc/kg H2 350 34 1.2E-09 0.003 37 3.5E-09 0.006
3-67

Figure 3-69 Optical Image of the Crack Growth Surface of the AREVA Alloy 52 

Specimen (CT024) 

Figure 3-70 Optical Image of the Crack Growth Surface of the MHI Alloy 52 Specimen 

(CT025). Yellow Boxes Indicate Regions of IG Growth and the Blue Box 

Identifies the Area of the SEM Image Shown in Figure 3-71
3-68

Figure 3-71 SEM Images Illustrating IG Regions on the Crack Growth Surface for the 

Alloy 52 Specimens: (left) Isolated IG Finger-like Area in AREVA Sample 

and (right) Typical IG Area in MHI Sample 

Side surface images of the cracks were also obtained on these specimens with cut lines for both 

specimens shown in Figure 3-72. Side surfaces where polished and etched to reveal the 

dendrite and grain structure and are shown in Figures 3-73 and 3-74, respectively for the 

AREVA and MHI materials. The edge of the crack wall is feathered over making it somewhat 

difficult to determine TG or IG growth along the crack front, but comparison with the crack 

growth surfaces allows the start of IG growth to be identified. Of interest in looking at these side 

surfaces was the number of opportunities a crack had to intersect a grain boundary. The 

AREVA material has an extremely large grain size (500 to 2000 μm) that provides little 

opportunity for a TG crack to intersect a grain boundary while the MHI material has a wider 

range of grain size with some falling down into the 200 μm range. It is in a region of smaller 

grain size where the MHI alloy 52 material went IG.
3-69

Figure 3-72 White Lines Indicate Where Crack Growth Surfaces Were Sectioned to 

Expose and Polish Crack Side Surfaces

Figure 3-73 Side Surface Image of the AREVA Alloy 52 Specimen CT024
3-70

Figure 3-74 Side Surface Image of the MHI Alloy 52 Specimen CT025

A key issue that remained unclear was whether any significant IGSCC growth occurred during 

constant K testing at 350°C after crack extension at 50°C. In order to better assess the effects 

of the temperature change on the DCPD-measured crack length, tests were performed on a 

second pair of AREVA (CT032) and MHI (CT033) alloy 52 specimens in simulated PWR primary 

water. An overview of the entire crack growth test is shown in Figure 3-75. This time the test 

can be separated into four phases. During the first phase, the specimens were transitioned for 

several weeks at 350°C and displayed similar cyclic crack growth response as specimens 

CT024 and CT025 as illustrated in Figure 3-76. The temperature was then decreased to 50°C 

in the second phase and the crack extended by ~1 mm under cyclic loading conditions. This is 

documented in Figure 3-77. Conditions used were similar to those for the first set of alloy 52 

specimens. Loading was then converted to constant K at a low value of 10 MPa√m and the

temperature brought back up to 350°C in the third phase of the test. Considering the resistance 

of these materials, no crack growth was expected at this low K value. However, nearly identical 

DCPD crack growth response can be seen when comparing Figure 3-78 (CT032/33, low K) to 

Figure 3-68 (CT024/25, high K). The final phase of the test increased K values up to 30 MPa√m 

and then to 40 MPa√m using dK/da loading. Constant K SCC propagation rates increased 

slightly at the higher K values, but remained extremely low (corrected rates of 1.5x10-9 mm/s for 

the MHI alloy 52 and <1x10-9 mm/s for AREVA) as shown in Figure 3-79 and it was decided to 

end the test. A summary of test conditions and corrected data for each phase of the test is 

shown in Table 3-16. 

Figure 3-75 Overall Response for the Second Test on the AREVA and MHI Alloy 52 

Specimens CT032 and CT033
3-71

Figure 3-76 Similar CGRs Were Seen During Early Transitioning Between First Test (a) 

CT024/25 and Second Test (b) CT032/33 on the AREVA and MHI Materials
3-72

Figure 3-77 Cyclic Loading Response at 50°C of AREVA (CT032) and MHI Alloy 52 

(CT033)

Figure 3-78 Crack Growth Response of a Second Set of AREVA and MHI 52 Specimens 

(CT032 & CT033) Tested at 350°C Following Crack Extension at 50°C
3-73

Figure 3-79 AREVA and MHI Alloy 52 Crack Growth Response at 40 MPa√m

After ending the test, the crack was sealed for crack-tip characterization by filling it with resin, 

and the specimens were each sectioned into two slices with one slice being fatigued open to 

reveal the crack growth surface, and the side of the other slice being polished to reveal the 

crack path through the material. The optical images of the crack growth surface, as shown in 

Figure 3-80, are somewhat difficult to discern because of resin coating the surface, but the large 

phases of the test are identifiable. It is also clear that there are regions of IG growth on the 

surface of both specimens. A side surface image of the AREVA (CT032) specimen is shown in 

Figure 3-81 revealing again that the material has very large grains. In this particular slice 

through the material, a significant amount of IG cracking was found; essentially the entire in-situ 

portion of the test appears to be IG along this section through the specimen. The side surface 

cut corresponds to a large protrusion on the crack growth surface in Figure 3-80. Several other 

protrusions are apparent indicating a higher degree of engagement than on the previous test 

(CT024). Figure 3-82 shows the side surface of the MHI (CT033) specimen with its smaller 

grains. Of interest in this photo is that while the crack eventually finds a grain boundary and 

cracks along it for some distance, it eventually goes off the boundary. Extensive cracking above 

and below the main crack is apparent. There is clearly some preference for IG cracking, but it 

appears that the grains must be well aligned for growth. Higher resolution SEM images of TG 

and IG cracks are presented in Figures 3-83 and 3-84. These micrographs reveal the shallow 

oxidation of the crack walls and extending to the crack tips.
3-74

Table 3-16 Summary of Test Conditions and Corrected Response for AREVA and MHI 

Alloy 52 Specimens CT032 & CT033

CT032 AREVA Alloy 52

Butt Weld Blank #1

CT033 MHI Alloy 52

U-groove Weld Blank #1

Test 

Phase

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax

(MPa√m)

CGR

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

Kmax 

(MPa√m)

CGR 

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

1 ~2 0.3 3 0 air precrack RT 25 1.5E-04 0.58 25 1.2E-04 0.48

2 ~2 0.5 3 0 air precrack RT 28 1.1E-04 0.46 28 8.1E-05 0.38

3 ~2 0.6 3 0 air precrack RT 31 6.8E-05 0.35 30 5.0E-05 0.29

4 ~3 0.7 3 0 air precrack RT 31 3.4E-05 0.35 30 2.3E-05 0.29

5 18 0.5 0.1 0 29 cc/kg H2 350 31 6.0E-06 0.301 30 7.9E-06 0.457

6 106 0.5 0.01 0 29 cc/kg H2 350 31 7.9E-07 0.303 31 1.4E-06 0.513

7 421 0.5 0.001 0 29 cc/kg H2 350 32 1.0E-07 0.160 32 1.4E-07 0.219

8 60 --- const K --- 29 cc/kg H2 50 32 not meas 0.015 32 not meas 0.007

9 37 0.5 0.1 0 29 cc/kg H2 50 32 2.3E-06 0.234 32 3.4E-06 0.410

10 200 0.5 0.01 0 29 cc/kg H2 50 32 2.5E-07 0.208 33 2.8E-07 0.254

11 425 0.5 0.01 0 29 cc/kg H2 50 32 3.9E-07 0.522 33 6.5E-07 0.873

12 192 0.5 0.01 0 29 cc/kg H2 50 33 4.4E-07 0.212 36 4.8E-07 0.357

13 504 --- const K --- 29 cc/kg H2 350 11 decreasing 0.025 12 decreasing 0.085

14 186 0.78 0.001 2.5 29 cc/kg H2 350 11 2.7E-09 0.024 12 8.3E-09 0.146

15 497 --- dK/da --- 29 cc/kg H2 350 11->33 1.2E-08 0.059 12->38 1.3E-08 0.104

16 367 --- const K --- 29 cc/kg H2 350 33 5E-10 <0.001 38 1.2E-09 <0.001

17 136 --- dK/da --- 29 cc/kg H2 350 33->38 2.4E-08 0.002 38->44 2.9E-08 0.003

18 458 --- const K --- 29 cc/kg H2 350 38 5E-10 <0.001 44 8E-10 <0.001

19 216 0.7 0.001 2.5 29 cc/kg H2 350 38->39 1.1E-08 0.009 44->45 1.2E-08 0.010

20 86 0.7 0.001 2.5 29 cc/kg H2 350 39->44 5.0E-08 0.009 45->51 5.4E-08 0.009

21 564 0.7 0.001 2.5 29 cc/kg H2 350 44 1.1E-08 0.022 51 1.2E-08 0.024

22 1034 --- const K --- 29 cc/kg H2 350 44 4E-10 0.001 51 1.5E-09 0.005

The crack growth results along with the crack surface observations support the conclusion that 

after going up to 350°C, slow oxidation of Ni-metal bridges is occurring in the crack produced at 

50°C, and this is reducing or removing DCPD current conduction paths behind the crack front 

causing an artificially high CGR during this oxidation event. The very similar CGRs between the 

tests at 10 and 30 MPa√m suggest that very little IGSCC growth occurred after returning to 

350°C even with ~35% IG engagement in the MHI specimen and ~20% IG engagement in the 

AREVA specimen produced by transitioning at 50°C.
3-75

 

Figure 3-80 Optical Image of the Crack Growth Surface of the AREVA Alloy 52 

Specimen CT032 (left) and the MHI Alloy 52 Specimen CT033 (right)

Figure 3-81 Side Surface Optical Image (top) and SEM-BSE Image (bottom) of Cracking 

in the AREVA Alloy 52 Specimen CT032 Showing Both TG and IG Growth
3-76

Figure 3-82 Side Surface Optical Image (top) and SEM-BSE Image (bottom) of Cracking 

in the MHI Alloy 52 Specimen CT033 Showing Both TG and IG Growth

Figure 3-83 SEM-BSE of the Side Surface of the Leading Crack Growth Front of CT033 

Showing Both IG and TG Cracking
3-77

Figure 3-84 SEM-BSE of a Leading Crack Tip in CT033 Highlighting IG Cracking

3.2.3 KAPL Alloy 52M Welds

Characterizations, sample preparations and testing have been performed on three alloy 52M 

weldments received from KAPL. A brief description of the welds and weld metal compositions 

was given earlier in Table 2-1. Photographs of the V-groove and narrow gap mockups are 

presented in Figure 3-85. These welds were produced under prototypic best practice conditions 

and welding procedures. The third alloy 52M weldment was the same weld metal heat and 

narrow-gap configuration as the prototypic narrow gap weld, but re-fuse passes were applied 

between each weld pass to intentionally produce ductility dip cracks. Based on metallographic 

examinations, the individual weld blocks were sectioned by electro-discharge machining to 

create blanks for CT and thin sheets for more detailed microstructural examinations. Most 

characterization effort was placed on the alloy 52M weld with known weld cracks.
3-78

Figure 3-85 Alloy 52M Welds from KAPL: (a) Dissimilar Metal V-Groove Weld of Alloy 

EN52M Joining 304 SS and Carbon Steel and (b) Alloy EN52M Narrow Gap 

Weld Joining Alloy 690

Specimens CT040 and CT041 were machined from the center of the alloy 52M narrow-gap weld 

and alloy 52M V-groove weld, respectively. This is illustrated in Figures 3-86 and 3-87. 

Metallographic and SEM analyses were performed on the alloy 52M weld with hot cracks to 

determine the location of the ductility dip cracks. Optical imaging was useful in mapping out the 

location of defects across entire width of the CT blanks while SEM was used to study the 

defects in greater detail. As shown in Figure 3-88, the majority of the defects were short cracks 

along grain boundaries, and the density of these cracks was low. Because the cross-sectional 

area of the as-received weldment was only slightly larger than a 0.5T CT specimen, only a few 

regions of the weld could be selected for crack growth testing. Figure 3-89 shows the 

positioning of specimens CT042 and CT043 on the CT blanks, while the yellow boxes in Figure 

3-88 show these CT locations relative to the observed weld defects in one of the metallography

KAPL 304SS-carbon steel 

alloy 52M V-groove weld

KAPL alloy 690/52M/690 

narrow gap weld

(a)

(b)
3-79

specimens. Specimen CT042 is positioned off-center to intersect a higher density of weld 

cracks, while CT043 is positioned near the center where fewer cracks were observed. All four 

alloy 52M specimens were pre-cracked in air to a depth of ~1.2 mm.

Figure 3-86 Photos of KAPL Alloy 52M Narrow Gap Weld Blank “A” and CT040 

Specimen Machined from the Blank

Figure 3-87 Photos of KAPL Alloy 52M V-Groove Weld Blank “A” and CT041 Specimen 

Machined from the Blank
3-80

Figure 3-88 Overview of Defects in the KAPL Alloy 52M Weld with Known Weld Cracks

Figure 3-89 Photos of Specimens Cut from KAPL Alloy 52M Narrow Gap Weld 

Containing Hot Cracks. Blank a (CT042) Is Positioned Off-Center and near 

the Bottom of the Weldment to Insect a High Density of Weld Cracks, While 

Blank B (CT043) Is Positioned near the Center of the Weld Where No Weld 

Cracks Were Observed
3-81

3.2.3.1 KAPL Alloy 52M Narrow Gap and V-Groove Weld Testing (CT040 & CT041)

Testing was performed in simulated PWR primary water at either 350°C with 20 cc/kg dissolved 

H2 or, later in the test, 360°C and 25 cc/kg H2. These hydrogen concentrations were selected to 

obtain ECP conditions at the Ni/NiO transition. An overview of the entire test is presented in 

Figure 3-90. During in-situ pre-cracking and initial transitioning steps at R = 0.7, low CGRs 

were observed, so steps were duplicated at a more aggressive R of 0.5 starting at ~180 h. 

CGR response increased significantly with both samples reaching rates >10-6 mm/s at 0.1 Hz. 

The V-groove weld sample exhibited higher CGRs than the narrow-gap weld as the cyclic 

frequency was reduced first to 0.01 and then to 0.001 Hz.

As transitioning steps continued, higher CGRs continued to be measured in the V-groove weld 

sample than for the narrow-gap weld sample. This is illustrated in Figure 3-91. Rates during 

cycle + hold were 1.6x10-8 mm/s for the V-groove weld, somewhat higher than identified for 

previous alloy 52 weld metal tests and ~2X higher than the narrow-gap weld. The decision was 

made to switch to constant K conditions at ~1130 h and investigate the SCC response. Crackgrowth rates of 3.6x10-9 mm/s and ~7x10-10 mm/s can be seen for the V-groove and narrow-gap 

alloy 52M weld specimens, respectively. Stable SCC propagation is seen throughout the 

constant K period for the V-groove weld specimen in Figure 3-96, while growth, if any, appears 

to have stalled in the narrow-gap weld specimen.

Figure 3-90 Overview of the Entire Test on the KAPL Alloy 52M Narrow Gap (CT040) 

and V-Groove (CT041) Specimens
3-82

Figure 3-91 Response During Initial Cycle + Hold Transitioning Steps on the KAPL 

Alloy 52M Narrow Gap (CT040) and V-Groove (CT041) Specimens

Figure 3-92 Response During Initial Constant K Step on the KAPL Alloy 52M Narrow 

Gap (CT040) and V-Groove (CT041) Specimens

Gentle cycling was restarted to move the crack front forward slightly and straighten the crack 

front, but since higher propagation rates were not observed during retransitioning, the decision 

was made to increase the K level for both specimens. Cycling at 0.1 Hz (R = 0.5) was 

established under dK/da loading at ~2165 h with the NG sample increasing from 30 to 

35 MPa√m and the V- groove (VG) sample increasing from 32 to 39 MPa√m. The CGR 
3-83

response during this step is documented in Figure 3-93 showing ~390 and 730 μm of crack 

extension respectively for the narrow groove (NG) and VG specimens over the 24-h period. 

Transitioning was then performed by decreasing the cyclic frequency and moving to a cycle + 

hold at ~2330 h. Higher CGRs were again observed during all loading conditions for the VG 

than for the NG sample. Transitioning steps were continued until constant K (35 MPa√m in the 

NG sample and 40 MPa√m in the VG sample) was established at ~2650 h as shown in Figure 

3-94. Propagation rate for the NG specimen was initially stable at 1.3x10-9 mm/s, similar to 

what has been observed in previous alloy 52M materials tested at PNNL. The V-groove 

specimen exhibited a higher growth rate of ~3.0x10-9 mm/s for about 600 h and then appeared 

to slow down at ~3200 h. The initial CGR for the V-groove specimen is similar to the value 

measured at the lower K value.

Figure 3-93 Crack-Growth Response During the K Increase by dK/da for KAPL Alloy 

52M Specimens CT040 and CT041
3-84

Figure 3-94 Crack-Growth Response from Cycle + Hold to Constant K for CT040 and 

CT041

To help promote SCC, a cycle + hold loading condition was re-established and the test 

temperature increased to 360°C while holding the ECP on the Ni/NiO line (25 cc/kg H2). Once 

again, CGRs started higher when switching back to constant K but decreased after ~500 h. 

This is illustrated in Figure 3-95 with the VG specimen slowing from 3.5x10-9 mm/s to 2.3x10-9

mm/s. The rate for the NG specimen starts off at a low rate of ~6x10-10 mm/s and growth stops

after 1000 h. This test was ended after ~1700 h under constant K (35-40 MPa√m) conditions at 

360°C and 25 cc/kg H2. The CGRs for both samples are similar to the previous measurements 

at 350°C with slightly lower K values. A summary of the corrected step-by-step data obtained 

during this test is presented in Table 3-15. 

Figure 3-95 Crack Growth Response During Constant K at 360°C for the KAPL Alloy 

52M Narrow Gap (CT040) and V-Groove (CT041) Weld Specimens
3-85

Table 3.8 Corrected Data Summary for KAPL Alloy 52M Specimens CT040 & CT041

CT040

KAPL A52M NG Blank A

CT041

KAPL A52M V-groove Blank A

Test 

Phase

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax 

(MPa√m)

CGR

(mm/sec)

Crack 

Extension 

(mm)

Kmax 

(MPa√m)

CGR 

(mm/sec)

Crack 

Extension 

(mm)

1 ~3 0.3 5 0 air precrack RT 21 6.8E-05 0.40 21 6.2E-05 0.40

2 ~2 0.5 5 0 air precrack RT 23 4.0E-05 0.35 24 3.7E-05 0.35

3 ~2 0.6 5 0 air precrack RT 26 2.6E-05 0.35 26 2.6E-05 0.35

4 ~3 0.7 5 0 air precrack RT 26 1.3E-05 0.20 26 1.2E-05 0.20

5 86 0.7 0.1 0 20 cc/kg H2 350 31 7.8E-07 0.241 32 9.8E-07 0.319

6 100 0.7 0.01 0 20 cc/kg H2 350 31 1.3E-07 0.062 32 1.4E-07 0.078

7 153 0.5 0.1 0 20 cc/kg H2 350 31 1.6E-06 0.443 33 3.5E-06 0.784

8 100 0.5 0.01 0 20 cc/kg H2 350 31 3.5E-07 0.116 34 9.6E-07 0.302

9 242 0.5 0.001 0 20 cc/kg H2 350 31 6.9E-08 0.055 34 1.4E-07 0.127

10 454 0.5 0.001 2.5 20 cc/kg H2 350 31 1.1E-08 0.012 34 1.8E-08 0.033

11 647 --- const K --- 20 cc/kg H2 350 31 ~8E-10 0.002 34 4.6E-09 0.011

12 380 0.5 0.001 2.5 20 cc/kg H2 350 31 1.8E-08 0.007 35 6.8E-09 0.021

13 26 0.5 0.1 0 20 cc/kg H2 350 31->37 increasing 0.439 35->45 increasing 0.899

14 47 0.5 0.01 0 20 cc/kg H2 350 37 1.1E-06 0.199 45 2.7E-06 0.436

15 94 0.5 0.001 0 20 cc/kg H2 350 37 1.6E-07 0.061 46 4.5E-07 0.158

16 84 0.5 0.001 2.5 20 cc/kg H2 350 37 1.3E-08 0.007 46 1.8E-08 0.017

17 32 0.5 0.001 0 20 cc/kg H2 350 37 1.4E-07 0.013 46 4.2E-07 0.044

18 195 0.5 0.001 2.5 20 cc/kg H2 350 37 2.3E-08 0.016 46 5.1E-08 0.041

19 704 --- const K --- 20 cc/kg H2 350 37 1.6E-09 0.004 46 3.8E-09 0.010

20 159 0.5 0.001 2.5 20 cc/kg H2 350 37 1.6E-08 0.008 46 5.3E-08 0.030

21 146 0.5 0.001 2.5 25 cc/kg H2 360 37 2.1E-08 0.010 47 7.8E-08 0.037

22A 500 --- const K --- 25 cc/kg H2 360 37 ~1E-09 0.001 47 4.2E-09 0.009

22A 1176 --- const K --- 25 cc/kg H2 360 37 ~5E-10 0.001 47 2.8E-09 0.011

After testing, a slice was taken from each of the two CT specimens for preparation of an interior 

crack profile observation, and the other piece was fatigued open in air to reveal the crack growth 

surface. Figures 3-96 and 3-97 show optical and SEM-BSE micrographs of crack growth 

surface of CT040 and CT041, respectively. Strong changes in loading conditions are apparent 

along the crack growth surface of both specimens and are indicated by the yellow lines. In 

comparing the two surfaces the higher CGR of the VG specimen is apparent in each major 

region of the test. While the final crack front of the narrow gap specimen (CT040) is relatively 

straight with little or no strong SCC protrusions, the VG specimen (CT041) appears to have 

clear SCC protrusions along the entire crack front. The cut line for the crack profile specimens 

is shown on the crack growth surface images, and optical micrographs of the crack profile 

images are shown in Figures 3-98 and 3-99 for CT040 and CT041, respectively. The final crack 

front of the narrow gap specimen (CT040) is relatively straight with no obvious indication of IG 

engagement. The crack profile image shows that along the cut line, the precracking ended in 

the interior of a grain, and the subsequent crack growth appears to be essentially straight 

through the grain. Towards the end of the test, a grain boundary is encountered, but the 

cracking does not appear to be IG as it moves along the boundary. This suggests that the 

majority of the cracking in the narrow gap specimen is TG. While the precracking of the VG

specimen (CT041) also ends in the interior of a grain, the crack does eventually find a grain 
3-86

boundary and grow intergranularly. The crack does wander away from the boundary for a 

period, but it eventually finds the boundary again. The crack profile reinforces the observations 

of the crack growth surface that the cracking is significantly IG. The clear difference in CGR

between the two types of welds made using the same wire is an interesting result that warrants 

further observations and supports the need to study welds made using production welding 

parameters.

Figure 3-96 Crack Growth Surface of the KAPL Alloy 52M Narrow Gap Specimen 

CT040: (a) Optical Image of the Overall Crack Growth Surface and (b) SEMBSE Image of the Area Highlighted in (a) 

(a)

(b)
3-87

Figure 3-97 Crack Growth Surface of the KAPL Alloy 52M V-Groove Specimen CT041: 

(b) Optical Image of the Overall Crack Growth Surface and (b) SEM-BSE 

Image of the Area Highlighted in (a) 

Figure 3-98 Crack Profile of the KAPL Alloy 52M Narrow Gap Specimen CT040 

(a)

(b)
3-88

Figure 3-99 Crack Profile of the KAPL Alloy 52M V-Groove Specimen CT041

Analytical electron microcopy analysis was performed on both CT040 (Figures 3-100 to 3-103) 

and CT041 (Figures 3-104 to 3-107) to provide a better understanding of the crack 

morphologies. High magnification SEM-BSE imaging of the leading crack tip of CT040 (Figures 

3-100 and 3-101) shows the TG nature of the crack even though it appears to be oriented with

the aligned grains. At the highest magnification (Figure 3-101), penetrative oxidation accented

the entire leading TG crack, suggesting the crack was not active for some time. The bright

contrast along the crack wall is most likely a Nb-rich matrix carbide that the TG crack

encountered. EBSD of the leading crack region (Figure 3-102) as well as of the base

microstructure ~1-2 mm ahead of the leading crack tip (Figure 3-103) was performed to better

illustrate not only the microstructure, but the local misorientation (which can be interpreted as a

measure of strain) in the region of the SCC test. The solid yellow line in the pattern quality map

in Figure 3-102 illustrates the TG nature of the SCC crack. The inverse pole figure (IPF) map

shows in more detail the grain microstructure, and the local misorientation map provides an

indication of a high amount of deformation in the grains surrounding the SCC crack. This

microstructure and local misorientation can be compared to the base microstructure of the weld

as seen in Figure 3-103 where the grains appear to be of similar shape and size, but with much

less local deformation.

EBSD of the leading crack tip as well as base microstructure (~1-2 mm ahead of the leading 

crack tip) of CT041 is presented in Figures 3-104 and 3-105, respectively. The IPF figure 

indicates that propagation during part of the SCC test was IG, but eventually ended TG 

(Figure 3-104). Similar as for CT040, the local misorientation map of the leading crack-tip 

region in CT041 (Figure 3-104) shows a high density of deformation as compared to the base 

microstructure (Figure 3-105).

A transmission electron microscopy (TEM) sample was prepared by a focused-ion beam (FIB) 

system from a secondary IG crack tip (dashed yellow box in Figure 3-99) to ascertain the local 

grain boundary chemistry of the sample (Figure 3-106). SEM-BSE imaging of the sample 

shows no obvious secondary IG precipitation, but the bright contrast ahead of the leading tip 

suggests Cr depletion/Ni enrichment. Penetrative oxidation tapers to the leading secondary tip, 

which suggests this was an actively growing crack during the end of the test. Approximately 

500 nm behind the IG crack tip, a TG crack can be seen without any contrast change ahead of 

the tip which would be associated with a chemistry change. Scanning TEM/EDS elemental 

maps taken of this crack region (Figure 3-107) confirm that there is Cr depletion/Ni enrichment 

~1 μm ahead of the leading IG tip, and no chemistry change ahead of the TG crack (which is 

not as evident due to the thickness of the TEM foil). Interestingly, a small IG oxide particle 

which is Al and Zr rich is observed ahead of the crack tip which was not observed in the SEMBSE image. Again, this is most likely due to the small interaction volume of the back-scatter 
3-89

technique. No other secondary IG phases were observed. The penetrative oxidation along the 

crack walls was observed to be Cr rich with some Ni, but with a lower Fe content.

Figure 3-100 SEM-BSE of the Leading Crack Tip in the CT040 Cross-Section Sample. 

Dashed Yellow Box Highlights the Region of Interest for EBSD Analysis in 

Figure 3-102

Leading crack tip
3-90

Figure 3-101 SEM-BSE High Magnification Micrograph of the Leading TG SCC Crack Tip 

in CT040 (higher magnification of the dashed yellow box shown in bottom 

figures). Note the Sample Is Rotated 90° from the Previous Figure

Possible hot 

cracking
3-91

Figure 3-102 EBSD of CT040 (IPF, misorientation, and image quality maps) from the 

Yellow Dashed Box in Figure 3-100. The Yellow Line in the Pattern Quality 

Map Shows the Approximate SCC Crack
3-92

Figure 3-103 EBSD of CT040 (IPF maps and a misorientation map) from ~1-2 mm Ahead 

of the Yellow Dashed Box in Figure 3-100
3-93

Figure 3-104 EBSD (IPF and misorientation density) of the Leading SCC Tip of CT041. 

Portions of the SCC Test Were Observed to Be IG, but the Leading Crack 

Tip Ended Transgranularly

. 

Figure 3-105 EBSD (IPF and misorientation density) ~1-2 mm Ahead of the Leading SCC 

Tip in CT041. Note That the Analysis Orientation Is Rotated 90 Degrees 

from the Previous Figure (i.e., the crack would be running top to bottom)
3-94

Figure 3-106 SEM Images of a Secondary Crack in CT041. A FIB-TEM Foil Was Prepared 

from This Region That Showed the IG Crack Split off into a TG Crack 

Before the End (identical orientation as Figure 3-99) 
3-95

Figure 3-107 STEM (BF) and EDS Elemental Maps of the Secondary SCC Tip of CT041 

Shown in Figure 3-106. Note That the Analysis Orientation of the SCC Tip 

Was Rotated from That Which Is Shown in Figure 3-106

3.2.3.2 KAPL Alloy 52M Narrow Gap Weld with Weld Cracks (CT042 and CT043)

The CT specimen aligned with the preexisting weld cracks (CT042) was cut from the weld blank 

so that the crack notch was ~2.8-3.0 mm from the region containing a low density of IG cracks. 

