( A11100 RAT03M

NBS

PUBLICATIONS

NBSIR 80-2039

Report No. 10

A Metallurgical Evaluation of Two

AAR Ml 28 Steel Tank Car Head

Plates Used in Switchyard Impact

Tests

J. G. Early and C. G. Interrante

Fracture and Deformation Division

National Measurement Laboratory

National Bureau of Standards

Washington, D.C. 20234

December 1979

Final Report

Issued May 1 980

Prepared for Federal Railroad Administration

Denartment of Transportation

•QG“"1^*ington, D.C. 20591

100

. 1)56

80-2039

1980

NBSIR 80-2039

» i / REPORT NO. 10

A METALLURGICAL EVALUATION OF TWO

AAR Ml 28 STEEL TANK CAR HEAD

PLATES USED IN SWITCHYARD IMPACT

TESTS

«ATIO»AL BUMAL

OF 89ANDAB1>3

MB*ARY

JUL 2 1 1980

. JSb

J. G. Early and C. G. Interrante

Fracture and Deformation Division

National Measurement Laboratory

National Bureau of Standards

Washington, D.C. 20234

December 1979

Final Report

Issued May 1 980

'This document has been prepared for the use of the

Federal Railroad Administration, Department of Transportation.

Responsibility for its further use rests with that

agency. NBS requests that if release to the general

public is contemplated, such action be taken only

after consultation with the Office of Public Affairs

at the National Bureau of Standards.”

Prepared for Federal Railroad Administration

Department of Transportation

Washington, D.C. 20591

U.S. DEPARTMENT OF COMMERCE, Philip M. Klutznick, Secretary

Luther H. Hodges, Jr., Deputy Secretary

Jordan J. Baruch, Assistant Secretary for Productivity, Technology, and Innovation

NATIONAL BUREAU OF STANDARDS, Ernest Ambler, Director
>: • jp.

.i’"' 3?i

'
Abstract

The National Bureau of Standards was requested by the Federal Railroad

Administration to correlate the mechanical properties and metallurgical

characteristics of two steel head plate samples taken from tank cars (GATX

93412 & UTLX 38498) subjected to switchyard impact tests. This metallurgical

evaluation included determining whether the samples conformed with the

appropriate specifications and to determine the impact test behavior of both

plate samples.

The results of check chemical analyses and ambient-temperature tensile

tests indicated that both plates met the chemical, tensile strength, and

tensile ductility requirements of AAR M128 steel. The results of metal! ographic

analyses of both plates revealed extensive banding with alternate layers of

ferrite and pearl ite, typical of carbon-manganese steel in the hot-rolled

condition. The GATX sample also contained a microstructural anomaly near

the inside plate surface, possible related to prior thermo/mechanical

processing of the plate.

The nil -ductil ity transition temperatures were determined to be -20 F and -40 F for the GATX and UTLX plates, respectively, similar to the lowest

values reported for a group of tank car plate samples. The results of

Charpy V-notch tests established that the transition temperatures of these

two plates are similar to one another, and are among the lowest of those

measured for all other tank car plates tested at NBS.

The comparatively low impact transition temperatures for both plates

are related to the high manganese-to-carbon ratio and relatively fine

ferrite grain size observed in the microstructures.

Table of Contents

Abstract

1 . INTRODUCTION 1

2. PURPOSE 2

3. EXPERIMENTAL PROCEDURE 2

3.1 Macroscopic Observations and Rolling

Direction Determination 2

3.2 Chemical Analysis 3

3.3 Tensile Testing 3

3.4 Impact Testing 4

3.5 Metallographic Studies and Hardness Testing 4

4. RESULTS AND DISCUSSION 5

4.1 Chemical Composition 5

4.2 Macroscopic Observations 5

4.3 Metallographic Analyses 6

4.4 Hardness Measurements 7

4.5 Tensile Properties 7

4.6 Inclusion Content 9

4.7 Impact Properties 10

4.7.1 Nil -Ductil ity Transition Temperature 10

4.7.2 Charpy V-notch (CVN) Tests 11

4.7.3 CVN Transition Behavior 11

4.7.4 Upper-Shelf Energy Absorption 13

4.7.5 Plate Anisotropy 14

4.7.6 Fracture Appearance 14

4.8 General Discussion 15
Table of Contents (continued)

5. CONCLUSIONS 16

6. ACKNOWLEDGEMENT 17

REFERENCES 19

TABLES

I. Chemical Composition of Head Plate Samples From Tank Cars GATX

93412 and UTLX 38498

II. Tensile Properties of Head Plate Samples From Tank Cars GATX 93412

and UTLX 38498

III. QTM Inclusion Content Rating of Head Plate Samples From Tank Cars

GATX 93412 and UTLX 38498

IV. Drop-Weight Test Behavior of Head Plate Samples From Tank Cars GATX

93412 and UTLX 38498

V. Charpy V-notch Impact Transition Temperatures For Six Head Plate

Steels Tested at NBS

VI. Comparison of Charpy V-notch Upper-Shelf Behavior of Six Head

Plates Tested at NBS

VII. Comparison of Selected Results From Check Chemical Analyses of Four

Head Plates Tested at NBS

FIGURES

1. Plate Sample Taken from Tank Car UTLX 38498

2. Plate Sample Taken from Tank Car GATX 93412

3. Plate Samples Showing Location and Orientation of Test Specimens

4. Schematic Shwoing the Three Mutually Perpendicular Planes Associated

With the Rolling Direction in a Plate

5. Representative Photomicrographs of Inclusions on Longitudinal and

Transverse Planes

6. Montage of Microstructure Through Cross-Section of the Plate Sample

From Tank Car UTLX 38498

7. Montage of Microstructure Through Cross-Section of the Plate Sample

From Tank Car GATX 93412

8. Photomicrographs of Typical Microstructure on Longitudinal Plane

From Tank Car UTLX 38498
Table of Contents (continued)

9. Photomicrographs of Typical Microstructure on Longitudinal Planes

From Tank Car GATX 93412

10. Phogomicrographs of Typical Microstructure on Longitudinal Planes

From Tank Car GATX 93412

11. Drop-Weight Test Specimens

12. Charpy V-notch Impact TEst Results for Head Plate Specimens Taken

From Two AAR Ml 28 Steel Plates

13. Fracture Appearance of Selected Charpy Specimens Taken From Tank

Car UTLX 38498

14. Fracture Appearance of Selected Charpy Specimens Taken From Tank

Car GATX 93412

15. Longitudinal CVN Upper-Shelf-Energy Absorption for Nine Tank Car

Steels of Various Yield Strength Levels

APPENDIX A - Charpy Impact Test Results

Table A1 . Energy Absorption for LT Orientation, UTLX 38498

Table A2. Energy Absorption for TL Orientation, UTLX 38498

Table A3. Lateral Expansion for LT Orientation, UTLX 38498

Table A4. Laterial Expansion for TL Orientation, UTLX 38498

Table A5. Shear Fracture Appearance for LT Orientation, UTLX 38498

Table A6. Shear Fracture Appearance for TL Orientation, UTLX 38498

Table A7. Energy Absorption for LT Orientation, GATX 93412

Table A8. Energy Absorption for TL Orientation, GATX 9341 2

Table A9. Lateral Expansion for LT Orientation, GATX 93412

Table A10. Lateral Expansion for TL Orientation, GATX 93412

Table All. Shear Fracture Appearance for LT Orientation GATX 93412

Table A12. Shear Fracture Appearance for TL Orientation GATX 93412

1 . INTRODUCTION

The National Bureau of Standards (NBS) was requested by the Federal

Railroad Administration, Department of Transportation (FRA-DOT) to

conduct metallurgical evaluations of two steel plate samples taken from

two railroad tank cars. These tank cars, identified as GATX 93412 and

UTLX 38498, were reportedly involved in two simulated switchyard impact

tests as part of the Phase 15 test program carried out in 1976 at the

DOT test facility at Pueblo, Colorado. (1

) ' '

Both the GATX and UTLX tank cars were filled with water and pressurized

to 100 psig. The temperature of the water in tank car UTLX 38498 was reported to be 74 F (23 C), and unknown in tank car GATX 93412.

In each of these two tests, it was reported (1) that a moving tank car impacted a stationary hopper car which subsequently impacted a stationary tank car coupled to five hopper cars. At the start of both

tests, the stationary hopper car was separated from the stationary tank car by a distance of two and one-half feet.

In the test involving UTLX 38498, neither the stationary tank car

(UTLX 38498) nor the moving tank car were equipped with head shields. It was reported 0) that at impact, the stationary hopper car was lifted

off its trucks, overrode the draft sill of the stationary UTLX 38498 and

struck the A-head of the tank car. The hopper-car coupler dented and

punctured the A-head of UTLX 38498 at the weld joint between the head

plate and the head-plate reinforcing pad. The head-plate sample removed

and sent to NBS for evaluation contained both the dent and puncture.

In the test involving GATX 93412, both the moving tank car (GATX 93412)

and the stationary tank car were equipped with head shields. It was reported (1) that after the impacted hopper car struck the stationary

tank car, the hopper car continued to rise upwards and subsequently

struck the moving tank car in the upper half of the A-head. The hopper

car coupler overrode the top of the head shield and punctured the A-head

of GATX 93412 just above the head shield. The head-plate sample removed

from GATX 93412 and sent to NBS for evaluation did not contain the

region of impact, and therefore the exact location of this plate sample

on the head plate is unknown.

The two head plates from which samples were taken for this metallurgical

evaluation are presumed to be in the hot-rolled, hot-formed, and stressrelieved condition. Details concerning the exact thermo/ mechanical

condition of these two head plates were not reported to NBS.

Very little if any evidence of cold work was observed to be present

in the GATX plate sample as a result of the puncture of the head plate.

The observations and properties reported for the GATX sample are therefore

believed to be relevant to the A-head of this tank car in service.

^

The isolated numbers in parentheses refer to references listed at

the end of this report.

- 1 -
The UTLX plate sample, however, exhibited substantial evidence of

cold work since it contained the dented and punctured region of the Ahead plate. Due to this severe deformation, all test specimens were

taken from the region with the least amount of cold work. Although some deformation from the denting and puncture of the head plate may be

present, results indicate that there does not appear to have been any

significant effect of the deformation on the properties measured for

this sample.

2. PURPOSE

The purpose of this metallurgical evaluation was to correlate the

mechanical properties and metallurgical characteristics of two head

plate samples taken from tank cars GATX 93412 and UTLX 38498. This

evaluation included determining whether the samples conformed with the

chemical -composition and tensile-property requirements of AAR M128, a specification for high strength carbon manganese steel plates for tank cars (AAR TCI 28-69), as well as a determination of the impact behavior

of these plate samples.

3. EXPERIMENTAL PROCEDURE

Chemical analyses and tensile properties were determined and compared

with the requirements of AAR Ml 28-69. In addition to these required

tests, standard Charpy V-notch impact tests, drop-weight nil -ductil ity

transition-temperature tests, inclusion content ratings and a hardness

survey were performed, and macroscopic and microscopic observations were

made. Longitudinal and transverse specimens were prepared for the

tensile tests and Charpy tests.

The principal rolling direction of each of the GATX and UTLX headplate samples had to be determined prior to the preparation of test

specimens. Head plates, as a result of their method of fabrication,

lack reference features that identify the principal rolling direction.

Thus, it was necessary to use studies of inclusion morphology and Charpy

V-notch impact test results from specifically oriented specimens to

identify the principal rolling direction.

Results of pre-cracked Charpy V-notch impact tests and dynamic-tear

tests, currently being conducted on these two plate samples, will be

reported in subsequent reports.

3 .1 Macroscopic Observations and Rolling Direction Determination

The plate samples taken from tank cars GATX 9341 2 and UTLX 38498

were rnacroscopical ly examined for evidence of deformation resulting from

the switchyard impact tests. The principal rolling direction was determined by testing a series of Charpy V-notch specimens oriented at

fixed angles with respect to an arbitrary reference line scribed

- 2 -
on the plate surface (Figures 1 and 2). A plot of energy absorption

versus reference angle revealed either a maximum or a minimum, which

identifies respectively the principal rolling direction (longitudinal)

or the perpendicular (transverse) direction. The locations and orientations of test specimens taken from each of the two head plates are shown

in Figure 3.

3.2 Chemical Analysis

Check chemical analyses (by combustion-conductometric and emission

spectroscopic methods) were conducted by a commercial testing laboratory

at the quarter-thickness location of the chemistry samples (Figures 1 and 2) from each plate to determine if the composition satisfied the

requirements of AAR Ml 28-69 steel.

