# Improvement of Surface Properties of Inconel718 by HVOF Coating with WC-Metal Powder and by Laser Heat Treatment of the Coating

Authors: Hui Gon Chun; Tong Yul Cho; Jae Hong Yoon; Gun Hwan Lee
Journal: Advances in Materials Science and Engineering
 (2015)

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## Abstract

High-velocity oxygen-fuel (HVOF) thermal spray coating with WC-metal powder was carried out by using optimal coating process on an Inconel718 surface for improvement of the surface properties, friction, wear, and corrosion resistance. Binder metals such as Cr and Ni were completely melted and WC was decomposed partially to W2C and graphite during the high temperature (up to 3500°C) thermal spraying. The melted metals were bonded with WC and other carbides and were formed as WC-metal coating. The graphite and excessively sprayed oxygen formed carbon oxide gases, and these gases formed porous coating by evolution of the gases. The surface properties were improved by HVOF coating and were improved further by CO2 laser heat  treatment (LH). Wear resistance of In718 surface was improved by coating and LH at 25°C and an elevated temperature of 450°C, resulting in reduction of wear trace traces, and was further improved by LH of the coating in reducing wear depth. Corrosion resistance due to coating in sea water was improved by LH. HVOF coating of WC-metal powder on a metal surface and a LH of the coating were highly recommended for the improvement of In718 surface properties, the friction behavior, and wear resistance.


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## Body

## 1. Introduction

Traditionally, electrolytic hard chrome plating (EHC) has been widely used for hard surface coating for over 60 years [1–3]. Recently, EHC has raised health and environmental problems; Cr+3 known as carcinogen is emitted and is forbidden in many developed countries. High-velocity oxygen-fuel (HVOF) thermal spray coating has been investigated as one of the most promising candidates for the replacement of EHC [4–6]. HVOF coatings of WC cermets have been widely used to protect machine components from wear and corrosion, to restore worn components, and to improve the durability of components.In this work, micron-sized WC-metal powders were coated on In718 (substrate) by HVOF thermal spraying to improve the surface properties, wear resistance, and the durability of the metal components. For further improvement, the surface was irradiated with a CO2 laser (10.6 μm, continuous mode, 400 W) on an oval-shaped focal spot (5 mm × 4 mm) for 0.6 s at the scanning speed of 400 mm/min, heating from 950°C to 1200°C from the edge to the center of the spot without heating the whole substrate not to change any structure and properties of substrate. In this experiment, the following were investigated; optimal coating process (OCP) using Taguchi experimental program, laser heat treatment (LH), changes of phases, micro-structures, surface properties, friction, wear and corrosion of HVOF coating and LH coating.


## 2. Experiment

### 2.1. Preparation of Coating

The chemical composition of WC-metal powder (hard cermet WC, bonding metals as Ni and Cr) was coated on the super alloy In718 substrate in Table1 by using JK3500 HVOF thermal spraying equipment. The substrates were pre-cleaned in acetone for 5 minutes and then blast cleaned using 60-mesh aluminum oxides to improve adhesion onto In718 substrate. As shown in Table 2, OCP was obtained among the best surface properties of the 9 coatings prepared Taguchi experimental program for 3 levels of 4 spray parameters. Hydrogen flow rate as value was 53 FMR (FMR = 12 scfh = 9.44 × 10−5 m3/s), oxygen flow rate as 38 FMR, powder feed rate as 25 g/min, and spray distance as 18 cm. Argon gas of 120–180 psi was used as a powder carrier gas at feed rate of 25–35 g/min. The preparation of coatings was provided by OCP and heat-treated by CO2 laser.Table 1
Major chemical compositions of In718 and WC-metal powder.
Elements
W
C
Cr
Ni
Fe
Nb
Mo
Others
In718
0.08
17–20
50–55
11–22
5-6
2-3
Mn, Ti, Si
WC-metal
68
5
21
6Table 2
Coating processes prepared by Taguchi program and OCP of the highest surface hardness.
Process
OxygenFR
HydrogenFR
Feedrate
Spraydistance (in)
Hardness(Hv)
1
30
53
25
6
973
2
30
57
30
7
943
3
30
61
35
8
913
4
34
53
35
7
976
5
34
57
25
8
942
6
34
61
30
6
930
7
38
53
30
8
1033
8
38
57
35
6
960
9
38
61
25
7
998
OCP
38
53
25
7
1150
FR: flow rate (FMR = 12 scfh = 9.44× 10−5 m3/s), feed rate: g/min, and OCP: optimal coating process.