A standard precracking procedure in air was used to produce a precrack length of ~1.2 mm in 

both specimens, thus allowing ~1.6-1.8 mm of in-situ crack extension before reaching the region 

of material in CT042 containing cracks. The test was initiated in 350°C water, and an overview 

of the entire in-situ test is provided in Figure 3-108. As indicated by the overview plot, several 

different transitioning steps were applied in the first phase of the test. With no prior information 

about the cracking susceptibility of the material, it was decided to begin in-situ precracking and 

transitioning at a conservative R of 0.7, however low CGRs indicative of a highly resistant 

material were obtained and R was changed to a more aggressive value of 0.5 at 300 h as 

shown in Figure 3-109. CGR values measured at 0.001 Hz and at this same cyclic frequency 

with a 2.5 h hold were typical low values observed in other tests on alloy 152/52 as shown in 
3-96

Figure 3-110. A higher CGR was not seen for the specimen aligned to intersect the preexisting 

weld cracks. Continuous cycling at 0.001 Hz was restarted at ~900 h and was followed by 

checking for an increase in susceptibility under two different sawtooth waveforms. The 

observed propagation rates were consistent with rates observed in prior steps, indicating typical 

response from both specimens.

Figure 3-108 Overview of the Entire Test on the KAPL Alloy 52M Narrow Gap Weld 

Specimens (CT042 and CT043) with Preexisting Weld Cracks
3-97

Figure 3-109 In Situ Precracking and Transitioning of the KAPL Alloy 52M Narrow Gap 

Weld Specimens (CT042 & CT043) with Known Hot Cracks

Figure 3-110 Continued Transitioning Steps Performed on the KAPL Alloy 52M Narrow 

Gap Weld Specimens (CT042 and CT043) with Weld Cracks

Having tried several different combinations of frequency and R during transitioning with typical 

alloy 152/52 crack growth response, and because the crack length was nearing the region in 

CT042 with aligned cracks, it was decided to transition to constant K. The sawtooth waveform 
3-98

was converted to 0.001 Hz symmetric cycle + 2.5 h hold with R of 0.5 at 1500 h, and a steady 

rate of ~1.0x10-8 mm/s was observed in both specimens as shown in Figure 3-111. This rate 

was consistent with CGRs observed in other alloy 152/52 specimens, and the test was 

converted to constant K at ~1750 h. A steady propagation rate of ~1.4x10-9 mm/s was observed 

over the next ~400 h with no sign of increased propagation rate in the specimen aligned to 

intersect the IG weld cracks. Transitioning was restarted, and over the next several thousand 

hours of testing, cyclic loading conditions were varied, the K level was increase by 5 MPa√m (by 

dK/da), and the temperature was brought up to 360°C (see overview in Figure 3-108). Cyclic 

loading conditions were then returned to 0.001 Hz + 2.5 h hold where propagation rates of 

1.6x10-8 and 1.9x10-8 mm/s were observed in the weld crack aligned and non-aligned 

specimens, respectively. These rates were ~1.7x higher than prior observations at these cyclic 

loading conditions, and the test was converted to constant K. Over the next 1300 h of testing, a 

relatively constant propagation rate of ~2.8x10-9 mm/s was observed (Figure 3-112) in the 

specimen not aligned with weld cracks while the specimen aligned to intersect preexisting

cracks showed a steady rate of ~1.1x10-9 mm/s for 1000 hours and then no further growth was 

observed for the remaining 300 h. With lower propagation rates consistently observed in the 

aligned specimen, it was decided to end the test to examine the specimens. Table 3-17 lists a 

summary of the corrected step-by-step data obtained during this test.

Figure 3-111 First Observation of Constant K Crack Growth Response on the KAPL 

Alloy 52M Narrow Gap Weld Specimens (CT042 & CT043) with Known Hot 

Cracks. Slightly Lower CGR in the Specimen Aligned to Intersect Hot 

Cracks
3-99

Figure 3-112 Second and Final Observation of Constant K Crack Growth Response of 

the KAPL Alloy 52M Narrow Gap Weld Specimens (CT042 & CT043) with 

Known Hot Cracks 

Table 3-17 Corrected Data Summary for KAPL Alloy 52M Narrow Gap Weld Specimens 

CT042 and CT043 with Preexisting Weld Cracks

CT042

KAPL A52M NG HC aligned

CT043 KAPL A52M

NG HC non-aligned

Test 

Phase

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax 

(MPa√m)

CGR

(mm/s)

Approx. 

Crack 

Extension 

(mm)

Kmax 

(MPa√m)

CGR 

(mm/s)

Approx. 

Crack 

Extension 

(mm)

1 ~3 0.3 5 0 air precrack RT 21 3.7E-05 0.40 21 5.0E-05 0.40

2 ~2 0.5 5 0 air precrack RT 23 2.2E-05 0.35 24 3.2E-05 0.35

3 ~2 0.6 5 0 air precrack RT 25 1.3E-05 0.35 26 2.2E-05 0.35

4 ~3 0.7 5 0 air precrack RT 25 7.8E-06 0.20 26 1.3E-05 0.20

5 86 0.7 0.1 0 20 cc/kg H2 350 30 4.7E-07 0.202 31 9.6E-07 0.281

6 159 0.7 0.01 0 20 cc/kg H2 350 30 9.1E-08 0.049 31 1.3E-07 0.107

7 49 0.5 0.01 0 20 cc/kg H2 350 30 4.7E-07 0.098 31 5.5E-07 0.145

8 261 0.5 0.001 0 20 cc/kg H2 350 30 6.7E-08 0.060 32 7.0E-08 0.105

9 338 0.5 0.001 2.5 20 cc/kg H2 350 30 1.3E-08 0.019 32 1.1E-08 0.051

10 241 0.5 0.001 0 20 cc/kg H2 350 30 5.3E-08 0.040 32 5.4E-08 0.076

11 156 0.5 480/20 0 20 cc/kg H2 350 30 1.0E-07 0.057 32 1.2E-07 0.093

12 193 0.5 980/20 0 20 cc/kg H2 350 30 6.1E-08 0.042 32 6.1E-08 0.077

13 280 0.5 0.001 2.5 20 cc/kg H2 350 30 9.4E-09 0.012 32 1.1E-08 0.048

14 420 --- const K --- 20 cc/kg H2 350 30 1.2E-09 0.004 32 1.6E-09 0.038

15 405 0.6 0.001 0 20 cc/kg H2 350 30 3.4E-08 0.040 32 3.6E-08 0.076

16 265 0.6 0.001 2.5 20 cc/kg H2 350 30 6.3E-09 0.010 32 6.6E-09 0.044

17 175 0.5 0.001 1 20 cc/kg H2 350 30 1.6E-08 0.009 32 1.6E-08 0.045

18 43 0.5 0.001 1 20 cc/kg H2 350 30->35 1.0E-07 0.014 32->37 1.2E-07 0.045

19 413 0.5 0.001 1 20 cc/kg H2 350 35 3.2E-08 0.067 37 3.7E-08 0.095

20 190 0.5 0.001 2.5 20 cc/kg H2 350 35 1.4E-08 0.010 37 2.1E-08 0.047

21 355 0.5 0.001 2.5 25 cc/kg H2 360 35 1.6E-08 0.019 37 1.9E-08 0.051

22 1289 --- const K --- 25 cc/kg H2 360 35 1.1E-09 0.003 37 2.8E-09 0.047
3-100

Post-test examinations consisted of characterizing both the crack growth surface and a series of 

crack profiles obtained from side surfaces of the crack. To accomplish this, both specimens 

were serially sectioned as shown in Figure 3-113 prior to air fatiguing open the specimens. Five 

slices were obtained from the CT042 (weld cracks aligned), but due to a machining error, only 

four slices were obtained from CT043. The serial slices were placed in metallography mounts 

and polished to a high luster using colloidal silica as the final polishing agent. Crack profile 

images for CT042 and CT043 are shown in Figures 3-114 and 3-115, respectively. The crack 

profiles of CT042 show that the density of the preexisting IG cracks was too low and the 

distance from the SCC crack was too far for any cracks to be intersected by the crack front. In 

addition, the grain boundaries (and IG weld cracks) were at a steep angle to the geometric 

crack plane of the specimen, and the steep angle made it difficult for the SCC crack to grow 

favorably along the grain boundaries. Somewhat surprisingly, the crack profile images of the 

specimen that was not supposed to be aligned with weld cracks shows that a few IG cracks 

were in the vicinity of the crack path. However, as with the crack-aligned specimen, only a few 

weld cracks were present, and they were far from the SCC crack and at a steep angle to it. The 

grain boundaries are much better aligned with the geometric crack plane of the specimen. 

Instances of growth along grain boundaries are apparent, and the more favorable alignment is 

likely responsible for the higher constant K CGR in CT043.

Figure 3-113 Post-Test Serial Sectioning Plan for KAPL Alloy 52M NG Weld Specimens 

with Weld Cracks (CT042 and CT043)
3-101

Figure 3-114 Crack Profile of Images from CT042, the Weld Specimen Aligned with Hot 

Cracks

Figure 3-115 Crack Profile of Images from CT043, the Weld Specimen Not Aligned with 

IG Weld Cracks. The Profile Images Show Hot Cracks Below the SCC Test 

Plane

Figures 3-116 and 3-117 show the crack growth surface of the remaining piece of the CT 

specimens that was not used for crack profile observations. The edge of the specimen 

corresponding to the last serial section taken from the specimens is indicated, and the yellow 

line denotes the boundary between air precracking and in situ testing. The in-situ crack growth 

surface of the crack-aligned specimen (CT042, Figure 3-116) shows a lower amount of growth. 

A large number of ridges run along the length of the crack, and it is thought that these indicate 

jumps in crack growth plane. The areas inside the yellow boxes are the only regions along the 

crack surface that are clearly IG based on the optical images. No obvious indications of 
3-102

intersected weld cracks are present. While there are no fingers of obvious SCC extension on 

the crack growth surface of the non-aligned specimen (CT043, Figure 3-117), the greater 

amount of in-situ crack extension and the fewer number of ridges are suggestive of better SCC 

engagement. As with CT042, there are no obvious indications of intersected weld cracks.

The post-test examination of these two specimens has revealed a density of weld cracks too 

low or too far from the SCC crack plane to provide any insight as to whether such preexisting IG 

cracks can affect SCC crack growth. An unintended outcome of the test on these two 

specimens is, however, a better understanding of the importance of grain boundary orientation 

relative to the geometric crack plane of the specimens. With these highly resistant welds that 

have very large, elongated grains with apparently low susceptibility to IG cracking, the 

difference in the CGR of the two specimens suggests that the highest possible CGR can only be 

determined if the grain boundaries are well aligned with the geometric crack growth plane of the 

specimen.

When considering the effect of poor welding conditions on CGR, there is also the possibility that 

unfavorable microstructure and/or segregation may be present in this weld containing hot 

cracks. One method to assess this affect is to compare the CGR of these specimens to the 

KAPL NG specimen that was fabricated without re-fuse passes (CT040). Since the grain 

boundaries in CT040 were favorably aligned with the geometric crack plane, CT043 with its

favorable grain boundary orientation is the appropriate specimen with weld cracks to use for the 

comparison. Using the highest constant K CGR observed, CT043 exhibits a ~2x higher CGR

than the standard specimen (CT040). This may indicate a small detrimental effect of chemistry 

or microstructure on SCC susceptibility for welds produced using parameters that promote weld 

cracks, however the current results are likely within the test reproducibility.

Figure 3-116 Crack Growth Surface from CT042, the Weld Specimen Aligned with Hot 

Cracks
3-103

Figure 3-117 Crack Growth Surface from CT043, the Weld Specimen Not Aligned with 

Hot Cracks

SEM-BSE analysis of the leading SCC crack tip was performed (Figure 3-118) and illustrates 

the high level of local deformation as evidenced by the mottled contrast in the grains 

surrounding the tip. Higher magnification of the leading tip shows that it ended intergranularly, 

but the penetrative oxidation surrounding the entire tip suggests that it was not an active crack 

tip at the end of the test. As shown in Figure 3-115, a TEM sample was prepared from an IG 

weld crack adjacent to the SCC plane in CT043 (Figure 3-119) and was subsequently analyzed 

(Figures 3-120 and 3-121). The discontinuous nature of the weld cracks can be observed in the 

SEM-BSE image in Figure 3-119, as well as very small (75-100 nm), IG precipitation. No 

apparent penetrative oxidation is observed in conjunction with the hot cracks, which suggests 

no water reached these preexisting cracks during SCC testing. Higher magnification 

STEM/EDS elemental mapping of the IG cracks and the adjacent grain boundary shows the 

presence of small (less than 100 nm) Cr, Ti and Nb rich precipitates, but no unique chemistry 

associated with the cracks themselves.
3-104

Figure 3-118 SEM-BSE Image of the Side Surface of the Leading Crack Growth Tip of 

CT043

Figure 3-119 SEM-BSE Image of a TEM FIB Sample of a Weld Crack in CT043 Taken from 

the Dashed Yellow Box Region of Figure 3-115. The Solid Green Box in the 

Top Image Shows the Region of Interest in the Higher Magnification Image 

at the Bottom
3-105

Figure 3-120 STEM BF Image and EDS Elemental Maps of the IG Weld Crack Region in 

CT043. A Higher Magnification Examination Was Taken of the Dashed 

Yellow Box and Is Shown in Figure 3-121. No O-K Signal Was Detected in 

These Cracks and Grain Boundary Precipitates Are Enriched in Cr and Ti

Figure 3-121 STEM-BF Image and EDS Elemental Maps of the Weld Crack in CT043 from 

the Yellow Dashed Box in Figure 3-120. At Higher Magnification, Small (100 

nm) Nb-Rich Precipitates Are Observed on the Grain Boundary

3.2.4 Special Metals Alloy 52MSS Weld (CT050)

The alloy 52MSS weld was provided to PNNL and EPRI by Special Metals and was a V-groove 

weld (NX77W3UK) in alloy 690 plate. Alloy 52MSS is identified as ERNiCrFe-13 and has been 

proposed as a replacement for alloy 52M (ERNiCrFe-7A) primarily for its improved resistance to 

ductility dip cracking (DDC). A standard 0.5T CT specimen was machined and was tested in 

combination with an ANL alloy 152v2 specimen CT049 discussed earlier in the chapter. The 

alloy 152v2 CT049 was a higher priority specimen and was the control specimen during the 

experiment. A summary of test conditions and corrected response for the alloy 52MSS CT050 

during each phase of the test is shown in Table 3-18 and an overview of the test highlighting 

constant K evaluations is presented in Figure 3-122. The measured SCC growth rates are also 

listed in Table 3-19 along with their corresponding K levels that were decreasing during the test 

because the cyclic CGRs were much higher for the controlling alloy 152v2 CT049 specimen. 

Load shedding to maintain a constant K for CT049 resulted in a lower applied K for CT050.
3-106

Table 3-18 Corrected Data Summary for SM Alloy 52MSS Narrow Weld Specimen 

CT050

Test 

Phase

Duration

(h) R Freq (Hz)

Hold 

(h)

Water 

Chem. 

Conditions

Tem

p 

(°C)

Kmax 

(MPa√

m)

CGR 

(mm/s)

Approx. 

Crack 

Ext 

(mm)

1 ~3 0.3 5 0 air precrack RT 21 5.2E-05 0.40

2 ~2 0.5 5 0 air precrack RT 23 3.2E-05 0.35

3 ~2 0.6 5 0 air precrack RT 25 2.2E-05 0.35

4 ~3 0.7 5 0 air precrack RT 25 8.6E-06 0.20

5 8 0.5 0.1 0 25 cc/kg H2 360 30 5.2E-06 0.141

6 85 0.5 0.01 0 25 cc/kg H2 360 30 9.5E-07 0.274

7 258 0.5 0.001 0 25 cc/kg H2 360 30 1.7E-07 0.147

8 119 0.5 980/20 0 25 cc/kg H2 360 30 1.7E-07 0.066

9 480 0.5 0.001 2.5 25 cc/kg H2 360 30 1.9E-08 0.039

10 310 --- const K --- 25 cc/kg H2 360 30 1.9E-09 0.003

11 53 0.5 0.001 2.5 25 cc/kg H2 360 30 Not 

Meas.

0.003

12 114 0.5 600/12 0 25 cc/kg H2 360 29 2.4E-07 0.084

13 220 0.5 600/12 1 25 cc/kg H2 360 29 3.3E-08 0.035

14 93 0.5 600/12 2 25 cc/kg H2 360 29 2.5E-08 0.010

15 367 0.5 600/12 1 25 cc/kg H2 360 29 4.4E-08 0.060

16 134 0.5 600/12 2 25 cc/kg H2 360 29 2.7E-08 0.012

17 267 --- const K --- 25 cc/kg H2 360 29 1.7E-09 0.001

18 156 0.5 0.01 0 25 cc/kg H2 360 28 8.9E-07 0.489

19 65 0.5 0.001 0 25 cc/kg H2 360 28 1.0E-07 0.027

20 93 0.5 600/12 0 25 cc/kg H2 360 28 2.1E-07 0.064

21 76 --- const K --- 25 cc/kg H2 360 28 <5E-10 0.006

22 115 0.5 600/12 0 25 cc/kg H2 360 27 1.9E-07 0.073

23 172 0.5 1000/12 0 25 cc/kg H2 360 27 1.1E-07 0.074

24 213 0.5 1000/12 2 25 cc/kg H2 360 27 2.1E-08 0.016

25 380 0.5 1000/12 10 25 cc/kg H2 360 27 5.7E-09 0.007

26 611 --- const K --- 25 cc/kg H2 360 27 9.2E-10 0.003

27 116 0.5 600/12 0 25 cc/kg H2 360 27 1.3E-07 0.049

28 70 0.35 600/12 0 25 cc/kg H2 360 26 2.9E-07 0.072

29 95 0.35 1000/12 0 25 cc/kg H2 360 26 1.7E-07 0.058

30 240 0.35 5000/12 0 25 cc/kg H2 360 26 3.8E-08 0.035

31 348 0.35 25000/12 0 25 cc/kg H2 360 26 1.2E-08 0.016

32 240 0.35 25000/12 3.5 25 cc/kg H2 360 25 1.2E-08 0.009

33 849 --- const K --- 25 cc/kg H2 360 25 3.9E-10 0.003
3-107

Figure 3-122 Overview of the Crack Growth Response of the Alloy 52MSS Specimen 

CT050

Table 3-19 SCC Crack Growth Test Conditions for CT050 Showing the CGRs for Each 

Constant K Evaluation

Loading Condition K (MPa√m) CGR (mm/s)

cyclic loading 30-25 Cyclic loading CGRs were comparable to 

prior tests on alloy 52/52M.

1st constant K 30 1.0x10-9

2nd constant K 29 1.9x10-9

3rd constant K 28 ≤5x10-10

4th constant K 27 ~8x10-10

5th constant K 25 1.0x10-9

Two examples of the low SCC growth rates measured at constant K are given in Figures 3-123

and 3-124 out of the five attempts made during the experiment. These evaluations revealed a 

reasonably stable crack growth response at ~1.9 and 1.0x10-9 mm/s over ~270 and 850 hours, 

respectively. It is important to note that the measured CGRs for various cycle + hold loading did 

not indicate SCC engagement or significant propagation during the hold times examined 
3-108

between 1 and 10 hours. The SCC transitioning approach employed for this test was selected 

to match the cyclic loading (rise/fall times of 600/12 and 1000/12 seconds + hold times) 

previously used by ANL for tests on the alloy 152v2 material. This approach was specifically 

requested for the ANL alloy 152v2 control specimen CT049. As a result, transitioning was not 

optimized to promote SCC engagement in the alloy 52MSS, nor was the applied K. 

Nevertheless, crack growth response during the ~6400 h test suggested that this material is 

resistant to corrosion fatigue and SCC in PWR primary water. Supporting this conclusion is the 

lack of IG cracking produced during most of the test as illustrated by the crack growth surface in 

Figure 3-125 and cross-section images in Figures 3-126 and 3-127. However, somewhat 

surprisingly some evidence for localized IG crack growth was discovered at the end of the test 

perhaps promoted by the alternative transitioning in steps 28-32 where a low R value (0.35) was 

applied along with long rise times (5000-25000 seconds). This result suggests that transitioning 

tailored for the alloy 52MSS specimen may be effective to increase SCC engagement and a 

second test may be warranted to assess SCC behavior.

Figure 3-123 Second Observation of Constant K Crack Growth Response on the Alloy 

52MSS Specimen CT050
3-109

Figure 3-124 Fifth and Final Observation of Constant K Crack Growth Response on the 

Alloy 52MSS Specimen CT050

Figure 3-125 Optical Micrograph of the CT050 Crack Growth Surface Showing Primarily 

TG Cracking. Small Partially IG Protrusions Can Be Seen at the Crack 

Front
3-110

Figure 3-126 SEM-SE of the Cross-Section of CT050 Showing the First Part of the Crack 

Growth Test Being TG and the Last 250 μM of the Test Being IG

Figure 3-127 SEM-SE of the Cross-Section of CT050 Showing the Final 250 μm of the 

Crack Growth Test Being IG

3.3 Summary of SCC Behavior in High Cr, Ni Alloy Welds

The CGR response of industry-made alloy 152, 152M, 52, 52M and 52MSS weld mockups was 

investigated in simulated PWR primary water with most tests performed at 360°C with a 

dissolved hydrogen concentration of 25 cc/kg (corresponding to the Ni/NiO stability line). A

summary of the measured constant K CGR response for the weld metal specimens at PNNL is 

shown in Figure 3-128. More than 60 measurements are identified with all CGRs <5x10-9 mm/s

and most <2x10-9 mm/s. These SCC propagation rates for the high Cr weld metals are >100X 

lower than the alloy 182/132 disposition curve also shown in Figure 3-128. Specific information 

on the individual welds is provided in Table 3-20 so that the data points can be linked back to 

the reported test data earlier in this chapter. Interestingly, slightly higher CGRs can been seen 

for several of the alloy 52 and 52M welds, while our general experience found that the alloy 152 

IG 
3-111

welds exhibited a higher degree of IG cracking on the post-test crack-growth surface. 

Estimated IG engagement is compared to the measured SCC CGRs in Figure 3-129 and 

demonstrates that the ANL v2 (alloy 152 B) and MHI (alloy 152 A) weld specimens did show 

more extensive IG cracking. Surprisingly, higher IG engagement did not result in a higher SCC 

CGR among the various weld specimens. Multiple evaluations of SCC on the ANL v2 weld 

specimens (Section 3.1.3) consistently revealed low propagation rates at constant K ending up 

at ~1x10-9 mm/s or less even though IG engagement was from 35 to 60%. Similar observations 

were observed for the MHI alloy 152 specimens where IG engagement was typically ~40%. The 

KAPL alloy 52M V-groove weld (Alloy 52M A) exhibited the most consistent and stable SCC 

CGRs (albeit only 2-5x10-9 mm/s) with an IG engagement of ~30% as indicated in Figure 3-129. 

Figure 3-128 Summary of PNNL-Measured Constant K SCC CGRs for Alloy 

152/152M/52/52M Weld Metal Specimens as a Function of Stress Intensity
3-112

Table 3-20 Weld and Specimen Information for Data Presented in Figures 3-128 to 

3-132

Weld ID Weld Information CT Specimens

Alloy 152 A MHI Alloy 152, heat 307380

U-groove weld

PNNL: CT013; CT017; CT018; CT052

ANL: MHI152-TS-1; MHI152-TS-11

Alloy 152 B ANL Alloy 152, heat WC04F6

V2 dissimilar metal weld

PNNL: CT049; CT080

GEG: c541; c576

ANL: N152-TS-1

Alloy 152 B1 ANL Alloy 152, heat WC04F6

V1 dissimilar metal weld ANL: A152-TS-2; A152-TS-4; A152-TS-5 

Alloy 152 C/C1 ANL Alloy 152, heat 509528

High/normal current weld ANL: HC152-CR-1; NC152-CR-1 

Alloy 152 D Alloy 152, heat 747136 GEG: c501

CIEMAT: E1W

Alloy 152 E Alloy 152, heat WC51G0 GEG: c510

Alloy 152 F Alloy 152, heat 146444 GEG: 525

Alloy 152 G Alloy 152, heat 706447 GEG: c555

Alloy 152M A KAPL Alloy 152M, heat WC83F8

V-groove dissimilar metal weld

PNNL: CT081

GEG: c577

Alloy 52 A AREVA Alloy 52, heat NX3926JK

butt weld 

PNNL: CT024; CT032

Alloy 52 B MHI Alloy 52, heat NX2686JK

U-groove weld

PNNL: CT025; CT033

GEG: c511

Alloy 52 C Alloy 52, heat NX6133JK GEG: c502

CIEMAT: EW

Alloy 52 D Alloy 52, heat NX6523JK GEG: c542

Alloy 52 E Alloy 52, heat NX4467JK ANL: MC52-CR-1 

Alloy 52M A KAPL Alloy 52M, heat NX5285TK 

V groove weld PNNL: CT041

Alloy 52M B1/B2/B3 KAPL Alloy 52, heat NX5285TK 

narrow groove weld PNNL: CT040; CT042; CT043

Alloy 52M C Alloy 52M, heat NX7859TK GEG: c636

Alloy 52MSS Alloy 52MSS, NX77W3UK

Special Metals V-groove weld PNNL: CT050

Comparisons were reported between SCC CGRs and IG engagement for PNNL tests on alloy 

690 CRDM, plate and bar materials in our previous NUREG/CR report [5]. These results did 

show a positive correlation with SCC propagation rates increasing with the %IG measured on 

the crack-growth surface. However, it is interesting to note that higher SCC CGRs (>1x10-8

mm/s) were not observed for the cold-worked alloy 690 materials until the IG engagement was 

greater than ~70%. IG engagement levels of 20-50% corresponded to SCC CGRs of 2-5x10-9

mm/s comparable to the highest SCC propagation rates measured on the weld specimens in 

Figure 3-129. 

In order to better assess SCC behavior for the alloy 152/152M/52/52M welds, reported crackgrowth test results from other laboratories have been obtained and plotted along with the PNNL 

data. General Electric Global Research (GEG) has evaluated the most different welds and have 

seen very similar behavior as illustrated in Figure 3-130. SCC has been evaluated on several 

welds at both laboratories including Alloy 152 B, 152M A and 52 B. The detailed comparison of 
3-113

tests on the ANL v2 weld (Alloy 152 B) was described in Section 3.1.4. In addition, GEG also 

tested Alloy 152 A and found similar CGR response during cycle + hold loading. 

Figure 3-129 PNNL Measured Constant K SCC CGRs for Alloy 152/42/52M Weld Metal 

Specimens as a IG Cracking Observed on the Post-Test Crack Growth 

Surface
3-114

Figure 3-130 Summary of PNNL- and GEG-Measured Constant K SCC Crack-Growth 

Rates for Alloy 152/152M/52/52M Weld Metals as a Function of Stress 

Intensity

The other major laboratory comparison is to the SCC CGR data reported by ANL and is 

presented in Figure 3-131. Without question, reported measurements on the ANL v1 (Alloy 152 

B1) and v2 (Alloy 152 B) welds are quite different showing higher CGRs from 1-5x10-8 mm/s in 

many cases along with much lower examples. The detailed comparison of tests at ANL, GEG 

and PNNL on the ANL v2 weld (Alloy 152 B) was described in Section 3.1.4. While the higher 

SCC susceptibility of these two ANL alloy 152 welds (same weld wire) could not be confirmed at 

other laboratories, the results were duplicated at ANL and suggests that the high Cr welds are 

not inherently resistant to SCC.

Even after characterizations and SCC tests on 18 different high Cr welds, it is not possible to 

directly link bulk composition or microstructure to SCC susceptibility for these weld metals. The 

key reasons for this stems from the limited observations of SCC growth for any of the alloy 

152/152M or 52/52M weld metals tested and the variations in microstructure (e.g., inclusions, 

precipitates and local strain densities) throughout individual welds. It is important to note that 

microstructural effects on SCC susceptibility of alloy 690 heats were determined in highly coldworked materials and could not be assessed in as-received alloy 690 because all heats were 

resistant to SCC. The current results on as-welded alloy 152/52 materials is entirely consistent 

with this behavior. In an attempt to improve understanding of compositional and microstructural 

effects on the SCC susceptibility of the high-Cr weld metals, crack-growth tests will be 

performed on cold-worked alloy 152/52 welds and will be reported in a future NUREG/CR 

report.
3-115

Figure 3-131 Summary of PNNL- and ANL-Measured SCC Crack-Growth Rates for Alloy 

152/152M/52/52M Weld Metals as a Function of Stress Intensity
3-116

Figure 3-132 Summary of PNNL-, GEG-, ANL- and CIEMAT-Measured SCC Crack-Growth 

Rates for Alloy 152/152M/52/52M Weld Metals as a Function of Stress 

Intensity
4-1 

4 ALLOY 52M OVERLAYS/INLAYS

Interactions with Pal Efsing of Ringhals made it possible to obtain both an overlay and an inlay 

mockup. The alloy 52M/182 overlay mockup was obtained directly from Ringhals and an 

overview of the mockup is shown in Figure 4-1(a). It was fabricated by robotically welding a 

10-mm-thick alloy 52M layer onto an alloy 690 plate and then by manually welding alloy 182 

onto the alloy 52M layer. The alloy 52M layer was applied by GTAW with a weld speed of 7.5 

cm/min at a current of 130 A while the alloy 182 was applied by SMAW with a weld speed of 

7-12 cm/min at a current of 95-125 A. The inlay mockup was obtained from Westinghouse and 

is from a full-scale inlay repair demonstration by Ringhals on a ring of A533 steel pipe. The 

inlay was fabricated first by carving a boat out of the inner surface of the ring as shown in Figure 

4-1(b), and then alloy 82 filler was robotically welded onto the pipe section. This was followed 

by the robotic application of the alloy 52M inlay. Lastly, an alloy 152 weld layer was manually

applied by Westinghouse to allow fabrication of compact tension specimens for SCC testing 

with an orientation allowing cracks to be grown from the alloy 82 into the alloy 52M. 