3.3 Tensile Testing

Longitudinal and transverse tension test specimens, 0.250 inches in

diameter with a 1 -inch-gage length, were taken as closely as possible

from the quarter thickness position in each plate and tested in accordance

with ASTM A370-73,( b ) Mechanical Testing of Steel Products.

The General Conditions for Delivery section of the specification for

AAR Ml 28-69 tank-car steel requires that materials furnished to these

specifications conform to the applicable requirements of ASTM Specification

A20-65. Specification A20-67 requires, for plates 1-1/2 inch and under in

thickness, tension test specimens shall be Standard Rectangular Tension

Test Specimens with 8-inch-gage length and for plates over 1-1/2 inches in

thickness, tension test specimens shall be Standard Round Tension Test

Specimens with 2- inch-gage length, 0.505 inches in diameter. However,

ASTM A20-67 requires the tests be conducted in accordance with the ASTM

Methods and Definitions A370, for the Mechanical Testing of Steel Products.

ASTM A370-73 allows Standard Round Tension Test Specimens and Small Size

Specimens proportional to the Standard Round Specimen to be used when it is

necessary to test material from which the Standard Rectangular Test

Specimens of 8-inch- and 2-inch-gage length cannot be prepared. Because

the amount of plate material available for machining test samples was

limited, it would not have been feasible to prepare the Standard

Rectangular Tension Specimens. The Standard Round Tension Test Specimen,

0.505 inches in diameter, has a 2-inch-gage length, thus allowing direct

comparison between test result and specification; however, the threaded

end section requires a diameter of 3/4 inches and due to the head-plate

curvature the plate thickness was insufficient. Thus, for test

consistency and to facilitate comparison with previous results (2-7), the

tensile test specimens were machined to standard 0.250-inch-diameter

round test specimens with a 1-inch-gage length.

- 3 -
3.4 Impact Testing

The results of two types of impact tests are discussed in this

report: drop-weight nil -ductil ity transition temperature (NDTT) tests,

carried out in accordance with ASTM E208-69, and standard Charpy V-notch

(CVN) tests, carried out in accordance with ASTM E23-72. Specimens for

the NDTT tests were full -plate-thickness type specimens with length and

width dimensions of 5 inches and 2 inches, respectively, and a saw-cut

notch located on a weld bead on the outside plate surface. The Charpy

specimens were standard size and were machined as closely as possible

from the quarter-thickness location of the plate, nearest the outside

plate surface. The Charpy data were analysed by methods described

earl ier. (2-8)

The drop-weight test was originally developed to study the initiation

of brittle fractures in low- and intermediate-strength structural steels.

This test is used to measure the nil -ductil ity transition (NDT) temperature

(the temperature above which many steels undergo a transition from

brittle to ductile fracture behavior) and permits the evaluation of the

ability of a steel to resist crack propagation. The NDTT, according to

ASTM E2Q8-69, is independent of the specimen orientation with respect to

the plate rolling direction.

The orientation of Charpy specimens used in this study are the

standard longitudinal (LT) and transverse (TL) orientations used in

previous reports (2-8). For all sets of impact specimens, tests were

conducted over a temperature range selected to demonstrate the transition

from ductile, to brittle fracture behavior.

3 . 5 Metal lographic Studies and Hardness Testing

Representative photomicrographs, oriented as shown in Figure 4,

were obtained on metal lographic samples located as shown in Figures 1 and 2. Metal lographic observations were made on selected polished and

etched areas of longitudinal C planes and transverse B planes. The

ferrite grain size was measured in accordance with the circular intercept

method from ASTM Ell 2-74, Intercept Method.

Rockwell B hardness measurements were taken on specimens adjacent

to the metal lographic specimens and correlated with the microstructure

of each plate sample.

The inclusion content was determined on longitudinal C planes by a Quantitative Television Microscope (QTM) method which rates the inclusion

content as an area percent of the section being rated. The area percentage

measurements were made at two quarter thickness locations and at the

mid-thickness. In addition, the worst field and the number of fields

with inclusion area greater than 0.5 percent, were tabulated. The QTM

methods used in this study are described in previous reports (2-6) and

in the literature (9).

- 4 -
4. RESULTS AND DISCUSSION

4.1 Chemical Composition

The chemical compositions, as determined by check chemical analysis

of the two plate samples, are given in Table I, along with the chemical

requirements for AAR Ml 28-69 steel. Grades A and B, and one producer's

ladle analysis. The results of the laboratory check analyses and the

producer's ladle analysis (where available) are in good agreement and

indicate that the composition of both plate samples satisfies the chemical

requirements for AAR Ml 28-69 steel. The carbon levels in both samples

are close to the maximum level allowed. The manganese level of the GATX

plate is 0.20 percent by weight below the maximum level allowed and that

for the UTLX plate is only 0.11 percent by weight below the maximum

allowed. The vanadium content of the GATX sample is 0.026 weight percent

and thus meets the specified minimum content of 0.02 for AAR Ml 28, Grade

A steel. The UTLX plate satisfies the chemical requirements for AAR

Ml 28, Grade B steel

Specification AAR Ml 28-69 requires the steel to be made to finegrain practice and the presence of aluminum in the UTLX sample, and

aluminum and vanadium in the GATX sample indicates that a fine-grain

steelmaking practice was followed.

4.2 Macroscopic Observations

The plate samples from tank cars GATX 93412 and UTLX 38498 had been

flame cut from the impacted head plates. The *GATX sample had a number

of small surface scratches and gouges but did not appear to have experienced

any significant amount of plastic deformation (Figure 2) as a result of

the switchyard impact test. The specimen layout (Figure 3a) was chosen

to avoid most of the gouged areas, and therefore the results for the

GATX plate sample are believed to represent the as-fabricated head

plate.

Visual examination of the UTLX plate sample revealed extensive

deformation and reforming over much of the sample. This apparently

resulted from the switchyard impact test. The plate sample appeared to

be centered about the principal impact site on the head plate and

contained numerous surface gouges, a puncture at the weld joint between

the head plate and head-plate reinforcing pad, and an extensive concave

dent (Figure 1). The portion of the plate sample adjoining the flamecut edge contained the least visible evidence of deformation. Therefore,

the specimen layout (Figure 3b) was selected so that all of the test

specimens used for mechanical property measurements were taken from this

region of minimum deformation. The results for the UTLX plate sample

are believed to be representative of the as-fabricated head plate even though a small amount of deformation from the switchyard test may have

been present in the areas selected. This possible level of deformation

appeared to have no significant effect on the mechanical properties

measured for this plate.

- 5 -
4.3 Meta 1 1 ographic Analyses

Representative photomicrographs taken at low magnification on longitudinal C planes and transverse B planes for the GATX sample and on longitudinal C planes for the UTLX sample are shown in the unetched

condition in Figure 5. A comparison at a magnification of XI 00 was made

of the inclusions in these two plate samples with those of the Winder

sample (6), an ASTM A21 2 steel head plate studied previously. For the

Winder sample, a substantial difference in the inclusion lengths on the

longitudinal and transverse planes was observed as compared to the GATX

and UTLX samples (shown in Figure 5a for the GATX plate sample). This

difference in inclusion length was greater for the Winder sample compared

to the UTLX and GATX samples and could result from differences in thermo/mechanic

processing procedure.

The method employed initially to identify the principal plate

rolling direction for the GATX and UTLX head plate samples, used successfully

on the Winder and other head plate samples, measured the change in

average inclusion length as a function of specimen orientation about an arbitrary reference line. The effectiveness of this technique is therefore

reduced as the difference in inclusion length between the longitudinal

and transverse directions decreases. The principal plate rolling directions

in the GATX and UTLX samples could not be established through examination

of inclusion morphology due to the inability to consistently distinguish

between the longitudinal and transverse directions as a result of the

small difference in inclusion length in these two directions. Therefore,

the principal plate rolling direction was finally determined by the

testing of Charpy V-notch specimens oriented about an arbitrary reference

line. *

Representative microstructures of both plate samples are shown in

the etched condition in Figures 6 through 10. The microstructures are

typical of carbon-manganese steel in the hot-rolled condition and

consist of a mixture of proeutectoid ferrite and pearl ite. Montages of

the longitudinal plane microstructures from the outside surface to the

inside surface of the GATX and UTLX plates (Figures 6 and 7) show the

existance of extensive banding with alternate layers (parallel to the

plate surfaces) of ferrite and pearl ite. The degree of banding observed

in these two head-plate samples is similar to that reported (5) for

other AAR Ml 28 head-plate samples studied at NBS. However, no quantitative

measure of the degree of banding was carried out.

The estimates of ferrite grain size of the GATX and UTLX plate

samples are ASTM Nos. 10 1/2 and 11 respectively . Ferrite grain size

and pearl ite colony size are strongly influenced by the prior austenite

grain size and by the cooling rate through the transformation temperature,

and are therefore affected by deoxidation practice and by finishing

temperature. The fine ferrite grain size observed in both plate samples

is consistent with the conclusion (based on the check chemical analyses)

that both steels were produced to fine-grain practice. A fine ferrite

grain size is one of the factors which promote low impact transition

temperatures.

- 6 -
The microstructure of the UTLX sample (Figure 8) shows that the

banded structure exhibits a high degree of regularity with generally

continuous layers of the lighter etching proeutectoid ferrite phase

separating the darker etching pearl ite phase. The microstructure in

this region of the plate (Figure 1) does not show any effects of deformation resulting from the impact that punctured this head plate.

The cross-sectional montage of the GATX sample (Figure 7) reveals

the presence of a microstructural anomaly near the inside plate surface.

In this region, the regularity of the banded structure (Figures 9a and

10a) has been disrupted resulting in local areas consisting of large

pearl ite colonies and large proeutectoid ferrite grains (Figures 9b and

10b). This microstructural anomaly is probably related to thermal and

mechanical effects resulting from processing of the plate, such as too

high a forming temperature, since the prior austenite grain size and

cooling rate can affect the grain sizes and distributions of ferrite and

pearl ite in these low-carbon steels. (10) This microstructure is similar

to that reported earlier (4) for the Callao K-l plate, a head plate

believed to have been improperly hot formed. The nonuniformity through

the cross-section of the GATX sample (Figure 7) is not as severe as that

of Callao K-l

4.4 Hardness Measurements

The results of hardness measurements on the plate cross-section are given for the UTLX and GATX plate samples in Figures 6 and 7 respectively

The Rockwell B hardness profiles for both plates are quite similar and

very uniform across most of the cross-section and can be correlated with

the microstructure. The region of the GATX plate containing the microstructural

anomaly has an average hardness of almost HRB 90 compared to HRB 86 1/2

for the remainder of the plate. The higher hardness observed in this

region near the inside plate surface is associated with the presence of

large pearl ite colonies and a somewhat higher fraction of the relatively

harder pearl ite phase.

4.5 Tensile Properties

The measured tensile properties of both the GATX and UTLX samples

are given in Table II along with the requirements of AAR Ml 28-69. The

results of the longitudinal and transverse specimens indicate that both

head-plate samples are within the allowed range of ultimate tensile

strength, 81 ksi to 101 ksi, and both samples meet the minimum yieldstrength and elongation requirements of 50 ksi and 19 percent, respectively..

The average values of longitudinal and transverse ultimate tensile

strength for the GATX plate were 84.4 ksi and 90.2 ksi, respectively,

while the average 0.2 percent offset yield-strength values were 55.2 ksi - and 56.4 ksi, respectively. For the UTLX plate, the average ultimate

tensile strength values of longitudinal, transverse, and 45° specimens

were 88.6 ksi, 88.2 ksi, and 88.3 ksi, respectively, while the average

0.2 percent offset yield-strength values were 58.5 ksi, 52.8 ksi, and

55.2 ksi, respectively. These results indicate that there was no significant

anistropy in the strength of the two plates in the plane of the rolling

direction; a finding consistent with earlier results on both head and

shell plates of ASTM A217 and AAR Ml 28 steel . (5,6,11

- 7 -
The yielding behavior of a plate sample can provide evidence as to

whether its mechanical properties have been affected by cold work. The

cold work sustained by the head plates in the switchyard impact tests

could lead to the elimination of a sharp yield point, increases in yield

strength, and increases in the ductil e-to-brittl e transition temperature,

as measured by Charpy V-notch impact tests. In tensile tests of these

plates, the presence of a sharp yield point is an indication that significant

cold work of the plate had not occurred since the tank car tank was stress relieved after fabrication. Further, unusually high yieldstrength values are another indication of significant cold work. In contrast to this observation, both plate samples have yield-strength

values within the specification requirements of AAR Ml 28 and these

values are consistent with the carbon and manganese levels determined by

the check chemical analyses. In addition, a sharp yield point was observed in eight of the ten tensile test specimens (Table II) tested.

