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Article

Post-Processing of Cold Sprayed CoNiCrAlY Coatings on Inconel 718 by Rapid Induction Heating

by
Yongjing Yang
1,2,
Aprilia Aprilia
2,
Kaiqiang Wu
1,2,
Sung Chyn Tan
3 and
Wei Zhou
1,2,*
1
School of Mechanical and Aerospace Engineering, Nanyang Technological University, 50 Nanyang Avenue, Singapore 639798, Singapore
2
Rolls-Royce@NTU Corporate Laboratory, Nanyang Technological University, 65 Nanyang Drive, Singapore 637460, Singapore
3
Rolls-Royce Singapore Pte. Ltd., 1 Seletar Aerospace Crescent, Singapore 797575, Singapore
*
Author to whom correspondence should be addressed.
Metals 2022, 12(3), 396; https://doi.org/10.3390/met12030396
Submission received: 29 January 2022 / Revised: 14 February 2022 / Accepted: 22 February 2022 / Published: 24 February 2022
(This article belongs to the Special Issue Advances in Welding, Joining and Surface Coating Technology)
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Versions Notes

Abstract

:
Cold spray is a solid-state additive manufacturing process that has been increasingly used for restoration of damaged parts. Due to the nature of powder solid-state bonding, cold spray coatings usually possess pores in the microstructures. Heat treatment has been widely used as a post-processing method to reduce the porosity of cold sprayed coatings. However, it usually requires the whole component to be treated in the furnace and typically takes a few hours to finish the treatment. This study aims to develop a localized and rapid post-processing method for cold sprayed coatings. Multi-layer cold sprayed coatings of CoNiCrAlY on an Inconel 718 substrate were produced. Then the coatings were heat treated at 800 °C, 900 °C, 1000 °C and 1100 °C by rapid induction heating. The porosity level of the coatings reduced significantly after induction heating for a short period of merely 10 min. This is attributed to the preferential Joule heating at pore regions, which results in pore closures within the coatings. The potential application of induction heating as a rapid post-processing method for cold spray coatings has been demonstrated in this work.

1. Introduction

Cold spray is an effective solid-state additive manufacturing technique. During the cold spray process, the preheated feedstock particles are accelerated to supersonic speed to hit the substrate, and then the particles would bond on the substrate with a fine microstructure through severe plastic deformation to form the coating [1,2]. Since the temperature is below the melting temperatures of the materials during the cold spray process, cold sprayed coatings usually contain less oxidation and less thermally induced distortion than the thermal sprayed coatings. Due to the advantages of the cold spray technique, it has been increasingly applied to repair damaged aerospace components.
Inconel 718 is a nickel-based superalloy that has been extensively used to make aerospace components such as gas turbine blades due to its excellent mechanical performance [3]. To provide more reliable performance and durability of the nickel-based superalloy at high temperatures, an appropriate coating is usually required to avoid the component damage. MCrAlY (where M = Ni, Co, or both) alloy has been widely used in thermal barrier coatings (TBCs) as the bond coat layer to provide corrosion and oxidation protection for nickel-based superalloys in harsh environments [4].
There has been considerable research on the preparation of MCrAlY coating by thermal spray [5,6,7,8,9,10,11,12,13]. Scrivani et al. [6] reported that the quality of MCrAlY coatings prepared by vacuum plasma spray is better than that prepared by high velocity oxygen fuel or axial plasma spray.
In the recent decade, some research has been carried out to study cold sprayed MCrAlY coatings [14,15,16,17,18]. For instance, Li et al. [14] reported that such coatings present a better thermal fatigue resistance than that of the low-pressure plasma sprayed coatings. Khanna et al. [15] found that the cold sprayed CoNiCrAlY coatings exhibit considerable improvement in wear and oxidation resistance compared with the high velocity oxy fuel coatings.
Although the cold sprayed coatings present desirable properties, the inter-particle bonding is usually limited in the as-sprayed condition, because the atomic diffusion is relatively restricted at low temperatures during the cold spray process [19]. The quality and performance of the coatings are affected by the poor inter-particle bonding and the porosity in the coatings [20]. Therefore, post-process treatment is sometimes carried out to improve the quality of the as-deposited coatings.
Maharjan et al. [21] reported that both deep cold rolling and controlled hammer peening are effective in reducing porosity and enhancing the bonding strength of cold spayed Ti-6Al-4V coatings. This method has the advantage of being a localized processing technique. However, the mechanical peening process may result in a higher surface roughness and the minimum achievable porosity level is relatively high at 2.67%.
Heat treatment is the most widely used method for post-processing of cold sprayed coatings. Boruah and Zhang [22] reported that the interfacial bonding strength of cold sprayed Ti-6Al-4V coating on Ti-6Al-4V substrate increased remarkably after 1 h of solution treatment at 940 °C followed by 8 h of aging at 480 °C, but it should be noted that the whole post heat treatment process is very long. The effect of post heat treatment at 350 °C for 4 h on cold sprayed A380 composites was revealed by Qiu et al. [23]. After the long period of heat treatment, the plasticity of the sample enhanced significantly, but the porosity increased slightly. Ren et al. [24] reported that the porosity only decreased slightly after heat treatment at 850 °C for 4 h in the cold sprayed Ti samples, while the majority of the large pores remained unaffected, except for a shape change. According to Huang et al. [25], the porosity of cold sprayed Ti coatings decreased by about half after heat treatment at 1000 °C for 4 h, but the porosity level was still high at ~7.6%. Al-Mangour et al. [26] studied the effect of heat treatment temperatures from 400 °C to 1100 °C on cold sprayed 316L stainless steel and found that the largest porosity reduction occurred at the highest heat treatment temperature of 1100 °C for 1 h. Generally, heat treatment at high temperatures is found to improve the quality of cold sprayed coatings; however, it usually requires the whole component to be put in the furnace chamber and usually takes a few hours to finish the whole process due to the low heating rate.
Chen et al. [27] studied the effect of hot isostatic pressing (HIP) on the porosity and mechanical properties of cold sprayed Ti-6Al-4V alloy. After HIP at 920 °C and 120 MPa for 2 h, the porosity in the sample was reduced to a negligible level of 0.037%. Nevertheless, HIP also takes a long processing time (typically a few hours), and it also requires the whole component to be put into the chamber for heating and pressing, and it is a much more expensive post-processing method than conventional heat treatment.
For aerospace repair, the prolonged heating of the whole component during the conventional post heat treatment or HIP leads to very low productivity and could have an adverse effect on the base metal. Therefore, a localized and rapid heat treatment method would be desirable. Induction heating is a non-contact rapid heating process by locally induced eddy currents. A previous study revealed that the localized repair of Inconel 718 can be achieved by induction heating within a very short period of 2 min [28]. However, there is little information about the effect of induction heating on the cold sprayed coatings.
The objective of the current research was to develop an effective localized and rapid post-processing method for pore closure of cold sprayed coatings via induction heating. In this study, cold sprayed CoNiCrAlY coatings on an Inconel 718 substrate were induction heat treated at different temperatures for the same soaking time, and then the microstructures were characterized.