Figure 4-1 Overview of the Ringhals Alloy 52M Overlay (a) and Inlay (b) Mockups

4.1 Ringhals Alloy 52M/182 Overlay Welds

4.1.1 Alloy 52M/182 Overlay Weld Sample Pair #1 (CT028 & CT029)

Two 0.5T CT samples (CT028 and CT029) of the Ringhals alloy 52M/182 overlay were 

machined to locate the notch in the alloy 182 weld metal ~3 mm from the alloy 52M interface. 

The sample and notch locations are indicated in Figure 3.66. Composition measurements were 

performed using SEM-EDS at two locations along the interface between the 182 weld and alloy 

52M weld as shown in Figures 4-3 and 4-4. Profile #1 was acquired at the bottom of an alloy 

182 weld puddle while profile #2 was acquired at the saddle point between two alloy 182 weld 

puddles. The two profiles indicate a dilution zone width ranging from ~70 μm to 150 μm with 

dilution occurring in both the alloy 182 and alloy 52 welds. These measurements illustrate the 

complexity of the dilution zone at the alloy 52M/182 interface and suggest that a simple 

assessment of Cr concentration effects on SCC propagation rates will be difficult.

(a) (b)
4-2

Figure 4-2 Photographs Showing Location of Specimens to Be Taken from Alloy 

182/52/690 Overlay Received from Ringhals. Machined Notch Was ~3 mm 

from the Alloy 182 – Alloy 52M Boundary

Figure 4-3 Compositional Profile #1 Across the Bottom of an Alloy 182 Weld Puddle 

and into the Alloy 52M of the Ringhals Alloy 52M/182 Overlay Material
4-3 

Figure 4-4 Compositional Profile #2 Across an Alloy 182 Weld Trough and into the 

Alloy 52M of the Ringhals Alloy 52M/182 Overlay Material

Fatigue precracking was performed in air to produce an initial crack extension of ~1.7 mm in the 

alloy 182 material. The overlay samples were mounted in series and tested in simulated PWR 

primary water at 350°C. A hydrogen concentration of 20 cc H2/kg H2O was maintained to 

produce an electrochemical potential at the Ni/NiO stability line in an attempt to promote 

maximum CGRs in the alloy 182 weld metal. An initial transitioning sequence was followed for 

crack growth through the alloy 182 weld metal similar to the test protocol used for two earlier 

alloy 182 CGR tests. The intent was to produce a fully engaged IGSCC crack front in the alloy 

182 at a position that is ~400 μm from alloy 182/52M interface and monitor growth under 

constant K conditions as it approached the high Cr alloy 52M weld metal.

After crack extension at 0.01 and 0.001 Hz (R=0.7), the crack front is estimated to be ~550 μm 

from the interface and a hold time of 2.5 h was added at ~670 h. The CGR at 0.001 Hz with a 

2.5 h hold was ~1.5x10-8 mm/s for both samples as shown in Figure 4-5. Because of this slower 

than expected CGRs, the R value was decreased to 0.5 to promote faster growth. Propagation 

rates increased to 2.5-3x10-8 mm/s for both samples, and an initial attempt to evaluate constant 

K response was made starting at ~1240 h. Unfortunately, very slow SCC CGRs of ~2x10-9

mm/s were observed as illustrated in Figure 4-6. 
4-4

Figure 4-5 Initial Cycle + Hold Steps in the Alloy 182 Portion of the Ringhals Alloy 

52M/182 Overlay Material

Figure 4-6 First Constant K Response of the Ringhals Alloy 52M/182 Weld Showing 

Very Low CGRs in the Alloy 182 Material
4-5 

Since there was no indication of significant SCC growth under cycle + hold or constant K 

conditions, the decision was made to evaluate another microstructural region closer to the alloy 

52M/182 dilution zone. Cycling at 0.01 and 0.001 Hz at R=0.5 was applied to straighten and 

extend the crack front by ~0.2 mm. This should have moved the crack front to within ~0.3 mm 

of the dilution zone. The R value was then increased back to 0.7 and cycling continued at 

350°C until a test time of ~1750 h as shown in Figure 4-7. Unfortunately, crack-growth rates 

were found to be similar to those established previously. 

The low crack growth response for the alloy 182 weld metal was unexpected based on prior 

SCC test results. Since most of this previous work on alloy 182 was performed at slightly lower 

temperatures, the decision was made to briefly assess response at 325°C at different DH 

concentrations (as in prior alloy 182 tests). In the end, constant K growth rates were extremely 

low (<1x10-9 mm/s) at 325°C, therefore the test temperature and H2 level were increased back 

to 350°C and 20 cc/kg. Propagation rates were initially ~3x10-9 mm/s under these conditions

(still slow for alloy 182) as shown in Figure 4-8, and decreased over the next two weeks to 

~1x10-9 mm/s similar to what was observed previously.

Figure 4-7 Crack Extension into New Microstructural Region and Growth Response 

During Cycle + Hold Loading with R = 0.7 and R = 0.5
4-6

Figure 4-8 Repeat Observation of Constant K and Cycle + Hold Response at 350°C in 

the Ringhals Alloy 52M/182 Overlay. Very Low CGRs Suggest the Crack 

Had Entered into the Alloy 52M Weld

Based on DCPD-measured crack extensions, it was estimated that the alloy 52M should still be 

a distance of ~150 μm away. However, considerable uncertainty exists both for the actual crack 

length and the position of the interface. The only practical way to determine where the crack 

front currently is would have been to remove the samples and polish the side surfaces. It was 

decided to determine CGRs one more time under the standard 0.001 Hz + 2.5 h hold condition. 

As shown in Figure 4-8, this change was made at 3115 h and new rates stabilized at 1.0 and 

1.3x10-8 mm/s. These rates are 3-4X slower than measured previously under identical 

conditions and suggested that the crack front has reached the alloy 52M interface even though 

it should be >100 μm away from the interface based on DCPD-measured crack extension.

Because of this uncertainty and the importance of evaluating SCC CGRs in the alloy 52M weld 

metal, the decision was made to drop the temperature and extend the crack well into the alloy 

52M by cycling at 50°C. A similar cycling sequence was chosen as for the alloy 152 weld metal 

samples where extensive IG cracking was produced along the crack front. The low-temperature 

response of the two samples is presented in Figure 4-9. Surprisingly, aggressive cycling at 0.1 

Hz and R=0.5 produced quite different behavior with much more crack extension in overlay 

specimen CT028 (~0.75 mm) than for specimen CT029 (~0.2 mm). This suggests that complex 

ligaments were present in the overlay specimen CT029 restricting crack growth or masking the 

true crack length. The decision was made to reduce the cyclic frequency to 0.001 Hz partially 

due to the significant crack length difference (~1.1 mm) between the samples. The applied K is 

maintained at 30 MPa√m based on the DCPD crack length for specimen CT028 and is 

estimated to be slightly lower for specimen CT029 (~26 MPa√m).
4-7 

Figure 4-9 Crack Extension in Alloy 52M During Cycling at 50°C in the Ringhals Alloy 

52M/182 Overlay

After a crack length increase of ~1.2 and 0.3 mm for the specimens CT028 and CT029 at 50°C, 

respectively, constant K conditions were established and the temperature was increased to 

350°C. The crack-growth response at 350°C and 20 cc/kg is shown in Figure 4-10. As with the 

previous tests on alloy 152 and alloy 52, the propagation rates at 350°C decreased from 

relatively high values (>5x10-8 mm/s) to ~4x10-9 mm/s over the following 600 h (25 days). While 

the rates appeared steady over the last ~100 hours, it is expected that the rates would have 

continued to decrease slightly over time. In order to help assess the reason for the slowing 

growth rate, a periodic unload every 2.5 h was added at ~4750 h and an immediate jump in 

DCPD crack length was observed. Expanding the time scale to focus on this rapid increase in 

length revealed that most of the change (~0.2 mm for specimen CT028 and ~0.1 mm for 

specimen CT029) occurred during the first three 0.001 Hz cycles. This suggests that ligaments 

had developed and were broken by the initial cycles at an R of 0.5. Since the growth rate under 

the cycle + hold condition then reverted to the expected steady-state values, constant K 

conditions were resumed at ~4800 h. No indication of SCC propagation was observed over the 

next few days and the DCPD-measured crack length slightly decreased before the test was 

ended at 4936 h. A summary of testing conditions, crack extension, and CGR for each phase of 

the test is shown in Table 4-1. In order to better understand crack-growth response in the alloy 

182 and alloy 52M regions, the specimens were removed, their side surfaces examined and 

then fatigue fractured in air to examine the crack growth surfaces. 
4-8 

Figure 4-10 Constant K Crack-Growth Response in the Alloy 52M Weld Material After 

Temperature Increase from 50°C to 350°C

Side-surface examinations were performed to find the crack front as demonstrated in Figure 

4-11(a). The crack can be identified within the side groove of the overlay sample CT028 and 

distance from the notch estimated as ~4.3 mm. This sample was subsequently removed from 

the system, the crack was resin impregnated, and then a slice was sectioned off to allow 

preparing a TEM crack tip specimen. The specimen was then air fatigue fractured and the resin 

burned off the crack growth surface by baking at 630°C followed by ultrasonic cleaning in DI 

water. The resulting, tinted crack growth surface is shown in Figure 4-11(b). The change from 

grey/gold to blue coloration on the crack growth surface results from the transition from crack 

growth in alloy 182 to alloy 52M. Consistent with the side-surface measurement, the overall 

crack length was 4.5 mm with ~2.9 mm in a water environment. This reveals an under

prediction of crack length by DCPD, since it reported a total crack length of ~2.1 mm produced 

in 350°C and 50°C water.
4-9 

Table 4-1 Corrected Data Summary for Ringhals Alloy 52M/182 Overlay Specimens 

CT028 & CT029

CT028

Ringhals Alloy 52M/182 

Overlay Pair #1

CT029

Ringhals Alloy 52M/182 

Overlay Pair #1

Test 

Phase

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax 

(MPa√m)

CGR

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

Kmax 

(MPa√m)

CGR 

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

1 ~3 0.3 3 0 air RT 25 1.0E-04 0.71 25 8.1E-05 0.57

2 ~2 0.5 3 0 air 

k

RT 28 5.7E-05 0.49 28 5.4E-05 0.38

3 ~3 0.6 3 0 air 

k

RT 30 3.4E-05 0.30 30 3.1E-05 0.28

4 ~5 0.7 3 0 air 

k

RT 30 1.5E-05 0.30 30 1.4E-05 0.32

5 74 0.7 0.1 0 20 cc/kg H2 350 30 1.0E-06 0.201 30 1.0E-06 0.236

6 214 0.7 0.01 0 20 cc/kg H2 350 30 2.7E-07 0.200 30 2.6E-07 0.196

7 359 0.7 0.001 0 20 cc/kg H2 350 30 5.3E-08 0.066 30 5.0E-08 0.074

8 345 0.7 0.001 2.5 20 cc/kg H2 350 30 1.2E-08 0.011 30 1.7E-08 0.015

9 518 0.5 0.001 2.5 20 cc/kg H2 350 30 2.5E-08 0.029 30 3.1E-08 0.033

10 267 --- const K --- 20 cc/kg H2 350 30 2.1E-09 0.003 30 2.1E-09 0.002

11 55 0.5 0.01 0 20 cc/kg H2 350 30 9.0E-07 0.177 30 9.0E-07 0.181

12 84 0.5 0.001 0 20 cc/kg H2 350 30 1.7E-07 0.051 30 9.7E-08 0.028

13 119 0.7 0.001 0 20 cc/kg H2 350 30 3.2E-08 0.017 30 1.6E-08 0.009

14 77 0.7 0.001 0 11 cc/kg H2 325 30 2.6E-08 0.007 30 8.3E-09 0.004

15 410 0.7 0.001 2.5 11 cc/kg H2 325 30 6.3E-09 0.009 30 2.4E-09 0.004

16 170 0.7 0.001 2.5 29 cc/kg H2 325 30 3.3E-09 0.002 30 1.9E-09 0.000

17 181 0.7 0.001 2.5 11 cc/kg H2 325 30 4.5E-09 0.003 30 2.4E-09 0.003

18 82 --- const K --- 11 cc/kg H2 325 30 no growth 0.001 30 no growth 0.000

19 422 --- const K --- 20 cc/kg H2 350 30 9E-10 0.004 30 no growth 0.000

20 365 0.5 0.001 2.5 20 cc/kg H2 350 30 1.3E-08 0.034 30 1.0E-08 0.010

21 184 0.5 0.1 0 20 cc/kg H2 50 30 2.0E-06 0.700 30 4.0E-07 0.179

22 249 0.5 0.01 0 20 cc/kg H2 50 30 3.2E-07 0.302 30 4.4E-08 0.052

23 239 0.5 0.001 0 20 cc/kg H2 50 30 4.3E-08 0.071 30 6.9E-09 0.010

24 602 --- const K --- 20 cc/kg H2 350 30 4.0E-09 0.039 30 2.4E-09 0.027
4-10

Figure 4-11 Optical Images Showing Crack in the Side Groove (top) and Fracture 

Morphology on the Crack-Growth Surface (bottom) for the Alloy 182/52 

Overlay Specimen #1 (CT028)
4-11

4.1.2 Alloy 52M/182 Overlay Sample Pair #2 (CT034 and CT035)

Based on previous experience obtained with the alloy 182 weld metal in the overlay samples 

CT028 and CT029, the decision was made to begin SCC transitioning at 30 MPa√m under 

oxidizing BWR water conditions (288°C high purity water with 2 ppm O2) with 30 ppb sulfate on 

the second alloy 52M/182 overlay specimens CT034 and CT035. This environment has been 

shown to give much more consistent SCC response for alloy 182 weld metals [7], and the intent 

was to promote maximum IGSCC crack-front engagement before switching to simulated PWR 

primary water. Initial transitioning steps were performed at an R value on 0.7 to reach constant 

K with the crack front a little more than 1 mm away from the alloy 182 - alloy 52M interface. The 

initial constant K growth rates were ~2x10-8 mm/s for both samples as shown in Figure 4-12. 

These rates were again lower than anticipated, but it was expected that the rate would increase 

with time as has been observed in previous tests on alloy 600 and alloy 182 under BWR 

oxidizing water conditions. However, the CGRs slowed slightly after ~300 h at constant K. A

cycle + hold loading step with R = 0.7 was initiated at ~1220 h to explore whether crack 

ligaments in the wake of the crack were affecting the DCPD measurement of crack length. The 

lack of a significant jump in crack extension suggested little or no breakage of ligaments, and 

the test was returned to constant K. Unfortunately, the propagation rates remained at lower 

than expected values for this aggressive oxidizing environment, so a second application of cycle 

+ hold loading, but at R = 0.5 was applied with similar results. While these rates indicate that 

IGSCC is occurring, the rates are 5-10X lower than other tests on alloy 182.

Figure 4-12 Transitioning Steps to Constant K Response Under BWR Oxidizing 

Conditions of the Second Pair of Ringhals Alloy 52M/182 Overlay 

Specimens (CT034 & CT035)
4-12

The decision was made to convert this test to PWR primary water conditions after the constant 

K CGRs were established in oxidizing BWR water conditions. As a first step, sulfate additions 

were stopped at ~1790 h and propagation rates slowly dropped by 25% in specimen #1 and 

35% in specimen #2 over a period of ~375 h. Oxygen was then removed, hydrogen added, and 

the temperature increased to 350°C at ~2150 h. A dissolved hydrogen level of 20 cc/kg (near 

the Ni/NiO line) was used to promote maximum SCC susceptibility. Boron and Li were not 

added to fully simulate PWR primary water conditions, but this difference is not believed to have 

a strong influence on SCC. Over the following 3+ weeks, measured CGRs for the two overlay 

samples slowly decreased as illustrated in Figure 4-13. CT035 revealed a more significant drop 

by more than 3 times and appears to be approaching a steady-state CGR of <1x10-9 mm/s. 

CT034 remained slightly higher, but its propagation rate was still extremely low. As was the 

case during the test of the first pair of overlay samples, the alloy 182 is very resistant to SCC. 

Even though transitioning in oxidizing water + sulfate should have promoted IGSCC, 

subsequent growth in hydrogenated water was difficult. As a result, it was again impractical to 

propagate SCC from the alloy 182 to the alloy 52M interface under these conditions. Even 

assuming a significant error (~40%) in the actual crack length, the required time to reach the 

interface under constant K or cycle + hold conditions in hydrogenated water would be greater 

than one year. Therefore, the decision was made to advance the crack front by 0.3-0.4 mm by 

aggressive cycling (hopefully removing any ligaments that may be present), then go through 

transitioning steps again in 288°C oxidizing water + sulfate.

Figure 4-13 Crack Growth Response on Switching from BWR Oxidizing to 

Hydrogenated Water in the Second Pair of Ringhals Alloy 52M/182 

Specimens (CT034 & CT035)
4-13

Initial cycling was conducted at 0.1 Hz with R=0.5 beginning at ~2960 h and revealed a 

reasonably rapid increase in DCPD-measured crack length of >100 μm in ~5 h before 

increasing the R value to 0.7 for another 50 μm. The transitioning sequence was continued at 

~2975 h by decreasing the cyclic frequency to 0.01 Hz and then to 0.001 Hz at ~3015 h. 

Somewhat surprisingly, the measured cyclic CGRs were 2-4X lower than measured under 

identical conditions at the beginning of the test. To confirm this response, cycle + hold 

conditions were established at ~3180 h showing a CGR of ~3x10-8 mm/s in Figure 4-14. Once 

again, this is more than 2X lower than measured earlier in this test. Since the mockup was 

created by overlaying alloy 182 on top of alloy 52M, a compressive residual stress is not 

expected in the alloy 182. Therefore, a more likely explanation for the lower propagation rate is 

the presence of ligaments behind the crack front or a highly uneven crack front with areas 

already intersecting the alloy 52M interface. Loading conditions were briefly changed to a 

periodic unload at R = 0.3 producing a high ∆K of 21 MPa√m. The lack of a significant jump in 

crack length and the small increase in CGR suggests that no ligaments are being removed. 

Returning to the cycle + hold condition produced a similar CGR and indicates that the periodic 

unload had no effect. The test was converted to constant K at ~3660 h as shown in Figure 

4-15. Specimen CT034 continued to exhibit low values with the propagation rate decreasing to 

1x10-9 mm/s. However, specimen CT035 slowed only slightly, stabilizing at a rate of 1.0x10-8

mm/s and is comparable to the constant K propagation rates measured in earlier steps of the 

test.

Figure 4-14 Response During the Second Transitioning Phase in BWR Oxidizing Water 

of the Second Pair of Ringhals Alloy 52M/182 Specimens (CT034 & CT035)
4-14

Figure 4-15 The Second Observation of Constant K Response for the Second Pair of 

Ringhals Alloy 52M/182 Specimens in BWR Oxidizing Water with Sulfate

The lower SCC CGRs being observed in the alloy 182 under aggressive oxidizing conditions 

creates even more doubt whether a useful evaluation of the alloy 182/52M interface can be 

obtained. If sustained higher SCC CGRs cannot be produced in alloy 182, it will be impossible 

to assess CGR changes during the approach to the interface. PNNL results on the four 

Ringhals overlay mockup samples clearly demonstrated the high SCC resistance of this alloy 

182 in hydrogenated water. It also revealed that the alloy 182 is somewhat resistant to SCC in 

oxidizing BWR water. While the measured CGRs suggest that IGSCC is occurring, rates are 

still >5X lower than expected in oxidizing water plus sulfate.

After discussion with the NRC project manager, it was decided to stop the test to remove 

specimen CT034 for examination the crack front location at side surfaces and then document 

the crack-growth surface. These characterizations clearly showed that the crack front had 

intersected the alloy 52M prompting the decrease in propagation rates. The decision was made 

to restart the test on specimen CT035 under simulated PWR primary water conditions and apply 

aggressive cycling to advance the crack front moving it completely into the alloy 52M.

After crack extension at 0.1 Hz and 0.01 Hz, a number of transitioning steps were applied with 

variations in R and hold time. A rate of 3.2x10-8 mm/s was eventually established under cycle + 

hold loading at R = 0.5 as shown in Figure 4-16. This rate is approximately 3X higher than has 

been observed in the previous tests on alloy 152/52/52M, and decision was made to evaluate 

constant K at this time. A small step increase in DCPD-measured crack length (~10 μm) was 

detected when constant K was established at 5825 h, similar to that seen when switching from 

cycling to cycle + hold conditions previously. A stable CGR of 9.4x10-9 mm/s was seen over the 

first 300 h at constant K and then decreased slightly to 7.6x10-9 mm/s over the next 400 h. This 

final constant K response is shown in Figure 4-17. A summary of test conditions, crack 

extension, and growth rate for each phase of the test is shown in Table 4-2. These SCC 

propagation rates are 6-20X higher than those previously measured for alloy 52 welds. 
4-15

Figure 4-16 Final Cycle + Hold Loading Response of Ringhals Alloy 52M/182 Specimen 

CT035 Showing a Relatively High Rate of 3.2x10-8 mm/s

Figure 4-17 Final Constant K Response of Ringhals Alloy 52M/182 Specimen CT035 

with Final Propagation in the Alloy 52M
4-16

Table 4-2 Data Summary for Ringhals Alloy 52M/182 Overlay Specimens CT034 & 

CT035

CT034

Ringhals Alloy 52M/182 

Overlay Pair #2

CT035

Ringhals Alloy 52M/182 

Overlay Pair #2

Test 

Phase

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax 

(MPa√m)

CGR

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

Kmax 

(MPa√m)

CGR 

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

1 ~2 0.3 5 0 air precrack RT 25 2.3E-04 0.50 25 9.5E-05 0.50

2 ~2 0.5 5 0 air precrack RT 28 6.0E-05 0.30 28 6.5E-05 0.30

3 ~2 0.6 5 0 air precrack RT 30 4.3E-05 0.20 30 4.3E-05 0.20

4 ~2 0.7 5 0 air precrack RT 30 2.2E-05 0.20 30 2.1E-05 0.20

5 8 0.7 0.1 0 O2 + SO4 A 288 30 2.1E-06 0.057 30 3.8E-06 0.090

6 69 0.7 0.01 0 O2 + SO4 A 288 30 6.4E-07 0.163 30 1.3E-06 0.311

7 138 0.7 0.001 0 O2 + SO4 A 288 30 2.2E-07 0.135 30 4.2E-07 0.269

8 415 0.7 0.001 2.5 O2 + SO4 A 288 30 7.1E-08 0.176 30 6.6E-08 0.127

9 23 0.5 0.001 2.5 O2 + SO4 A 288 30 - - 0.012 30 - - 0.015

10 140 0.7 0.001 2.5 O2 + SO4 B 288 30 6.6E-08 0.033 30 8.2E-08 0.039

11 402 --- const K --- O2 + SO4 B 288 30 1.4E-08 0.025 30 1.6E-08 0.030

12 31 0.7 0.001 2.5 O2 + SO4 B 288 30 6.1E-08 0.009 30 7.5E-08 0.011

13 116 --- const K --- O2 + SO4 B 288 30 1.3E-08 0.006 30 1.1E-08 0.005

14 32 0.5 0.001 2.5 O2 + SO4 B 288 30 1.1E-07 0.014 30 1.2E-07 0.018

15 387 --- const K --- O2 + SO4 B 288 30 1.1E-08 0.018 30 6.7E-09 0.011

16 363 --- const K --- 2 ppm O2 288 30 8.1E-09 0.012 30 4.4E-09 0.006

17 813 --- const K --- 20 cc/kg H2 350 30 2.2E-09 0.013 30 6.9E-10 0.001

18 5 0.5 0.1 0 O2 + SO4 B 288 30 7.7E-06 0.110 30 9.3E-06 0.134

19 7 0.7 0.1 0 O2 + SO4 B 288 30 2.6E-06 0.042 30 2.3E-06 0.043

20 43 0.7 0.01 0 O2 + SO4 B 288 30 3.1E-07 0.050 30 3.8E-07 0.056

21 160 0.7 0.001 0 O2 + SO4 B 288 30 8.9E-08 0.050 30 1.0E-07 0.059

22 168 0.7 0.001 2.5 O2 + SO4 B 288 30 3.1E-08 0.018 30 2.9E-08 0.018

23 95 0.7 0.025 1 O2 + SO4 B 288 30 5.6E-08 0.026 30 5.7E-08 0.026

24 218 0.7 0.001 2.5 O2 + SO4 B 288 30 2.7E-08 0.020 30 2.7E-08 0.020

25 288 --- const K --- O2 + SO4 B 288 30 1.0E-09 0.006 30 1.0E-08 0.013

26 52 0.7 0.001 0 20 cc/kg H2 350 specimen removed from test 32 6.9E-09 0.016

27 21 0.3 0.2 0 20 cc/kg H2 350 " 33 1.9E-05 2.049

28 230 0.5 0.1 0 20 cc/kg H2 350 " 33 6.0E-06 0.461

29 184 0.7 0.01 0 20 cc/kg H2 350 " 33 5.8E-07 0.396

30 395 0.7 0.001 0 20 cc/kg H2 350 " 33 6.7E-08 0.032

31 64 0.7 0.001 2.5 20 cc/kg H2 350 " 33 5.9E-09 0.008

32 115 0.5 0.001 2.5 20 cc/kg H2 350 " 33 - - -

33 427 0.5 0.001 0 20 cc/kg H2 350 " 33 4.9E-07 0.168

34 332 0.5 0.001 2.5 20 cc/kg H2 350 " 33 5.2E-08 0.081

35 660 --- const K --- 20 cc/kg H2 350 " 49 1.0E-08 0.034

A 2 ppm O2 + 30 ppb SO4- ; B 2 ppm O2 + 60 ppb SO4-
4-17

After testing was completed, CT035 was cut into two slices (1/3 and 2/3 of the thickness, 

respectively) of which the 2/3 section was fractured open, and the 1/3 section polished in crosssection to analyze the crack growth morphology using analytical microscopic analysis. Figure 

4-18 shows the section of CT035 that was fractured open, illustrating the location of the 

182/52M interface as well as the IG cracking within the 52M near the leading crack front when 

the test was transitioned to constant K. At the leading crack front, fingers of IG cracking appear 

consistent along solidification grain boundary packets, hence the entire front is not engaged at 

the the same time.

Figure 4-18 Optical Micrograph of the Crack Growth Surface of CT035

Optical micrographs of the side surface (which were highly polished and etched, Figure 4-19a) 

show the crack morphology of the entire test, with the first portion of the crack propagating 

through the A182 and the second through various weld passes of 52M. Higher magnification 

(the yellow box in the Figure 4-19b) shows the portion of the test within various weld passes of 

52M and the approximate cycling regimes. The final ~1.25 mm of the test was run under 

constant K conditions, and the light surface etching revealed that it propagated intergranularly 

through a weld pass. The majority of the crack growth past the 182/52M interface was 

determined to be TG, with some incidental IG cracking most likely due to aligned boundaries. 

EDS elemental mapping (Figure 4-20) of the SCC test between the 182/52M interface and the 

end of the test shows the variability in the composition of each of the 52M weld passes. To 

better illustrate the differences, color maps of Ni (in green), Cr (in red) and Fe (in blue) were 

overlaid on the SEM-BSE images to form a montage (Figure 4-21). Elemental linescans were 

taken along either side of the crack (as indicated in the overlay image), and are also presented 

in Figure 4-21. The elemental maps and linescans clearly indicate the transition from the 182 to 

52M as well as the different 52M weld passes through the Ni and Cr-K signals. In the 52M, the 

first two passes have Cr content close to 30 wt% (Ni ~60 wt%), whereas in the third weld pass 

(of which the majority of the constant K testing was performed) the Cr content dropped to ~25 

wt% and the Ni composition rose to close to ~70 wt%. In the final portion of the test, the SCC 

crack grew through a weld pass that was closer in composition to the first two weld passes.

While the slightly etched cross-sections (Figure 4-19) provided some grain boundary relief, 

EBSD performed on the last 2 mm of the test (Figure 4-22) clearly highlights the microstructure 

and crack growth path. Traces taken from the EDS elemental maps of the various weld passes 
4-18

in the alloy 52M are overlaid on the EBSD maps to show the chemistry in relation to the 

microstructure. In weld pass #2 the majority of the crack is TG continuing on through half of 

weld pass #3 where the crack becomes IG. The transition to IG could be coincidental with the 

grain boundary being oriented almost perfectly with the growing crack. Approximately 500 μm 

before the final weld pass the crack becomes TG as it passes through a smaller grain packet, 

but quickly becomes IG again through the end of the test. A higher magnification EBSD pattern 

quality map of the end of the crack growth test is presented along with a trace of the crack (red 

line) to better illustrate the IGSCC cracking. Local misorientation maps of the final crack growth 

test show higher misorientations around the propagating crack, and possibly higher 

misorientation in weld pass #2 as compared to passes #3 and #4.