These results suggest that the plastic deformation received by these two

plate samples as a result of the switchyard tests was insufficient to

significantly affect the mechanical properties in regions of the plates

from which test specimens were taken.

The average tensile ductility values, as measured by percent

elongation, were 31.7 percent and 26.9 percent respectively for longitudinal

and transverse specimens taken from the GATX plate sample. The longitudinal

elongation values were approximately 18 percent higher than the transverse

values. This finding is in agreement with the general observation that

the tensile ductility of rolled steel plates tends to be greater in the

longitudinal direction than in the transverse direction.

The average tensile ductility values of the UTLX plate sample,

measured by percent elongation, were 31.4 percent, 33.9 percent, and

30.6 percent respectively for the longitudinal, transverse, and 45

degree specimens. The transverse elongation value was about eight

percent higher than the longitudinal value, but only single test values

are available for each orientation. The average percent elongation

(four specimens) for the 45 degree orientation was about three percent

smaller than the longitudinal value. These results are contrary to the

behavior of the GATX sample and can be interpreted as: (i) a reflection

of the variability of the properties within this plate, and (ii) an indication that this plate was more extensively cross-rolled.

Reduction-in-area requirements are not specified in AAR Ml 28, but

they provide a useful check of the elongation results since percent

reduction-in-area measurements are independent of the gage length of the

test specimen. The results for the GATX sample (Table II) show that the

percent reduction-in-area values were 63.2 percent and 57.4 percent,

respectively, for the longitudinal and transverse specimens. The

longitudinal value is approximately ten percent higher than the transverse

value and the trend is similar to that observed for the GATX elongation

data. The UTLX sample exhibited isotropic behavior with reduction-inarea values of 61.0 percent, 61.0 percent, and 60.6 percent respectively

for the longitudinal, transverse and 45 degree specimens and this behavior

is similar to that shown by the UTLX elongation data.

- 8 -
Previous studies at NBS (5), with both head-plate and shell -plate

samples of AAR Ml 28 steel, revealed that: (i) there was little difference

between the average ultimate tensile strength and yield strength values

of longitudinal and transverse specimens; (ii) the average longitudinal

tensile ductility, measured by percent elongation, was approximately ten

percent higher than the transverse ductility; and (iii) the anisotropy

of tensile ductility was attributed to the rolling operation used in the

fabrication the steel plates. The greater longitudinal tensile ductility

observed in the GATX sample indicates that this plate experienced less

cross-rolling than the previous AAR Ml 28 samples studied. Conversely,

the lack of definite anisotropy in tensile ductility properties found

for the UTLX sample suggests that this plate experienced greater crossrolling than either the GATX sample or any of the other AAR Ml 28 plates

studied.

The ultimate-tensile-strength data can be compared with the hardness

measurements and the results of the metal lographic analyses. Using an empirical relationship between hardness and tensile strength (12), the

measured hardness range of HRB 86 to 90 for the GATX sample and HRB 86

1/2 to 89 for the UTLX sample correspond to ul timate-tensil e-strength

ranges of 81 ksi to 89 ksi and of 83 ksi to 87 ksi, respectively . The

measured average ultimate tensile strength of slightly more than 87 ksi

for both longitudinal and transverse specimens of the GATX plate is

within the predicted range. For the UTLX plate, the average ultimate

tensile strength of somewhat more than 88 ksi is slightly above its

predicted strength range. This general agreement between the measured

hardness data and the empirically derived strength data is as good as can be expected for this type of correlation and the small discrepancy

in the UTLX comparison is not believed to be significant.

4.6 Inclusion Content

The results of the inclusion content rating of both the GATX and

UTLX samples are given in Table III. The QTM area-percentage rating at

an effective magnification^) of XI 00 indicates an overall average

inclusion content (based on 100 fields) for the GATX and UTLX samples of

0.21 area percent and 0.27 area percent, respectively. There were no fields found with an inclusion area equal to or greater than 0.5 percent.

The results of earlier QTM inclusion analyses^ of one head and

two shell plates of AAR Ml 28 steel (3,4) showed higher average overall

inclusion contents of 0.35, 0.33, and 0.45 area percent respectively.

The observed number of fields with inclusion areas equal to or greater

than 0.5 percent were 21, 15, and 34 respectively, for the head and

shell plates. Thus, the results of inclusion content ratings indicate

The effective magnification of the QTM system represents the actual

magnification of the image used by the internal electronic measuring

scale of the instrument. The image magnification or apparent magnification,

as measured on the visual display monitor, has no meaning because the

monitor is not part of the measuring system. ^

These QTM measurements were reported for an apparent magnification of

X338. This is equivalent to an effective magnification of XI 20 for

the particular instrument used.

- 9 -
that the GATX and UTLX samples of AAR Ml 28 steel were similar to each

other and cleaner than the other AAR Ml 28 steels studied to date at NBS.

Further, these results indicate that the cleanliness of the GATX and

UTLX samples are similar to NBS test results previously reported for

ASTM A212-B steel .(5,6)

A further comparison can be drawn between the GATX and UTLX results

and data reported(e) for production heats of steels with a broad range

of composition and strength levels. (9) These production heats of steel

were not produced to cleanliness specifications but were taken from

regular production heats of basic oxygen or open-hearth steel. The

average inclusion area percent range reported was 0.10 to 0.38 and the

reported range for number of fields with inclusion area equal to or greater than 0.5 percent was 1 to 28. The results for the GATX and UTLX

plate samples lie towards the low end of this ranges and indicates that

the cleanliness of these two samples compares favorably with that

attained in production heats of other steels.

4.7 Impact Properties

The results of drop-weight tests and Charpy V-notch (CVN) tests for

these two AAR Ml 28 steel • head plates lead to the following observations:

(i) these two plates have very similar impact properties; only minor

differences are observed; (ii) the nil -ductil ity transition temperature

(.NDTT) for each plate is close to the lowest NDTT values recently

reported (13) for steels produced according to AAR Ml 28; (iii) in

comparison with other head-plate steels tested at NBS, these two plates

have low [generally desirable) transition temperatures and their uppershelf energy-absorption levels are comparable with those of steels

produced according to AAR Ml 28; [iv) like other head plates tested at

NBS, these plates were produced with extensive cross rolling as compared

to shell plates; and (v) a lamellar fracture appearance observed on broken Charpy specimens from both the GATX and UTLX plates and on other

tank-car plate steels appears to be associated with a banded microstructure of alternate layers of ferrite and pearl ite, while the fracture

surfaces of two plates that do not appear lamellar do not have banded

microstructures.

4.7.1 Nil -Ductil i ty Transition Temperature

The results of the drop-weight tests are given for both the GATX

and UTLX samples in Table IV. Inspection of the drop-weight test

specimens taken from the GATX plate (pictured in Figure 11a) shows that

in both specimens tested at -10 F the weld starter crack did not propagate

to either edge of the specimen surface. At -20 F and below, the weld

starter crack propagated to at least one edge of the surface. Inspection

of the UTLX plate test specimens (pictured in Figure lib) shows that in

both specimens tested at -30 F, the starter crack did not propagate to

either edge of the specimen surface. At -40 F and below the starter

crack propagated to at least one edge of the surface. Thus, according

to the test criteria of ASTM E 208-69, the nil -ductil ity transition

temperature (NDTT) values for the GATX and UTLX samples are -20 F and -40 F,

respectively.

The reported data were obtained at an apparent magnification of X350

which was equivalent to an effective magnification of XI 00.

- 10 -
The NDTT values for these two plates compare favorably with those

given in a recent review (13) of fracture toughness properties of samples

of steels of several grades of plate materials currently and formerly

specified for use in tank cars. This review reported a broad NDTT range

of from -60 F to +30 F for 17 plates representative of plates in various

conditions of heat treatment and fabrication and of plates from tank cars involved in accidents.

For the AAR Ml 28 steels, this range is -60 F to +20 F for all eight

plates tested. The individual NDTT values are: -60 F for an as-rolled,

normalized and stress-relieved (A-N-S) shell plate; -20 F for an as- rolled and normalized (A-N) head plate; 0 F for each of three as-rolled

and stress-relieved (A-S) shell plates; +20 F for an as-rolled, hotformed and stress-relieved (A-H-S) head plate; and -10 F and +20 F for

two shell plates taken from accidents. In general, AAR Ml 28 plates that

were normalized have NDTT values that are lower than those for plates

that were not normalized. The NDTT values for the GATX and UTLX plates

are -20 F and -40 F, respectively, and these values are within the range

reported for the A-N-S and A-N plates tested. They are lower than the one A-H-S plate tested, and are at the low end of the range of all AAR

Ml 28 plates tested. Thus, the NDTT values for the GATX and UTLX plates

appear to be generally similar to those reported for the group of plates

that had been normalized but they are lower than the value for the head

plate reported to have been hot-formed (A-H-S).

4.7.2 Charpy V-notch (CVN) Tests

The results of Charpy V-notch (CVN) impact tests are given for the

UTLX plate in Figures 12a, 12b, and 12c, and for the GATX plate in

Figures 1 2d , 12e, and 12f, with each figure representing one of the

three fracture criteria. These criteria, respectively, are energy

absorption, lateral expansion, and shear fracture appearance (SFA). In

the figures, observed values and calculated curves are shown, for both

the longitudinal (LT) specimens and the transverse (TL) specimens. In

addition, raw data and results of calculations associated with these

figures are given in separate tables in Appendix A: Tables A1 through

A6 represent the GATX plate and Tables A7 through A12 represent the UTLX

plate.

The figures reinforce some of the findings of previous investigations (6,8) of head-plate steels taken from failed tank cars. For each

of the three fracture criteria, the transition zone for a given plate

begins and ends over approximately the same range of temperatures.

Further, the magnitude of the values of energy absorption and those for

lateral expansion, are nearly proportional to the percent SFA, and the

transition regions, as measured by SFA, are independent of specimen

orientation. Further discussion of the lateral expansion is omitted

below because of the similarity in trends between lateral expansion data

and energy absorption data.

4.7.3 CVN Transition Behavior

The transition region is the range of temperatures over which a transition from brittle to ductile fracture is observed. Brittle fracture

is observed at temperatures below the lowest temperature of the transition

- 11 -
the fracture mode is described as cleavage (or quasi-cleavage) fracture.

Ductile fracture is observed above the highest temperature of the transition

region; the fracture mode is described as shear fracture. The transition

regions for the GATX and UTLX plates are similar. This is shown in the

SFA plots of Figures 12c and 12f, which also show that the SFA is independent

of specimen orientation. The CVN transition of the UTLX plate extends

from -80 F to about 60 F, and that of the GATX plate extends from -80 F to about 30 F, a slightly narrower range of temperatures.

A transition temperature is a temperature, normally within the

transition region, at which an arbitrary level of a fracture criterion

is met. The CVN transition temperatures for longitudinal and transverse

specimens for the six head plates tested to date at NBS (6,8) are given

in Table V for three commonly reported fracture criteria: 15 ft-lb

energy absorption, 15 mil lateral expansion, and 50% SFA.

In the table, it is seen that of the six head plate samples tested

at NBS, three AAR Ml 28 samples (the GATX, UTLX, and Belle plates) had

comparatively low transition temperatures. A fourth plate of AAR Ml 28

steel is Callao K-l , which is believed to have been improperly heat

treated during fabrication (4). This plate, K-l, and the remaining two

plates, both of which were produced to ASTM A-212-B specification, have

transition temperatures that are more than 80 F above those of the three

head plate samples of AAR M128 steel with the comparatively low transition

temperatures. v') Thus, the GATX and UTLX plates have very favorable

transition temperatures, when compared with all head plates tested at

NBS, and these transition temperatures are similar with those observed

for the Belle head plate, an AAR M128 steel.

The 50 percent SFA transition temperature is given here to generally

characterize the transition temperatures of head plates tested at NBS.

The average of longitudinal and transverse results for this CVN transition

criterion are the average 50% SFA value is -2 F, -23 F, and -16 F for

the UTLX, GATX, and Belle plates, respectively. Thus, transition temperatures

of these three steel plates are similar to one another and are significantly

more favorable (lower) transition temperatures than the values of 92 F,

105 F, and 140 F, which represent the other three head plates tested at

NBS.