### 2.2. Preparation of LH Coating

A 5-kW TJ-HL-T 5000-type equipment was used for CO2 laser heat treatment. The laser beam (10.6 μm, continuous mode, a top-hat laser beam energy distribution in the focal spot) irradiated the substrate from the spot 18.5 mm above in an atmospheric environment. The laser beam with a focal spot of 5 mm × 4 mm (oval shape) moved along the beam direction of the 4 mm at velocity of 400 mm/min, resulting in a LH time of 0.6 s on the spot. Argon gas (10 MPa pressure and 5 L/min flow rate) was used for shrouding the LH region to prevent oxidation during the process.The laser power was turned off for 5 s at the end of each pass for a new starting position. The laser beam tracks were overlapped by 40% to each other. The optimal laser LH parameters were laser power of 400 W, scanning speed of 400 mm/min, average power density of 20 W/mm2, and laser irradiation of 0.6 s on spot. The samples were heat-treated in a furnace at 150°C for 2 hours before and after laser heat treatments. The temperature from edge to center of the laser spot was in the range from 950°C to 1200°C using a multiwavelength pyrometer.


### 2.3. Investigation of Surface Properties, Friction, Wear, and Corrosion in HVOF Coating and LH Coating

The microstructures of HVOF coating and the LH coating were investigated by using scanning electron microscope (SEM). The phase changes by HVOF powder coating and LH coating were investigated using X-ray diffraction (XRD). Surface hardness was measured by using a Micro Vickers hardness tester with a load of 200 g and a dwelling time of 10 s. Porosity was measured by analyzing the images of optical microscope.Friction and the wear behaviors were investigated by using a reciprocating slide tester (TE77 AUTO, Plint & Partners). The surfaces were slid by using SUS 304 balls (diameter 9.53 mm and hardness 227 Hv) without lubricants. Before the test, the surfaces were polished to Ra 1–1.4μm by using silicon carbide abrasive paper and DP-paste. The sliding distance, frequency, speed, load, and sliding time were 16 mm, 2.5 Hz, 0.161 m/s, 10 N, and 10 min, respectively. Sliding wear tests were carried out for the substrate, HVOF coating, and LH coating to study the friction and wear behaviors. Wear traces were investigated using SEM and EDS. The depth profiles of the wear traces were investigated using a surface profiler (Tencor P-11).The corrosion behavior of HVOF coating and LH coating was investigated in sea water (3.5 wt% NaCl solution).The sample was mounted in the electrochemical cell with an exposing area of 1.0 cm2 to the electrolyte. In the electrochemical test, saturated calomel electrode (SCE) and graphite were used as the reference and counter electrode, respectively.The electrochemical tests included the open-circuit potential (EOC) measurements and potentiodynamic polarization tests. The EOC was measured after 30 min immersion of the coating surface in 3.5 wt% NaCl solution for potential stabilization. The samples were potentiodynamically polarized (anodically) and the tests were performed at a scanning rate of 0.5 mV/s. At least, two sets of measurements were made per sample to ensure reproducibility of the results.