Figure 4-19 Optical Micrographs (low and high magnification with solid yellow box 

showing high mag region of interest) of the Side Surface of CT035. The 

Dashed Green Box Shows the Location of EBSD Analysis. Two FIB 

Samples (Regions 1 and 2) Were Prepared from This Cross-Section and Are 

Highlighted by the Solid Red Boxes

FIB 

region 

2 

FIB 

region 1

a)

b)
4-19

Figure 4-20 SEM-BSE Image and EDS Elemental Maps of the CT035 Cross-Section 

Following the SCC Crack Path from the Alloy 182 Through Several Weld 

Passes of the Alloy 52M (approximately the same region as solid yellow 

box in Figure 4-19a). The Crack Ends in an Alloy 52M Region of Distinctly 

Different Composition (higher Ni, lower Cr and Fe)
4-20

EDS Line Scan LS1

EDS Line Scan LS2

Figure 4-21 SEM-BSE Image with an Overlaid Composite EDS Elemental Maps for the 

CT035 Cross-Section Following the SCC Crack Path from the Alloy 182 

Through Several Weld Passes of the Alloy 52M. EDS Line Scans Are 

Shown Illustrating the Composition Changes from the Alloy 182 to Alloy 

52M and into the Ni-Rich Pass

15.0

20.0

25.0

30.0

35.0

40.0

45.0

50.0

0.0 1.0 2.0 3.0 4.0 5.0 6.0 7.0

Distance (mm)

Cr wt %

30.0

35.0

40.0

45.0

50.0

55.0

60.0

65.0

70.0

75.0

80.0

Ni wt %

Cr Ni

0.0

1.0

2.0

3.0

4.0

5.0

6.0

7.0

8.0

9.0

10.0

0.0 1.0 2.0 3.0 4.0 5.0 6.0 7.0

Distance (mm)

Fe, Mn wt %

0.0

1.0

2.0

3.0

4.0

5.0

6.0

7.0

8.0

9.0

10.0

Nb wt %

Mn Fe Nb

15.0

20.0

25.0

30.0

35.0

40.0

45.0

50.0

0.0 1.0 2.0 3.0 4.0 5.0 6.0 7.0

Distance (mm)

Cr wt %

30.0

35.0

40.0

45.0

50.0

55.0

60.0

65.0

70.0

75.0

80.0

Ni wt %

Cr Ni

0.0

1.0

2.0

3.0

4.0

5.0

6.0

7.0

8.0

9.0

10.0

0.0 1.0 2.0 3.0 4.0 5.0 6.0 7.0

Distance (nm)

Fe, Mn wt %

0.0

1.0

2.0

3.0

4.0

5.0

6.0

7.0

8.0

9.0

10.0

Nb wt %

Mn Fe Nb

LS1

LS2 FIB 

region 2

FIB 

region 1

Alloy 

182 Alloy 52M 

Pass #1

Alloy 52M 

Pass #2

Alloy 52M 

Pass #3

Alloy

182

Alloy52M 

pass #1

Alloy52M 

pass #2

Alloy52M 

pass #3

Alloy

182

Alloy52M 

pass #1

Alloy52M 

pass #2

Alloy52M 

pass #3

Alloy

182

Alloy52M 

pass #1 Alloy52M 

pass #2

Alloy52M 

pass #3

Alloy

182

Alloy52M 

pass #1 Alloy52M 

pass #2

Alloy52M 

pass #3

#P4

#P4 #P4

#P4 #P4
4-21

Figure 4-22 SEM-EBSD Pattern Quality Map, IPF Images and Local Misorientation Maps 

for the Final Length of the SCC Crack on the Side Surface of Specimen 

CT035. The Pattern Quality Map Is Shown for the Leading SCC Crack Tip 

(with a red line overlay to show approximate location of the crack)

In order to ascertain as to whether the local chemistry could be affecting the SCC crack growth, 

two plan view FIB samples were prepared (see locations in Figure 4-19 and Figure 4-21) from 

CT035, one from the leading SCC tip (52M weld pass#4) and one from a secondary crack in the 

A182.

Figure 4-23 shows medium (a) and high (b) magnification SEM-BSE and SE images of the 

leading IGSCC tip that corresponds to FIB Region #1. While the medium magnification image 

appears to corroborate previous images (Figures 4-19 and 4-22) showing the leading SCC tip is 

IG, at higher magnification it appears there are both IG and TG components to the tip. The plan 

Alloy52M 

pass #2 Alloy52M 

pass #3

Alloy52M 

pass #4

Alloy52M 

pass #2

Alloy52M 

pass #3

Alloy52M 

pass #4

Alloy52M 

pass #3

Alloy52M 

pass #4

IPF

Local 

misorientation map

Pattern quality
4-22

view FIB sample prepared from the dashed yellow box in Figure 4-23b was examined in SEM 

(Figure 4-24), illustrating this IG and TG appearance of the final tip. The crack appears to be 

traveling along the grain boundary, but there are TG offshoots at least near the crack front. The 

extensive penetrative oxidation around the primary and TG cracks suggests that the crack tip 

had been exposed to water for an extended period of time, therefore this is not an active crack. 

STEM/EDS elemental maps of this TEM sample were collected, but did not show any unique 

chemical segregation along the grain boundary. The penetrative oxidation is mostly Cr rich with 

some increased Ni content. Ni-rich oxide was observed to be deposited on the crack walls. A

higher magnification STEM/EDS elemental map was collected at the end of the IG crack (Figure 

4-25) and illustrates that there are small (75-100 nm) Cr-rich precipitates ahead of the crack.

Figure 4-23 SEM-BSE Micrographs of the Leading SCC Crack in CT035 Corresponding 

to FIB Region 1 in Figures 4-19 and 4-22. The Solid Yellow Box in a) Shows 

the Location of b), and the Dashed Yellow Box in b) Indicates the Location 

of the Plan View FIB Sample

Figure 4-24 SEM-BSE Images of the Leading IGSCC Crack Tip in the Alloy 52M Pass of 

Altered Composition

a) b)
4-23

Figure 4-25 STEM/EDS Elemental Maps of an IG Crack Tip from the Dashed Yellow Box 

in Figure 4-24

A second FIB sample from a secondary IGSCC tip in the A182 region close to the A182/52M 

interface was prepared (see Figures 4-19, 4-21, and 4-26). In this instance, the secondary SCC 

was moving in a plane ~400 μm below the main crack, but still in the same direction as the main 

crack. From Figure 4-26, it can be observed that the secondary crack encountered a triple point 

and began moving along a grain boundary interface in a direction towards the main crack. The 

location of the plan view FIB sample is shown in the dashed yellow box in Figure 4-26b, and 

should be noted that the presentation of data in further figures re-aligns the crack orientation 

laterally instead of vertically as in Figure 4-26. 

High resolution low kV SEM-BSE imaging of the plan view FIB sample better illustrates the 

microstructure of the secondary IGSCC tip (Figure 4-27). From this image, the penetrative 

oxidation along the crack walls is sparse, and appears to taper towards the front of the crack 

suggesting that this was an active secondary crack. The crack appears to be primarily IG, with 

one small TG offshoot. The density of IG precipitation can be observed ahead of the leading 

crack tip, with precipitates on the order of 50-100 nm. STEM/EDS elemental mapping of the 

leading tip (Figure 4-28) indicates that the IG precipitates are a mixture of Cr, Nb and Ti rich 

particles. The penetrative oxidation is mostly Cr rich, with some enrichment of Ni as indicated 

by the colored elemental map (Fe in red, Cr in green, and Ni in blue). As well, in both the Ni-K 

and colored map, there is slight Ni enrichment ahead of the crack tip. The FIB sample was 

slightly too thick to get a good indication of this Ni enrichment, and hence projection issues 

convoluted the oxide signal with the adjacent Cr depletion/Ni enrichment.
4-24

Figure 4-26 SEM-BSE Image of Secondary IGCSCC Cracks in the Alloy 182 Weld Metal 

for CT035. Solid Yellow Box in a) Provides the Location of b), and the 

Dashed Yellow Box in b) Illustrates the Location of the Plan View FIB 

Sample. Note the Orientation of These Images Is Identical to Those Shown 

Earlier in This Section

Figure 4-27 SEM-BSE Images of Secondary IGSCC Cracks (FIB region 2 in Figures 4-19

and 4-22) In the Alloy 182 Weld Metal for Specimen CT035. Note the FIB 

Orientation of the Sample Has Changed (crack orientation is now left to 

right instead of bottom to top) From the Previous Figures 

a) b)

Triple 

point
4-25

Figure 4-28 STEM/EDS Elemental Maps of a Secondary IGSCC Crack Tip in the A182 

Region of the CT035 Sample

4.2 Ringhals Alloy 52M/82 Inlay Mockup (CT030 & CT031) 

As mentioned in the beginning of this chapter, a section of an alloy 52M weld inlay mockup 

produced for Ringhals was obtained from Rich Jacko of Westinghouse. It consists of alloy 82 

robotically deposited onto a low-alloy steel ring followed by a robotically deposited 10 mm thick 

inlay of alloy 52M. A layer of alloy 152 was manually welded on top of the inlay by 

Westinghouse to provide sufficient material to obtain CT specimens from the mockup. The 

approximate location of the 0.5T CT specimens (CT031 and CT032) is shown in the Figure 

4-29. The notch was positioned to enable the precrack to be placed in the alloy 82 at a distance 

of ~0.5 mm from the alloy 52M interface. Side grooves of the machined samples were polished 

and etched to reveal the alloy 52M inlay and the alloy 82 weld. Examples of these regions are 

shown in Figure 4-30. 

Ni enrichment

oxide
4-26

Figure 4-29 Profile of Ringhals Alloy 52M Inlay Mockup Weld Received from 

Westinghouse. Alloy 52M Inlay Is 10 mm Thick

Figure 4-30 Optical Images of the Alloy 52M/82 Inlay Sample CT031

The goal of this test on the inlay samples was similar to that for the overlay samples; produce a 

fully engaged IGSCC crack front in the more susceptible alloy 82 and monitor growth under 

Alloy 52M Alloy 82

2.0 mm
4-27

constant K conditions as it approaches the alloy 52M interface. An overview of the entire test is 

shown in Figure 4-31. Testing began at 350°C and 29 cc/kg H2 and was switched to 20 cc/kg 

(ECP at Ni/NiO line for expected maximum SCC growth rate) at ~130 h during the gentle cycling 

at 0.001 Hz. Surprisingly, the change to a hydrogen level near the Ni/NiO line prompted a small 

decrease in propagation rates. A 2.5-h hold time was added at ~220 h and the propagation 

rates dropped to ~5.4 and 2.2x10-8 mm/s for the two inlay specimens. After ~100 h in this cycle

+ hold condition, the rates stabilized at 2.9 and 2.1x10-8 mm/s. Based on prior alloy 82 results 

by GE Global, the R value was increased from 0.5 to 0.7 to help promote SCC. Propagation 

rates decreased by 2-3X after this change to values <10-8 mm/s suggesting limited SCC 

engagement across the crack front. Consistent with this interpretation, rates further decreased

to ~3x10-9 mm/s or lower when switching to constant K conditions as illustrated in Figure 4-32. 

Figure 4-31 Test Overview for the Ringhals Alloy 52M/82 Inlay Mockups (CT030 & 

CT031)
4-28

Figure 4-32 Initial Cycle + Hold and Constant K Response in PWR Primary Water of the 

Ringhals Alloy 52M/82 Inlay Mockup (CT030 & CT031)

In an attempt to promote IGSCC, environmental conditions were switched from hydrogenated to 

oxygenated and the temperature reduced to 290°C. Under these BWR-like water conditions, a 

higher IGSCC susceptibility has been observed for alloy 82 particularly with a low level sulfate 

addition. The goal was again to improve SCC engagement across the crack front under 

oxidizing conditions and then determine whether more rapid IGSCC rates could be maintained 

after returning to PWR primary water. Figure 4-33 shows that the CGR was relatively 

unaffected by the more BWR-like water conditions. At 1700 h, ~60 ppb sulfate was introduced 

to the water and gentle cycling was performed at 0.01 and 0.001 Hz (R = 0.7) to help restart 

crack advance followed by the addition of a 2.5 h hold. Unfortunately, CGRs during these 

transitioning steps were significantly lower than anticipated based on reported alloy 82 behavior 

in BWR oxidizing water with sulfate additions. The decision was made to stop the test and exam 

side surfaces to estimate the crack front location. Surprisingly, the cracks were determined to 

have reached the alloy 52M interface.
4-29

Figure 4-33 Constant K and Cyclic Loading Response of the Ringhals Alloy 52M/82 

Inlay Mockup (CT030 & CT031) After Switching from PWR Primary Water to 

BWR Oxidizing Water

Crack-growth testing continued for the two Ringhals alloy 52M/82 inlay mockup samples after 

the restart at an accumulated test time of ~2275 h. Aggressive cycling was initiated to extend 

the crack well into the alloy 52M inlay region and evaluate SCC CGR response in the alloy 52M 

weld metal. A typical transitioning sequence was used and the cyclic frequency was reduced 

over multiple steps. Propagation rates during cycling at R = 0.5 were very similar to those 

measured previously for the alloy 52 weld metal samples (CT024, CT025, CT032 and CT033) 

and somewhat lower than seen for the alloy 82 weld metal under identical loading and 

environmental conditions. A 2.5-h hold time was added at ~2600 h and a CGR of 1x10-8 mm/s 

was observed (Figure 4-34). Once again, this propagation rate matched that documented 

previously for the alloy 52 samples, suggesting that limited SCC engagement had been created 

and constant K propagation rates would probably be <2x10-9 mm/s. It was then decided to 

examine the crack growth response with a less aggressive load ratio. Cyclic loading was 

changed to continuous cycling at 0.001 Hz, R = 0.7 for ~200 h, and then a 2.5 h hold was 

added. Propagation rates for both specimens under these loading conditions are similar to the 

MHI alloy 52 material (CT025 and CT033) where limited (if any) IGSCC was observed at 350°C.

Loading was changed to constant K at ~3820 h and low propagation rates of ~1x10-9 mm/s were 

observed for both samples as illustrated in Figure 4-35. Since limited crack-growth data exists 

for alloy 52M, the test was continued at constant K to help build confidence in the measured 

rates. For these low rates, the measured crack extension under constant K loading was ~5 μm 

after testing for ~1 month.
4-30

Figure 4-34 Alloy 52M Response During Cycle and Cycle + Hold Loading at R=0.5 in the 

Ringhals Alloy 52M/82 Inlay Mockup Specimens (CT030 & CT031)

Figure 4-35 Alloy 52M Response During Constant K Loading in the Ringhals Alloy 

52M/82 Inlay Mockup Specimens (CT030 & CT031)
4-31

The decision was made at ~4600 h to change back to cycle + hold loading and increase the 

applied K value from 30 to 40 MPa√m using a programmed dK/da response. The initial dK/da 

rate was ~0.05 MPa√m/μm, giving growth rates of ~6.5x10-9 mm/s during the 0.001 Hz cycle + 

2.5 h condition with R = 0.7. At these slow propagation rates, the increase to 40 MPa√m would 

have taken months, and therefore, the dK/da was changed to 0.80 MPa√m/μm at ~4950 h 

producing a ~5 times increase in rate (to ~3x10-8 mm/s) as documented in Figure 4-36. 

Although systematic evaluations of dK/da effects were not being attempted, it is clear that the 

gradual increase in K and delta-K accelerates crack growth. It is important to note that while K is 

slowly increasing with time, the actual dK/da is high compared with what may be expected in 

actual piping components. In this case, K is being changed over μm dimensions whereas similar 

changes in K might be expected over mm dimensions in a component. 

Final steps for this test were to evaluate SCC CGRs in the alloy 52M inlay at a higher K level of 

40 MPa√m. The cycle + hold response was 1.3x10-8 mm/s for the two samples as shown in

Figure 4-33. This compares to rates of 4.5 and 2x10-9 mm/s (3-4X lower) under this loading 

condition at 30 MPa√m earlier in this test. The higher CGRs at 40 MPa√m are similar to that 

measured for the MHI alloy 152 weld metal where localized regions of IGSCC were observed. 

Constant K conditions were established at ~5495 h and steady growth was observed in both 

specimens during this period with CGRs of 1.0x10-9 and 1.6x10-9 mm/s as shown in Figure 4-37. 

These rates are identical to those obtained on these specimens at 30 MPa√m, and the test was 

ended at 6500 h. A summary of test condition and corrected specimen response for each 

phase of the test is shown in Table 4-3. 

Figure 4-36 dK/da Response Going from 30 to 40 MPa√m of the Ringhals Alloy 52M/82 

Inlay Mockup Specimens (CT030 & CT031)
4-32

Figure 4-37 Constant K Response at 40 MPa√m of the Ringhals Alloy 52M/82 Inlay 

Mockup Specimens (CT030 & CT031)
4-33

Table 4-3 Corrected Data Summary for Ringhals Alloy 52M/82 Inlay Specimens #1 

and #2 (CT030 & CT031)

CT030

Ringhals Alloy 52M/182 Inlay 

Specimen #1

CT031

Ringhals Alloy 52M/82 Inlay 

Specimen #2

Test 

Phase

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chemistry 

Conditions

Temp 

(°C)

Kmax 

(MPa√m)

CGR

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

Kmax 

(MPa√m)

CGR 

(mm/sec)

Approx. 

Crack 

Extension 

(mm)

1 ~3 0.3 5 0 air precrack RT 25 2.1E-04 0.40 25 1.7E-04 0.40

2 ~2 0.5 5 0 air precrack RT 29 1.2E-04 0.35 28 9.7E-05 0.35

3 ~2 0.6 5 0 air precrack RT 31 8.1E-05 0.35 31 5.6E-05 0.35

4 ~3 0.7 5 0 air precrack RT 31 2.4E-05 0.20 31 2.2E-05 0.20

5 11 0.5 0.1 0 29 cc/kg H2 350 31 5.5E-06 0.218 29 3.4E-06 0.108

6 43 0.5 0.01 0 29 cc/kg H2 350 31 1.4E-06 0.209 28 1.1E-06 0.173

7 60 0.5 0.001 0 29 cc/kg H2 350 31 2.8E-07 0.067 28 2.5E-07 0.052

8 101 0.5 0.001 0 20 cc/kg H2 350 31 1.8E-07 0.086 28 2.5E-07 0.084

9 568 0.5 0.001 2.5 20 cc/kg H2 350 31 3.2E-08 0.063 28 2.7E-08 0.058

10 183 0.7 0.001 2.5 20 cc/kg H2 350 31 3.2E-08 0.006 28 2.7E-08 0.007

11 534 --- const K --- 20 cc/kg H2 350 31 7.3E-10 0.021 28 4.3E-09 0.006

12 197 --- const K --- 2 ppm O2 288 31 6.6E-09 0.006 28 7.7E-09 0.011

13 111 0.7 0.01 0 2 ppm O2 + 

SO4-

288 31 1.2E-07 0.055 28 1.6E-07 0.072

14 95 0.7 0.001 0 2 ppm O2 + 

SO4-

288 31 2.4E-08 0.010 28 2.8E-08 0.008

15 209 0.7 0.001 2.5 2 ppm O2 + 

SO4- 288 31 5.2E-09 0.005 28 6.0E-09 0.005

16 161 0.5 0.001 2.5 2 ppm O2 + 

SO4-

288 31 1.3E-08 0.008 28 1.3E-08 0.006

17 14 0.4 0.2 0 29 cc/kg H2 350 32 1.2E-05 0.640 27 7.7E-06 0.198

18 31 0.5 0.1 0 29 cc/kg H2 350 32 4.2E-06 0.445 27 2.9E-06 0.339

19 52 0.5 0.01 0 29 cc/kg H2 350 32 7.6E-07 0.148 27 4.9E-07 0.097

20 232 0.5 0.001 0 29 cc/kg H2 350 32 9.9E-08 0.100 27 7.6E-08 0.109

21 390 0.5 0.001 2.5 29 cc/kg H2 350 32 1.1E-08 0.018 27 1.3E-08 0.016

22 163 0.7 0.001 0 29 cc/kg H2 350 32 3.4E-08 0.015 27 2.3E-08 0.007

23 649 0.7 0.001 2.5 29 cc/kg H2 350 32 4.6E-09 0.019 27 4.4E-09 0.021

24 846 --- const K --- 29 cc/kg H2 350 32 1.1E-09 0.021 27 2.0E-09 0.027

25 257 0.7 0.001 2.5 29 cc/kg H2 350 32->34 7.1E-09 0.004 27->28 8.3E-09 0.006

26 112 0.7 0.001 2.5 29 cc/kg H2 350 34->43 3.1E-08 0.010 28->35 4.8E-08 0.012

27 484 0.7 0.001 2.5 29 cc/kg H2 350 43 1.4E-08 0.021 35 1.6E-08 0.024

28 1033 --- const K --- 29 cc/kg H2 350 43 1.1E-09 0.005 35 2.0E-09 0.005

After ending the test, CT030 was fatigue fractured in air whereas CT031 was first backfilled with 

resin, sectioned into two pieces, and then one side was fatigue fractured in air while the other 

side was set aside for crack tip examinations. The most apparent feature of the crack growth 

surface of CT030 in Figure 4-38 is the very large uncracked ligament in the wake of the crack. 

This ligament formed at the onset of high temperature water testing, and was never broken 

during the entire test. Another feature of interest in the crack growth surface of CT030 is the 

rather uniform tan layer along the final crack front. This is likely representative of the final 

transitioning and constant K at 40 MPa√m. The jagged, uneven final crack front suggests a 

relatively high degree of engagement (but still with a very slow CGR). The side surface image 
4-34

of the crack growing in the CT031 alloy 52M material in Figure 4-39 shows evidence of a large 

crack resulting from rapid extension with a narrower cracking extending out. The narrower 

crack, likely formed during cycle + hold and constant K, shows some preference for cracking 

along dendrites. This can be better seen in the SEM image of the same region in Figure 4-40. 

Figure 4-38 Crack Growth Surface of Ringhals Alloy 52M/82 Specimen CT030

Figure 4-39 Optical Image of Side Surface of Crack Growing into Alloy 52M in the 

Ringhals Alloy 52M/82 Specimen CT031
4-35

Figure 4-40 SEM Image of Side Surface of Crack Growing into Alloy 52M in the 

Ringhals Alloy 52M/82 Specimen CT031

4.3 Summary of SCC Tests on Alloy 52M Overlay and Inlay Mockups

Four SCC crack growth tests were performed on an alloy 52M/182 overlay mockup weld and 

two tests on an alloy 52M/82 inlay mockup weld. The intent for all tests was to first establish 

stable IGSCC growth in the more susceptible, alloy 182 or 82 weld metal then to evaluate SCC 

propagation response through the transition region and into the more resistant alloy 52M weld 

metal. Unfortunately, step 1 turned out to be extremely difficult with limited SCC growth rates 

produced in the alloy 182 and 82 weld metals plus propagation rates decreased even further as 

the crack front approached the alloy 52M interface. Multiple attempts were made in simulated 

PWR primary water at 350°C and in more aggressive oxidizing BWR water conditions with 

sulfate additions. While localized IG cracking was promoted particularly in the alloy 182 weld 

metal, the SCC growth rates under constant K loading were typically <3x10-9 mm/s in PWR 

primary water and only reached ~1x10-8 mm/s in oxidizing BWR water with high sulfate impurity 

additions. As a result, it was not possible to effectively assess the effect of the alloy 52M 

interface on the propagation of a highly engaged, rapidly growing IGSCC crack front. However, 

the crack growth response during periodic unloading and at constant K decreased significantly 

as crack front approached the alloy 52M interface. This may be due to local fingers of IG 

growth reaching and slowing at the alloy 52M as well as due to residual stresses near the 

interface influencing the applied crack-tip stresses and slowing growth at the crack front. In 

either case, the beneficial effect of the alloy 52M overlay or inlay to impede SCC propagation 

was observed.

A final step in all tests was to use aggressive cycling to move the crack front into the alloy 52M 

weld metal and evaluate SCC response under PWR primary water conditions. In nearly all 

cases, the measured SCC growth was limited with propagation rates at or below ~4x10-9 mm/s. 

The one exception was for the alloy 52M overlay specimen CT035 where a weld pass was 

discovered with a much lower bulk Cr concentration of ~24 wt%. In this region, an SCC growth 
4-36

rate of 1x10-8 mm/s was measured at the high K level of 49 MPa√m. Since this was an offnormal and lower Cr weld metal composition, the observation of a moderate SCC propagation 

rate is not considered of practical importance. Overall, the alloy 52M weld metal employed for 

the overlay and inlay mockups were quite resistant to SCC in PWR primary consistent with the 

weld metals discussed in Chapter 3.

Additional tests on high-Cr weld overlays and inlays are clearly warranted and plans are in place 

to fabricate at least two alloy 52M overlays on alloy 182 pipe welds. Detailed microstructural 

characterizations will be performed followed by crack-growth tests investigating and quantifying 

SCC propagation from the alloy 182 weld metal into the alloy 52M weld metal. Selected 

experiments may also be conducted evaluating SCC growth along the interface region between 

the alloy 182 and the alloy 52M overlay.
5-1 

5 INTERFACES AND DILUTION ZONES IN DM WELDS 

Part of this effort to investigate SCC susceptibility in alloy 152/52/52M welds has included 

studying the response of these materials in DM weld mockups where there is a potential for 

dilution zones, high fabrication-induced stresses/strains and hardening that may increase SCC 

susceptibility. Studies of DM weld dilution zone, fusion line, and heat affected zone (HAZ) SCC 

response have been subject of investigation for BWR reactor conditions. The primary focus of 

these studies has been to assess the CGR as a crack grows through the weld dilution zone 

and/or along the interface between the Ni-alloy weld metal and the steel. In some cases, the 

crack path has crossed the fusion line and propagates into the steel. The effect of dilution on 

SCC CGR in these studies utilizing alloy 182 has been indeterminate which is not surprising 

because alloy 182 is an SCC-susceptible material, but cessation of constant load crack growth 

has consistently occurred when the crack reaches the bulk low alloy steel (LAS). Studies have 

attempted to assess fusion line or LAS HAZ response of DM welds by positioning specimens 

parallel to the fusion line. These studies have shown no accelerated SCC growth in these 

regions that were made using prototypic fabrication methods that included a post weld heat 

treatment (PWHT).

Alloy 152/52 is a much more SCC resistant material than alloy 182, and the possibility of 

increased susceptibility in weld dilution or fusion line regions of DM welds is of greater concern. 

This chapter describes the primary water SCC response at or near the fusion line of four DM 

weldments (alloy 152/304SS, alloy 152M/carbon steel (CS), alloy 52M/CS and alloy 152/LAS) 

where specimens have been aligned for crack growth to occur parallel to the fusion line in either 

the weld dilution zone, on the fusion line, or in the HAZ.

5.1 Dissimilar Metal Welds: Materials and Specimens

The fabrication and composition of the alloy 152/304SS U-groove weld (made by MHI for 

Kewaunee, supplied by EPRI) and the alloy 52M-CS V-groove weld (provided by George Young 

of KAPL) have both been described earlier in this report. The alloy 152M/CS V-groove weld is 

identical in geometry to the alloy 52M/CS V-groove weld. However, manual welding was 

employed for the alloy 152M instead of automated welding for the alloy 52M. The compositions 

of these weld materials are listed in Table 5-1, while the compositions of the 304SS and the 

A516 CS were not available. The alloy 152 U-groove weld was fabricated using buttering 

applied to the 304SS, but neither of the V-groove welds were made with butter weld steps, and 

neither were given a PWHT that is part of standard practice for nuclear reactor component 

joining of CS or LAS to nickel-base alloys. A slice was also obtained from ANL of an alloy 152 – 

LAS DM weld designated as V2. This weld used two different alloy 152 weld wire heats 

(WC04F6 and 146444) with reported compositions given in Table 5-1. The final DM weld 

evaluated was an alloy 52M temper bead repair weld produced by EPRI and no PWHT was 

required or applied.
5-2

Table 5-1 Composition of the Alloy 152/152M/52M Used for the DM Welds

Material - Source Heat Numbers and Description Weld Metal Composition 

(wt%)

Alloy 152/SS - MHI

Filler and Butter: heat 307380

U-groove mock-up weld using 304SS

plate for Kewaunee reactor used for

specimens CT075 and CT076.

Ni-28.7Cr-9.1Fe-0.03C-3.6Mn0.33Si-0.15Al-0.12Ti-0.003S

Alloy 152M/CS - 

KAPL

Filler: heat WC83F8

V-groove weld, carbon steel and

316SS plate, no butter used on the 

CS, no PWHT applied to the CS used 

for specimens CT066 and CT082.