The less favorable (higher) transition temperature of the ASTM A212-B

steel plates is a result primarily of their larger ferrite grain size and

lower manganese-to-carbon (Mn/C) ratio. For the A212-B steels, the ratios

are less than three, whereas the ratios for the AAR Ml 28 steels are higher,

about five. In general, the transition temperature decreases as the ferrite

grain size decreases and the Mn/C ratio increases. Another important

factor influencing the transition temperature is the effect of heat treatmen

Although the Callao, K-l, plate had a high Mn/C ratio, its ferrite grain siz was large and within the range seen in the A212-B plates. This is probably

a result of improper heat treatment and it has resulted in the increased

transition temperature of this plate to the comparatively higher levels

observed in the A212-B plates.

- 12 -
In comparison with these transition temperatures for the UTLX and

GATX plates, the NDTT values of -40 F and 20 F, as given earlier in this

report, are observed to be approximately 20 F lower than the 50 percent

SFA values for these steels. Further, the data in Appendix A indicate

that on average, 46 percent of the upper-shelf values of energy absorption,

lateral expansion, and percent SFA is available at the NDTT for these

two steels.

4.7.4 Upper-Shelf Energy Absorption

On the upper shelf, the fracture appearance is 100% shear fracture.

For specimens of all orientations taken parallel to the rolling plane of

the plate, the minimum Charpy V-notch upper-shelf energy-absorption is

measured using specimens of the transverse (TL) orientation. As seen in

Table VI, the transverse upper-shelf energy-absorption values for both

the GATX and the UTLX plates, 38 ft-lbs and 37 ft-lbs respectively, are

similar to values obtained for the other AAR Ml 28 plates tested, 38 to

40 ft-lbs. The maximum CVN upper-shelf values are measured using

longitudinal (LT) specimens. The longitudinal results for these two

plates also overlap the range of values observed for the two previously

tested AAR Ml 28 head plates. The upper-shelf energy absorption values

for the four AAR Ml 28 steel plates, for longitudinal and transverse

specimens, are less than those of the two ASTM A212-B plates. Thus, the

results of CVN tests of two orientations show that the upper-shelf behavior

of the four AAR Ml 28 head-plate steels tested at NBS are similar, and that

two ASTM A212-B steels previously tested have comparatively higher uppershelf values for both longitudinal and transverse specimens.

The upper-shelf energy-absorption values of longitudinal (LT)

specimens obtained for these two AAR Ml 28 steels (GATX and UTLX) and an ASTM A212-B steel (6) are generally supportive of earlier findings

reported (8) for head plates and shell plates of other tank-car steels

produced to these same specifications. These findings are shown. Figure

15, in a plot of upper-shelf energy absorption as a function of yield

strength for longitudinal specimens of all nine steels tested. In

addition to the data and trend line for these tank-car steels, there is

shown a trend line taken from the literature (14) representing the

behavior of a wide variety of steels, including ferritic-pearl itic

steels, as discussed earlier (8). A linear fit for the tank-car steels

is shown by the solid line and that for the literature values is given

by the dotted line. A comparison of these two lines, representing

upper-shelf energy absorption values, indicates that at all levels of

yield strength, the tank-car steels generally absorbed less energy than

that reported in the literature trend line.

The four tank-car plates with the highest shelf-energy values do

not contain vanadium and these data are close to the literature trend

line. All three of the ASTM A212-B plates previously tested are part of

this group along with one Ml 28 plate which apparently was not produced

to fine-grain practice. Using an arbitrary inclusion ranking system

described in a previous report (5) (Rank 1 - lowest inclusion content

observed, Rank 3 - highest inclusion content observed), these four

plates include a head plate (Crescent City, A212-B) and a shell plate

(Crescent City, A212-B) of Rank 1, and a shell plate (Callao, M128) and

a head plate (Winder, A212-B) of Rank 2.

- 13
The five tank-car plates with the lowest shelf-energy values are AAR Ml 28 steels and four of the five plates contain vanadium. The four

plates with vanadium include a head plate (Belle) and a shell plate

(South Byron) of Rank 3, a head plate (Callao, K-l) of Rank 2, and a head plate (GATX) of Rank 1. The last plate in this group, a head plate

(UTLX) without vanadium, has an inclusion content of Rank 2. Thus, on the basis of results for all nine steels, it appears that in general,

higher inclusion content levels and the presence of vanadium are associated

with lower levels of upper-shelf energy absorption values, and is supportive

of earlier reported (8) findings.

4.7.5 Plate Anisotropy

Plate anisotropy, as measured by an anisotropy index (8), has been

used as a measure of the extent of cross rolling. This index is the

ratio of the transverse to longitudinal energy absorption on the upper

shelf. It has a value of one for an isotropic material, and the value

decreases with increasing plate anisotropy. As the amount of cross

rolling increases, the difference between longitudinal and transverse

upper-shelf energy absorption decreases (15), and this index approaches

a value of one.

Anisotropy index values, as determined from CVN tests of the six

head-plate steels tested to date at NBS, are given in Table VI. This

index is 0.79 for the UTLX plate, 0.63 for the GATX plate, and for the

other four head plates it ranges from 0.59 to 0.70. Compared with the

four other head plates tested at NBS, the UTLX plate is the most isotropic

of this group of plates and the GATX plate is one of the least isotropic.

Shell plates, however, are given less cross rolling and the anisotropy

indices for CVN tests of three shell plates tested at NBS (5) varied

from 0.46 to 0.54. As expected, the shell plates are observed to be

considerably less isotropic than the head plates.

4.7.6 Fracture Appearance

Photographs of selected fractured Charpy specimens are shown in

Figure 13 and 14, respectively for the UTLX and GATX plates. At temperatures

above -50 F and -60 F respectively for the UTLX and GATX plates, where

the shear fracture appearance was above 15 percent, the fracture surfaces

of both longitudinal and transverse specimens were similar, and contained

regions of cleavage fracture, fiberous fracture, and shear lips. At the

highest test temperatures they contained only regions of fiberous fracture

and shear lips. Generally, the size of the shear lips increased with

increasing test temperature, and at a fixed temperature, were larger for

longitudinal specimens than for transverse specimens.

Previously reported studies (2,3) of shear fracture appearance from

broken Charpy specimens of shell plates, taken from an ASTM A212-B plate

(Crescent City (2)) and an AAR Ml 28 plate (South Byron (3)) revealed

large scale lamellar fracture on both longitudinal and transverse specimens,

with the lamellae oriented parallel to the rolling plane of the plate.

A lamellar fracture appearance was not observed in specimens of either

orientation from two previously reported ASTM A212-B head plates (Crescent

City (2) and Widner (6)). These two head plates do not exhibit microstructural
banding. Other previously reported steels showing microstructural

banding include the AAR Ml 28 head plates Belle (7) and Callao K-l (4),

and an AAR Ml 28 shell plate, Callao K-5 (4). Examination of the fracture

surfaces of broken Charpy specimens revealed a lamellar fracture appearance

in each of these three plates. In the present study of two AAR Ml 28

steel head plate samples, GATX and UTLX, a lamellar fracture appearance

was observed in fractured Charpy specimens of both orientations. However,

the extensiveness of these lamellae was not quantified for any of the seven plates studied at NBS. Thus, it is observed that all seven steels,

including three shell plates and four head plates, that exhibit microstructural

banding v9) show some degree of lamellar fracture appearance and two

head-plate steels that did not have microstructural banding did not show

a lamellar fracture appearance.

4.8 General Discussion

The purpose of this metallurgical evaluation was to correlate the

mechanical properties and metallurgical characteristics of two head

plate samples taken from tank cars GATX 9341 2 and UTLX 38498, involved

in simulated switchyard impact tests. This evaluation included a determination

as to whether these plates conformed to the chemical composition and

tensile property requirements of specification AAR Ml 28 for railroad

tank car steel, to which the plates were produced, and to investigate

the impact behavior of the plates.

The results of check chemical analyses indicated that both plate

samples met the chemical composition requirements of AAR Ml 28-69. The

results further show a strong compositional similarity between the two

plates with the following exceptions: (i) the presence of vanadium in

the GATX plate and the absence of vanadium in the UTLX plate; (ii) a lower manganese content in the GATX plate; and (iii) a higher silicon

level in the UTLX plate.

Generally, the strength properties of ferritic-pearl i tic steels

such as AAR Ml 28 are governed by both the carbon and manganese contents

and by the thermo/mechanical history. The average ultimate tensile

strength and yield strength values for the two plates (averaging all

orientations) are 87.3 ksi and 55.8 ksi respectively for the GATX plate

and 88.4 ksi and 55.5 ksi respectively for the UTLX plate, indicating

very little difference in the overall average strength values between

the two plates. Thus, any effect on strength properties as a result of

differences in chemistry or thermo/ mechanical history between these two

plates is minimal

.

The observation that both the GATX and UTLX samples satisfied all

of the strength and tensile ductility requirements is in agreement with

the results of the check chemical analyses. The measured hardness

profiles for both plates are consistent with their respective microstructures

and correlate reasonably well with the measured ultimate tensile strength

values. The tensile strength of the UTLX plate as predicted from the

hardness data is lower than the actual measured strength values, but is

^

It should be noted that steels with microstructural banding were shown (4,8)

to have very favorable resistance to fracture in the through-thickness

direction in tests conducted with CVN specimens of the LS and TS

orientations.

- 15 -
of an acceptable level for this type of correlation. The yielding

behavior for both the GATX and UTLX plates supports the conclusion that

the mechanical properties of these two samples have not been significantly

affected by the extsent of damage received by the plates during the

switchyard impact tests.

The Charpy V-notch ductil e-to-brittl e transition temperature of

carbon steels, often characterized by the 15 ft-lb transition temperature

or the 50 percent shear-fracture-appearance transition temperature, is

primarily controlled by the steel chemistry and ferrite grain size.

Increasing the ferrite grain size raises the transition temperature.

Carbon and manganese affect the transition temperature of these tank car steels primarily from their effects on the ferrite grain size and pearl ite

content. Increasing the carbon level raises the transition temperature

by increasing the fraction of pearl ite while increasing the manganese

level lowers the transition temperature through refinement of the ferrite

grain size. Although vanadium is added to these steels primarily to

strengthen the ferrite phase through precipitation hardening by vanadium

carbides and nitrides, the transition temperature can also be increased

(15) due to these strengthening effects.

A comparison of the four AAR Ml 28 head plate samples tested to date

at NBS revealed a large variation in their ferrite grain sizes (Table

VII), from a relatively coarse ASTM No. 7 for the Callao plate to a much

finer ASTM No. 11 for the UTLX plate. This large difference in ferrite

grain size was observed in spite of the fact that the four head plates

were produced to fine-grain practice, and the difference is believed to

reflect primarily differences in plate forming practice.

0 In this group of six head plates, the Crescent City plate with the

largest ferrite grain size and highest carbon content had the highest

transition temperature. The Belle, GATX, and UTLX plates with the

smallest ferrite grain sizes, higher manganese contents and lower carbon

contents, had the lowest transition temperatures. Thus the data indicate

that for head plates produced to the ASTM A212-B and AAR M128 specifications,

the manganese-to-carbon ratio and the ferrite grain size are the most

important factors influencing the Charpy V-notch transition temperature

behavior.

The NDTT values of -40 F and -20 F measured for the UTLX and GATX

plates respectively, occur at the temperatures at which 40 percent SFA

and about 50 percent of the upper-shelf values of energy absorption and

lateral expansion, based on the average of both plates and both orientations,

are observed in CVN tests results from these two plates. These results

suggest that the NDTT is a slightly less conservative measure of the

ductile to brittle transition than is the 50 percent SFA criterion and

that the NDTT is more conservative than either the 15 ft-lb energy

absorption or the 15 mils lateral expansion fracture criteria.

5. CONCLUSIONS

1. The chemical composition of the GATX and UTLX plate samples, as determined by check chemical analyses, satisfied the chemical requirements

- 16 -
of specification AAR Ml 28 . A strong compositional similarity was found

between the two plates with the exception that the GATX plate contained

vanadium and a lower manganese content than the UTLX plate.

2. The tensile strength properties and tensile ductility properties of

both the GATX and UTLX plates satisfied the requirements of specification

AAR Ml 28. Very little difference in the overall average strength values

was observed between the two plates.

3. U1 timate-tensil e-strength and yield-strength values for both plates

indicate little anisotropy in the strength of the plate in the plane of

the rolling direction. Tensile-ductility values, measured by both

percent elongation and reduction-in-area, indicated that longitudinal

ductility was greater than transverse ductility for the GATX plate,

while no significant difference between longitudinal and transverse

tensile ductility was observed in the UTLX plate.