## 2.1. Preparation of Coating

The chemical composition of WC-metal powder (hard cermet WC, bonding metals as Ni and Cr) was coated on the super alloy In718 substrate in Table1 by using JK3500 HVOF thermal spraying equipment. The substrates were pre-cleaned in acetone for 5 minutes and then blast cleaned using 60-mesh aluminum oxides to improve adhesion onto In718 substrate. As shown in Table 2, OCP was obtained among the best surface properties of the 9 coatings prepared Taguchi experimental program for 3 levels of 4 spray parameters. Hydrogen flow rate as value was 53 FMR (FMR = 12 scfh = 9.44 × 10−5 m3/s), oxygen flow rate as 38 FMR, powder feed rate as 25 g/min, and spray distance as 18 cm. Argon gas of 120–180 psi was used as a powder carrier gas at feed rate of 25–35 g/min. The preparation of coatings was provided by OCP and heat-treated by CO2 laser.Table 1
Major chemical compositions of In718 and WC-metal powder.
Elements
W
C
Cr
Ni
Fe
Nb
Mo
Others
In718
0.08
17–20
50–55
11–22
5-6
2-3
Mn, Ti, Si
WC-metal
68
5
21
6Table 2
Coating processes prepared by Taguchi program and OCP of the highest surface hardness.
Process
OxygenFR
HydrogenFR
Feedrate
Spraydistance (in)
Hardness(Hv)
1
30
53
25
6
973
2
30
57
30
7
943
3
30
61
35
8
913
4
34
53
35
7
976
5
34
57
25
8
942
6
34
61
30
6
930
7
38
53
30
8
1033
8
38
57
35
6
960
9
38
61
25
7
998
OCP
38
53
25
7
1150
FR: flow rate (FMR = 12 scfh = 9.44× 10−5 m3/s), feed rate: g/min, and OCP: optimal coating process.


## 2.2. Preparation of LH Coating

A 5-kW TJ-HL-T 5000-type equipment was used for CO2 laser heat treatment. The laser beam (10.6 μm, continuous mode, a top-hat laser beam energy distribution in the focal spot) irradiated the substrate from the spot 18.5 mm above in an atmospheric environment. The laser beam with a focal spot of 5 mm × 4 mm (oval shape) moved along the beam direction of the 4 mm at velocity of 400 mm/min, resulting in a LH time of 0.6 s on the spot. Argon gas (10 MPa pressure and 5 L/min flow rate) was used for shrouding the LH region to prevent oxidation during the process.The laser power was turned off for 5 s at the end of each pass for a new starting position. The laser beam tracks were overlapped by 40% to each other. The optimal laser LH parameters were laser power of 400 W, scanning speed of 400 mm/min, average power density of 20 W/mm2, and laser irradiation of 0.6 s on spot. The samples were heat-treated in a furnace at 150°C for 2 hours before and after laser heat treatments. The temperature from edge to center of the laser spot was in the range from 950°C to 1200°C using a multiwavelength pyrometer.


## 2.3. Investigation of Surface Properties, Friction, Wear, and Corrosion in HVOF Coating and LH Coating

The microstructures of HVOF coating and the LH coating were investigated by using scanning electron microscope (SEM). The phase changes by HVOF powder coating and LH coating were investigated using X-ray diffraction (XRD). Surface hardness was measured by using a Micro Vickers hardness tester with a load of 200 g and a dwelling time of 10 s. Porosity was measured by analyzing the images of optical microscope.Friction and the wear behaviors were investigated by using a reciprocating slide tester (TE77 AUTO, Plint & Partners). The surfaces were slid by using SUS 304 balls (diameter 9.53 mm and hardness 227 Hv) without lubricants. Before the test, the surfaces were polished to Ra 1–1.4μm by using silicon carbide abrasive paper and DP-paste. The sliding distance, frequency, speed, load, and sliding time were 16 mm, 2.5 Hz, 0.161 m/s, 10 N, and 10 min, respectively. Sliding wear tests were carried out for the substrate, HVOF coating, and LH coating to study the friction and wear behaviors. Wear traces were investigated using SEM and EDS. The depth profiles of the wear traces were investigated using a surface profiler (Tencor P-11).The corrosion behavior of HVOF coating and LH coating was investigated in sea water (3.5 wt% NaCl solution).The sample was mounted in the electrochemical cell with an exposing area of 1.0 cm2 to the electrolyte. In the electrochemical test, saturated calomel electrode (SCE) and graphite were used as the reference and counter electrode, respectively.The electrochemical tests included the open-circuit potential (EOC) measurements and potentiodynamic polarization tests. The EOC was measured after 30 min immersion of the coating surface in 3.5 wt% NaCl solution for potential stabilization. The samples were potentiodynamically polarized (anodically) and the tests were performed at a scanning rate of 0.5 mV/s. At least, two sets of measurements were made per sample to ensure reproducibility of the results.