2. Materials and Methods

2.1. Materials

Gas-atomized Diamalloy 4700 CoNiCrAlY powder purchased from Oerlikon Metco (Pfäffikon, Switzerland) was used as feedstock in the cold spray process. The powder morphology and size distribution are shown in Figure 1. Inconel 718 (Haynes International, Kokomo, IN, USA) with 8 mm thickness was used as the substrate. The substrate was ground and cleaned in ethanol prior to the cold spray process. The chemical composition of the materials is shown in Table 1.

2.2. Cold Spray

Cold spray deposition was performed using a high-pressure system (Impact Innovations GmbH, Rattenkirchen, Germany) through a SiC nozzle with an exit diameter of 6 mm. The feed rate of the CoNiCrAlY powder was about 45 g/min. Pure nitrogen was used as the propellant gas at a temperature of 1000 °C and a pressure of about 4.5 MPa. The temperature and pressure used were close to the capacity of the cold spray system in order to gain a high particle velocity [2,29]. The average particle velocity was 746 m/s, which was calculated from 600 particles measured by a cold spray meter (CSM EVOLUTION, Tecnar Automation Inc., Saint-Bruno-de-Montarville, QC, Canada).
During the deposition, the traverse speed of the spray gun was 500 mm/s, the step size of each spray pass was 1 mm, and the stand-off distance was 30 mm. The coating consisted of 10 layers with a total coating thickness of about 850 μm.

2.3. Induction Heating

After the cold spray deposition, the samples were heat treated via induction heating equipment (GH Induction Atmospheres, Rochester, NY, USA). This equipment uses a high-frequency power supply with the frequency set at 107 kHz. It is equipped with a bell jar system which allows the samples to be heated in a vacuum environment. The vacuum environment prevents surface oxidation during the heating process. The bell jar’s vacuum pressure was set to about 5 × 10−4 torr before induction heating was carried out.
For each induction heating process, the samples were positioned with the coating sides facing an induction coil of 30 mm in diameter. The stand-off distance was fixed at 5 mm. The experimental setup is shown in Figure 2. The samples were heated and held at target temperatures of 800 °C, 900 °C, 1000 °C and 1100 °C respectively for the same period of 10 min. The temperatures selected were all within the heat treatment temperature range commonly used for CoNiCrAlY coatings [11,30,31].
After the time was up, the samples were cooled inside the bell jar in its vacuum environment for 5 min and then in an argon environment for another 5 min before they were taken out of the bell jar to the open air.