Ni-30.2Cr-8.7Fe-<0.005C3.0Mn-0.22Si-<0.01Al-0.03Ti1.18Nb

Alloy 52M/CS - 

KAPL

Filler: heat NX5285TK

V-groove weld, carbon steel and

316SS plate, no butter used on the 

CS, no PWHT applied to the CS used 

for specimens CT065 and CT083.

Ni-30.0Cr-7.9Fe-0.014C0.75Mn-0.13Si-0.11Al-0.21Ti0.81Nb+Ta

Alloy 152/LAS - 

ANL

Filler and Butter: heat WC04F6 (1) top 

portion, specimen CT117 and heat 

146444 (2) bottom portion, specimen 

CT119

(1) Ni-28.7Cr-10.4Fe-0.048C3.48Mn-0.41Si-0.06Al-0.09Ti1.54Nb+Ta

(2) Ni-29.0Cr-9.4Fe-0.040C3.56Mn-0.46Si-0.24Al-0.15Ti1.84Nb+Ta

Alloy 52M/LAS 

temper bead 

repair- EPRI

Filler: heat NX8956TK used for 

specimen CT136

Ni-29.9Cr-8.6Fe-0.020C0.72Mn-0.03Si-0.13Al-0.21Ti0.81Nb+Ta

Two alloy 152/304SS DM weld fusion line specimens (CT075 and CT076) were cut from blanks 

as shown in Figure 5-1. After machining, the side grooves of the specimens were polished and 

etched to reveal the fusion line region to confirm the target location and to provide information 

on the microstructure that the crack would encounter (Figures 5-2 and 5-3). Based on these 

side-groove images, the geometric crack growth plane is very well aligned with the fusion line in 

both specimens. Specimen #1 appears to be exactly on the fusion line, while specimen #2 is in 

the 304SS at no more than 100-150 um from the fusion line.
5-3 

Figure 5-1 Photograph Showing the Target Orientation of the Two Alloy 152/304SS DM 

Weld Fusion Line Specimens (CT075 and CT076)

Figure 5-2 Polished and Etched Side Grooves of the MHI Alloy 152/304SS DM Weld 

Fusion Line Specimen #1 (CT075). Notch Can Be Seen on the Left Edge of 

the Optical Image

 

Figure 5-3 Polished and Etched Side Grooves of the MHI Alloy 152/304SS DM Weld 

Fusion Line Specimen #2 (CT076). Notch Can Be Seen on the Left Edge of 

the Optical Image
5-4

Two alloy 52M/CS and two alloy 152M/CS weld specimens were machined and SCC tested. 

The target SCC test region in the first pair of specimens (one alloy 52M and one alloy 152M) 

was the weld dilution zone and the fusion line was the target for the second pair. Photos 

showing the orientation of the first specimens relative to the welds are shown in Figure 5-4, 

while higher magnification images of the polished and etched side grooves are shown in 

Figure 5-5 for the alloy 52M (CT065) and Figure 5-6 for the alloy 152M (CT066). Based on 

these images, the notch of the alloy 52M specimen was well positioned at ~0.5 mm offset from 

the fusion line in the weld metal. The notch in the alloy 152M specimen was positioned 

somewhat further away at 0.5-1.5 mm offset from the more undulating fusion line of the 

manually joined weldment. Examination of the side-groove images (most easily seen in the 

images of the alloy 52M), shows that the grain boundaries are at a ~60 degree angle to the 

geometric crack growth plane. This is clearly not an optimal geometry for IGSCC testing, and 

other geometries were considered such as aligning the specimens so that notch was in the alloy 

152M or 52M and the crack was aligned to grow towards the fusion line on a trajectory parallel 

to the weld grain boundaries. While this produces the best possible alignment to the grain 

boundaries for IG cracking, assessment of the dilution zone is limited to just that one region 

where the crack can grow. The orientation selected for this study allows for a much greater 

amount of material to be tested, and if a dilution zone is susceptible, IG cracking will occur even 

at this suboptimal orientation relative to the grain boundaries.

Figure 5-4 Optical Images Showing the Target Location of the Alloy 52M and Alloy 

152M Dilution Zone CT Specimens (CT065 and CT066)

Figure 5-5 Polished and Etched Side Grooves of the Alloy 52M/CS Dilution Zone 

Specimen (CT065) Showing That the Crack Growth Plane Is ~0.5 mm into 

the Alloy 52M
5-5 

 

Figure 5-6 Polished and Etched Side Grooves of the Alloy 152M/CS Dilution Zone 

Specimen (CT066) Showing That the Crack Growth Plane Is ~0.5-1.5 mm 

into the Alloy 152M

The second pair of specimens was oriented to specifically target the fusion line and CS HAZ. 

The specimens were again positioned parallel to the fusion line, but in this case, the goal was to 

line up the geometric crack path with the fusion line or slightly into the CS. Figure 5-7 shows 

that geometric crack path of the alloy 152M fusion line specimen (CT082) was very well aligned 

with the fusion line in side groove A, while side-groove B was slightly further into the CS than 

was desired. Figure 5-8 shows that the alloy 52M fusion line specimen (CT083) was very well 

aligned in both side grooves with the geometric crack path starting exactly on the fusion line and 

drifting no more than ~0.4 mm into the CS.

 

Figure 5-7 Polished and Etched Side-Grooves of the Alloy 152M/CS Fusion Line 

Specimen (CT082) Showing That the Crack Growth Plane Is ~0.5-1 mm into 

the A516 CS
5-6

Figure 5-8 Polished and Etched Side-Grooves of the Alloy 52M/CS Fusion Line 

Specimen (CT083) Showing That the Geometric Crack Growth Plane Starts 

on the Fusion Line and Drifts ~0.4 mm into the A516 CS

The next two tests were conducted on an alloy 152 – LAS DM weld received from ANL 

designated as v2. This followed prior crack growth experimentation at ANL that revealed high 

SCC propagation rates in the alloy 152 dilution zone adjacent to the LAS. A metallographic 

slice was taken from the weld enabling detailed characterizations to be performed on the alloy 

152 – LAS regions of interest. As expected, the weld microstructure in the dilution zone 

contained large solidification grain oriented perpendicular to the 152/LAS interface and the 

crack-growth path in the CT specimens. However, isolated areas were also found where grain 

boundaries aligned with the crack path were discovered along with Type II boundaries as 

illustrated in Figure 5-9. The dilution zone composition was mapped by SEM EDS and revealed 

bands of Fe enrichment and Cr depletion near several of these aligned boundaries in Figures 

5-10 and 5-11.

Figure 5-9 SEM-BSE Image Highlighting the Microstructure in the Alloy 152 – LAS 

Dilution Zone of the ANL V2 Alloy 152 DM Weld
5-7 

Figure 5-10 SEM-EDS Composition Maps from the Area near Aligned Grain Boundary 

#1

Figure 5-11 SEM-EDS Composition Maps from the Area near Aligned Grain Boundary 

#2
5-8

Figure 5-12 Optical Image Showing the Location of the Alloy 152 - LAS Dilution Zone

CT Specimens (CT117 and CT119). Alloy 152 Weld Metal in Upper Portion 

Is Heat WC04F6 and in Lower Portion Is Heat 146444

Specimens CT117 and CT119 were machined from the slice as shown in Figure 5-12 and 

macro images of the CT specimens presented in Figures 5-13 and 5-14. Higher magnification 

side groove images illustrating the position of the notch and crack growth plane for CT119 are 

given in Figure 5-15 along with a SEM/EDS composition map for Fe in Figure 5-16. Significant 

Fe enrichment (and Cr depletion) is present before and after the first and second weld passes 

with a particularly high Fe concentration just entering the second pass along the crack growth 

plane. Polished and etched side-groove images for specimen CT117 are presented in Figure 

5-17. Side B etching revealed very distinctive Fe-rich regions before and after the transition

from the first to second weld pass. Much less compositional change is apparent from the

etched appearance for Side A.

CT117

CT119
5-9 

Figure 5-13 Macro Images of the Alloy 152v2 DZ CT117 Specimen

Figure 5-14 Macro Images of the Alloy 152v2 DZ CT119 Specimen

Weld pass where 

IGSCC occurred in 

N152-LAS-11.
5-10

Figure 5-15 Polished and Etched Side-Grooves of the ANL 152v2 Specimen CT119

Figure 5-16 SEM-EDS Elemental Maps of Fe-K on Side-Grooves of the ANL 152v2 

Specimen CT119

alloy 152

LAS

strong Fe enrichment
5-11

Figure 5-17 Polished and Etched Side-Grooves of the ANL 152v2 Specimen CT117

The final weld examined within this chapter is the EPRI temper-bead, alloy 690 – alloy 52M – 

LAS DM repair weld and a cross-section picture of the slice obtained at PNNL is presented in 

Figure 5-18. Detailed SEM and hardness characterizations were performed at several locations 

including the alloy 52M – LAS dilution zone region where CT specimen 136 was machined as 

documented in the lower image in Figure 5-18. Once again, side grooves for the CT specimen 

were polished to reveal the crack growth path (Figure 5-19) and higher resolution SEM exams 

identified local areas with aligned grain boundaries and Fe enrichment (Figure 5-20, side A). 

This region started at ~2 mm from the specimen notch and continued for more than 1 mm. 

However, such areas were isolated and were not found on side B side groove in Figure 5-20. 

Beyond the microstructural and microchemical features in the dilution zone, lack of fusion (LOF) 

cracks were discovered at a few local 52M/LAS interface regions. One of the LOF regions was

positioned immediately ahead of the notch, providing an opportunity for its effect on SCC growth 

to be assessed. Two small cracks can be seen at identical locations on the Side A and B side 

grooves shown in Figures 5-21 and 5-22, respectively.
5-12

Figure 5-18 Etched Cross-Section Slice from the EPRI Temper Bead DM Repair Weld, 

Measured Hardness Maps and CT Specimen Layout Positions Are 

Superimposed in the Bottom Image. The Alloy 52M – LAS Dilution Zone 

Specimen CT136 Is on the Right

LAS 52M 

Butter

52M 

Repair

52M 

Original 

Weld

Alloy 690
5-13

Figure 5-19 Polished and Etched Side-Grooves of the EPRI Temper Bead DM Repair 

Weld Specimen CT136
5-14

Figure 5-20 Highlighted Area of Fe Enrichment (and Cr depletion) Region 

Corresponding to the Presence of Two Aligned Grain Boundaries in the 

First Weld Pass of Side A for the EPRI Temper Bead DM Repair Weld 

Specimen CT136

Composition maps for Fe and Cr are included to confirm the interface location and indicate 

small regions in the weld metal where Fe ingress has occurred causing Cr depletion. A minor 

dilution zone can be identified near the LAS interface immediately before the LOF cracks. 

Higher magnification SEM images and composition maps document that two small cracks are 

present and there is a sharp transition from the LAS to the 52M weld metal without any dilution. 

Additional details on the LOF defect morphologies can be seen in Figure 5-22 where the cracks 

are primarily along the 52M/LAS interface, but do extend a small distance off the interface. 

alloy 52M

LAS

Side A - EDS Fe Map
5-15

Figure 5-21 SEM-BSE Images and EDS Elemental Maps Showing the 52M/LAS Interface 

Ahead of the Notch in the Side A Side Groove for the CT136 Specimen. 

Bottom Images Highlight the Local LOF Cracks

LOF Cracks

LOF Cracks

Side A

Fe Enrichment

Cr Depletion
5-16

Figure 5-22 SEM-BSE Images and EDS Elemental Maps Showing the 52M/LAS Interface 

Ahead of the Notch in the Side B Side Groove for the CT136 Specimen. 

Bottom Images Highlight the Local LOF Cracks

5.2 MHI Alloy 152-SS DM Weld Interface Specimens (CT075 and CT076)

SCC testing was initiated in January 2012 on two specimens made from MHI alloy 152 mockup 

U-groove weld (heat 307380) joining two pieces of 304SS plate. As noted in Section 1.1, CT

specimens were machined to evaluate the fusion line and dilution zone regions between the

alloy 152 butter (also heat 307380) and the stainless steel. An overview of the entire test on

these two specimens is shown in Figure 5-23 and summarized in Table 5-2. As can be seen in

the plot, CT076 exhibited much higher CGRs during aggressive cycling at ~1700-1900 h and

~3000-3250 h. As a result, the K value increased for CT076 during the test and slightly

decreased for CT075. A total of four constant K crack growth assessments were made in three

separated microstructural regions that were selected based on side-groove images (Figures 5-2

and 5-3). The crack growth response for the first and second constant K assessments (when

CT076 was still at moderate K level) is shown in Figure 5-24. Variations in hold time from 1 to

10 h were applied during the final transitioning steps in attempt to improve IG engagement, but

it did not obviously affect the constant K crack growth response with all measurements lying

between 1.9 and 3.8x10-9 mm/s. When considered on a per specimen basis, the constant K

CGRs are suggestive of a very small dependency on stress intensity. Application of gentle

LOF Cracks

LOF Cracks

Side B
5-17

cycle + hold loading after constant K assessments did not produce transient high CGRs that 

would be suggestive of ligament/contact formation or an uneven crack front during constant K.

Figure 5-23 Overview of the Entire Test on the Two Alloy 152/304SS Fusion Line 

Specimens 
5-18

Table 5-2 Test Summary for MHI Alloy 152/304SS Weld Fusion Line Specimens CT075 

and CT076

CT076

MHI A152 UG/304SS FL 

#2

CT075

MHI A152 UG/304SS FL 

#1

Test 

Phas

e

Start 

(h)

Time

(h) R

Freq. 

(Hz)

Hold 

(h)

Dis

s H2

(cc / 

kg)

T 

(°C

)

Kmax 

(MPa

√m)

CGR 

(mm/s)

Crack 

Ext

(mm)

Kmax 

(MPa

√m)

CGR 

(mm/s)

Crack 

Ext 

(mm)

0 0 123 --- const K --- 25 360 35 --- --- 32.5 --- ---

1 123 239 0.

5

0.001 2.5 25 360 35 1.1E-07 0.093 32.5 1.9E-08 0.019

2 361 448 0.

5

0.001 10 25 360 35 3.1E-08 0.045 32.5 7.4E-09 0.012

3a 809 615 --- const K --- 25 360 35 4.0E-09 0.005 32.5 3.3E-09 0.006

3b 1424 351 --- const K --- 25 360 35 2.5E-09 0.005 32.5 2.6E-09 0.003

4 1775 42 0.

5

0.01 0 25 360 36 5.3E-06 0.813 31.5 1.3E-06 0.199

5 1817 75 0.

5

0.001 0 25 360 38 8.9E-07 0.264 31 1.8E-07 0.057

6 1892 235 0.

5

980s/20s 2.5 25 360 39 1.3E-07 0.118 30 3.4E-08 0.029

7 2127 315 0.

5

980s/20s 10 25 360 39 3.7E-08 0.041 30 2.0E-08 0.008

8 2442 605 0.

5

const K --- 25 360 39 2.5E-09 0.004 30 2.6E-09 0.005

9 3047 38 0.

5

0.01 0 25 360 44 7.1E-06 0.937 29 1.8E-06 0.179

10 3085 125 0.

5

0.001 0 25 360 50 1.9E-06 0.844 28 3.1E-07 0.128

11 3210 268 0.

5

980s/20s 2.5 25 360 54 2.2E-07 0.292 27.5 2.6E-08 0.031

12 3478 524 --- const K --- 25 360 54 3.8E-09 0.019 27.5 2.4E-09 0.010

13 4002 118 0.

5

980s/20s 2.5 25 360 55 2.0E-07 0.144 27.5 2.4E-08 0.010

14 4120 140 0.

5

980s/20s 10 25 360 56 5.7E-08 0.032 27.5 3.9E-09 0.004

15 4260 314 --- const K --- 25 360 56 2.9E-09 0.001 27.5 1.9E-09 0.000

Total 4574 3.748 0.702

After SCC testing, the side grooves of the specimens were again photographed as shown in 

Figure 5-25 for CT075 and Figure 5-26 for CT076 to document crack length and crack path. 

Cracking on the fusion line is clearly evident in CT075 in the latter part of the test. With such 

good alignment to the fusion line, it is unclear whether the crack has a preference to stay on the 

fusion line. Also notable is that the crack length in side-groove A is ~3.0 mm, while it is 

~2.1 mm in side-groove B. The side-groove images of CT076 show that it reaches the fusion 

line part way through the test, but then continues to follow a straight path back into the 304SS 

suggestive of no preference to stay on or near the fusion line. Crack length is essentially 

identical on both sides of the specimen. The large crack opening for CT076 is due to the very 

high K later in the test.
5-19

Figure 5-24 Crack Growth During the First and Second Constant K Assessments of the 

Alloy 152/304SS Fusion Line Specimens (CT075 and CT076)
5-20

Figure 5-25 Post-Test Optical Images of the Polished and Etched Side Grooves for the 

First Alloy 152/304SS Fusion Line Specimen (CT075). Approximate 

Locations for the Constant K or Constant Load Exposures Are Indicated by 

the Arrows
5-21

Figure 5-26 Post-Test Optical Images of the Polished and Etched Side Grooves for the 

Second Alloy 152/304SS Fusion Line Specimen (CT076). Approximate 

Locations During Constant K or Constant Load Exposures Are Indicated by 

the Arrows

Next, the specimen was sliced into an 8-mm thick piece and a 4-mm thick piece. The thicker 

piece was fatigued open for crack growth surface examinations, while the thinner piece was 

used for crack profile examinations. Images of the crack profile of CT075 and CT076 are shown 

in Figures 5-27 and 5-28, respectively. The optical image of CT075 shows a highly branched 

precrack (first ~1.2 mm) driven through the alloy 152 weld metal. In-situ testing begins in the 

alloy 152, and then the crack passes through the fusion line and stays within 100-200 μm from 

the fusion line in the 304SS. The fact that the crack did not remain on the fusion line suggests 

no strong preference for this region. The crack profile for CT076 (SEM images in Figure 5-28) 

shows the crack growing in the 304SS until the final ~1.5 mm where it meets the fusion line. 

Instead of following the fusion line, the crack appears to deflect back into the 304SS. When 

considering all the crack profile images together, there does appear to be a tendency for 

cracking to take place in the 304SS instead of the alloy 152. SEM-EDS maps did not reveal 

strong dilution effects in the alloy 152.
5-22

Figure 5-27 Optical Image of the Interior Crack Profile of the Alloy 152/304SS Specimen 

#1 (CT075)

Figure 5-28 SEM-SE and EDS Elemental Maps of the Interior Crack Profile of the Alloy 

152/304SS Specimen #2 (CT076)

Optical images of the crack surface for CT075 and CT076 are shown in Figures 5-29 and 5-30, 

respectively. Notations are written on the images to show how the sides of the specimen 

correspond to either the crack profile or the side grooves to allow comparison to those images. 

CT075 has a more undulated crack with a minimum length of ~2 mm in this image and also a 

minimum length of ~2 mm as observed in side-groove B (Figure 5-25). Some evidence of 

limited crack extension into the alloy 152 weld metal was observed in CT075 and was confirmed 

by SEM. A key result from the optical and SEM characterizations of crack-growth surfaces is 

that no IG cracking was found as illustrated in Figures 5-31 and 5-32. The TG cracking

provides confirmation that the alloy 152/304SS weld fusion line is indeed resistant to IGSCC in 

PWR primary water. 
5-23

Figure 5-29 Optical Image of the Crack Surface of Alloy 152/304SS Fusion Line 

Specimen #1 (CT075)

Figure 5-30 Optical Image of the Crack Surface of Alloy 152/304SS Fusion Line 

Specimen #2 (CT076)
5-24

Figure 5-31 SEM-SE Montage of the Crack Surface of Alloy 152/304SS Fusion Line 

Specimen #2 (CT076) Illustrating TG Cracking Morphology

Figure 5-32 SEM-SE Images of the Typical Crack Surface Regions of Alloy 152/304SS 

Fusion Line Specimen #2 (CT076) Illustrating TG Cracking Morphology

5.3 Alloy 152/52-LAS/CS Interfaces

5.3.1 KAPL 52M/152M-CS DM Weld Interface (CT065 and CT66)

Crack-growth testing was conducted on CS dilution zone specimens from the alloy 52M and 

alloy 152M dissimilar metal V-groove welds provided by KAPL. As described in section 5.1, the 

geometric crack plane was positioned ~0.5 mm from the fusion line in the weld metal for both 

specimens as illustrated in Figures 5-5 and 5-6. An overview crack growth plot of the entire test 

on these two specimens is shown in Figure 5-33 and a test summary is given in Table 5-3. 

These two specimens behaved quite similarly during the first transitioning and constant K 

assessment, and constant K CGRs were found to be very low at ~3x10-9 mm/s. However during 

the second transitioning sequence, the alloy 152M-CS specimen began exhibiting higher and 

higher cyclic CGRs, and as more gentle load cycling conditions were applied, this response 

persisted while the alloy 52M-CS specimen continued to exhibit low CGRs. For the second 

SCC CGR evaluation, constant load was used instead of constant K. As shown in Figure 5-34, 

the alloy 152M-CS specimen CT066 initially showed a low CGR of ~3x10-9 mm/s, but the CGR 

evolved with time reaching ~2x10-6 mm/s after ~1200 h at constant load. The test was ended at 

this point to examine the specimens.
5-25

Because of the differing response between the two specimens and the desire to analyze for 

weld dilution, the decision was made to section half of each specimen into five crack profile 

slices, and then fatigue open the other half of the specimen as depicted in Figure 5-35. The 

side grooves of the specimen were also examined. Specimen characterizations focused first on 

the alloy 52M-CS specimen (CT065) that exhibited consistently low CGRs throughout the test. 

Initial observations of the side grooves (Figure 5-36) revealed that the crack followed a straight 

trajectory staying within the alloy 52M at a distance of no more than ~0.5 mm away from the 

fusion line. SEM-EDS observations of the crack profile in Figure 5-37 confirmed this trajectory 

and also showed that the crack did not sample any regions of significant dilution during SCC 

testing. In particular, the locations of constant K observations are noted. Other crack profile 

observations showed a similar lack of dilution in the region of SCC testing. Crack surface 

observations revealed entirely TG crack growth that was not surprising due to the lack of dilution 

and the ~60° misorientation between the geometric crack path and the weld grain boundaries.

Figure 5-33 Overview of the Entire SCC Test on the Alloy 52M/152M-CS Dilution Zone 

Specimens (CT065 and CT066)
5-26

Table 5-3 Test Summary for KAPL Alloy 52M/CS and Alloy 152M/CS Dilution Zone 

Specimens CT065 and CT066

CT065

KAPL A52M/LAS VG DZ

CT066

KAPL A152M/LAS VG DZ

Test 

Phas

e

Start 

(h)

Tim

e 

(h) R

Freq. 

(Hz)

Hol

d (h)

Dis

s H2

(cc / 

kg)

Tem

p 

(°C)

Kmax 

(MPa√m

)

CGR 

(mm/s)

Crack 

Exten

. 

(mm)

Kmax 

(MPa√m

)

CGR 

(mm/s)

Crack 

Exten

. 

(mm)

1 0 25 0.

5

0.1 0 25 360 30 2.6E060.256 32 4.1E060.381

2 25 120 0.

5

0.01 0 25 360 30 6.4E070.225 33 9.2E070.351

3 145 440 0.

5

0.001 0 25 360 30 9.6E080.152 33 1.7E070.256

4 585 340 0.

5

0.001 2.5 25 360 30 1.7E080.012 33 2.4E080.021

5 925 175 0.

5

980s/20

s

0 25 360 30 1.1E070.063 33 2.1E070.116

6 110

0

830 0.

5

980s/20

s

1 25 360 30 2.0E080.072 34 3.8E080.128

7 193

0

179 0.

5

980s/20

s

2.5 25 360 30 1.6E080.007 34 2.2E080.013

8 210

9

550 --- const K --- 25 360 30 3.2E090.006 34 2.9E090.004

9 265

9

158 0.

5

0.01 0 25 360 31 6.4E070.358 35 1.0E060.549

10 281

7

317 0.

5

0.001 0 25 360 31 1.1E070.115 35 2.1E070.180

11 313

4

243 0.

5

0.001 1 25 360 31 1.9E080.018 35 4.5E080.039

12 337

7

182 0.

5

0.001 0 25 360 31 9.9E080.057 36 1.7E070.093

13 355

9

246 0.

5

480s/20

s

0 25 360 31.5 1.6E070.273 37 1.8E070.404

14 380

5

247 0.

5

980s/20

s

0 25 360 32 1.2E070.111 37 1.4E070.126

15 405

2

744 0.

5

980s/20

s

2.5 25 360 32 1.8E080.053 42 3.5E070.898

16 479

6

420 0.

5

980s/20

s

10 25 360 32 3.7E090.009 44 2.7E070.288

17 521

6

1350 --- const K --- 25 360 32 1.5E090.007 53 1.9E061.058

Total

656

6 1.791 4.903
5-27

Figure 5-34 Crack Growth of the Alloy 52M/152M-CS Dilution Zone Specimens CT065 

and CT066 During the Second SCC Assessment

Figure 5-35 Post-Test Specimen Sectioning Plan for the Alloy 52M/152M-CS Dilution 

Zone Specimens CT065 and CT066
5-28

Figure 5-36 SEM-BSE Images of the Side Grooves for the Alloy 52M-CS Dilution Zone 

Specimen (CT065) After SCC Testing

Figure 5-37 SEM-EDS Fe Map of the Alloy 52M-CS Dilution Zone Specimen (CT065) 

Crack Profile Slice #5 Showing Composition in the Region Around the 

Crack

Examination of the alloy 152M-CS dilution zone specimen also started with side-groove 

examinations, however the length of the crack in the side grooves was much shorter than the 

DCPD crack length indicating that not all the crack was visible in the side grooves. Therefore, 

characterizations focused on the crack profile and crack-growth surface. The SEM-BSE image 

of the inner-most slice (slice #5) of the alloy 152M-CS specimen in Figure 5-38 and the 

corresponding SEM-EDS Fe map in Figure 5-39 provides a good representation of what 
5-29

microstructures the crack encountered during testing. During the first transitioning and constant 

K observation, the crack was entirely within the alloy 152M weld metal, and as shown in the 

EDS map, the crack encountered a region of significant dilution (single pass region shows Cr 

depletion to ~20 wt% and Fe enrichment to ~40 wt%) during the first constant K assessment. 

The step-like crack path during the first transitioning suggests some preference for crack growth 

parallel to the long grain boundaries, however higher resolution images of this slice, the other 

slices (Figure 5-40) and the crack growth surface (Figure 5-41) revealed that the crack was 

predominately TG during constant K SCC testing in the ~20 wt% Cr dilution zone.

Figure 5-38 SEM-BSE Image of the Inner Most Slice (#5) Cut from the Alloy 152M-CS 

Dilution Zone Specimen (CT066)

Figure 5-39 Corresponding SEM-EDS Fe-K Map for the SEM-BSE Image in Figure 5-38 

of the Alloy 152M-CS Specimen (CT066). Locations of Constant K or 

Constant Load Evaluations Are Indicated by the Arrows
5-30

Figure 5-40 SEM-BSE Images of Slices #2 and #3 from the Alloy 152M-CS DZ Specimen. 

The Crack Can Be Seen to Intersect and Remain on the Fusion Line for a 

Short Distance in Both Slices

During the second transitioning sequence, the crack continued on a downward trajectory that it 

had started during the first transitioning sequence and eventually reached the fusion line. 

Comparison of the crack growth plot to the crack profile and crack surface images indicated that 

the very high CGRs happened after the crack reached the fusion line and then grew partly on 

the fusion line and partly in the CS HAZ. Subsequent EBSD examinations of slice #5 (Figure 

5-42) showed that the CS has an extremely fine grain size in the immediate vicinity of the fusion

line, while microhardness measurements (Figure 5-43) showed correspondingly high Vickers

hardness ranging from 200-300 kg/mm2 in this ~1 mm wide zone along the fusion line. This fine

grain, high hardness region was due to a martensitic transformation that occurred during the

welding process. In a typical nuclear reactor pressure boundary component that is fabricated by

a DM weld involving carbon or low alloy steel, the steel is first buttered and then given a PWHT

that tempers the martensite and reduces its strength.
5-31

Figure 5-41 Optical Image of a ~6 mm Width of the Crack Growth Surface for the Alloy 

152M-CS Specimen CT066. A Reconstruction of the Other Half Is Included 

Based on Crack Profile Exams

Figure 5-42 SEM-EBSD Analysis of the Alloy 152M-CS Specimen CT066 in the Region 

of the Fusion Line
5-32

Figure 5-43 Map of Microhardness Measurements Across the CS – Alloy 152M Interface 

Region in Slice #5 from the Alloy 152-CS DM Weld Specimen CT066.KAPL 

52M/152M-CS DM Weld Interface (CT082 and CT083)

A second set of specimens was machined from the KAPL DM welds and tested to assess SCC 

susceptibility of the fusion line and CS HAZ region including the influence of a PWHT. Side 

grooves for these specimens were presented in Figures 5-7 and 5-8. As shown in the overview 

plot in Figure 5-44 and Table 5-4, the first portion of the test was run with the materials in the 

as-welded condition. Constant K testing in simulated PWR primary water at ~30 MPa√m 

produced a ~7x10-9 mm/s CGR for the alloy 52M-CS fusion line specimen (CT083) but only 

~2x10-9 mm/s CGR for the alloy 152M-CS fusion line specimen (CT082). Increasing the stress 

intensity by a dK/da sequence and then re-transitioning to constant K at 36-40 MPa√m resulted 

in a ~10X CGR increase to ~6x10-8 mm/s for the alloy 52M-CS fusion line specimen, but did not 

affect the CGR of the alloy 152M-CS fusion line specimen (Figure 5-45). Having produced a 

CGR in the alloy 52M-CS fusion line specimen that was similar to the first test on these 

V-groove welds, the test was stopped, and the specimens were removed and given a prototypic

PWHT of 621°C for 10 hours followed by air cooling. The specimens were reloaded into the

autoclave and testing was resumed. After ~200 μm of crack extension during transitioning,

constant K conditions were established resulting in ~2x10-9 mm/s CGRs for both specimens.