## 3. Results and Discussion

### 3.1. HVOF Coating and LH Coating

Inhomogeneous WC pieces were imbedded in binder metals such as Ni, Cr, Ni-Cr alloy, and WC powders [3, 6, 7]. During the flight of 0.02 s in the HVOF spraying, its velocity and temperature of the flame were reached up to 1000 m/s and 3500°C. The binder metals and some metal carbide were melted, and the metal carbides were decomposed into metals and free carbon. Small portion of WC was found in forms of crystalline compounds such as W2C [7, 8]. The melts or partially molten splats were impacted on the In718 surface, forming bonds with the surface and subsequently building the porous coating as seen in Figure 1. Although the powder consisted of crystalline carbides such as WC, Cr7C3, and metastable Ni3C, the coating showed that only crystalline WC and a new phase W2C were observed in Figure 2.Figure 1
(a) Porous coating and interface between coating and substrate; (b) interface compacted by laser heating.
(a)
(b)Figure 2
Crystalline phases of powder, coating, and LH coating.
(a)
(b)However, the other forms of crystalline carbides disappeared due to the decomposition during heating and rapid cooling processes. According to the phase diagram, WC is decomposed to W2C and free carbon above its decomposition temperature of 1250°C [9, 10]. The free carbon and excessively sprayed reagent oxygen formed carbon oxide gases, producing pores and voids inside the porous coating as shown in Table 3 and Figure 1.Table 3
Improvement of surface properties by coating and LH coating.
Surface
In718
Coating
LH coating
Surface hardness (Hv)
400 ± 10
980 ± 100
1430 ± 90
Porosity (%)
0.00
2.5 ± 0.5
0.35 ± 0.05
Friction coefficient
0.45 ± 0.08
0.32 ± 0.02
0.20 ± 0.03During laser heat treatment of the HVOF coating for 0.6 s, the temperature of the irradiated focal area was in the range from 950°C to 1200°C; the porous coating and porous strips at the interface were compacted as seen in Figure1 and Table 3. The crystalline metal carbides such as Ni3C and Cr3C2 phases were formed due to the longer heating time (~0.6 s) and proper heating temperature (950°C to 1200°C). This can be compared with spray coating time of about 0.02 s and temperature of up to 3500°C.


### 3.2. Improvement of Surface Properties by HVOF Coating and LH Coating

As seen in Table3 and Figure 3, the surface hardness and friction coefficient were improved by HVOF coating and LH coating for 0.6 s. These properties of HVOF coating and LH coating were better than the traditional electrolytic hard chrome plating (EHC) as seen in Table 3 according to Fang et al.’s report [6]. The friction coefficient of the coating showed lower value than that of EHC (0.52
±
0.07 Hv), and surface hardness of HVOF coating showed higher value than that of EHC (950
±
50 Hv). The porous coating was formed by HVOF coating due to formation of carbon oxide gases by the reaction of free carbon (produced by the thermal decompositions of WC and metal carbides) with excessively sprayed oxygen as shown in Table 2. With laser heating, the porosity decreased drastically and HVOF coating was compacted as seen in Table 3 and Figure 1.Figure 3
Depth profiles of surface hardness of coating and LH coating.The surface hardness of In718 (400
±
10 Hv) increased more than twice to 980
±
100 Hv due the coating; it was increased 46% to 1430
±
90 Hv by laser heating for 0.6 s. The porosity of In718 surface (0%) was increased to 2.5
±
0.5% by HVOF coating due to formation of carbon oxide gases inside the coating; it was reduced to 0.35
±
0.05% (to 14%) by laser heating. As seen in Figure 1, laser heating could reduce their porosity by compacting of the coating and the interface of coating/substrate In718. The friction coefficient of In718 was reduced by 30% from 0.45
±
0.08 to 0.32
±
0.02 by coating and 10% to 0.20
±
0.03 by laser heating. One of the reasons could be the lubrication by the free carbon formed by the decomposition of WC and metal carbides during the spraying and the metal-oxide debris worn during sliding test.