4. The results of Charpy V-notch impact tests of the GATX and UTLX

plates indicated that:

a. The transition from ductile to brittle fracture mode for each

of these two plates, as measured by percent shear fracture appearance

(SFA), occurs over a range of 120-140 F, from +30 F to -80 F for the

GATX plate and from +60 F to -80 F for the UTLX plate.

b. The transition temperatures of these two plates, for three

commonly used criteria, are similar to one another, and their transition

temperatures are among the lowest of those measured for all other tank- car plates tested to date at NBS.

c. Based on an average for the two steel plates, two specimen

orientations, and the three CVN fracture criteria, the NDTT is determined

to be the temperature at which 46 percent of the upper-shelf values for

these criteria is obtained.

d. The comparatively low impact transition temperatures for both

plates are related to the high manganese- to-carbon ratio and relatively

fine ferrite grain size.

e. All seven steel plates, including three shell plates and four

head plates, that exhibit microstructural banding show some degree of

lamellar fracture appearance, and two head-plate steels that did not

show microstructural banding did not exhibit a lamellar fracture appearance.

6. ACKNOWLEDGEMENT

The authors wish to express thanks to Mr. D. E. Harne for his

excellent contributions to the metal lographic, photographing and mechanical

testing portions of this report. Special thanks to Mr. S. R. Low for

his assistance in conducting the impact tests and in the impact data

analysis. Thanks to Mr. C. H. Brady for the grain size measurements.

- 17 -
CONVERSION FACTORS

1 ksi = 6.89 MPa

1 ft-lb = 1.36 Joules

1 mil = 0. 025 mm

t

o =

(t° - 32)

18
References

(1) Orringer, 0. and Tong, P. "Results and Analysis of the Switchyard Impact

Tests," Transportation Systems Center, Department of Transportation,

Cambridge, MA. , 1979.

(2) Interrante, C. G., Hicho, G. E. and Harne, D. E. "A Metallurgical

Analysis of Five Steel Plates Taken From A Tank Car Accident Near

Crescent City, Illinois," Report No. FRA OR&D 75-48, National Bureau of

Standards, March 1972, NTIS PB 250530.

(3) Interrante, C. G. and Hicho, G. E. "Metallurgical Analysis of a Steel Plate Taken From a Tank Car Accident Near South Byron,

New York," Report No. FRA OR&D 75-47, National Bureau of Standards,

October 1971, NTIS PB 250063.

(4) Interrante, C. G., Hicho, G. E. and Harne, D. E. "A Metallurgical

Analysis of Eleven Steel Plates Taken From A Tank Car Accident Near

Callao, Missouri," Report No. FRA OR&D 75-49, National Bureau of Standards,

September 1972, NTIS PB 250544.

(5) Interrante, C. G., Early, J. G., and Hicho, G. E. "Analysis of

Findings of Four Tank-Car Accident Reports," Report No. FRA OR&D 75-50,

National Bureau of Standards, Jan. 1975, NTIS PB 251097.

(6) Early, J. G. "A Metallurgical Analysis of an ASTM A212-B Steel Tank

Car Head Plate," Report No. NBSIR-78-1582 , National Bureau of Standards,

September 1978.

(7) Hicho, G. E. and Brady, C. H. "Hazardous Materials Tank Cars - Evaluation

of Tank Car Shell Construction Material," Report No. FRA OR&D 75-46,

National Bureau of Standards, September 1970, NTIS PB 250607.

(8) Interrante, C. G. "Impact Properties of Steels Taken From Four Failed

Tank Cars," Report No. FRA OR&D 75-51, National Bureau of Standards,

June 1976.

(_9) Rege, R. A., Forgeng, W. D. Jr., Stone, D. H. and Alger, V. V. , "Microcleanliness of Steel - A New Quantitative TV Rating Method,"

ASTM STP 480, American Society for Testing and Materials, 1970,

pp. 249-272.

(10) Atlas of Isothermal Transformation and Cooling Transf ormation Diagrams,

American Society for Metals, 1977.

(11) Early, J. G., "Elevated -Temperature Mechanical Behavior of a CarbonManganese Pressure Vessel Steel," J. Engineering Materials and Technology,

99, 1977, pp. 359-365.

(12) Army-Navy Approximate Hardness Tensile Strength Relationship of

Carbon and Low Alloy Steels (AN-QQ-H-201)

- 19 -
(13) Eiber, R. J. and Olson, L. L. , "Material Study on Steels Used in

Current and Former Tank Car Construction and From Cars Involved in

Accidents," AAR Report RA-03-5-33, August 21, 1975.

(14) Gross, J. H. , "The Effective Utilization of Yield Strength,"

J. Engr. Industry, 1971, ASME Paper No. 71-PVP-ll.

(15) Kozasu, I. and Tanaka, J. , "Effects of Sulfide Inclusions on Notch

Toughness and Ductility of Structural Steels," Proceedings International

Symposium on Sulfide Inclusions in Steel, American Society for Metals,

197 5.

(16) Bain, E. C. and Paxton, H. W. , "Alloying Elements in Steel,"

American Society for Metals, 1966.

- 20 -
Table I Chemical Composition of Head Plate Samples

Prom Tank Cars GATX 93412 and UTLX 38498

Percent by Weight

Specification

AAR M128-69

Element Ladle Analysis

Tank Car Tank Car

GATX 93412 UTLX 38498

Check Analysis^ a ^

Grade A Grade B

Carbon 0.25 max 0.23 0.24

Manganese 1.35 max 1.15 1.24

Phosphorus 0.04 max 0.01 0.01

Sulfur 0.05 max 0.017 0.014

Silicon 0.30 max 0.19 0.28

Copper (b) 0.35 max 0.02 0 . 06

Nickel (b) 0.25 max 0.20 0.15

Chromium (b) 0.25 max 0.09 0.06

Molybdenum (b) 0.08 max 0.05 0.01

Vanadium 0.02 min (c) 0.026 0 . 01

Aluminum (c) 0.02 0.025

C 3. ) Carbon was determined by combustion-conductometric analysis;

all other elements were determined by emission spectroscopy.

/

1^

\ Element not specified.

Element not specified, fine grain practice is

required

/ ^

\ Producers Report: UTLX 38498 plate sample is reported to be

Kawasaki heat number 91-7850, AAR M128-B, with the ladle

analysis of 0.25 carbon, 1.30 manganese, 0.0015 phosphorus,

0.0019 sulfur, 0.29 silicon, 0.08 copper, 0.15 nickel,

0.05 chromium, and 0.0015 molybdenum; all weight percent.

II X CO 0 cn

i—t -=r aco E co

cO CO

XX

a) E-t P 3

CO

1-t

X

CL, c

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on

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to E-< 0 «=c x a

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cn

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co CO rH rH pH rH as as OV as ov as 3 X ax

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TO0XX0

0)CL

co poXo

Table

III

QTM

Inclusion

Content

Rating

of

Head

Plate

Samples

Prom

Tank

Cars

GATX

93^12

and

UTLX

38^98 **

T3

rH

0) P

PhP

cqGo

cq

cq0 1 C

73

X P O S •H,C

Eh

cq

G CQ 0 0 P G G ^

cd o G 1-1 <y sz

Eh

p * p G LO 0 :s O • P O G cq W A I 0 Td G ' 0 0 P rH rH G £ 0 O 0 G -H C G S Pi H <

CQ CQ

CQ

C T3

p 0 O rH G PT C P 0 CO 0 \ ^ P P C\J cvj 0 on 0 P pH • • G P CQ 0 0 0 P O IP

CP Eh CP CM

v-' 00G r-N < CQ CQ 0 C Td c 0 0 p 0 1 G P 0 OJ 3T P Td P p p CM C\J 0 •H O P pH • • O S tH CQ 0 0 1H p O O O Eh CP LO GH0 CQ CQ 60 CQ c Td C 0 0 p P 3T C P 0 0

OV P \ P p p 1—1

cm 0 rH O p pH • • CP •H CQ 0 0 P O LTV 2 Eh CP C\J Eh<y 0>P

-PO coPP

cdo

1—I 0 P P P P G H &0

cd

vo

-=r o

-3T ooo

rHX

vo

on

-3- 3TO1—I X 0 P CM 00 P P 1—1

CdV

cd cd 3T -=r p 0 on 00

CP Pp

o> on

Td

X

X

G P Eh P 0 G < Eh

PC 0

idH

Cd PC

CQ Td1—1 0P

PhOog0

cp

G0

CP * **

50

Fields

Table IV Drop-Weight Test Behavior of Head Plate

Samples Prom Tank Cars GATX 93412 and

UTLX 38498

AAR M128 Steel

Tank Car GATX 93412

Specimen Test

Code Temperature, P Comments

GN5 -50 Starter crack propagated to both edges of

specimen

.

GN2 -30 Starter crack propagated to both edges of

specimen.

GN3 -20 Starter crack propagated to both edges of

specimen.

GN1 -10 Starter crack did not propagate to either

edge of specimen.

GN7 -10 Starter crack did not propagate to either

edge of specimen.

Nil-Ductility Transition Temperature = -20 P

Tank Car UTLX 38498

Specimen

Code

Test

Temperature, F Comments

UN 6 -70 Starter crack

of specimen.

propagated to both edges

UN 2 -60 Starter crack

of specimen.

propagated to both edges

UN 7 -40 Starter crack

of specimen.

propagated to both edges

UN 8 -30 Starter crack did not propagate to either

edge of specimen.

UN 4 -30 Starter crack did not propagate to either

edge of specimen.

Nil-Ductility Transition Temperature = -40 P

Table V Charpy V-notch Impact Transition

Temperatures For Six Head Plate

Steels Tested at NBS

Transition Temperature, F

Steel

Type

Plate

Identity

Specimen

Orientation

15 ft-lbs

Energy

Absorption

15 mil

Lateral

Expansion

50 percent

Shear

Fracture

AAR . GATX 93412 Long. (LT) -58 -64 -30

M128-A (aJ Trans. (TL) -46 -50 -17

AAR UTLX 38498 Long. (LT) -47 -46 - 7

M128-B Trans. (TL) -42 -46 + 4

AAR Belle (b

)

Long. (LT) -47 -43 -11

M128-A Trans. (TL) -49 -50 -21

AAR Callao ( b

)

Long. (LT) 56 41 86

M128-a(sO K-l Trans. (TL) 72 64 98

A212-B Winder

(

c ) Long. (LT) 66 50 111

SOEX 3033 Trans. (TL) 67 44 100

A212-B Crescent Long. (LT) 92 72 137

City ( t)

)

Trans. (TL) 84 69 143

FRA2

(a) Designation of Grade A is based on NBS check chemical analysis.

(b) Reference (8)

(c) Reference (6)

Table

VI

Comparison

of

Charpy

V-notch

Upper-Shelf

Behavior

of

Six

Head

Plates

Tested

at

NBS

^5 >3 W hO

XgG 0 0 0 0 c a £ 0 g w H o 01 H /-V G 0

<0 0 3 cd cp

>3 rH i—i 0 a 0 0 on CO o o^ on o> 0 0 C o 0 0 MO 10 c— in VO t— 0 cd cd G CO CO • • • • • • cd 0

p> o o o o o o 0 g c o G Ci > O 0 0 0 0 0 0 0 d a 'O T! 50 G Q< a G < g> D >3 O 0

cd 0 0 Eh £ 1—1 Eh 0 0 3 0

EhO

co

G 0) 0 0 0 30 TOr—I 3 0300

co0G

>3 00g0£0 0 O 0 G in in CO o c— oo >30 0 0 -=r in on ^=r on on 0 0 >3 0 > 0 cd bO >3 0 o 0 G 0

>3 0 c > 0 3

b£)0 cd 0 0 CC

G i—1 gC 0 0 3 0 1 Eh 0 C 0 a >30 0 W 0 0 C 0 3 0 < 0 O

<0 « G 0 • 0 0 G O 0 X £ 0 O • 0 0 0 0 Eh TO 0 G 0 0

CO 0 0 c c 0 C

a

a •

- cd o 0 0 g g 0 a 0 0 o i—1 0 0 3 >3 o a 0 cd 0 O a 0

C10 c 1—1 0 0 o 0 D < 0 CM i—i

-=r CO cn oo 0 G Eh

G o 0 C— CO in \o in -=r 0 0 0 3 0 0 o CO 0 0 0 0 CQ 0 0 0 0 0

bO 0 0 c C G 0 3 C O £ 0 0 o 0 O > 3 0 G 0 0 0 0 0 G G 0

cd

O 0 0 G C «G 3 C 0 0 O 0

>3 0 0 £ 0 0 0 0 0 0 i—i 0 G C 3 0 0 O I CM oo o cd 3 0 O « 0 cn 0 3 < O 0 -=r xr a0 >3 > C A on CO 0 cd bO 0 0 G 0 o CT\ on G G G 0 0 0 o cd 0 <0 0 0 0 3

cd 0 0 i—i 0 X

X

O 0 C 0 G 1—1 C 0 i—i 1—1 Eh 0 3 0 bO a 0 0 G cd 0 < Eh G 0 0

3:

a o 0 a

D

O 0 0 0 0 0 oO i

1 o 0 C 0 >3 3 O 0 0 c 0 0 0 I—1 o G 3 •H 0 0 0 0 G 0 0 ' 0 3 0 O 3 < < < 0 G G 0 0 G 1 1 1 1 O 0 00 bO OO OO CO CO 3 0 0