Cycle + hold loading was restarted to move the crack forward and test for ligament formation.

Steady growth was observed over ~100 μm, and the test was converted to constant K for the

last time. Low CGRs were again observed over a period of ~800 h as documented in Figure

5-46. The test was ended and the specimens were sliced up and fatigued open for

examinations. The optical and SEM images in Figure 5-47, suggest that the alloy 152M-CS

fusion line specimen (CT082) exhibited low crack growth because the geometric crack growth

plane was not well aligned with the fusion line. On side-groove side B of the specimen, the

fusion line was in the CS, but a considerable distance from the fusion line (~1 mm). On side A,

the crack grew primarily in the alloy 152M until reaching the fusion line at the very end of the

test. The optical image collage of the alloy 52M-CS fusion line specimen (CT083) in Figure

5-48 reveals that cracking was well aligned with the fusion line and significant growth occurred

either on the fusion line or in the CS HAZ region both before and after the PWHT.
5-33

Figure 5-44 Overview Crack Growth Plot of the Entire Test on the Alloy 152M/52M-CS 

Fusion Line Specimens (CT082 and CT083)
5-34

Table 5-4 Test Summary for KAPL Alloy 152M/CS and Alloy 52M/CS Dilution Zone 

Specimens CT082 and CT083

CT082

KAPL 152M/CS FL test

CT083

KAPL 52M/CS FL test 

Test 

Phas

e

Start 

(h)

Tim

e 

(h) R

Freq. 

(Hz)

Hol

d (h)

Dis

s H2

cc / 

kg)

Tem

p 

(°C)

Kmax 

(MPa√m

)

CGR 

(mm/s)

Crack 

Exten

. 

(mm)

Kmax 

(MPa√m

)

CGR 

(mm/s)

Crack 

Exten

. 

(mm)

1 0 29 0.

5

0.1 0 25 360 30 5.5E060.566 32 6.7E060.664

2 29 74 0.

5

0.01 0 25 360 30 5.5E070.134 33 2.8E070.069

3 103 209 0.

5

0.001 0 25 360 30 9.1E080.076 33 4.0E080.024

4 312 193 0.

5

980s/20

s

0 25 360 30 9.1E080.067 33 3.0E080.028

5a 505 738 0.

5

980s/20

s

2.5 25 360 30 2.2E080.074 33 2.4E080.087

5b 124

3

123 0.

5

980s/20

s

2.5 25 360 30 2.4E080.013 33 2.9E080.012

6 136

6

333 0.

5

980s/20

s

10 25 360 30 8.8E090.011 33 1.3E080.015

7 169

9

1186 --- const K --- 25 360 30 2.8E090.005 33 7.9E090.020

8 288

5

94 0.

5

980s/20

s

2.5 25 360 30 1.2E080.031 33.5 5.5E080.057

9 297

9

90 0.

5

980s/20

s

2.5 25 360 30->36 8.3E080.038 34->40 1.5E070.075

10 306

9

501 --- const K --- 25 360 36 1.9E090.002 40 6.3E080.064

PWHT PWHT

11 357

0

468 0.

5

980s/20

s

2.5 25 360 36 3.7E080.082 40 4.2E080.115

12 403

8

338 --- const K --- 25 360 36 1.6E090.005 40 3.4E090.005

13 437

6

144 0.

5

980s/20

s

2.5 25 360 36 3.2E080.019 40 3.7E080.022

14 452

0

810 --- const K --- 25 360 36 3.3E090.010 40 5.3E090.012

Total 533

0

1.135 1.270
5-35

Figure 5-45 Constant K Crack Growth Response at 36-40 MPa√m of the Alloy 

152M/52M-CS Fusion Line Specimens Before Application of a Prototypic 

PWHT

Figure 5-46 Constant K Crack Growth Response at 36-40 MPa√m of the Alloy 

152M/52M-CS Fusion Line Specimens After Application of a Prototypic 

PWHT
5-36

Figure 5-47 Optical (upper four) and SEM-BSE (bottom) Images Showing Cracking in 

the Alloy 152M-CS Specimen (CT082) That Is Primarily in the Alloy 152M

Carbon steel Alloy 152M

Interior Crack Profile
5-37

Figure 5-48 Collage of Optical Images of the Cracking in the Alloy 52M-CS Specimen 

(CT083) Revealing Cracking Either in the CS HAZ or on the Fusion Line

SEM imaging and microhardness measurements were performed on the crack profile slices of 

the DM weld fusion line specimens CT082 and CT083 (after the PWHT). They confirmed that 

the PWHT modifies the CS HAZ microstructure as illustrated in Figure 5-49. The alloy 

152M-CS specimen CT082 exhibited a significant localized increase in the CS grain size along 

the fusion line when compared to the non-heat treated CT066 specimen. Hardness mapping on 

the CT082 specimen in Figure 5-50 revealed a decreased CS hardness (150-170 kg/mm2

) near 

the fusion line, much lower than before the PWHT (200-300 kg/mm2

). This change in hardness 

is spatially consistent with the microstructural features and suggests that the reduction in HAZ 

SCC susceptibility was due to this hardness reduction.
5-38

Figure 5-49 Collage of SEM-BSE Images Comparing Microstructural Differences 

Between the PWHT alloy152M-CS CT082 Specimen and the Non-Heat 

Treated CT066 Specimen
5-39

Figure 5-50 SEM Image of Weld Metal and HAZ (top left) with Overlaid Hardness 

Contour Plot (top right) of the Alloy 152M-CS Fusion Line Specimen 

(CT082). The PWHT Had a Significant Effect on the Measured Hardness 

near the HAZ. The Lowest Measured Hardness Values Are Seen in the 

Large Grain Region in the CS

5.3.2 Characterization of ANL 152/LAS Interface DM Weld Specimen (N152-LAS-11)

Post-test analysis of the N152-LAS-11 dilution zone CT specimen was performed in an attempt 

to better understand the observation of high crack-growth rate of this specimen at constant load. 

An example of the ANL data is shown in Figure 5-50 with an apparent SCC growth rate of 

1-2x10-7 mm/s. After testing was completed, the specimen was sectioned into several pieces by 

ANL. First, both sides of the specimen were machined flat to remove the side grooves. After 

images were obtained of the cracks on these outer sides, the specimen was fatigued open. 

One piece (denoted as Piece A) was left intact to allow studying the crack growth surface as a 

whole, while the other (denoted as Piece B) was cross-sectioned into three slices as shown in 

Figure 5-51 to enable examinations of crack profile. All four pieces were loaned to PNNL for 

analysis in support of providing further microchemistry measurements, additional imaging and to 

assist in determining where to cut DZ specimens from a section of this weldment for PWSCC 

tests on the identical dilution region at PNNL.

microhardness

plot overlay
5-40

Figure 5-50 Crack-Growth Response Reported for the Alloy 152/LAS Dilution Zone 

Specimen N152-LAS-11 with SCC Propagation Averaging ~1.4x10-10 m/s 

(1.4x10-7 mm/s)

Figure 5-51 Schematic Illustrating the Cross-Section of Face A of the ANL N152-LAS-11 

Dilution Zone CT. The Inner Portions of Section 11 and Section 22 Were 

Analyzed by PNNL

SEM BSE and SE images of the uncut crack-growth face (Face A) of ANL N152-LAS-11 are 

shown in Figure 5-52. The mass contrast generated by the SEM-BSE imaging provides a 

generally clear delineation between oxidized regions that were exposed to high temperature 

water and unoxidized regions that were fatigued open after the test was completed. The 

Section 11 and Section 22 cuts were performed on Piece B, but the corresponding section 

planes are also shown here on Face A to provide a relative location to the SCC response 

across the width of the specimen. Consistent with ANL observations, the region listed as 

"predominantly cyclic loading" was found to consist of TG cracking with isolated regions of IG 

Section 22

(polished by 

PNNL)

Crack 

growth face

Notch

Exterior Section 11

surface

Exterior 

Surface

~ 2.1 mm ~ 6.4 mm ~ 1.1 mm

Clevis pin 

hole outline

N152-LAS-11 Piece "B" Sections as cut by ANL

Constant Load

Kmax = 38 MPa√m

CORRECTED ANL DATA
5-41

cracking, all of which was in the weld. However beyond that portion of the crack growth surface, 

the surface morphology changed to either IG cracking in the weld or cracking very near or on 

the fusion line. Regions of these two types of cracking are illustrated in Figure 5-53. 

Higher magnification imaging was performed on these regions of fusion line and IG cracking. 

An SEM-BSE example of cracking on or near the fusion line is provided in Figure 5-54. IG-like 

features with a size of ~20-70 μm are apparent in portions of this region. SEM EDS scans of 

this area revealed >95Fe showing that crack growth was either on the fusion line or slightly into 

the LAS. A comparison of the cracking on Face A and the (cross) Section 11 view from Piece B 

is presented in Figure 5-55. The proximity to the fusion line is apparent in the Section 11 view. 

It appears that the unbroken ligament before the fusion line cracking is a region just prior to 

reaching the high point in the LAS in that image. SEM EDS maps show it to be weld metal.

SEM-BSE, SE and EDS examinations of Face A corresponding to the IGSCC region near 

Section 22 are presented in Figures 5-57 to 5-59. The general region of examination is shown 

in the SEM BSE image in Figure 5-57 with progressively higher magnification images revealing 

the surface morphology in Figures 5-58 and 5-59. This extensive region of “flat” IG morphology 

is unexpected and has not been previously observed on crack growth surfaces for alloy 152/52 

weld metals. SEM EDS maps were also taken within selected IG regions as documented in 

Figure 5-60 and indicated compositions of ~23 wt% Cr, ~40 wt% Ni and ~27 wt% Fe.

Figure 5-52 SEM-SE Micrographs of the Face A Crack-Growth Surface for the ANL 

N152-LAS-11 Specimen 

Corresponds 

to Section 22 Corresponds 

to Section 11

Face A - SEM BSE

Face A - SEM SE

notch location

predominantly cyclic loading
5-42

Figure 5-53 Crack-Growth Surface for the Alloy 152/LAS Dilution Zone Specimen 

N152-LAS-11

Figure 5-54 Higher Magnification SEM BSE Image of N152-LAS-11 Face A near Section 

11 Showing the Cracking Morphology on or near the Fusion Line
5-43

Figure 5-55 Comparison Between the SEM-BSE Crack Appearance on Face A and the 

Corresponding Cross Section View of the Crack on Section 11 (from Piece 

B). Cracking on or near the Fusion Line Is Between the Two Blue Arrows

Figure 5-56 SEM-BSE Micrograph of Face A with Dotted Box Showing Where Higher 

Magnification Imaging Was Performed. The Dotted Line Is a Reminder of 

the Location of the Section 22 Cut

Section 11

from Piece B 

Face A

alloy 152

LAS

crack 

growth 

direction

Face A

crack 

growth 

direction
5-44

Figure 5-57 SEM-SE Micrographs of the Primary IGSCC Region on Face A Shown in 

Figure 5-56. Dashed Box Shows Where the Higher Magnification Image 

Was Taken in the Figure on the Right. Dashed Lines in the Figure on the 

Right Illustrate Examples of Grain Boundaries

Face A

IG boundaries
5-45

Figure 5-58 SEM (SE and BSE pairs) of Regions on the Face A Crack Growth Face 

Corresponding to Figures 5-56 and 5-57 Where IGSCC Cracking Occurred

SE

SE

SE

BSE

BSE

BSE
5-46

Figure 5-59 SEM-SE Image and Elemental Maps of an IGSCC Region on Face A Similar 

to That Shown in Figure 5-58

In order to better understand the cracking morphology and the grain structure in the alloy 152 

dilution zone region, additional characterizations were performed starting with SEM EDS and 

EBSD scans on cross-section 22 as shown in Figures 5-60-5-62. An overview SEM SE image 

of the etched cross-section is presented in Figure 5-60. Cracking is from left to right with the 

notch position annotated in the image. The crack runs down towards the fusion line and after 

crossing into the second weld pass, it steps down and then continues across. The region of 

SCC growth that is documented in Figures 5-57 and 5-58 is denoted with the blue arrows. The 

etching (performed at ANL) preferentially attacked the lower Cr, making the compositional 

variations apparent in this secondary electron image.

After documenting the etched surface, the specimen was polished to a colloidal finish for SEM 

EDS and EBSD examination. SEM EDS mapping of Region 1 in Figure 5-61 shows a relatively 

uniform composition in the weld away from the fusion line. However, as shown in Figure 5-62, 

Region 2 with much more compositional variation followed the same contrast trends as in the 

SE image. The results of SEM EDS area scans are presented in Table 5-5. Areas S2, S4, and 

S6 all have ≤23 wt% Cr. These compositional streaks are spread throughout the weld pass all 

the way up to the crack growth surface. Complimentary SEM EBSD orientation imaging of 

Region 2 shows that with one exception, the composition streaks did not line up with grain 

boundaries. The grain boundary where this one exception occurred is indicated by the large 

yellow arrow in Figures 5-62 and 5-63. This grain boundary is very linear in the cross section 

(aligned with the crack-growth direction) just as with the grain boundary where the IGSCC 

cracking occurred. It is our belief that such aligned boundaries in the dilution zone are required 

for significant IGSCC to occur. These measurements also provided important insights into 

characterizations and specimen machining from the ANL alloy 152/LAS weld slice for PNNL 

CGR testing that is reported in the next section.

SE

~23Cr ~28Fe

~40Ni ~0.8Nb
5-47

Figure 5-60 SEM-BSE of a Cross-Section Through Crack-Growth Surface for the Alloy 

152/LAS Dilution Zone Specimen N152-LAS-11 Revealing Etched 

Microstructure of the Dilution Zone. Lighter Regions in the Alloy 152 

Dilution Zone Indicate Fe-Rich, Cr-Depleted Areas

Figure 5-61 SEM-SE and Elemental Maps of EDS Region 1 in Figure 5-60. Dashed Lines 

Show the Extent of the Cross-Section. Elemental Indications Beyond the 

Dotted Lines Are Due to X-Ray Signals Detected from the Crack Growth 

Face Rather than the Cross Section

LAS

152 DZ

Cr

Fe Ni

SE

crack growth direction
5-48

Figure 5-62 SEM EDS Composition Maps in the N152-LAS-11 Cross-Section in 

Figure 5-60

Table 5-5 SEM EDS Area Scan Composition (wt%) Measurements from Figure 5-62

Area Cr Mn Fe Ni

S0 0 0.6 98.7 0.2

S1 5.28 2.35 84.07 8.3

S2 21.53 2.72 32.3 41.01

S3 25.26 3.74 27.52 42.77

S4 22.78 4.38 34.17 38.67

S5 29.64 3.93 16.04 50.39

S6 21.9 3.04 35.42 39.64

S7 23.69 3.72 30.85 41.74

aligned GB
5-49

Figure 5-63 SEM-SE and SEM-EBSD IPF-Z Map Revealing Grain Structure in the Alloy 

152 Dilution Zone and the Presence of Grain Boundaries Aligned with the 

Crack Growth Direction in the ANL N152-LAS-11 Specimen Cross-Section 

(see Figure 5-62)

5.3.3 ANL 152v2 DM Weld: Specimen CT117 - 152/LAS Interface

The two crack-growth tests on the alloy 152 - LAS dilution specimens (CT117 and CT119) 

turned out to be extremely complex and each ran for >10,000 hours. The CT117 specimen will 

be described first, since the dilution zone location was selected to match that for the 

N152-LAS-11 specimen from ANL described in the previous section. The ANL-tested specimen 

exhibited a high DCPD-measured CGR (~10-7 mm/s) at constant load during the test as 

documented in Figure 5-50 and extensive IG cracking on the crack-growth surface shown in 

Figures 5-54 and 5-58. 

Crack-growth test results will be discussed in two parts separated by a shut down so that the 

side grooves could be examined and the crack extension estimated. An overview of the first 

part of the test is summarized in Figure 5-64 and Table 5-6 documenting three evaluations of 

constant K response and two evaluations during a cycle + 24 h hold loading. Cyclic loading at 

0.1, 0.01 and 0.001 Hz (with R=0.5) was applied over the initial ~1000 hours creating a crack 

extension of ~1.1 mm before transitioning to a 980s/20 s cycle with and without a 2.5 h hold to 

investigate whether the propagation response suggested SCC growth. Best SCC CGR results 

were measured during the first constant K evaluation at ~1345 hours as documented in Figure 

5-65. Altering crack growth response was observed over this exposure with SCC CGRs of 

~1x10-8 mm/s over the first 450 hours before slowing down to ~4x10-9 mm/s over the last 100 

hours. Subsequent cycle + hold loading response appeared to be promising and produced 

CGRs of >1x10-8 mm/s (Figure 5-66) during a 24h hold, however propagation rates at constant 

K were quite low as shown in Figure 5-67. In this case, an immediate jump in crack length was 

observed when switching back to cycle + hold suggesting that ligaments or crack contacts were 

removed and the actual crack advance was slightly greater. However, the adjusted SCC CGR 

remained low at 3.3x10-9 mm/s.

aligned GB
5-50

Figure 5-64 Overview Crack Growth Plot of the First Part for Test on the ANL Alloy 

152 - LAS Dilution Zone Specimen (CT117)

Several more attempts were made to assess SCC behavior in steps 27-32 as documented in 

Table 5-6. Response during 980s/20s cycle + hold loading was promising with both the 2.5h 

(steps 28 and 31) and 24h hold (steps 29 and 32) CGRs similar to previous behavior, but 

propagation at constant K was limited. The inability to reproduce the higher SCC CGR at 

constant K in step 7 (Figure 5-65) during the following 5 constant K evaluations prompted a 

closer examination of cycle + hold response. Indications of ligament formation (steps in crack 

length during cycle + hold loading) became more pronounced as the test progressed leading to 

a need to better determine the optimum loading condition to break ligaments. The goal is to 

break the ligaments while not disturbing SCC engagement and not having the load cycle add 

significantly to the CGR. This has to be balanced by applying the load cycle frequently enough 

to keep ligaments from building up.
5-51

Table 5-6 Data Summary for the First Part of the Test on the ANL Alloy 152 - LAS 

Dilution Zone Specimen CT117

Test 

Phase

Start 

(h)

Time

(h) R

Freq. 

(Hz)

Hold 

(h)

Diss.

H2 (cc

/ kg)

Temp 

(°C)

Kmax 

(MPa√m)

CGR 

(mm/s)

Crack 

Exten. 

(mm)

0 0 505 --- const K --- 25 360 30 --- ---

1 505 5 0.5 0.1 0 25 360 30 7.5E-06 0.180

2 510 57 0.5 0.01 0 25 360 30 1.3E-06 0.236

3 567 267 0.5 980s/20s 0 25 360 30 2.1E-07 0.220

4 834 74 0.5 0.01 0 25 360 30 1.2E-06 0.255

5 908 141 0.5 980s/20s 0 25 360 30 2.4E-07 0.101

6 1049 286 0.5 980s/20s 2.5 25 360 30 4.6E-08 0.056

7 1335 555 --- const K --- 25 360 30 9.3E-09 0.019

8 1890 212 0.5 980s/20s 2.5 25 360 30 6.5E-08 0.050

9 2102 392 --- const K --- 25 360 30 4.4E-09 0.005

10 2494 601 0.5 980s/20s 2.5 25 360 30 3.5E-08 0.097

11 3095 261 --- const K --- 25 360 30 2.3E-09 0.003

12 3356 101 0.5 980s/20s 0 25 360 30 3.0E-07 0.120

13 3457 110 0.5 980s/20s 2.5 25 360 30 4.1E-08 0.017

14 3567 191 0.5 980s/20s 24 25 360 30 7.4E-09 0.005

15 3758 79 0.5 980s/20s 0 25 360 30 4.3E-07 0.070

16 3837 89 0.5 980s/20s 2.5 25 360 30 7.2E-08 0.036

17 3926 319 0.5 980s/20s 24 25 360 30 1.4E-08 0.017

18 4245 280 0.5 980s/20s 12 25 360 30 1.6E-08 0.018

19 4525 50 0.5 980s/20s 0 25 360 30 3.4E-07 0.062

20 4575 163 0.5 980s/20s 12 25 360 30 1.4E-08 0.019

21 4738 93 0.5 980s/20s 2.5 25 360 30 6.9E-08 0.032

22 4831 416 --- const K --- 25 360 30 3.3E-09 0.005

23 5247 95 0.5 980s/20s 2.5 25 360 30 4.7E-08 0.014

24 5342 90 0.5 980s/20s 0 25 360 30 6.1E-07 0.159

25 5432 215 0.5 980s/20s 2.5 25 360 30 6.6E-08 0.048

26 5647 768 0.5 980s/20s 24 25 360 30 8.9E-09 0.027

27 6415 150 --- const K --- 25 360 30 <1E-09 0.000

28 6565 191 0.5 980s/20s 2.5 25 360 30 6.7E-08 0.040

29 6756 416 0.5 980s/20s 24 25 360 30 1.5E-08 0.019

30 7172 521 --- const K/L --- 25 360 30 4.0E-09 0.007

31 7693 76 0.5 980s/20s 2.5 25 360 30 7.9E-08 0.022

32 7769 639 0.5 980s/20s 24 25 360 30 1.1E-08 0.026

8408 Stop for Exam 
5-52

Figure 5-65 First Evaluation of SCC Response at Constant K for Specimen CT117

Figure 5-66 Crack-Growth Response at Cycle + 24h Hold Loading for Specimen CT117

~3.3 mm from notch
5-53

Figure 5-67 Fourth Evaluation of SCC Response at Constant K for Specimen CT117

Figure 5-68 Crack-Growth Response at Cycle + 24h Hold Loading for Specimen CT117
5-54

An approach used at ANL and elsewhere to estimate SCC response from cycle + hold loading 

data has been to consider the cycle + hold response as a sum of the cyclic response and the 

hold time response. The mathematical representation is:

aaTṪ ttTT = aaCC

̇ ttCC + aaHḢ ttHH (5.1)

Where aaṪ , aaĊ and aaḢ are the CGRs for cycle + hold loading, continuous cyclic loading and for 

the hold time during cycle + hold loading respectively. ttT, ttC, and ttH are the time period for one 

cycle + hold load cycle, a continuous load cycle and the hold time, respectively. aaḢ is 

considered to be an estimate of the constant K SCC CGR response. aaṪ , aaĊ , ttT, ttC, and ttH are 

all readily determined from the available data. This method is very sensitive to the CGR 

measured during pure cyclic loading because this value is typically over an order of magnitude 

larger than the constant K SCC CGR response of a material. A variation in the measured pure 

cyclic loading CGR in the first decimal place can cause up to 10X variations in the estimated 

SCC CGR response (aaḢ ) and often times can lead to negative estimated SCC CGRs or 

unrealistically high SCC CGRs. The most reasonable estimates are obtained when the pure 

cyclic loading value is measured directly before the cycle + hold loading step. Another issue 

that affects this technique is that the SCC response at the start of a hold is typically elevated 

due to changes in the crack tip during the load cycle, e.g., oxide film rupture caused by the load 

cycle. Because of this, short hold times typically produce inflated constant K SCC CGR 

estimates. Thus, in order for this method to produce reasonable values, a balance needs to be 

established between having enough load cycles to sufficiently break ligaments while not unduly 

sampling non-representative propagation behavior during the early portion of the hold time. 

Related to this is the selection of the load cycle. The load cycle should be aggressive enough to 

break ligaments while not being so aggressive that it drives IG cracking back to TG cracking. 

For susceptible materials such as alloy 182, a rapid unload-reload cycle appears to accomplish 

this. Our judgment for SCC-resistant, high Cr welds is that a more gentle cycle is needed to 

prevent driving the crack TG and a 980s/20s load cycle with R = 0.5 has been selected.

With these limitations and goals in mind, the estimated constant K CGRs from the cycle + hold 

loadings are presented in Table 5-7. Five different 980s/20s continuous cycling measurements 

have been made over many months of testing with each value a little bit different. For the table, 

five columns have been created to show the estimated constant K rates using the two most 

recent 980s/20s CGRs for the estimated SCC CGR calculation. In most cases, calculated SCC 

rates are similar for the two different baseline 980s/20s values. Estimated SCC rates are listed 

for the most appropriate values based on the behavior of the specimen at that portion of the 

test. Reviewing the constant K observations reveals that the highest SCC growth was seen 

early in the test during step 7 at 9.3x10-9 mm/s. The next two constant K evaluations decreased 

to 4.4 and 2.3x10-9 mm/s, somewhat consistent with the decreasing SCC rates calculated from 

cycle + 2.5h hold CGRs in steps 8 and 10. As the test continued, cycle + hold and constant K 

values decreased further, but cycle+hold response in steps 16, 17, 18, 20 and 21 suggested 

some SCC growth may be occurring during the hold time. The final steps from 22 to 32 did not 

indicate any significant growth at constant K and any estimated SCC growth during cycle + hold 

was unclear. These results support the observation of lower SCC response over the last 

section of the test and the decision was made to stop the test and examine the specimen side 

grooves at 8408 hours.
5-55

Table 5-7 Estimated Constant K SCC CGR for CT117 from Cycle+Hold Loading Data 

Using a 980s/20s Load Cycle

Test 

Step 

Hold Time 

(h) 

CGR for 

Test Step 

(mm/s)

Est. SCC 

CGR Using 

Step 5

(mm/s)

Est. SCC 

CGR Using 

Step 12

(mm/s)

Est. SCC

CGR Using 

Step 15

(mm/s)

Est. SCC 

CGR Using 

Step 19

(mm/s)

Est. SCC 

CGR Using 

Step 24

(mm/s)

5 0 2.4x10-7

6 2.5 4.6x10-8 3.3x10-8

7 Const K 9.3x10-9

8 2.5 6.5x10-8 5.2x10-8 4.1x10-8

9 Const K 4.4x10-9

10 2.5 3.8x10-8 1.7x10-8 1.2x10-8

11 Const K 2.3x10-9

12 0 3.0x10-7

13 2.5 4.1x10-8 1.2x10-8 -2.9x10-9

14 24 7.4x10-9 4.0x10-9 2.5x10-9

15 0 4.3x10-7

16 2.5 7.2x10-8 4.7x10-8 3.2x10-8

17 24 1.4x10-8 9.7x10-9 8.1x10-9

18 12 1.6x10-8 9.1x10-9 6.0x10-9

19 0 3.4x10-7

20 12 1.4x10-8 4.5x10-9 6.6x10-9

21 2.5 6.9x10-8 2.9x10-8 3.8x10-8

22 Const K 3.3x10-9

23 2.5 4.7x10-8 1.4x10-8 -1.6x10-8

24 0 6.1x10-7

25 2.5 4.4x10-8 -1.9x10-8

26 24 1.3x10-8 6.1x10-9

27 Const K <1x10-9

28 2.5 6.6x10-8 5.6x10-9

29 24 8.9x10-9 3.1x10-9

30 Const K/L 4.0 x10-9

31 2.5 7.9x10-8 2.0x10-8

32 24 1.1x10-8 4.1x10-9

Optical and SEM examinations were conducted to determine both the crack length on the side 

surfaces and the morphology of cracking. SEM-BSE images in Figures 5-69 and 5-70 highlight 

the cracking on side A of the CT117 specimen. The lower magnification montage in Figure 5-69

shows a reasonable straight crack from the notch extending to and beyond the interface 

between weld passes #1 and #2. The extent of crack propagation into pass #2 is best seen in

Figure 5-70 where there is also evidence of deformation and fine secondary cracks at the 

surface near the crack tip. In order to indicate the dilution zone chemistry along the crack path, 

EDS elemental composition maps were taken at several magnifications starting with the overall 

leading crack region shown in Figure 5-71. The Fe and Cr maps illustrate more significant 

dilution in pass #2 than pass #1 with very little changes near the transition from pass #1 to pass 

#2 as best seen in Figure 5-72. Figure 5-73 highlights a local region of extremely high Fe and 

very low Cr, Ni and Mn that corresponds to a complex crack morphology immediately behind the 

leading crack tip. It appears that the crack is blocked at the high Fe pocket of material and 

complex secondary cracking is produced before the primary crack emerges beyond the Fe-rich 

phase. The composition in this region is characterized at higher resolution by the Fe map in 

Figure 5-74 with local concentrations for the major elements identified in Table 5-8. 
5-56

Figure 5-69 SEM-BSE Low Magnification Montage of the Crack in Side Groove A at mid 

Test

Figure 5-70 SEM-BSE Higher Magnification Image of Leading Crack Region in Side 

Groove A (area from dashed yellow box in Figure 5-69). Considerable 

Secondary Cracking Can Be Seen in Pass #2 as Highlighted by Dashed Red 

Box

Pass #1

Pass #2

Pass #1

Pass 

#2
5-57

Figure 5-71 SEM-BSE Montage from Figure 5-70 and Corresponding EDS Elemental 

Maps of the Leading Crack Region in Side Groove A

Figure 5-72 SEM-BSE Montage and Corresponding EDS Elemental Maps near the Weld 

Pass Boundary Behind the Leading Crack Region in Side Groove A
5-58

Figure 5-73 SEM-BSE Micrograph and Corresponding EDS Elemental Maps at a Region 

of Secondary Cracking Just Behind the Leading Crack Tip on Side A

Figure 5-74 SEM-EDS Fe-K Map of the Leading Crack and Crack-Tip Region from the 

Side Groove on Side A

1

2

3

5

4

6 7

10

8

9

11

12

13

14

15
5-59

Table 5-8 Composition of Regions Near Crack Front (wt%) in Figure 5-74

Region Fe Cr Ni

1 25.4 28.9 45.7

2 16.5 31.0 52.5

3 27.0 27.3 45.7

4 22.8 28.9 48.3

5 31.3 26.2 42.6

6 30.4 26.5 43.1

7 66.3 12.5 21.2

8 37.6 23.0 39.4

9 36.2 24.4 39.5

10 25.7 27.7 46.6

11 34.1 24.3 41.6

12 29.6 26.4 44.0

13 29.5 26.6 43.9

14 43.3 21.0 35.7

15 27.7 27.1 45.2

The SEM-EDS measurements in the side groove shown in Table 5-8 should be considered only 

estimates of the actual concentration due to surface oxide complications leading to higher Cr 

and Fe with lower Ni. More quantitative measurements of compositions were obtained on 

polished cross-section samples after the test was completed. However, the current results 

illustrate the strong Fe enrichment in pass #2 and confirm that the region of extensive 

secondary cracking surrounds a phase of primarily Fe.