### 3.3. Improvement of Surface Wear Resistance by HVOF Coating and by LH Coating

A reciprocating slide test was carried out for the investigation of wear resistance and temperature dependence of wear resistance of In718, coating, and LH coating. As seen in Figures4~6, the wear resistance was improved by HVOF coating and followed by LH coating, since the surface hardness increased by coating, followed by LH coating in Section 3.2. The temperature dependence of wear resistance of the coating was better than that of In718 which showed a narrower wear trace and shallower wear depth at 25°C and 450°C in Figures 4 and 5. With surface temperature increase from 25°C to 450°C the wear width and depth increased at In718 and the coating. This showed that the wear resistances decreased with surface temperature increase at In718 and the coating because thermal effect softens the surface and there was wear debris of metal oxides and free carbon decomposed by thermal effect functioning as solid and liquid lubricants. The lubricating effect was higher at higher temperature. As seen in Figure 6, the wear resistance of the coating increased by laser heating, showing a decrease of wear depth from 5000 nm to 2000 nm due to the increase of surface hardness by laser heating as discussed in Section 3.2.Figure 4
Wear traces of (a) coating and (b) In718 at both 25°C and 450°C.
(a)
(b)Figure 5
Wear depth profiles; (a) coating and (b) In718 at both 25°C and 450°C.
(a)
(b)Figure 6
Wear depth profiles of coating and LH coating at room temperature.


### 3.4. Improvement of Corrosion Resistance by Coating and by LH Coating

Corrosion behaviors of In718, HVOF coating, and LH coating in 3.5% NaCl solution (sea water) were investigated. As previously reported by S. Y. Park and C. G. Park [4], corrosion resistance of In718 surface was improved by HVOF coating of WC-metal powder in 3.5% NaCl solution and 1 M HCl acid, but it decreased in 1 M NaOH base solution. In718 with 100% metals was more corrosive (chemically active) than the coating (WC-metal) with more than 50% inactive cermet of WC. As shown in Figures 7 and 8, the corrosion resistance of coating in 3.5% NaCl solution was improved by laser heating. As seen in Figure 7, corrosion potential decreased and then stayed steady with corrosion time; this suggested the corrosion films on both coating and LH coating were not passive films and did not protect the inner materials of the coating.Figure 7
Corrosion potential and time of coating and LH coating in sea water (3.5% NaCl).Figure 8
Potentiodynamic polarization of coating and LH coating in sea water (3.5% NaCl).The LH coating with lower porosity (dense coating) had higher corrosion potential than the coating. Therefore the LH coating had more corrosion resistance than the coating. As seen in Figure8, LH coating had a smaller corrosion current density and higher breakdown potential (pitting potential or corroded film breakdown potential), showing LH coating was a better corrosion resistance. The corrosion current density increased rapidly with a small increase of applied potential and there was no significant passive region for both the coating and LH coating. This showed that no protective corrosion films were formed at both coating and LH coating. The very active chlorine ions strongly reacted with the surface atoms but did not form protective passive films on the surface [11].