2.4. Microstructural Characterization

Prior to microstructural observation, the samples were mounted, ground, and polished to mirror-like finish. The microstructures were observed using an LEXT OLS4000 laser confocal microscope (Olympus, Tokyo, Japan) and a JEOL-7600 scanning electron microscope (JEOL, Tokyo, Japan). The porosity percentages were measured using ImageJ software (NIH, Bethesda, MD, USA), with ten optical micrographs collected for each sample using the 20× objective lens of the LEXT OLS4000 microscope. The average values and standard deviations were then calculated from the ten measured data.
Electron backscattered diffraction (EBSD, Oxford Instruments, Abingdon, UK) was conducted using a step size of 0.2 μm at an accelerating voltage of 20 kV, and then the analysis was performed with Channel 5 (Oxford Instruments, Abingdon, UK) software.
Microhardness measurements were carried out on the cross-sections using a Future-Tech FM-300e Vickers microhardness indenter (Future-Tech, Kawasaki, Japan). An indenter load of 200 gf and dwell duration of 10 s were used. Ten microhardness data were collected for each location of interest to get the average microhardness and standard deviation.

3. Results and Discussion

Figure 3 shows the cross-section microstructures of the cold sprayed CoNiCrAlY coatings and the porosity percentage before and after induction heating. As shown in Figure 3a, the pores were uniformly distributed in the as-sprayed coating, and the porosity percentage of the as-sprayed coating was measured to be 3.1%. After induction heating at 800 °C, the porosity percentage was found to be reduced to 2.1%. For induction heating at 900 °C, the porosity percentage was further reduced to 1.6%, which was almost half of the porosity in the as-sprayed coating. Further increasing the temperature to 1000 °C led to even further reduction of the porosity percentage to 0.7%.
It can be observed that the porosity level of the coatings decreased with the increase in the induction heating temperature. The most significant reduction of the porosity occurred in the induction-heated sample at the highest temperature of 1100 °C, where the porosity was reduced to 0.3%, which is about one tenth of the as-sprayed sample’s porosity. Saeidi et al. [30] reported that the porosity reduced in the CoNiCrAlY coating due to a sintering effect after being heat treated at 1100 °C for 3 h in a vacuum. It should be noted that the time used in this work was only 10 min, which is significantly shorter than that in the previous work using the same heat treatment temperature.
In our previous study, the porosity percentage of the cold sprayed coatings was below 0.2% and did not show significant difference after induction heating from 800 °C to 1100 °C [32]. This could be attributed to the low magnification of the images used for porosity measurement (4× objective lens only). When an image with low magnification was chosen, the small pores could not be resolved or identified clearly. Therefore, the porosity percentage was much lower in the previous study. To improve the accuracy of the porosity measurement, more optical micrographs with a higher magnification (20× objective lens) were used in the current study.
Another important engineering issue for coatings is their bonding with the substrate. Some voids were observed at the coating–substrate interface in the as-sprayed coating and after induction heating at 800 °C, as shown in Figure 3a,b. Such features indicate low interfacial bonding strength. As shown in Figure 3c–e, after induction heating at or above 900 °C, no obvious unbonded regions were observed at the interface. The elimination of the voids at the interface could be attributed to the improved diffusion of the constituent elements between the coating and the substrate at higher induction heating temperatures.
Figure 4 shows the top surface morphologies of the cold sprayed samples before and after induction heating. The relatively big gap was observed in the as-sprayed sample (as indicated by the red ellipses in Figure 4a), indicating poor bonding between the particles. In the as-sprayed sample, the bonding of the particles was formed through plastic deformation. Due to the low atomic diffusion rate in the solid state, the bonding of the particles is usually weak. After induction heating, because of the enhanced diffusion effect by the eddy current and Joule heating, the bonding of the particles improved, as marked by the yellow ellipses in Figure 4b,c.
To further reveal the effect of the induction heating temperature on the microstructure of the cold sprayed coatings, backscattered electron SEM images are presented in Figure 5. Figure 5a shows large pores at the particle boundary regions in the as-sprayed coating. These pores were caused by the poor inter-particle bonding, as can be clearly seen in the higher magnification image in Figure 5b. As shown in Figure 5c,d, after induction heating at 800 °C, some inter-particle pores were still observed, although the pores became smaller compared with those in the as-sprayed sample. After induction heating at 900 °C and above, the particle boundaries in the coatings became indistinguishable. An almost pore-free microstructure was achieved at an induction heating temperature of 1100 °C, and no gap between the particles was observed, as shown in Figure 5i,j.
Figure 6 presents the EBSD results of the cold sprayed coatings after induction heating at different temperatures. As shown in Figure 6a, large unindexed black areas were observed in the inverse pole figure (IPF) map after induction heating at 800 °C. This could be attributed to the following two factors. First, the EBSD scan step size used was 0.2 μm, so grains smaller than this size could not be indexed. Second, due to the severe plastic deformation in the cold spray process, high strain would occur in the coatings, thus lowering the index rate [29,33] if the strain was not fully relieved at the lowest treatment temperature. With the increase of induction heating temperature, the degree of strain relief increases [34], and the grains grow in size. Therefore, a much higher index rate was achieved, as shown in Figure 6b–d. The grain size of the cold sprayed coatings after induction heating is shown in Figure 6e.
Induction heating is a non-contact method to heat the sample rapidly by the eddy current. The pores have almost infinite electrical resistivity, so the eddy current cannot go through them in the cold sprayed coatings. This would cause the current to detour and crowd around the pores as shown in Figure 7a. This would lead to the preferential Joule heating around these regions (Figure 7b), resulting in closure of the pores (Figure 7c). This mechanism is similar to the mechanism of crack healing by electropulsing [35].
The microhardness results of the coatings before and after induction heating are shown in Figure 8. The microhardness of the as-sprayed CoNiCrAlY coatings was measured to be 519 ± 21 HV. After induction heating at the lowest temperature of 800 °C, a similar microhardness (528 ± 26 HV) was obtained. A reduction in the porosity level (Figure 3f) is usually expected to increase the microhardness. However, the strain relief effect tends to reduce the microhardness. As a result, the microhardness value remained similar.
For the coatings which were induction heated at the higher temperatures of 900 °C, 1000 °C and 1100 °C, decreases in the microhardness were observed (Figure 8). This can be attributed to the grain growth and strain relief with the increase in the processing temperature, as indicated by the EBSD results in Figure 6. It is clear to see from the figure that the grains of the α-phase were coarsened (from 0.7 μm for 800 °C to 1.56 μm for 1100 °C) with the increase of the processing temperature. In the meantime, the grain size of the β-phase increased from 0.56 μm for 800 °C to 0.94 μm for 1100 °C. The increase in grain size seemed to be small, but the increase was in fact significant since it was an increase of 122.9% for the α-phase and 67.9% for the β-phase. Such an increment in grain size can result in a noticeable reduction in yield strength [36] and thus a reduction in hardness. The decrease in the microhardness of the CoNiCrAlY coatings after high temperature (900 °C to 1100 °C) heat treatment was also reported by Bardi et al. [8] and Picas et al. [31].
Further microhardness measurements at different locations of the coatings were also carried out. The microhardness of the coatings at the locations of 250 μm, 500 μm and 750 μm from the coating–substrate interface was measured. The results are shown in Figure 9. No significant variation of the microhardness was observed with the different locations in the coatings, indicating the quality of the coating is almost homogeneous.