Cracking observed in side groove B (Figure 5-75) was discovered to be quite different. Instead 

of extending well into pass #2, the crack ends ~0.7 mm before the transition into pass #2 near 

an interesting microstructural feature as better shown in Figure 5-76. The image contrast for 

this feature suggests that it may be a LAS “island” that was drawn into the weld metal. This 

conclusion is supported by the EDS maps in Figure 5-77 where an extensive plume of Fe 

enrichment is present corresponding to low Ni and Cr concentrations. A very similar 

microstructure and compositional variation can be seen at the pass #1 – pass #2 boundary. 

The Fe composition map is highlighted in Figure 5-78 along with locations where local elemental 

concentrations were determined. Table 5-9 lists these measurements and establishes the 

extremely high Fe concentration in the region associated with the microstructural feature in front 

of the crack tip. It appears likely that crack growth on this side of the specimen was restricted 

during the test due to the presence of the large plume of Fe-rich metal. This is somewhat 

consistent with complex secondary cracking around the smaller Fe-rich area observed in pass 

#2 on side A. 
5-60

Figure 5-75 SEM-BSE Low Magnification Montage of the CT117 Side Groove on Side B

Figure 5-76 SEM-BSE High Magnification Montage Showing the Microstructural Feature 

Immediately Ahead of Crack Tip in Side Groove B

Two important aspects were discovered by the side grove examinations of the ANL dilution 

zone specimen CT117. First, the crack length was considerable longer on side A at ~5 mm 

(well into pass #2) from the notch that on side B at <3 mm from the notch. As a result, the 

expectation is that we have a highly irregular crack front across the CT117 specimen thickness. 

The second indication is that regions of extremely high Fe dilution (possible trapped regions of 

LAS) in the weld may restrict crack growth. As a result, there may be complex microstructure 

and microchemistry characteristics influencing corrosion fatigue and SCC growth in the weld 

metal adjacent to the LAS interface. The decision was made to continue crack-growth testing 

on the CT117 specimen and eventually move the crack front completely into weld pass #2.

Pass #1

Pass #2

Pass #2

LAS

LAS

Pass #1
5-61

Figure 5-77 SEM-BSE Montage and Corresponding EDS Elemental Maps of the CT117 

Leading Crack Region on Side B
5-62

Figure 5-78 SEM-EDS Fe-K Map of the Leading Crack Region for CT117 Side B 

(Figure 5-77)

Table 5-9 Composition (wt%) near the Leading Crack Region on Side B (Figure 5-78) 

Region Fe Cr Ni

1 27.4 28.1 44.5

2 22.3 29.0 48.7

3 30.4 26.5 43.1

4 32.3 25.6 42.2

5 66.7 12.8 20.5

6 29.6 26.5 43.9

7 29.4 26.7 44.0

8 20.4 29.3 50.3

9 69.9 11.2 18.9

10 29.2 27.0 43.8

An overview of the second part of the test is summarized in Figure 5-79 and Table 5-10

documenting four evaluations of constant K response loading. Cyclic loading at a 980 s/20 s 

cycle with and without a 2.5 h or 24 h hold was again employed to indicate whether the 

propagation response suggested SCC growth. Steps 33-50 were applied to once again 

investigate crack-growth response at 30 MPa√m and confirm behavior observed in part 1 

testing. 

1

2

3

5 4 6 7

10

8

9
5-63

Figure 5-79 Overview Crack Growth Plot of Second Part for Test on the ANL Alloy 

152 - LAS Dilution Zone Specimen CT117

Three transitioning sequences to constant K were performed that included evaluations of 

response during cyclic + 24 h hold loading. Evidence for ligament and/or contact formation in 

the crack was observed as illustrated in Figures 5-80, 5-81 and 5-82. The first constant K 

examination (Figure 5-80) after the restart exhibited a small increase in crack length early 

followed by no growth after ~100 hours. After switching back to cyclic + 2.5 h hold loading, an 

immediate jump in crack length was seen suggesting additional growth at constant K with an 

adjusted CGR of 2.6x10-9 mm/s. Contact formation was also indicated during a subsequent 

cyclic + 24h hold loading where DCPD crack length drops during the hold time after each 

980s/20s cycle as shown in Figure 5-81. The final example highlighted is a constant K exposure 

in Figure 5-82 where the crack length decreases throughout. As a result of these issues, the 

decision was made to advance the crack front forward and increase the applied K level from 30 

to 38 MPa√m. This was done in steps 50 and 51 with an increase in the 980s/20s cyclic CGR 

from 3.6x10-7 to 1.1x10-6 mm/s. Different response was observed during the cycle + 24h hold 

loading as documented in Figure 5-83. Although small jumps can be seen at each cycle, the 

DCPD crack length did not decrease during the 24h hold period. This might suggest some SCC 

growth during the hold in comparison to the previous response. A final SCC evaluation was 

then performed as presented in Figure 5-84 revealing a low CGR of 1.5x10-9 mm/s over ~1100 

hours at constant K. 
5-64

Table 5-10 Data Summary for the Second Part of the Test on the ANL Alloy 152 - LAS 

Dilution Zone Specimen CT117

Test 

Step

Start 

(h)

Time

(h) R

Freq. 

(Hz)

Hold 

(h)

Diss. 

H2 (cc / 

kg)

Temp 

(°C)

Kmax 

(MPa√m)

CGR 

(mm/s)

Crack 

Exten. 

(mm)

33 8408 15 0.5 980s/20s 0 25 360 30 5.8E-07 0.058

34 8423 104 0.5 980s/20s 2.5 25 360 30 6.2E-08 0.043

35 8527 456 0.5 980s/20s 24 25 360 30 1.6E-08 0.021

36 8983 366 --- const K --- 25 360 30 2.6E-09 0.003

37 9349 212 0.5 980s/20s 2.5 25 360 30 5.8E-08 0.065

38 9561 40 0.5 980s/20s 0 25 360 30 5.6E-07 0.116

39 9601 125 0.5 980s/20s 2.5 25 360 30 9.4E-08 0.059

40 9726 545 0.5 980s/20s 24 25 360 30 1.2E-08 0.031

41 10271 106 --- const K --- 25 360 30 <5E-10 0.000

42 10377 182 0.5 980s/20s 2.5 25 360 30 7.4E-08 0.051

43 10559 41 0.5 980s/20s 0 25 360 30 6.7E-07 0.083

44 10600 128 0.5 980s/20s 2.5 25 360 30 9.0E-08 0.058

45 10728 433 --- const K --- 25 360 30 <5E-10 0.000

46 11161 96 0.5 980s/20s 2.5 25 360 30 9.2E-08 0.033

47 11257 203 0.5 980s/20s 24 25 360 30 1.5E-08 0.011

48 11460 108 0.5 980s/20s 0 25 360 30 4.9E-07 0.183

49 11568 169 0.5 980s/20s 2.5 25 360 30 9.7E-08 0.037

50 11737 72 0.5 980s/20s 0 25 360 30 3.6E-07 0.087

51 11809 66 0.5 980s/20s 0 25 360 30->38 1.1E-06 0.241

52 11875 28 0.5 980s/20s 2.5 25 360 38 1.7E-07 0.027

53 11903 27 0.5 980s/20s 0 25 360 38 1.1E-06 0.092

54 11930 94 0.5 980s/20s 2.5 25 360 38 1.5E-07 0.061

55 12024 169 0.5 980s/20s 24 25 360 38 1.7E-08 0.010

56 12193 1103 --- const K --- 25 360 38 1.5E-09 0.007

Total 13296 3.385

For comparison purposes, the SCC CGRs were again estimated from the cycle + hold data in 

Table 5-10 as was done for the part 1 data in Table 5-7. Several higher estimated SCC rates 

were calculated for the cycle + 2.5 h hold data in steps 32, 39, 42, 44, 46 and 56. In addition, 

the cycle + 24h data also suggested some SCC growth in steps 35, 40 and 45. Unfortunately, 

this possible SCC behavior was not confirmed by constant K evaluations in steps 36, 41, 45 and 

56. The overall conclusion remained that in-situ DCPD did not revealing any significant crack

growth without a periodic unload.
5-65

Figure 5-80 Evaluation of SCC Response After Specimen CT117 Restart and 

Transitioning

Figure 5-81 Crack-Growth Response at Cycle + 24 H Hold Loading Showing Distinct 

Jumps During Cycle and Decrease in Crack Length During Hold Time
5-66

Figure 5-82 Evaluation of SCC Response for Specimen CT117 Showing No Growth at 

Constant K

Figure 5-83 Crack-Growth Response at Cycle + 24 H Hold Loading at Higher K Level
5-67

Figure 5-84 Tenth and Final Evaluation of SCC Response at Higher K for Specimen 

CT117

The decision was made to end the test after this last constant K result showed no indication of 

enhanced SCC growth. A remaining question for this alloy 152 weld is whether any significant 

localized SCC propagation occurs at constant K. Since in-situ DCPD does not reveal an 

answer, more detailed post-test characterizations were required. Ending this test after 13,296 

hours made it one of the longest SCC crack-growth tests we have run at PNNL. Consistent with 

our normal approach to characterize the cracking morphology for our SCC crack-growth tests, 

the CT117 specimen was sectioned 1/3-2/3 and the 1/3 section was cross-sectioned for detailed 

examinations while the 2/3 section was fatigued open to document the cracking morphology. 

Before that was done, the side grooves were documented as shown in Figures 5-85 and 5-86. 

The biggest difference from the mid-test examination in Figures 5-69 and 5-75 can be seen in 

Figure 5-86 where cracking has clearly propagated into weld pass #2. A critical next step was 

to integrate the side groove images with the crack-growth surfaces documented in Figure 5-87. 

This integration is shown in Figure 5-88 exhibiting the side groove images with the cross-section 

at 1⁄4 thickness and the remaining 3⁄4 specimen crack growth surface. One aspect that is the 

most prominent in each image is the transition from weld pass #1 to pass #2 where cracking 

occurs along the alloy 152 – LAS fusion line. 
5-68

Table 5-11 Estimated Constant K SCC CGR from Cycle + Hold Loading Data Using a 

980s/20s Load Cycle for the Second Part of the Test on CT117

Test 

Step

Hold Time 

(h)

CGR for 

Test Step 

(mm/s)

Est. Constant K 

CGR Using Step 

33 or 38 (mm/s)

Est. Constant K 

CGR Using 

Step 43 (mm/s)

Est. Constant K 

CGR Using 

Step 48 (mm/s)

Est. Constant K 

CGR Using 

Step 53 (mm/s)

Restart K = 30 MPa√m

33 0 9.7x10-7

34 2.5 1.1x10-7 4.6x10-8

35 24 1.3x10-8 6.2x10-9

36 Const K 2.6x10-9

37 2.5 5.8x10-8 2.2-4.2x10-9

38 0 5.6x10-7

39 2.5 6.0x10-8 4.4x10-9

40 24 1.2x10-8 6.7x10-9

41 Const K <5x10-10

42 2.5 7.4x10-8 2.0x10-8 1.4x10-8

43 0 6.7x10-7

44 2.5 9.1x10-8 2.7x10-8

45 Const K <5x10-10

46 2.5 9.1x10-8 2.7x10-8 4.6x10-8

47 24 1.5x10-8 7.4x10-9 9.4x10-9

48 0 4.7x10-7

49 2.5 5.0x10-8 3.3x10-9

50 0 3.6x10-7

K = 38 MPa√m

53 0 1.1x10-6

56 2.5 1.4x10-7 3.3x10-8

55 24 1.6x10-8 3.5x10-9

56 Const K 1.5x10-9

SEM-SE imaging was performed to determine the cracking morphology produced in PWR 

primary water across the fracture surface. An overall montage is presented in Figure 5-89 that 

reveals TG cracking from precracking and initial transitioning in water (steps 1-6) until the crack 

front moved beyond the pass #1 to pass #2 boundary. Extensive IG cracking was discovered in 

weld pass #2 as documented by the dashed yellow lines in the upper montage. Just beyond the 

pass #1 to pass #2 boundary, the cracking is >80% IG for ~1 mm into pass #2 across most of 

the CT specimen width. The cracking becomes more complex with a mixture of TG and IG over 

the next several mm of growth to the final crack front produced in water. In particular, the 

middle of the specimen became predominately TG while two areas of predominately IG cracking 

can be seen closer to sides A and B that extended deeper. Examples of the IG morphology are 

shown at higher magnification in the lower two SE images. The bumpy appearance on the IG 

facets reflects the dendrite packets intersecting the grain boundary surface.

Although the cracking morphology has now been assessed, it remains difficult to directly relate 

the measured crack-growth behavior to locations across the fracture surface. The mid-test, 

side-groove exams (Figures 5-69 and 5-75) clearly revealed that near side A the crack front had 

propagated well into pass #2 while the crack front near side B was still well within pass #1. 

These mid-test crack locations are identified on Figure 5-85 and are consistent with the final 

side-groove exams where the crack length was ~1.1 mm longer on side A than side B.
5-69

Figure 5-85 Side Groove SEM-BSE Montages Showing the Overall Crack Path on Side A 

(top) and Side B (bottom)

Figure 5-86 Higher Magnification SEM/BSE Image from Side B Showing Crack Has 

Propagated into Weld Pass #2

5.24 mm

4.13 mm

Pass #2

Pass #1

Pass #2

Pass #1

LAS

LAS

LAS

Pass #2

Mid Test

Mid Test
5-70

Figure 5-87 Upper Image Is a SEM-BSE Montage Showing the Entire Crack Growth 

Surface and Lower Image Is a SEM-SE Montage Revealing the Cracking 

Morphology in the Dashed Red Box. Darker Contrast in the Crack-Growth 

Surface BSE Image Identifies Region Exposed to High-Temperature Water 

with Lighter Upper Area Opened by Fatigue in Air After the SCC Test

Air Precrack

~2.3 mm

Post Test Air Fatigue
5-71

Figure 5-88 SEM-BSE Images from Left to Right: (a) Side Groove A, (b) Side Surface 

Cross-Section, (c) Crack-Growth Surface Montage and (d) Right Side 

Groove B. The Dashed Line in the CGF Image Illustrates Approximate 

Location of the Boundary Between the Two Weld Passes. Darker Contrast 

in the Crack-Growth Surface Image Identifies Region Exposed to HighTemperature Water with Lighter Upper Area Opened by Fatigue in Air After 

the SCC Test

More detailed characterizations of the cross-section removed from side A are presented in 

Figures 5-90 and 5-91. The cracking morphology can be identified in Figure 5-90 with TG 

cracking through large elongated grains in pass #1 of the alloy 152 weld metal that are oriented 

perpendicular to crack path. As the crack enters pass #2, it follows the LAS – alloy 152 

interface for ~0.5 mm before finding grain boundaries better aligned for IG cracking. These 

aligned grain boundaries are created at the intersection of several large elongated grains with 

smaller equiaxed grains close to the fusion boundary. The IG crack path is maintained for 

>1 mm and cracking ends at a region where large elongated grains are again oriented 

perpendicular to crack path. Not only is the microstructure favorable for IG growth in pass #2, 

but the aligned grain boundaries also corresponded with an area of Fe-rich, Cr-depleted weld

metal. SEM-EDS composition maps are shown in Figure 5-91 and reveal the IG crack path 

closely follows the dilution region. Along the IG crack, it was estimated that Fe concentrations 

ranged from ~28-34 wt% and Cr levels ranged from ~21-25 wt%. Therefore, environmentassisted IG cracking occurred in this cross-section only where aligned grain boundaries and Cr 

depletion were both present.

(a) (b) (c)

(d)

Post Test Air Fatigue

Air Precrack
5-72

Figure 5-89 Upper SEM-SE Montage Maps the Entire Crack-Growth Surface Area and 

Identifies IG Regions That Are Surrounded by the Fine Dashed Yellow 

Lines. Two Typical IG Regions Are Highlighted by Orange and Light Blue 

Boxes in the Montage and Shown at Higher Magnification in the Lower 

Images

IG

IG

IG

IG

IG

TG TG TG

IG IG

TG

TG TG
5-73

Figure 5-90 Characterization of the Cross-Section Sample off Side A of the Specimen 

CT117 Showing the Overall Crack Produced in Water (top image) and the 

Final Crack Path After It Propagated into Weld Pass #2 (below)

Fusion Line 

Cracking

IG

IG

Pass #1 Pass #2

Pass #2
5-74

Figure 5-91 SEM-BSE Image and EDS Elemental Maps of the Cross-Section Sample off 

Side A of the Specimen CT117

5.3.4 ANL 152v2 DM Weld: Specimen CT119 – Alloy 152/LAS Interface

The second crack-growth test on an alloy 152 - LAS dilution specimen (CT119) was conducted 

in a similar fashion to CT117 with two parts separated by a shut down so that the side grooves 

could be examined. An overview of the first part of the test is summarized in Figure 5-92 with 

three evaluations of constant K response and two evaluations during cycle + 24 h hold loading. 

Details on the initial 31 steps are listed in Table 5-12. Cyclic loading at 0.1, 0.01 and 0.001 Hz 

(with R=0.5) was applied over the first ~1000 hours creating a crack extension of ~1.1 mm 

before transitioning to a 980s/20s cycle with and without a 2.5 h hold to indicate whether the 

propagation response suggested SCC growth. More aggressive cycling at 0.01 Hz was again 

applied in steps 10 and 12 when low CGRs were observed during cycle + hold loading. Best 

CGR results for the 2.5 h hold were seen at ~1900 hours in step 16 and constant K was 

evaluated for ~1200 hours as documented in Figure 5-93. Altered propagation response was 

observed over this exposure with CGRs reaching ~1x10-8 mm/s, then slowing to ~4x10-9 mm/s. 

The decision was made to assess ligament formation at 3340 hours by switching back to cycle 

+ hold and the DCPD-measured crack length jumped by ~35 μm during the first cycles and then

settled back to a normal cycle + hold CGR. This indicated unmeasured crack extension at

constant K and the actual SCC growth rate is estimated at 1.4x10-8 mm/s.

LAS

Pass #1 Pass #2
5-75

Figure 5-92 Overview Crack Growth Plot of First Part for Test on the ANL Alloy 152 - 

LAS Dilution Zone Specimen (CT119)

Figure 5-93 Second Evaluation of SCC Response at Constant K Showing Slowing 

Growth with Time over 1200 Hours. Evidence for Ligament Formation and 

Unmeasured Crack Extension by DCPD Indicating Higher SCC Propagation 

Rate
5-76

Table 5-12 Data Summary for the First Part of the Test on the ANL Alloy 152 - LAS 

Dilution Zone Specimen CT119

Test 

Step

Start 

(h)

Time

(h) R

Freq. 

(Hz)

Hold 

(h)

Diss. 

H2 (cc

/ kg)

Tem

p 

(°C)

Kmax 

(MPa√m

)

CGR 

(mm/s)

Crack 

Exten. 

(mm)

1 0 505 --- const K --- 25 360 20 --- ---

2 505 6 0.5 0.1 0 25 360 30 6.9E-06 0.130

3 511 41 0.5 0.01 0 25 360 30 1.3E-06 0.196

4 552 15 0.5 0.001 0 25 360 30 1.9E-07 0.012

5 567 268 0.5

980s/20

s 0 25 360 30 2.5E-07 0.211

6 835 136 0.5 0.01 0 25 360 30 7.1E-07 0.467

7 971 50 0.5 0.001 0 25 360 30 8.3E-08 0.017

8 1021 28 0.5

980s/20

s 0 25 360 30 7.4E-08 0.008

9 1049 215 0.5

980s/20

s 2.5 25 360 30 1.7E-08 0.019

10 1264 56 0.5 0.01 0 25 360 30 5.1E-07 0.105

11 1320 46 0.5

980s/20

s 0 25 360 30 1.6E-07 0.029

12 1366 22 0.5 0.01 0 25 360 30 1.4E-06 0.108

13 1388 137 0.5

980s/20

s 0 25 360 30 3.8E-07 0.149

14 1525 170 0.5

980s/20

s 2.5 25 360 30 5.2E-08 0.050

15 1695 195 --- const K --- 25 360 30 1.0E-08 0.006

16 1890 257 0.5

980s/20

s 2.5 25 360 30 1.1E-07 0.071

17 2147 1205 --- const K --- 25 360 30 1.4E-08 0.039

18 3352 90 0.5

980s/20

s 2.5 25 360 30 1.4E-07 0.057

19 3442 480 0.5

980s/20

s 24 25 360 30 2.0E-08 0.030

20 3922 319 0.5

980s/20

s 48 25 360 30 8.7E-09 0.010

21 4241 280 0.5

980s/20

s 12 25 360 30 3.1E-08 0.026

22 4521 49 0.5

980s/20

s 0 25 360 30.1 4.1E-07 0.065

23 4570 164 0.5

980s/20

s 12 25 360 30.1 1.5E-08 0.016

24 4734 93 0.5

980s/20

s 2.5 25 360 30.2 7.9E-08 0.052

25 4827 416 --- const K --- 25 360 30.2 ~6E-10 0.001

26 5243 95 0.5

980s/20

s 2.5 25 360 30.2 7.2E-08 0.031

27 5338 89 0.5

980s/20

s 0 25 360 30.4 4.6E-07 0.140

28 5427 215 0.5

980s/20

s 2.5 25 360 30.5 6.1E-08 0.065

29 5642 503 0.5

980s/20

s 24 25 360 30.5 1.1E-08 0.014

30 6145 182 0.5

980s/20

s 0 25 360 31.1 3.9E-07 0.259

31 6327 228 0.5

980s/20

s 2.5 25 360 31.1 5.3E-08 0.046

6555 Stop for Exam 
5-77

In an attempt to better confirm this SCC propagation behavior and the influence of ligament 

formation, several different hold times were evaluated. Once stable CGR was observed during 

the 2.5 h hold, a 24 h hold was applied as documented in Figure 5-94. The stepped DCPD 

response for crack length again suggests the breaking of ligaments and the overall CGR of 

2x10-8 mm/s supports the previously measured SCC rate at constant K. However, the

evaluation of an even longer hold time of 48 hours (Figure 5-95) resulted in a CGR lower than 

that extrapolated from the constant K response. Apparently a single cycle is not sufficient to 

completely remove the ligaments/contacts formed during the 48h hold. One additional periodic 

unload was tried at a 12 h hold time (Figure 5-97) and the CGR increased back to 3.2x10-8

mm/s. Another evaluation of constant K behavior was performed in step 25 as presented in 

Figure 5-97. DCPD indicated noisy response with little if any crack growth during the 416-hour 

exposure. The subsequent cycle + hold loading revealed no evidence for a jump in crack length 

that would suggest ligament formation. Final attempts were made to find an area of enhanced 

SCC by switching between 980s/20s cycling to move the crack front forward followed by 

cycle + hold evaluations. After several attempts showing lower CGRs, the decision was made 

to stop the tests and examine the crack morphology in the specimen side grooves.

Figure 5-94 Crack Growth Response During Cycle + 24 h Hold Loading
5-78

Figure 5-95 Crack Growth Response During Cycle + 48 h Hold Loading

Figure 5-96 Crack Growth Response During Cycle + 12 h Hold Loading
5-79

Figure 5-97 Crack Growth Response for the 3rd Constant K Evaluation Showing Little 

or No Growth

Optical and SEM exams revealed that the crack diverted downward toward the LAS peak at the 

transition from weld pass #1 to pass #2 in both side groove A and side groove B as illustrated in 

Figure 5-98. The crack extension in side groove A was slightly greater than in side groove B, 

but the crack front was clearly into weld pass #2 for both. As was noted during the pre-test side 

groove exams for CT119 (Figure 5-15), a region of strong Fe enrichment and Cr depletion was 

present in weld pass #2 including two second phase islands in the alloy 152 weld metal that 

appeared to be trapped LAS. These two LAS islands are identified in Figure 5-98 and the crack 

clearly interacted with them causing fine secondary cracks. A higher magnification image of the 

leading crack in side A is shown in Figure 5-99 and no cracking could be seen in the LAS 

islands themselves. The leading crack tip with TG and IG components is highlighted in Figure 

5-100. 

An overview of the second part of the test is summarized in Table 5-13 and Figure 5-101. 

Cyclic loading at a 980s/20s cycle with and without a 2.5 h or 24 h hold was again employed to 

indicate whether the propagation response suggested SCC growth. Steps 34-46 were applied 

to once again investigate crack-growth response at ~31 MPa√m and confirmed behavior 

observed at the end of part 1 testing with no indication of SCC enhancement. An example of 

this response is shown in Figure 5-102 for steps 37-40 where the measured CGRs for the 2.5 h 

hold evaluations remained below previous values. As a result, the decision was made to move 

the crack front forward into a new microstructure. Aggressive cycling at 0.1 and 0.01 Hz in 

steps 47 and 48 moved the crack forward by ~2 mm and increased the K level, however a low

CGR was seen during 980s/20s cycling in step 49. Transitioning was continued in steps 50-58 

with CGRs remaining much lower than previous attempts and the test was then shut down to 

evaluate the cracking morphology.
5-80

Figure 5-98 SEM-BSE Images of Side Groove A (top) and Side Groove B (bottom) for 

Specimen CT119 After 6555 Hours of Testing

Crack Tip

Crack Tip LAS

LAS

LAS 

islands
5-81

Figure 5-99 Higher Magnification SEM-BSE Image of the Leading Crack Region in Side 

Groove A with Crack Tips Highlighted in Small Circles

Figure 5-100 Fine Cracks and Leading Crack Tips for the Side Groove B. Cracks Are 

Shown in Yellow with Apparent Grain Boundaries in Dashed Green Based 

on the Nb Composition Map
5-82

Table 5-13 Data Summary for the Second Part of the Test on the ANL Alloy 152 - LAS 

Dilution Zone Specimen CT119

Test 

Step

Start 

(h)

Time

(h) R

Freq. 

(Hz)

Hold 

(h)

Diss. 

H2 (cc / 

kg)

Temp 

(°C)

Kmax 

(MPa√m)

CGR 

(mm/s)

Crack 

Exten. 