## 3.1. HVOF Coating and LH Coating

Inhomogeneous WC pieces were imbedded in binder metals such as Ni, Cr, Ni-Cr alloy, and WC powders [3, 6, 7]. During the flight of 0.02 s in the HVOF spraying, its velocity and temperature of the flame were reached up to 1000 m/s and 3500°C. The binder metals and some metal carbide were melted, and the metal carbides were decomposed into metals and free carbon. Small portion of WC was found in forms of crystalline compounds such as W2C [7, 8]. The melts or partially molten splats were impacted on the In718 surface, forming bonds with the surface and subsequently building the porous coating as seen in Figure 1. Although the powder consisted of crystalline carbides such as WC, Cr7C3, and metastable Ni3C, the coating showed that only crystalline WC and a new phase W2C were observed in Figure 2.Figure 1
(a) Porous coating and interface between coating and substrate; (b) interface compacted by laser heating.
(a)
(b)Figure 2
Crystalline phases of powder, coating, and LH coating.
(a)
(b)However, the other forms of crystalline carbides disappeared due to the decomposition during heating and rapid cooling processes. According to the phase diagram, WC is decomposed to W2C and free carbon above its decomposition temperature of 1250°C [9, 10]. The free carbon and excessively sprayed reagent oxygen formed carbon oxide gases, producing pores and voids inside the porous coating as shown in Table 3 and Figure 1.Table 3
Improvement of surface properties by coating and LH coating.
Surface
In718
Coating
LH coating
Surface hardness (Hv)
400 ± 10
980 ± 100
1430 ± 90
Porosity (%)
0.00
2.5 ± 0.5
0.35 ± 0.05
Friction coefficient
0.45 ± 0.08
0.32 ± 0.02
0.20 ± 0.03During laser heat treatment of the HVOF coating for 0.6 s, the temperature of the irradiated focal area was in the range from 950°C to 1200°C; the porous coating and porous strips at the interface were compacted as seen in Figure1 and Table 3. The crystalline metal carbides such as Ni3C and Cr3C2 phases were formed due to the longer heating time (~0.6 s) and proper heating temperature (950°C to 1200°C). This can be compared with spray coating time of about 0.02 s and temperature of up to 3500°C.


## 3.2. Improvement of Surface Properties by HVOF Coating and LH Coating

As seen in Table3 and Figure 3, the surface hardness and friction coefficient were improved by HVOF coating and LH coating for 0.6 s. These properties of HVOF coating and LH coating were better than the traditional electrolytic hard chrome plating (EHC) as seen in Table 3 according to Fang et al.’s report [6]. The friction coefficient of the coating showed lower value than that of EHC (0.52
±
0.07 Hv), and surface hardness of HVOF coating showed higher value than that of EHC (950
±
50 Hv). The porous coating was formed by HVOF coating due to formation of carbon oxide gases by the reaction of free carbon (produced by the thermal decompositions of WC and metal carbides) with excessively sprayed oxygen as shown in Table 2. With laser heating, the porosity decreased drastically and HVOF coating was compacted as seen in Table 3 and Figure 1.Figure 3
Depth profiles of surface hardness of coating and LH coating.The surface hardness of In718 (400
±
10 Hv) increased more than twice to 980
±
100 Hv due the coating; it was increased 46% to 1430
±
90 Hv by laser heating for 0.6 s. The porosity of In718 surface (0%) was increased to 2.5
±
0.5% by HVOF coating due to formation of carbon oxide gases inside the coating; it was reduced to 0.35
±
0.05% (to 14%) by laser heating. As seen in Figure 1, laser heating could reduce their porosity by compacting of the coating and the interface of coating/substrate In718. The friction coefficient of In718 was reduced by 30% from 0.45
±
0.08 to 0.32
±
0.02 by coating and 10% to 0.20
±
0.03 by laser heating. One of the reasons could be the lubrication by the free carbon formed by the decomposition of WC and metal carbides during the spraying and the metal-oxide debris worn during sliding test.