CM CM CM CM 0 0 0 0 i—i

CQ CQ 0 i—1 i—1 i—1 0 0 EhG 0 0 0 1 1 s s S S Eh 0 0 3 Q 0 a CM CM 0 >3 i—1 i—1 K 0 ^ v CO Eh CM CM < < < < 3 0 < < < <C < <

Table

VII

Comparison

of

Selected

Results

Prom

Check

Chemical

Analyses

of

Pour

Head

Plates

Tested

at

NBS. pc0ou0

cup£

50

•H00

-P

•HP0

Ph 3 CM VO LO c o 1 1 CM /-N CM CM

•H o o O 02O

O s • • • ' • • 3 o o O O O i—1 V V <s3 to VO

•H C\J rH CO CM rH

'3 o o o O

O o

cd • • • • • • c o o o o o o

cd

V

V

V >0

co0 co c rH co LO o ION -=r •H

cd CO c

CM CM rH CM co o0 • • • • • • >5 C o o rH rH rH rH 1 1 cd cd S C

cd

rH

cda c •H o a\ -=X VO VO CO p- s O CM CM CM CM CM OJ 0

o:

cdOO o o O o o O

PsJ O03o 0

Csl CO

•H CQ CO

CM CM 2 c VO [— \ X rH C

•H rH rH rH o

cdu oo o 3

CO rH 0

CO

cd O

co 0 •H a

>5 cd cd <

CQ CQ < < < CQ 0

iH 1 1 1 l 1 1 3 0 CM CM CO CO co CO cd 0 rH 1 1 CM CM CM CM 0, P CM CM rH rH rH rH co

CO < < s s s s <p 3 o 0a c •H o s

>5 •H

p 0 P p 0 3 •H i—1

cd P O O i CM co c 0 O rH av 50 TO P •H 0 C r\ CO co w P P 0 o CTs co 0 o

cd o 0 cd 0 Q s rH CQ id rH rH X X

CL, 0 c rH i—1

Eh

J

SL, •H cd 0 < Eh cd 02 O o CQ CD D V-X

Figure 1. Plate Sample Taken from Tank Car UTLX 38498

Principal plate rolling direction determined with respect

'

to an arbitrary reference line scribed on the plate

surface, marked REF. Chemistry and metallographic

samples were taken from locations marked CHEM and MET,

respectively.

!

I Figure 2. Plate Sample Taken From Tank Car GATX 93412

Principal plate rolling direction determined with respect to

an arbitrary reference line scribed on the plate surface,

marked REF. Chemistry and metallographic samples were taken

from locations marked CHEM and MET, respectively.

i

l

I Figure 3

a.

b.

Plate Samples Showing Location and Orientation of Test Specimens

Principal rolling direction and arbitrary reference line are shown marked as RD and REF, respectively.

a. Tank Car GATX 93412

b. Tank Car UTLX 38498

1

Figure 4. Schematic Showing the Three Mutually Perpendicular Planes

Associated with the Rolling Direction in a Plate

The A plane is parallel to the plate surface. The C plane

contains an arrow which indicates the plate rolling direction

or longitudinal direction.

Longitudinal

a Transverse

Longitudinal

b.

Figure 5. Representative Photomicrographs of Inclusions on Longitudinal

and Transverse Planes

a. Tank Car GATX 93412

b. Tank Car UTLX 38498

Unetched Mag. X 100

OUTSIDE

PLATE SURFACE MIDTHICKNESS

INSIDE

PLATE SURFACE

Figure 6. Montage of Microstructure Through Cross-Section of the Plate

Sample from Tank Car UTLX 38498

Hardness values are representative of the locations shown.

Etch: 1% Nital Original Micrographs Mag. X 40

OUTSIDE

PLATE SURFACE

MIDTHICKNESS

MIDTHICKNESS

INSIDE

PLATE SURFACE

Figure 7. Montage of Microstructure Through Cross-Section of the Plate

Sample from Tank Car GATX 93412

Hardness values are representative of the locations shown.

Etch: 1% Nital Original Micrographs Mag. X 40

b„

Figure 8. Photomicrographs of Typical Microstructure on Longitudinal

Plane from Tank Car UTLX 38498

a. Mag. X 100

b. Mag. X 400

Etch: 4% Picral

Figure 9.

b.

Photomicrographs of Typical Microstructure on Longitudinal

Planes from Tank Car GATX 93412

a. near outside plate surface, Mag. X 100

b. near inside plate surface, Mag. X 100

Etch: 4% Picral

Figure 10. Photomicrographs of Typical Microstructure on Longitudinal

Planes from Tank Car GATX 93412

a. near outside plate surface, Mag. X 200

b. near inside plate surface, Mag. X 200

Etch: 4% Picral
.
a. b.

Figure 11. Drop-Weight Test Specimens

a. Tank Car GATX 93412, Nil-Ductility Transition

Temperature = -20 F

b. Tank Car UTLX 38498, Nil-Ductility Transition

Temperature = -40 F

i

ENERGY

RBS0RPTI0N

(FT-LB)

20.0

30.0

40.0

50.0

60-0

70. a SPECIMEN IDENTIFICATION

II SPECIMENS. IT ORIENTATION.

+ 1J SPECIMENS. TL ORIENTATION.

o

o_

o• °-320 .

0

0

- 220.0 - 120.0 - 20.0

TEST TENPERRTURE

80.0

(F)

180.0 280.0

Fig-are 12a CHRRPY IMPACT TEST RESULTS FOR HERD PLATE SPECIMENS

TAKEN FROM RRR TC128 STEEL PLATE U

LATERAL

EXPANSION

(MILS]

20.0

30-0

40.0

50.0

60. o SPEC THEN IDENTIFICATION

TEST TEMPERATURE C F

)

Figure 12b CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE U

/

SHEAR

FRACTURE

APPEARANCE

25.0

37.5

50.0

62-5

75.0

87.5

100.

SPECIMEN [DENT I F [CAT [ 0N

TEST TEMPERATURE (F)

Figure 12c CHflRPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TCI28 STEEL PLATE U

ENERGY

RBS0RPTI0N

(FT-LB)

20.0

30.0

40.0

50.0

60-0

70. o

SPECIMEN IDENTIFICATION

8 SPECIMENS * L T ORIENTATION.

+• 17 SPECIMENS. TL ORIENTATION.

m

o

OJ

-320.0 -220.0 -120.0 -20.0 80.0

TEST TEMPERATURE (F)

180.0 28Q.0

Figure 12d CHARPY I MP ACT TEST RESULTS FOR HERO PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE G

LATERAL

EXPANSION

(MILS)

20.0

30.0

40.0

50.0

60.0

70.

SPECIMEN IDENTIFICATION

o

o 8 SPECIMENS. LT ORIENTATION.

TEST TEMPERATURE (F)

Figure 12e CHflRPY IMPACT TEST RESULTS FOR HERO PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE G

/

SHEAR

FRACTURE

APPEARANCE

25-0

37.5

50.0

62.5

75-0

87-5

100

. SPECIMEN [IDENTIFICATION

TEST TEMPERATURE (F)

Figure 12f CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE G

Longitudinal

Transverse

0)

1 CD in in O' rH m rH CT> a 0

§

s

CO

CN m CM CN CN "5T m

Eh Eh Eh Eh Eh Eh Eh Eh D D D D D D D P

2

>i i—

l

O' 1 p 4-> CN CN CN

(1) 4-1 \ \ \

C

rH rH i

H

w CD O rH 00 CN rr 00 w

rH rH rH CN CN co ro

P

CDP

VP Em Cm fr< Em Em Em Em m

<D Eh

rtp O O O O O O O O

CD CN 00 CD CN CN 00 CD 1

rH

1 1 1 1 1 i—

1

CDp

s Em Em Em Em Em Em Em Em Em -Pw p

CO O O O O O O O O CN

<D p

CN 00 cD CN CD CN iH

Eh CDi

4

CD Eh

rH

1 1 1 1 i—

1

CN

rH

>i i CP -P p ip

CD w

g

co

CN\iHO 00

CN\iH

rH 00 CN

CN\rHin 00 rH W • rH CN CN co HJ1 LO

co

rH CD in O

rH co iH CN CDrH o

CD

PI PI PI PI PI P P P P

co D D D D D D D o D

Transverse

Longitudinal

co

O 0) rH • Q< 0

•40

CN

r*a 0

coO oID0

.Q

>1 1 CN CN O' 4J \ \

iH 44 r—1

rH

0)

—

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a)P3 b

b

bb Eli

bb

4J

4->

cfl

O

OOO

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tf) V4 CN

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d) 0

1*

0) Eh

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asp

4J 34->

bb

b

b

bb

b

b

b

tn ns

O

O

O

O

OO

OOO CD Eh p

as

as Eh

CNiH1

001

ID 1

CM 00O

rH 3rH

>i 1 O' -P P 44

as ^

CN\rHCN\rH

CN\rH

CN\rH c CO o CN a> in r~ ["• E

Abs.

iH rH f—1 CN CO CO CO CO

as tH • a 0 CN CN

CO

co

co »H

LOrH in

co

O

rH rHrH ID

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(N

COO' X

Eh<0P

ns 0c

(0 Eh!p

44C

<D

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cnC0) E

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>16

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4->O

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440

asoc

nsPm

<u6&

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4-> O

(0pb

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SUBSCRIPTS

ON

THE

SYMBOL

REPRESENT

THE

FOLLOWING

SAMPLES

i CD

i CO

<M<

Q

<

UJX

i <

O

6

0

0

1 00

CO

CO

1 CJ o

CO X

o

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o

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g

X

g

o

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1 o1— X

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X

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<

COX

X X

_J

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COX

COX

Q

X

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COX

1 X

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X o

X

X

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oX

XX

o

X Q

oX Q

o

X

<

X

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X X X - CO

““ < < X

X

_l

< i£

iXo

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X

X

< it:

X

CO>

h-

<

X

co

ro

1 CDX

x

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to

it:

<<o

<

X

<

1 00CO

CO

i^ X

o

X

N_

<1 00

CO

ro

it:

X

X

X

<

1 00

CO it:

X

X

X

128- B

CO

it: X

X

X

o\

X

<

_J<

o\

X

< o X

X X

<

XX

1 o

X

<

X

< o

X

<

co 1 o

X

<

h-<

1 o

X

<

X

H o

X

< Q

cc o cc d X X CD 1- X o 1- X CO 1- X CO 1— X x i— X >

cvi JO d d 00 d

COXX

o

m w

1 it: “ x

co <

< cc

<u (Si pH c <j 0 > H a) X X

a

3 X

0 V

cn a

- X G < <33X

CP CO u

<3 r} c >H M <3

1 H

X >• pH

<3 cn X 3

CO 0

1 •H u 3

<3 id a. >

a

D 4-J0 > cn u pH

<3 pH (3

id X

g CO •H

13 H

3 (d -3 CJ •H

CP X

C G

0 id J E-i

m

(H

<3H

3

CP -H

91 - Id A9d3N3 J13HS-a3ddn NAO

Appendix A, Table Al

CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE U

CALCULATIONS FOR ENERGY ABSORPTION DATA OF

/

T

SPECIMENS, LT ORIENTATION.

SPECIMEN TEMPERATURE (F) OBSERVED ENERGY

A6S0RPT IQN(FT—L8)

CALCULATED ENERGY

ABSOR PTI ON( FT—LB)

UL13 -120.0 3.00 4.8

UL6 -80.0 10.50 8.7

UL5 -60.0 8.00 12.1

UL 1 0 -4 0.0 21.50 16. 6

UL3 • 0 27.80 28.3

UL 1 20.0 32.00 34.4

UL2 60.0 45.50 43. 8

UL 7—19 30.0 46.50 46.2

UL 1-16 120.0 48.00 48.0

UL7-20 160.0 47.00 48. 1 60 212.0 51.00 43. 1

TRANSITION REGION • CALCULATED VALUES

ENERGY CALCULATED / TEMPERATURE CALCULATED ENERGY

ABSORPTION TEMPERATURE

(

F ) / (F) ABSORPTION! FT—L 3 ) 5.0 -1 17.