(mm)

33 6555 154 --- const K --- 25 360 31.1 1.7E-09 0.001

34 6709 85 0.5 980s/20s 2.5 25 360 31.1 8.3E-08 0.022

35 6794 95 0.5 980s/20s 0 25 360 31.1 4.2E-07 0.151

36 6889 185 0.5 980s/20s 2.5 25 360 31.1 4.4E-08 0.033

37 7074 128 0.5 980s/20s 0 25 360 31.1 3.2E-07 0.153

38 7202 87 0.5 980s/20s 2.5 25 360 31.1 5.6E-08 0.021

39 7289 138 0.5 980s/20s 0 25 360 31.2 2.4E-07 0.145

40 7427 419 0.5 980s/20s 2.5 25 360 31.2 3.3E-08 0.055

41 7846 66 0.5 980s/20s 0 25 360 31.3 2.3E-07 0.051

42 7912 72 0.5 980s/20s 0 1 360 31.3 2.8E-07 0.069

43 7984 124 0.5 980s/20s 0 25 360 31.4 3.0E-07 0.117

45 8108 164 0.5 980s/20s 2.5 25 360 31.4 3.1E-08 0.025

46 8272 101 0.5 980s/20s 24 25 360 31.4 1.7E-09 0.001

47 8373 125 0.5 0.1 0 25 360 33.4 4.7E-06 1.889

48 8498 50 0.5 0.01 0 25 360 33.4 5.6E-07 0.092

49 8548 44 0.5 980s/20s 0 25 360 33.4 2.2E-08 0.006

50 8592 25 0.5 0.1 0 25 360 33.5 4.2E-06 0.265

51 8617 95 0.5 0.01 0 25 360 33.5 3.5E-07 0.122

52 8712 143 0.5 980s/20s 0 25 360 33.5 4.4E-08 0.021

53 8855 20 0.5 0.1 0 25 360 33.7 3.7E-06 0.226

54 8875 120 0.5 0.01 0 25 360 33.8 3.5E-07 0.177

55 8995 228 0.5 980s/20s 0 25 360 33.8 1.3E-08 0.024

56 9223 12 0.5 0.1 0 25 360 33.8 3.8E-06 0.152

57 9235 63 0.5 0.01 0 25 360 33.8 4.2E-07 0.106

58 9309 315 0.5 980s/20s 0 25 360 33.8 2.5E-08 0.011

Total 9613 6.424

Post-test side groove images are in Figure 5-103 revealing what appears to be completely TG 

cracking from the mid-test crack location through all of weld pass #2 with cracks ending in the 

LAS. The final crack tips propagating into the LAS are highlighted Figure 5-104. One possible 

reason for the lack of IG cracking during the second phase of this test was the lack of both a 

favorable microstructure (aligned grain boundaries) and significant dilution. Composition maps 

for weld pass #2 associated with the crack path are presented in Figures 5-105 and 5-106

revealing no significant dilution zone. Consistent with the observations of some SCC 

susceptibility early in the test, the crack-growth surface exhibited several areas of IG cracking 

corresponding to the first part of the test. The overall crack-growth surface is documented in 

Figure 5-107 and considerable IG regions can be seen closer to side A of the specimen over a 

depth of ~1.5 mm. This region of IG cracking corresponds to the area in weld pass #2 just 

beyond the pass #1 to pass #2 transition where aligned grain boundaries were observed along 

with significant Fe enrichment and Cr depletion. An example of one of these IG regions is 

shown at higher magnification in Figure 5-108. Although more limited environment-assisted IG 

cracking was found for the CT119 specimen than the CT117 specimen, the microstructural and 

microchemical features were similar for areas of IG cracking.
5-83

Figure 5-101 Overview Crack Growth Plot of Second Part for CT119 Specimen Test

Figure 5-102 Cyclic and Cycle + 2.5 h Hold Response After Restarting Specimen CT119
5-84

Figure 5-103 Post-Test Side Groove Images for Specimen CT119

Figure 5-104 Final Crack Tips in the LAS for CT119 in Side Grooves A (top) and B 

(bottom)
5-85

Figure 5-105 Crack Path in Side Groove A Through Weld Pass #2 During Second Part of 

the Test on CT119 Along with EDS Composition Maps Showing No 

Significant Dilution in This Region

Figure 5-106 Crack Path in Side Groove B Through Weld Pass #2 During Second Part of 

the Test on CT119 Along with EDS Composition Maps Showing No 

Significant Dilution in This Region
5-86

Figure 5-107 SEM-SE Montage Maps the Entire Crack-Growth Surface Area and 

Identifies IG Regions Outlined in Yellow
5-87

Figure 5-108 A Typical IG Region from Figure 5-107 (blue box), Bumpy Appearance 

Results from the Termination of Dendrite Packets at the Surface

5.3.5 EPRI Temper Bead DM Repair Weld: Specimen CT136 – Alloy 52M/LAS Interface

The final weld examined within this chapter is the EPRI temper-bead, alloy 690 – alloy 52M – 

LAS DM repair weld. Characterization and testing on the repair weld will be described in a 

future report, however crack-growth results for tests on the temper-bead alloy 52M – LAS 

interface region will be summarized in this section. Pre-test characterizations on the interface 

and dilution zone regions were presented in section 5.1 and Figures 5-18-5-22. The air precrack was extended by aggressive cycling in water (steps 1-4) and transitioning attempts started 

using 980s/20s cycling with and without a 2.5 h hold time in steps 5-10. This crack length 

should correspond to an Fe-rich and Cr-depleted region where aligned grain boundary were 

identified in side groove A. A summary of the test can be observed in Table 5-14 and Figure 

5-109. The first attempt to assess SCC propagation was made at a test time of 1514 hours as 

shown in Figure 5-110. A reasonably steady, but low growth rate of 3.4x10-9 mm/s was 

measured over an exposure time of ~1000 hours. Additional transitioning was attempted 

(including the use of longer hold times) and the crack front was moved forward approaching and 

possibly reaching the LOF cracks identified in both side groves at a distance of ~3.5 to 4.3 mm 

from the notch. The most promising DCPD response was found for the periodic unload with a 

24 h hold time (step 25) presented in Figure 5-111 where a CGR of 1.5x10-8 mm/s was 

observed, two times larger than the previous attempt in step 17 suggesting SCC growth during 

the hold time. However, the subsequent constant K evaluation (step 27) did not reveal a higher 

CGR as illustrated by the plot in Figure 5-112. 

This result and the uncertainty whether the crack front had reached the LOF cracks prompted 

the decision to shut down the test at 5923 hours and examine the CT136 specimen side 

grooves. Optical images are shown in Figure 5-113. The crack front on these surfaces has 

clearly reached the end of LAS plateau and propagated through the preexisting LOF defects. 

Based on the side groove examinations, DCPD appears to have underestimated the crack 

length for CT136 by nearly 1 mm and the applied K level by ~10%. Based on this crack front 

location, it appears that the second and third constant K observations and the second 24 h hold 

may have all taken place as the crack grew through the LOF region.
5-88

Table 5-14 Data Summary for the Test on the EPRI DM Repair Weld Specimen CT136

Test 

Step

Start 

(h)

Duration

(h) R

Freq 

(Hz)

Hold 

(h)

Water 

Chem. 

(cc H2 

/ kg)

Temp 

(°C)

Kmax 

(MPa√m)

CGR 

(mm/s)

Approx. 

Crack 

Extension 

(mm)

1 0 16 0.5 0.1 0 25 360 30 3.4E-06 0.182

2 16 84 0.5 0.01 0 25 360 30 7.9E-07 0.205

3 100 262 0.5 0.001 0 25 360 30 1.4E-07 0.119

4 362 63 0.5 0.01 0 25 360 30 8.2E-07 0.167

5 425 271 0.5 980s/20s 0 25 360 30 1.5E-07 0.221

6 696 287 0.5 980s/20s 2.5 25 360 30 2.5E-08 0.024

7 983 98 0.5 980s/20s 0 25 360 30 1.2E-07 0.049

8 1081 235 0.5 980s/20s 2.5 25 360 30 1.5E-08 0.013

9 1316 64 0.5 980s/20s 0 25 360 30 1.1E-07 0.021

10 1380 134 0.5 980s/20s 2.5 25 360 30 2.2E-08 0.008

11 1514 1014 --- const K --- 25 360 30 3.4E-09 0.011

12 2528 262 0.5 980s/20s 2.5 25 360 30 1.6E-08 0.009

13 2790 210 0.5 980s/20s 0 25 360 30 1.1E-07 0.068

14 3000 96 0.5 280/20s 0 25 360 30 3.0E-07 0.118

15 3096 168 0.5 980s/20s 0 25 360 30 1.7E-07 0.096

16 3264 263 0.5 980s/20s 2.5 25 360 30 2.5E-08 0.026

17 3527 384 0.5 980s/20s 24 25 360 30 8.4E-09 0.007

18 3911 107 0.5 280/20s 0 25 360 30 4.9E-07 0.209

19 4018 36 0.5 980s/20s 0 25 360 30 4.0E-07 0.053

20 4054 96 0.5 980s/20s 2.5 25 360 30 5.7E-08 0.026

21 4150 239 --- const K --- 25 360 30 2.4E-09 0.003

22 4389 96 0.5 980s/20s 2.5 25 360 30 4.7E-07 0.017

23 4485 56 0.5 980s/20s 0 25 360 30 1.6E-08 0.127

24 4541 59 0.5 980s/20s 2.5 25 360 30 1.2E-07 0.032

25 4600 421 0.5 980s/20s 24 25 360 30 1.5E-08 0.026

26 5021 259 0.5 980s/20s 2.5 25 360 30 9.4E-08 0.061

27 5280 547 --- const K --- 25 360 30 3.5E-09 0.039

28 5827 96 0.5 980s/20s 2.5 25 360 30 1.0E-07 0.036

Side Groove Exams

29 5923 26 0.5 980s/20s 2.5 25 360 30 2.3E-07 0.017

30a 5949 541 --- const K --- 25 360 34 4.2E-09 0.012

30b 6390 400 --- const K --- 25 360 34 <5E-10 0.001

30 6790 175 0.5 980s/20s 2.5 25 360 34 1.5E-07 0.093

31 6965 806 --- const K --- 25 360 34 3.2E-09 0.011

Total 7771 2.105
5-89

Figure 5-109 Overview Crack Growth Plot for Test on the EPRI Alloy 52M - LAS Interface 

and Dilution Zone Specimen (CT136)

Figure 5-110 First Constant K Evaluation of SCC Response in the CT136 Specimen
5-90

Figure 5-111 Cycle + 24 h Hold CGR Response in the CT136 Specimen

Figure 5-112 Third Constant K Evaluation of SCC Response in the CT136 Specimen
5-91

Figure 5-113 Optical Images Showing Cracking in CT136 Side Grooves After a Test Time

of 5900 Hours. Crack Front Has Reached the LOF Defects (black arrows) at 

the LAS Interface on Both Sides and Small Cracks Appear to Extend to the 

End of the LAS Plateau

The CT136 specimen were then reloaded and testing continued under cycle + 2.5 h hold 

loading in step 29 exhibiting a somewhat higher CGR of 2.3x10-7 mm/s. Since the crack front 

was near the LOF defects, SCC response was again assessed. The early CGR at constant K 

was similar to previous measurements at 4.2x10-9 mm/s, however the test system experienced 

water chemistry and flow rate issues that directly impacted DCPD response as shown in Figure 

5-114. After a sharp spike in outlet conductivity and DCPD signal at ~6325 hours, corrective 

actions were taken to restore proper flow rate and adjust water chemistry. After ~100 hours, 

proper conditions were restored but the DCPD-indicated CGR was quite different. Essentially 

no SCC growth was measured during the last 400 hours at constant K. Because of this problem 

and the resulting questionable DCPD behavior, cycle + hold loading was again applied in step 

30 before one final attempt to asses SCC. The final constant K evaluation is presented in 

Figure 5-115 and revealed a low CGR under stable water chemistry conditions similar to prior 

observations on this specimen. After discussions with the NRC, the decision was made to end 

this test after 7771 hours and characterize the crack growth morphology.

This CT specimen was cut into 1/3 and 2/3 sections with the cross-section metallography exams 

performed on the internal surface of the 1/3 piece removed from side A. An SEM-EBSD pattern 

quality image is presented in Figure 5-116(a) that illustrates the crack path through the alloy 

52M grain microstructure. The cracking morphology in this cross-section location appears to be 

predominately TG with only one region where the cracking may have followed aligned grain 

boundaries. It is important to note that several fine grain areas are present with better aligned 

grain boundaries (yellow arrows in Figure 5-116a) in pass #1 consistent with what we observed 

for side groove A (Figure 5-20). The composition variation measured on the cross-section also 

matched what was seen for side groove A with a protrusion of Fe-enrichment and 

Cr/Ni-depletion into the alloy 52M weld metal located where finer grain were present creating 

the grain boundaries aligned with the CT specimen crack path from the notch. However, it is 

clear that the crack path did not intersect or preferentially follow the aligned grain boundaries in 

this cross-section and no significant IG cracking was present.
5-92

Figure 5-114 Fourth Constant K Evaluation of SCC Response in the CT136 Specimen 

Immediately After Restart. Problems with Water Flow and Chemistry 

Impacted DCPD Measurements and Corrective Action Was Taken at ~6325 

Hours

Figure 5-115 Fifth and Final Constant K Evaluation of SCC Response in the CT136 

Specimen
5-93

Figure 5-116 SEM-EBSD Pattern Quality Image Showing Crack Path Through the Weld 

Metal Microstructure (a) and the Corresponding SEM-BSE Image and EDS 

Compositional Maps (b) from This Region

(a) Elongated Grains in Alloy 52M

(b)

TG TG IG? TG

Pass #1

Pass #2
5-94

Additional EBSD examinations were performed to better characterize the alloy 52M 

microstructure, crack path and local strain misorientations. An IPF map of the crack path 

matching the pattern quality image in Figure 5-116(a) is shown in Figure 5-117 to better 

highlight the grain orientations in the alloy 52M weld metal. Large, elongated grains in the weld 

metal can be easily resolved along with local regions of smaller grains (and aligned grain 

boundaries) closer to the LAS interface. The one area identified where the crack path may have 

followed an aligned grain boundary is shown at higher magnification in Figure 5-118 along with 

an EBSD local misorientation map. Higher misorientation (strain) is present along the crack path 

and suggests that the crack propagated near the aligned grain boundaries, but remained TG. It 

also revealed that crack branching likely occurred in this local region.

Figure 5-117 EBSD IPF Image of the Alloy 52M Microstructure Along the Crack Path in 

CT136

Figure 5-118 EBSD IPF Image and Local Misorientation Map of a Region Along the Crack

Path. A Higher Magnification IPF Image of the Plateau Region Is Presented 

in Figure 5-119 Along with an EBSD Local Misorientation Map
5-95

Figure 5-119 EBSD IPF Image and Local Misorientation Map at the LOF Region in CT136
5-96

High-resolution SEM characterizations were also performed along the crack path and at the 

leading crack tip for the cross-section sample. Results for three regions are highlighted and are 

identified in Figure 5-120. The crack tip region 1 is presented in Figure 5-121 showing a TG 

crack emanating from the second preexisting LOF defect that intersects with and propagates a 

short distance along a grain boundary. The boundary in this case is nearly perpendicular to the 

CT specimen crack path, so a reduced K would be expected for continued IG growth. Region 2 

captures the site where the propagating TG crack intersects in Figure 5-122 with the first 

preexisting LOF defect and an oddly shaped open feature is formed. The crack path appeared 

to be headed for the alloy 52M – LAS interface in region 3, but instead shifted upward to LOF 

defect in region 2.

Figure 5-120 SEM-BSE Image of the Crack Path in CT136 with Regions Identified for 

Exams

Figure 5-121 SEM-BSE Images Showing the Crack Region 1 from Figure 5-120 at 

Increasing Magnifications Revealing Short Propagation Along a Grain 

Boundary off the Main TG Crack Tip

1

2

3

LAS
5-97

Figure 5-122 SEM-BSE Images Showing the Crack Region 2 from Figure 5-120 Where the 

Crack Intersected the First Preexisting LOF Defect at the LAS Interface

The final area highlighted is region 3 near the alloy 52 – LAS interface documented in Figure 

5-123. Tight cracks can be seen near the interface including what could be growth along a 

Type 2 boundary and two cracks that reach the LAS. No crack propagation was observed into 

the LAS at any location in this cross section, which is interesting since temper-bead welding 

produced a layer of high hardness in the LAS (presented in Figure 5-18). The fact that cracks 

stopped at the interface and formed pit-like corrosion suggests that the LAS is effectively 

tempered and resistant to environment-assisted cracking. Figure 5-123 also illustrates the 

extremely fine-grained microstructure in the LAS except within ~10 μm of the alloy 52 – LAS 

interface where some grain growth has occurred.

Figure 5-123 SEM-BSE Images Showing the Crack Region 3 from Figure 5-120 at Higher 

Magnifications Revealing Cracks in the Alloy 52M near the LAS Interface. 

Two Cracks Are Seen to Reach the Interface and Form Pit-like Corrosion 

into the LAS

In order to establish the overall crack propagation morphology, the remaining 2/3 specimen was 

fatigued open in air and the crack-growth surface examined by optical and SEM techniques. An 

SEM-SE montage is shown in Figure 5-124 documented the cracking morphology across the 

CT136 specimen. The two preexisting LOF fusion defects present at LAS plateau interface 

have a flat smooth appearance and extend across the entire fracture surface with a short 

LAS LAS

LAS LAS
5-98

section of complex cracking between the two LOF defects. The crack growth during the test in 

PWR primary water ended near the edge of the second LOF defect as indicated by the 

horizontal arrows. Morphology of cracking through weld pass #1 (below the LOF defects) was 

predominately TG with the exception being two islands of predominately IG. These two islands 

are outlined in yellow and the one on the right is shown at higher magnification in Figure 5-125. 

Figure 5-124 SEM-SE Image Montage Revealing the Crack Growth Surface Produced in 

Water for Specimen CT136. Two Islands of Primarily IG Cracking Were 

Observed in Pass #1

Air Fatigue

Side B Side A 

cross 

section

LOF

LOF

Air Fatigue
5-99

Figure 5-125 SEM-SE Image Highlighting One of the Two IG Islands Present on the 

CT136 Crack Growth Surface

5.4 Summary of Testing at Alloy 152/152M/52M DM Weld Interfaces

PWSCC testing was performed on five DM welds in the region of the fusion line between alloy 

152, 152M or 52M weld metal and either 304SS, CS or LAS. Low constant K SCC CGRs of 

<5x10-9 mm/s were observed during testing on the fusion line of the alloy 152/304SS mockup. 

The crack growth path in the specimens suggested a preference for crack propagation in the 

304SS HAZ. In the as-welded condition without a prototypic PWHT, laboratory-fabricated alloy 

152M/52M-CS welds exhibited high constant K SCC CGRs ranging from ~7x10-8 mm/s at 

40 MPa√m to 2x10-6 mm/s at 53 MPa√m when the crack path was either on the fusion line or in 

the CS HAZ. Application of a prototypic PWHT to these materials eliminated the high 

susceptibility suggesting that the high CGRs were due to substantial hardening in the CS HAZ 

as a result of a martensitic transformation during the welding process. Finally, PWSCC testing 

was also performed in the dilution zone region of these alloy 152M/52M-CS DM weldments. 

When dilution down to ~20 wt% Cr was encountered in weld metal near the fusion line of the 

alloy 152M-CS specimen, CGRs did not increase, and there was no tendency for the crack to 

prefer an IG path. 

While these tests suggest good PWSCC resistance in materials that are fabricated following 

acceptable procedures, additional testing was performed on specimens oriented for propagation 

in the alloy 152 or 52M weld near the fusion line with LAS. The first tests were conducted on a 

DM weld produced by ANL using different alloy 152 weld wires for the top half and bottom 

sections of the weld as described in Figure 5-12. Significant constant K rates (up to ~1.4x10-8 

mm/s) were measured during certain parts of the tests on the ANL DM weld specimens. Posttest analyses indicated that these isolated results showing moderate SCC growth rates 

corresponded to regions of IG cracking on the crack-growth surface. Microstructural 

examinations of cross-section samples revealed that the regions of IG cracking and higher 

growth rates were consistent with the presence of aligned grain boundaries in the alloy 152 

dilution zone adjacent to LAS interface. The combination of aligned grain boundaries and some 

degree of Cr depletion is believed to be important to promote IGSCC. In all cases, the lengths 

of aligned grain boundaries were limited within individual passes and reasonably match the local 

regions of IGSCC on the crack growth surface. A final test was performed on an alloy 52M – 

LAS DM temper bead weld from EPRI. Microstructural and microchemical characterizations in 

the alloy 52M first layer identified regions of Fe enrichment and Cr depletion along with a few 
5-100

aligned grain boundaries. In addition, LOF defects were discovered at the alloy 52M/LAS 

interface between many weld passes. Finally, hardness mapping revealed a continuous band 

of higher hardness in the LAS HAZ suggesting that the temper bead welding may not have been 

completely effective. Crack growth testing indicated very low SCC susceptibility along the alloy 

52M dilution zone and the alloy 52M/LAS interface. This was consistent with the observation of 

only a few, small isolated regions of IG cracking on the post-test crack-growth surface. There 

was no tendency for the crack path to enter the LAS to follow the higher hardness band as was 

seen previous for the non-tempered CS HAZ.

Although the current results on dissimilar metal welds are limited, we believe they do show that 

the alloy 152/52M weld interfaces with CS or LAS consistently creates local regions of 

significant Fe enrichment and Cr depletion in the alloy 152/52M. In our opinion, this dilution 

zone does increase susceptibility to IGSCC in PWR primary water but crack growth is limited by 

the availability of properly aligned grain boundaries. The combination of both characteristics is 

required for significant IGSCC. Additional research is needed and planned to produce and 

evaluate dissimilar metal welds to better determine whether dilution zones represent a concern 

for SCC in reactor service. 
6-1 

6 SUMMARY AND FUTURE RESEARCH NEEDS

Stress corrosion crack growth of alloy 690 and its weld metals has been a focus of research at 

PNNL and several other laboratories over the last decade. Overall results have revealed 

excellent resistance to SCC and extremely low CGRs in PWR primary water environments in 

agreement with PWR service experience. This resistance can change with a moderate-to-high 

degree of cold work as demonstrated for alloy 690 materials [5]. Even though this cold-worked, 

high-strength condition is not believed to exist for alloy 690 or its weld metals in operating 

reactor components, it remains critical to understand the limiting material conditions that can 

promote SCC susceptibility. 

The current report has documented SCC results on a large number of industry-made alloy 152, 

152M, 52, 52M and 52MSS weld mockups revealing low CGRs (all <5x10-9 mm/s and most 

<2x10-9 mm/s) in 360°C simulated PWR primary water. Moreover, specialized tests performed 

on alloy 52M overlay and inlay mockups supported very low SCC CGRs in the alloy 52M weld 

metal. The main conclusion from these experiments on alloy 152, 152M, 52, 52M and 52MSS

weld metals with typical Cr bulk concentrations (28-30 wt%) is that they are resistant to SCC 

crack growth. 

Some differences were observed for alloy 152 and 52M welds in regions where the local Cr 

concentration was found to equal to or below ~24 wt%. SCC propagation rates up to ~1.4x10-8

mm/s were measured in an alloy 52M weld pass for the Ringhals overlay (CT035) and within 

DM weld alloy 152 dilution zones adjacent to the LAS interface (CT117 and CT119). The 

presence of aligned grain boundaries along the crack path were a key requirement for 

significant SCC growth in the dilution zone specimens and limited the extent of observed IGSCC 

to local areas. Overall, these results support the excellent SCC resistance of the high Cr welds 

in the as-welded condition.

Based on our investigations at PNNL over the last decade and interactions with the international 

community, additional research is recommended in several areas for alloy 690 and its weld 

metals:

1) Continue to investigate alloy 690 heat-to-heat and alloy 152/52/52M weld-to-weld 

variability. The early results by Bettis showing high SCC CGRs in moderately coldworked alloy 690 at low K levels still raise a potential concern that certain heats (and 

microstructures) may show more significant SCC susceptibility. Attempts should be 

made to determine what microstructural/microchemical features were responsible for the 

observed behavior. 

2) Improve understanding of strength effects on IGSCC particularly for cold/warm work 

levels that bound what may exist in existing and planned LWRs. Additional SCC testing 

is needed in the 10-15% cold work range on additional alloy 690 heats and is also 

suggested for selected alloy 152/52/52M weld metals. 

3) Repairs during installation may have created alloy 152/52/52M welds in reactor service 

that have a higher degree of residual plastic strain and have regions of much higher 

strength than for the typical as-welded condition. It is important to better understand 

what a “worse case” condition might be and produce repair weld mock ups to properly 

evaluate whether this higher strength condition increases SCC susceptibility. Proper 
6-2

analysis of effects due to repair welding can help establish levels of cold/warm work that 

should be applied to simulate the strength change.

4) Weld defects remain an issue of potential concern, since it is difficult to produce

pertinent weld mock ups and also to directly assess their effects on SCC initiation and

growth using conventional testing approaches. One approach that appears promising

for this issue is to machine blunt notch CT specimens where pre-existing weld defects

(i.e., DDC and/or solidification cracks) intersect the notch surface, thereby enabling SCC

initiation and growth processes to be evaluated from the pre-existing defects.

5) Additional DM weld dilution zones need to be characterized and tested, particularly

those produced between alloy 152/52M and LAS. A better understanding of the local

composition changes (Fe enrichment, Cr depletion) and its continuity along the interface

region is required plus the grain boundary microstructure that would enable IGSCC

propagation over significant distances.

6) Long range ordering has been shown to occur in alloy 690 and its weld metals at

temperatures slightly higher than PWR service and cause significant hardening. At this

time, it is not known whether ordering is a concern for these materials after long-term

service. Better quantification of this process at lower temperatures is needed along with

the evaluation of its effect on SCC resistance for pertinent materials.

7) For nearly all of the items listed above, characterization and testing of materials removed

from PWR service would be extremely helpful. Access to selected alloy 690

components and alloy 152/52/52M welds may become possible due to reactor

shutdown. The ability to perform detailed examinations of welds may provide unique

insights into variabilities among microstructures, residual plastic strains, local strength,

defects and dilution zones. These results would help confirm whether mock-up welds for

laboratory testing have been sufficient to address material variations in service and their

effects on SCC. Similar assessments of microstructure and SCC behavior for alloy 690

component materials would also help ensure that laboratory studies on many heats have

been sufficient and that long-term aging in service does not significantly impact

properties.
7-1 

7 REFERENCES

[1] "Materials Reliability Program: Resistance of Alloys 690, 152, and 52 to Primary Water 

Stress Corrosion Cracking (MRP-237, Rev. 1) ", Product ID 1018130, Electric Power 

Research Institute, August 2008.

[2] "Materials Reliability Program: Resistance of Alloys 690, 152, and 52 to Primary Water 

Stress Corrosion Cracking (MRP-237, Rev. 2) Summary of Findings Between 2008 and 

2012 from Completed and Ongoing Tests", Product ID 3002000190, Electric Power 

Research Institute, April 2013.

[3] S.M. Bruemmer and M.B. Toloczko, "Pacific Northwest National Laboratory Investigation 

of Stress Corrosion Cracking in Nickel Base Alloys, Volume 2", NUREG/CR-7103, Vol. 1, 

ML11277A230 and ML11294A228, U.S. NRC, September 2011.

[4] S.M. Bruemmer, M.B. Toloczko, M.J. Olszta, "Pacific Northwest National Laboratory 

Investigation of Stress Corrosion Cracking in Nickel Base Alloys, Volume 2", NUREG/CR7103, Vol. 2, ML12114A011, U.S. NRC, April 2012.

[5] M.B. Toloczko, N.R. Overman, M.J. Olszta, S.M. Bruemmer, Stress corrosion cracking in 

nickel-base alloys: stress corrosion cracking of cold worked alloy 690, U.S. Nuclear 

Regulatory Commission, NUREG/CR-7103, Vol. 3, July 2016.

NUREG/CR-7103 Vol. 4

S. Bruemmer, M. Olszta, R.J. Seffens, R.A. Bouffioux, N.R. Overman,

M. Toloczko

Pacific Northwest National Laboratory, Richland, Washington, 99352

Same as above

The objective of this program is to evaluate the primary water stress corrosion cracking (PWSCC) susceptibility 

of high chromium Ni-base weld metals, establish quantitative measurements of crack-growth rates and 

determine relationships among cracking susceptibility, environmental conditions and metallurgical 

characteristics. Stress-corrosion, crack-growth rates have been determined for 11 alloy 152/52/52M weld metal 

specimens, 4 alloy 52M/182 overlay specimens and 2 alloy 52M/82 inlay specimens in simulated PWR primary 

water environments. Weld metal, overlay and inlay specimens were machined from industry mock ups to 

provide plant-representative materials for testing. Specimens have been tested for one alloy 152 weld, two alloy 

52 welds and three alloy 52M welds. The overlay and inlay specimens were prepared to propagate stresscorrosion cracks from the alloy 182 or 82 material into the more resistant alloy 52M. In all cases, crack 

extension was monitored in situ by direct current potential drop (DCPD) with length resolution of about +1 μm 

making it possible to measure extremely low growth rates approaching 5x10-10 mm/s. Most SCC tests were 

performed at 325-360°C with hydrogen concentrations from 11-29 cc/kg; however, environmental conditions 

were modified during a few experiments to evaluate the influence of temperature, water chemistry or 

electrochemical potential on propagation rates.

Alloy 690

Nickel alloys

Cold work

Stress corrosion cracking

April 2019

Technical

Pacific Northwest National Laboratory Investigation of Stress Corrosion 

Cracking in Nickel-Base Alloys: Behavior of Alloy 152 And 52 Welds



NUREG/CR-7103 Vol. 4 Pacific Northwest National Laboratory Investigation of Stress Corrosion Cracking 

in Nickel-Base Alloys: Behavior of Alloy 152 And 52 Welds

April 2019