## 3.3. Improvement of Surface Wear Resistance by HVOF Coating and by LH Coating

A reciprocating slide test was carried out for the investigation of wear resistance and temperature dependence of wear resistance of In718, coating, and LH coating. As seen in Figures4~6, the wear resistance was improved by HVOF coating and followed by LH coating, since the surface hardness increased by coating, followed by LH coating in Section 3.2. The temperature dependence of wear resistance of the coating was better than that of In718 which showed a narrower wear trace and shallower wear depth at 25°C and 450°C in Figures 4 and 5. With surface temperature increase from 25°C to 450°C the wear width and depth increased at In718 and the coating. This showed that the wear resistances decreased with surface temperature increase at In718 and the coating because thermal effect softens the surface and there was wear debris of metal oxides and free carbon decomposed by thermal effect functioning as solid and liquid lubricants. The lubricating effect was higher at higher temperature. As seen in Figure 6, the wear resistance of the coating increased by laser heating, showing a decrease of wear depth from 5000 nm to 2000 nm due to the increase of surface hardness by laser heating as discussed in Section 3.2.Figure 4
Wear traces of (a) coating and (b) In718 at both 25°C and 450°C.
(a)
(b)Figure 5
Wear depth profiles; (a) coating and (b) In718 at both 25°C and 450°C.
(a)
(b)Figure 6
Wear depth profiles of coating and LH coating at room temperature.


## 3.4. Improvement of Corrosion Resistance by Coating and by LH Coating

Corrosion behaviors of In718, HVOF coating, and LH coating in 3.5% NaCl solution (sea water) were investigated. As previously reported by S. Y. Park and C. G. Park [4], corrosion resistance of In718 surface was improved by HVOF coating of WC-metal powder in 3.5% NaCl solution and 1 M HCl acid, but it decreased in 1 M NaOH base solution. In718 with 100% metals was more corrosive (chemically active) than the coating (WC-metal) with more than 50% inactive cermet of WC. As shown in Figures 7 and 8, the corrosion resistance of coating in 3.5% NaCl solution was improved by laser heating. As seen in Figure 7, corrosion potential decreased and then stayed steady with corrosion time; this suggested the corrosion films on both coating and LH coating were not passive films and did not protect the inner materials of the coating.Figure 7
Corrosion potential and time of coating and LH coating in sea water (3.5% NaCl).Figure 8
Potentiodynamic polarization of coating and LH coating in sea water (3.5% NaCl).The LH coating with lower porosity (dense coating) had higher corrosion potential than the coating. Therefore the LH coating had more corrosion resistance than the coating. As seen in Figure8, LH coating had a smaller corrosion current density and higher breakdown potential (pitting potential or corroded film breakdown potential), showing LH coating was a better corrosion resistance. The corrosion current density increased rapidly with a small increase of applied potential and there was no significant passive region for both the coating and LH coating. This showed that no protective corrosion films were formed at both coating and LH coating. The very active chlorine ions strongly reacted with the surface atoms but did not form protective passive films on the surface [11].


## 4. Conclusions

The following conclusions were derived from the investigation of improvement of surface properties of In718 by HVOF coating of WC-metal powder and by laser heating of the coating.(1)
Metal carbides and WC decomposed during the HVOF coating, forming less hard W2C phase and free carbon.
(2)
Porous coating was formed by HVOF coating, but it was compacted from2.5
±
0.5% to 0.35
±
0.05% (to 14%) by the laser heating.
(3)
The surface hardness of In718 surface improved from400
±
10 Hv to 980
±
100 Hv by the coating; it was further increased to 1430
±
9
0 Hv by laser heating.
(4)
Friction coefficient of In718 reduced from0.45
±
0.08 to 0.32
±
0.02 by the coating and to 0.20
±
0.03 by the laser heating.
(5)
Wear resistance of In718 surface was improved by the coating and further improved by LH coating. And these resistances were decreased with increasing surface temperature in the temperature range from 25°C to 450°C.
(6)
Corrosion resistance improved by HVOF coating, followed by LH coating.
(7)
For the improvement of surface properties and durability of materials, HVOF coating of WC-metal powder on the surface and laser heat-treated coating were strongly recommended.



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*Source: 468120-2015-07-16.xml*