1

/ -110.0 5.5

10.0 -71.6 / -105.0 5.9

15.0 -46.6 / -100.0 6.3

20.0 -27.3 / -95.0 6.9

25.0 -10.5 / -90.0 7.4

30.0 5.6 / -85.0 8.0

35.0 22. 1 / -80.0 8.7

40.0 4 1.1 / -75.0 9.5

45.0 68.6 / -70.0 10.3

/ -65.0 11.1

/ -60 • 0 12.1

/ -55.0 13. 1 / -50.0 14.2

/ -45.0 15.4

/ -40 • 0 16.6

/ -35. 0 17.9

/ -30.0 19.3

/ -25.0 20.7

/ -20.0 22.1

/ -15.0 23.6

Appendix A, Table A2

CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TCI 23 STEEL PLATE U

CALCULATIONS for energy absorption data of

13 specimens, tl orientation.

specimen TEMPERATURE (F) OBSERVED ENERGY

ABSORPTIONCFT-LB

)

CALCULATED ENERGY

A8S0R PT 1 ON ( FT—LB

)

UT26 -120.0 5.80 6. 9

UT33 1 co 0 • O 8.50 9.7

UT35 -80.0 10.50 9.7

UT 25 -60.0 11.00 12. 1 UT23 -40*0 13.00 15.4

UT 29 -40.0 13.50 15.4

UT 1 8 -20.0 21.00 19.5

UT 2

1

-20.0 22.30 19.5

UT 6—40 -20. 0 19. 00 19. 5

UT2-43 20.0 24.50 23. 3

UT 5—4

1

80,0 38.00 36. 6

UT 2—44 120.0 38.50 37.7

UT6-39 160. 0 37.00 37. 8

TRANSITION REGION • CALCULATED VALUES

ENERGY CALCULATED / TEMPERATURE CALCULATED ENERG

ABSORPTION TEMPERATURE (F) / (F ) ABSORPTI ONI FT-LB

10.0 -76.9 / 1 N Q • O 10.8

15.0 -42.3 / -65.0 1 1 .4

20.0 -17.5 / -60.0 12.1

25.0 4.9 / -55.0 12.9

30.0 28.5 / — 50.0 13.7

35 .0 6 1 .3 / -45.

0

14.5

/ -40.0 •

*-4 in / -35.0 16.4

... / -30.0 17.4

/ -25.0 13.4

/ -20.0 1 9.5

/ 1 in . 0 20.5

/ 1 —4 0 • o 21.7

/ -5.0 22.8

/ • 0 23.9

/ 5.0 25.0

/ 10.0 26.1

/ 15.0 27.2

/ 20.0 23.3

/ 25.0 29.3

Appendix A, Table A3

CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE U

CALCULATIONS FOR LATERAL EXPANSION DATA OF

ir SPECIMENS, LT ORIENTATION,

SPECIMEN TEMPERATURE ( F ) OBSERVED LATERAL CALCULATED LATERAL

EXPANSION { M ILS) EXPANSION (MILS)

UL 13 -120,0 .00 2. 1 UL6 -80,0 3.00 7. 0

UL5 -60,0 8.00 11.3

UL 1 0 -40.0 21.00 16. 8

UL 3 • 0 30.50 30.5

UL 1 20,0 36.00 37.2

UL2 60.0 48. 00 46. 5

UL7-19 80.0 46.50 48. 7

UL 1 — 16 120.0 52.00 50.

0

UL7-20 160,0 46.00 50. 1 60 212. 0 54.00 50. 1

TRANSITION REGION • CALCULATED VALUES

LATERAL CALCULATED / TEMPERATURE CALCULATED LATERAL

EXPANSION! MILS) TEMPERATURE ( F

)

/ (F) EXPANSION! M ILS)

5.0 -92. 3 / 1 O • o 5.3

10.0 -65.3 / -80.0 7.0

15.0 -46. 1 / 1 "J O . o 9.0

20 .0 -30.1 / -60.0 1 1 .3

25.0 -15.6 / -50.0 13.9

30.0 -1 .5 / -40 • 0 1 6 .3

35.0 13.0 / -30.0 20.0

40.0 29.4 / -20.0 23.5

45.0 50.9 / -10.0 27.0

50.0 117.9 / . 0 30.5

/ 10.

0

34.0

/ 20.0 3 7.2

/ 30.0 40.-2

/ 40.0 42.7

/ 50.0 44.8

/ 60.0 46 • 5

/ 70.0 47.3

/ 80.0 43.7

/ 90.0 49.3

Appendix A, Table A4

CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TCI 28 STEEL PLATE U

CALCULATIONS FOR LATERAL EXPANSION DATA OF

\? SPECIMENS* TL ORIENTATION*

SPECIMEN TEMPERATURE (F) OBSERVED LATERAL CALCULATED LATERAL

EXPANSION (MILS) EXPANSION ( MILS

)

UT 26 -120*0 3.50 4.1

UT33 -80.0 8.00 7. 7

UT35 -80.0 7.50 7.7

UT 25 -60.0 11.00 1 1.5

UT23 -40*0 14.00 16.6

UT29 -40.0 18.50 16.6

UT I 8 -20.0 22.50 22.5

UT 2 1 -20.0 24.50 22.5

UT 6— AO -20.0 22.50 22.5

UT 2—43 20*0 31.50 33.6

UT5-41 80.0 42.00 40.3

UT2-44 120.0 41.50 40.8

UT 6—39 160*0 39.00 40. a

TRANSITION REGION* CALCULATED VALUES

LATERAL CALCULATED / TEMPERATURE CALCULATED LATERAL

EXPANSI ON( MILS) TEMPERATURE ( F

>

/ (F) EXPANSION! M ILS)

5.0 -103.5 / -100.0 5.3

10 .0 -66.9 / -95.0 5.8

15.0 -45.8 / -90.0 6.3

20.0 -28.4 / -85.0 7.0

25.0 -11.9 / —80 .-0 7.7

30.0 5.5 / -75*0 8.5

35.0 26.9 / -70 .0 9.4

40 .0 71.6 / —65 .

0

10.4

/ -60.0 1 1 .5

/ -55.0 12.6

/ -50.0 13*9

/ -45.0 15.2

/ -40.0 16.6

/ -35.0 18.0

/ -30.0 19.5

/ -25.0 21.0

/ -20.0 22.5

/ -15.0 24.1

/ -10.0 25.6

/ -5.0 27.1
,
Appendix A, Table A5

CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE U

CALCULATIONS FOR SHEAR FRACTURE APPEARANCE DATA OF

If SPECIMENS, LT ORIENTATION*

SPECIMEN TEMPE RATUREI F

I

OBSERVED

FRACTURE

SHEAR

( X)

CALCULATED SHEA

FRACTURE (%}

UL13 -120.0 • o o • 9

UL6 -80*0 • o o 5.6

UL5 -60*0 6.00 11.7

ULIO -40 .

0

34.00 22. 1 UL3 • 0 54.00 56.9

UL1 20*0 76.0 0 76. 3

UL2 60.0 100.00 97. 7

UL7-19 80* 0 100.00 99.

7

UL 1-16 120*0 100.00 100.0

UL7-20 160.0 1 00.0

0

100. 0

60 212.0 100.00 100.0

TRANSITION REGION, CALCULATED VALUES

X SHEAR CALCULATED / TEMPERATURE CALCULATED

FRACTURE TEMPERATURE ( F

)

/ (F ) FRACTURE iX

2.0 -103.9 / -100.0 2.4

5.0 -82.8 / -95.0 3.0

10.0 -64.5 / -90 .O 3.7

15.0 -52.5 / -85.0 4.6

50.0 -6.8 / -30 • 0 5.6

85.0 30.9 / -7 5.0 6.8

90.0 38.7 / 1 o » o 8.2

95.0 49.8 / -65.0 9.8

98.0 6 1.4 / -60 .

0

11.7

/ -55.0 13.3

/ -50.0 16.3

/ -45.0 19.0

/ 1 <t 0 • o 22. 1 / -35 .

0

25.4

/ -30.0 29.2

/ -25.0 33.2

/ -20.0 37.5

/ -15.0 42.1

/ -10.0 46.9

/ -5.0 5 1.8

Appendix A, Table A6

CHARPY IMPACT TEST RESJLTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE U

CALCULATIONS FOR SHEAR FRACTURE APPEARANCE DATA OF

l? SPECIMENS, TL ORIENTATION.

SPECIMEN TEMPERATURE (F) OBSERVED SHEAR CALCULATED SHEAR

FRACTURE {%) FRACTURE (£>

UT 26 -120.0 .00 1.7

UT3 3 -80.0 6.00 6.4

UT35 -80 • 0 .00 6.4

UT 25 -60. 0 5.00 11.6

UT23 -40.0 35.00 19.7

UT 29 -40. 0 19.00 19. 7

UT 1 8 -20.0 42.00 31 .

5

UT 2

1

-20.0 38.00 31.5

UT 6—40 -20.0 26.00 31.5

UT 2—43 20.0 54.00 64. 4

UT5-41 80.0 1 00.00 93.0

UT 2—44 120. 0 100.00 100.0

UT 6 — 39 160.0 1 00.00 100. 0

# TRANSITION REGION, CALCULATED VALUES

% SHEAR CALCULATED / TEMPERATURE CALCULATED SHEAR

FRACTURE TEMPERATURE (F ) / (F) FRACTURE! X ) 2.0 -l 15.4 / -110.

0

2.4

5.0 —88. 1 / -105.0 2.9

10.0 -65.2 / -100.

0

3.4

15.0 -50.5 / -95.0 4.0

50 m 0 3.6 / -90.0 4.7

85.0 46.3 / -85.0 5.5

90.0 55.0 / -80.0 6.4

95.0 67.2 / -75.0 7.5

98.0 79.8 / -70.0 8.7

/ -65.0 10.1

/ -60.0 1 1 .6

/ -55.0 13.3

/ -50.0 15.2

/ -45.0 17.3

/ -40.0 19.7

/ -35.0 22.3

/ -30.0 25.1

/ -25 •

0

28.2

/ -20.0 31 .5

/ -15,0 35.0

Appendix A, Table A7

CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE G

CALCULATIONS FOR ENERGY ABSORPTION DATA OF

8 SPECIMENS, LT ORIENTATION*

SPECIMEN TEMPERATURE (F ) OBSERVED ENERGY CALCULATED ENERGY

ABSORPT ION(FT-LB) A8S OR PT I ON ( FT -LB

)

GL1 3 -120.0 2.50 2. 6

GL9 -100.

0

3.00 3. 5

GL12 • 1 CD O • o 12.30 6. 6

GL7 -40.0 25.80 26. 9

GL10 • 0 55.30 53. 9

GL3 40.0 57.30 59. 2

60 212.0 60.00 59. 3

70 212.0 60.00 59.3

TRANSITION REGION, CALCULATED VALUES

ENERGY CALCULATED / TEMPERATURE CALCULATED ENERGY

ABSORPTION TEMPERATURE C F

)

/ <F ) ABSORPTION! FT-LB)

5. 0 -87.8 / -80.0 6.6

10.0 -69. 0 / -75.0 8.0

15.0 -58.

1

/ -70.0 9.6

20.0 -49.8 / -65.0 1 1 .7

25.0 -42.6 / -60.0 14.0

30.0 -36. 0 / -55.0 16.8

35.0 -29.6 / -50.0 19.9

40.0 -23.2 / -45.0 23.3

45.0 -16.2 / -40 .0 26.9

50 .0 -8.2 / -35.0 30.3

55.0 3. 1 / -30.0 34.7

/ -25.0 33.6

/ » IS) o • o 42.4

/ -15.0 45.3

/ -10.0 49.0

/ -5.0 51.7

/ .0 53.9

/ 5.0 55.6

/ 10.0 56.9

/ 15.0 57.8

Appendix A, Table A8

CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE G

CALCULATIONS FOR ENERGY ABSORPTION DATA OF

17 SPECIMENS-. TL ORIENTATION.

SPECIMEN TEMPERATURE (F) OBSERVED ENERGY

ABSORPTI ON ( FT—LB I CALCULATED ENERGY

ABSORPTI ON (FT -LB)

GT27 -120.0 3.00 4.3

GT 25 -100.0 2.80 6.2

GT32 -80.0 10.00 3. 5

GT33 -60.0 11.80 11.9

GT 1 -40.0 19.50 16.4

GT 1 a -40.0 18.30 16.4

GT26 -20.0 13.30 21.9

GT 1 9 -20.0 24.50 21.9

GT3

1

• 0 21.50 27.6

GT 1 5 .0 25.00 27. 6

GT2 8 • 0 17.50 27.6

GT 22 20.0 35.00 32.3

GT35 20.0 34.50 32.3

GT 1 0 40.0 37.50 35. 4

GT 34 60.0 37.00 36. 3

GT 1 1 30.0 37. 00 37.2

GT 6 100.0 37.50 37.2

TRANSITION REGION. CALCULATED VALUES

ENERGY CALCULATED / TEMPERATURE CALCULATED ENERGY

ABSORPTION TEMPERATURE (F) / (F ) ABSORPTI ON ( FT—LB

)

5.0 -115.8 / -110.0 5.4

10.0 -70. 1 / -105.0 5.8

15.0 -45.7 / -100.0 6.2

20.0 -26.7 / -95.0 6.7

25.0 -9.2 / -90.0 7.2

' 30.0 9.5 / -85. 0 7.3

35.0 36.4 / -80.0 8.5

/ -75.0 9.2

/ -70.0 10.0

/ -65.0 10.9

/ -60.0 1 1 .9

/ -55.0 12*9

/ -50. 0 14.0

/ -45.0 15.2

/ -40.0 16.4

/ -35.

0

17.7

/ -30.0 19.1

/ -25.0 20.5

/ -20 .

0

21.9

/ -15.0 23.3

Appendix A, Table A9

CHARPY I MP ACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR T Cl 28 STEEL PLATE G

• - CALCULATIONS FOR LATERAL EXPANSION DATA OF

8 SPECIMENS, LT ORIENTATION.

SPECIMEN TEMPERATURE (F ) OBSERVED LATERAL CALCULATED LATERAL

EXPANSION (MILS) EXPANSION (MILS)

GL13 -120.0 1 .50 2. 6

GL9 -100.0 • 00 4.6

GL12 -80.0 9.50 9. 0

GL 7 -40.0 27.00 29. 5

GL1 0 • 0 54.00 53.7

GL3 40.0 59. 00 58. 8

60 212.0 53.50 53. 3

70 212.0 59.00 58. 8

TRANSITION REGION, CALCULATED VALUES

LATERAL CALCULATED / TEMPERATURE CALCULATED LATERAL

EXPANS IQN( MILS) TEMPERAT URE ( F

)

/ (F ) EXPANSI 0N( M ILS)

5 • 0 -97.3 / -90.0 6.4

10.0 -76.8 / -85.0 7.6

15 • 0 -64.4 / -80.0 9.0

20 .0 -54.8 / -75.0 10.6

25.0 -46. 7 / -70.0 12.5

30.0 -39.2 / -65.0 14.7

35.0 -32.1 / -60.0 17.2

40.0 -25.0 / -55.0 19.9

45.0 -17.4 / -50.0 22.9

50.0 -8.6 / -45.0 26.1

55.0 3.8 / -40 .0 29.5

/ — 35 .0 33.0

/ -30.0 36.5

/ -25.0 40.0

/ -20.0 43.3

/ -15.0 46 • 5

/ -10.0 49.3

/ -5.0 ol.7

/ • 0 53.7

/ 5.0 55.3

Appendix A, Table A10

CH ARP Y IMPACT TEST RESULTS FOR HE AO PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE G

CALCULATIONS FOR LATERAL EXPANSION DATA OF

17 SPECIMENS. TL ORIENTATION.

SPEC IMEN TEMPERATURE ( F) OBSERVED LATERAL CALCULATED LATERAL

EXPANSION (MILS) EXPANSION (MILS)

GT27 -120.0 1.50 3.6

GT 25 -100.0 1 .50 5.3

GT32 -80.0 10.00 3. 1 GT33 -60.0 14.50 12.2

GT I -40 .

0

22.50 17.9

GT 1 a -40.0 21.00 1 7. 9

GT 26 -20.0 14.00 24. a GT 1 9 -20.0 28.00 24.3

GT3 1 • 0 26.00 32. 1 GT 1 5 • 0 28.50 32. 1 GT 28 • 0 20.50 32.1

GT 22 20.0 36.50 38.2

GT35 20.0 39.00 38. 2

GT 1 0 40.0 43.00 42. 1 GT34 60.0 44.50 43. 3

GT 1 1 30.0 45.00 44.3

GT 6 100.0 45.00 44.4

TRANSITION REGION. CALCULATED VALUES

LATERAL CALCULATED / TEMPERATURE CALCULATED LATERAL

EXPANS ION( MILS) TEMPER ATURE ( F

)

/ (F ) EXPANS I QN( M ILS)

5.0 -102.6 / -100.0 5.3

10.0 -69. 7 / -95.0 5.9

15.0 -49.5 / -90.0 6.5

20.0 -33.7 / -85.0 7.2

25.0 -19.5 / -80. 0 3.1

30.0 -5. 8 / -75.0 9.0

35.0 8.9 / -70.0 9.9

40.0 27.8 / -65.0 11.0

/ -60.0 12.2

/ -55.0 13.5

/ -50.0 14.9

/ -45.0 16.3

/ -40. 0 17.9

/ -35.0 19.5

/ -30.0 21 .3

/ -25.0 23.0

/ -20.0 24.3

/ -15.0 26.7

/ -10.0 28.5

- / -5.0 30.3

Appendix A, Table All

CHARPY IMPACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TC128 STEEL PLATE G

CALCULATIONS FOR SHEAR FRACTURE APPEARANCE DATA OF

Q SPECIMENS. LT ORIENTATION.

SPECIMEN TEMPERATURE (F) OBSERVED

FRACTURE

SHEAR

(%)

CALCULATED SHE Al FRACTURE (%>

GLI3 -120.0 . 00 . 3

GL9 -100.0 . O O 1.3

GL12 -80.0 5.00 4. 8

GL7 -40.0 33.0 0 35. 7

GLIO • 0 94.0 0 92.2

GL3 <* o • O 100.00 1 00. 0

60 212.0 100.00 100.0

70 212.0 100.00 1 00.0

TRANSITION REGION. CALCULATED VALUES

X SHEAR CALCULATED / TEMPERATURE CALCULATED

FRACTURE TEMPERATURE! F

)

/ ( F ) FRACTURE (%)

2.0 -93.9 / -90.0 2.6

5.0 -79.5 / -85.0 3.6

10.0 -67.3 / -80.0 4.3

15.0 -59.5 / -75.0 6 .5

50.0 -30.4 / -70.0 3.6

85.0 -7.3 / -65.0 1 1 .3

90.0 -2.5 / -60.0 14.6

95.0 4. 1 / -55.0 18.7

98.0 11.0 / -50.0 23.5

/ -45.0 29.2

/ -40.0 35.7

. - •

1 / -35.0 42.9

/ -30.0 50.7

/ -25.0 58.8

/ -20.0 66.9

/ -15.0 74.7

/ -10.

0

8 1.7

/ -5.0 87.6

/ .0 92.2

/ 5.0 95.5

Appendix A, Table A12

CHARPY I MP ACT TEST RESULTS FOR HEAD PLATE SPECIMENS

TAKEN FROM AAR TCI 28 STEEL PLATE G

CALCULATIONS FOR SHEAR FRACTURE APPEARANCE DATA OF

17 SPECIMENS, TL ORIENTATION,

SPECIMEN TEMPERATURE (F) OBSERVED SHEAR CALCULATED SHEAR

FRACTURE (%) FRACTURE ( % ) GT 27 -120.0 • o o 1.2

GT25 -100.0 • 00 3. 0

GT32 -80. 0 5.00 6. 7

GT 33 -60.0 .00 13. 9

GT 1 -40.0 • o o 26. 7

GT 1 3 -40.0 34.00 26. 7

GT 26 -20.0 23.00 46. 0

GT 1 9 -20.0 55.00 46.0

GT 3

1

• 0 43.00 69. 3

GT 1 5 • 0 58.00 69. 3

GT28 • 0 40.00 69. 3

GT22 20.0 100.00 88.

8

GT35 20.0 94.00 88. 3

GT 1 0 40.0 1 00.00 98. 1 GT 34 60.0 100.00 99.9

GT 1 1 80.0 100.00 100.0

GT 6 100.0 100.00 1 00. 0

TRANSITION REGION. CALCULATED VACUES

X SHEAR CALCULATED / TEMPERATURE CALCULATED SHEAR

FRACTURE TEMPERATURE IF) / (F ) FRACTURE ( %

)

2.0 - 109.3 / -100.0 3.0

5.0 -87.4 / -95.0 3.7

10.0 -6 9.3 / -90.0 4.5

15.0 -57.8 / -85.0 5.5

50 .0 -16.5 / -80.0 6.7

85.0 15.3 / -75.0 3. 1 90.0 21.7 / -70.0 9.7

95.0 30.5 / -65.0 11.7

98.0 39.7 / -60.0 13.9

/ -55.0 16.5

/ -50.0 19.5

/ -45.0 22.9

/ -40.0 26.7

/ -35.0 30.9

/ -30.0 35.6

/ -25. 0 40.6

/ -20.0 46 .0

/ -15.0 51 .7

/ -10.0 57.6

/ -5.0 63.5

NBS-114A (REV. 9-7*)

U.S. DEPT. OF COMM.

BIBLIOGRAPHIC DATA

SHEET

1. PUBLICATION OR REPORT NO.

NBSIR 80-2039

2.Gov't Accession No.

V\v.'' \

'

' -:V ” :

-

• -

3. Pectptenfs Accession No.

4. TITLE AND SUBTITLE

A METALLURGICAL EVALUATION OF TWO AAR Ml 28 STEEL TANK CAR

HEAD PLATES USED IN SWITCHYARD IMPACT TESTS, REPORT NO. 10

5. Publication Date

MAY 1980

6. Performing Organization Code

7. AUTHOR(S)

J. G. Early and C. G. Interrante

8. Performing Organ. Report No.

9. PERFORMING ORGANIZATION NAME AND ADDRESS

NATIONAL BUREAU OF STANDARDS

DEPARTMENT OF COMMERCE

WASHINGTON, DC 20234

10. Project/Tasi</Wort< Unit No.

11. Contract/Grant No.

12. SPONSORING ORGANIZATION NAME AND COMPLETE ADDRESS (Street, City, state, ZIP)

Federal Railroad Administration

Department of Transportation

Washington, D.C. 20234

13. Type of Report & Period Covered

14. Sponsoring Agency Code

15. SUPPLEMENTARY NOTES

|

I Document describes a computer program; SF-185, FIPS Software Summary, is attached.

16. ABSTRACT (A 200-word or less factual summary of most s i gni ficant information. If document includes a significant bibliography or

literature survey, mention it here.) T^e National Bureau of Standards was requested by the Federal

Railroad Administration to correlate the mechanical properties and metallurgical characteristics of two steel head plate samples taken from tank cars (GATX 93412 & UTLX

38498) subjected to switchyard impact tests. This metallurgical evaluation included

determining whether the samples conformed with the appropriate specifications and to

determine the impact test behavior of both plate samples. The results of check chemica

analyses and ambient-temperature tensile tests indicated that both plates met the

chemical, tensile strength, and tensile ductility requirements of AAR M128 steel. The

results of metallographic analyses of both plates revealed extensive banding with

alternate layers of ferrite and pearlite, typical of carbon-manganese steel in the

hot-rolled condition. The GATX sample also contained a microstructural anomaly near

the inside plate surface, possible related to prior thermo/mechanical processing of

the plate. The nil-ductility transition temperatures were determined to be -20 F and

-40 F for the GATX and UTLX plates, respectively, similar to the lowest values reported

for a group of tank car plate samples. The results of Charpy V-notch tests established

that the transition temperatures of these two plates are similar to one another, and

are among the lowest of those measured for all other tank car plates tested at NBS

.

The comparatively low impact transition temperatures for both plates are related to

the high manganese-to-carbon ratio and relatively fine ferrite grain size observed in

the microstructures.

17. KEY WORDS ("six to twelve entries; alphabetical order; capitalize only the first letter of the first key word unless a proper name;

separated by semicolons)

AAR M128 steel; Charpy V-notch; impact properties; head plates; nil-ductility

transition temperatures; railroad tank cars; switchyard impact tests; tensile

properties

.

18. AVAILABILITY Unlimited

For Official Distribution. Do Not Release to NTIS

Order From Sup. of Doc., U.S. Government Printing Office, Washington, DC

20402, SD Stock No. SN003-003-

Order From National Technical Information Service (NTIS), Springfield,

VA. 22161

19. SECURITY CLASS

(THIS REPORT)

UNCLASSIFIED

20. SECURITY CLASS

(THIS PAGE)

UNCLASSIFIED

21. NO. OF

PRINTED PAGES

22. Price

USCOMM'DC