4. Conclusions

In this study, CoNiCrAlY coatings were deposited on an Inconel 718 substrate using a high-pressure cold spray system and then post-processed by induction heating. The microstructures and microhardness were carefully characterized. The main conclusions are as follows:
(1)
A localized and rapid post-processing method for cold sprayed coatings was developed through the use of a bell jar for creating a local vacuum and the use of induction for rapid heating.
(2)
After the cold sprayed coatings were processed at 800 °C, 900 °C, 1000 °C and 1100 °C for a short period of merely 10 min, the porosity level was found to reduce significantly. With the increase of temperature, the porosity was reduced and the inter-particle bonding was enhanced to achieve the microstructural improvement. At the highest temperature of 1100 °C, the coatings contained only 0.3% porosity, which was about one tenth of the porosity in the as-sprayed coatings.
(3)
During induction heating, preferential Joule heating occurs around the pores due to current crowding and detouring, resulting in closure of the pores.
(4)
The microhardness of the CoNiCrAlY coatings reduced after induction heating at 900 °C and higher temperatures, and this is attributed to the grain growth and strain relief.

Author Contributions

Conceptualization, W.Z. and Y.Y.; methodology, W.Z.; validation, Y.Y., A.A. and S.C.T.; formal analysis and investigation, Y.Y., A.A. and K.W.; data curation, Y.Y. and A.A.; writing—original draft preparation, Y.Y.; writing—review and editing, W.Z., Y.Y., A.A., K.W. and S.C.T.; visualization, Y.Y. and A.A.; supervision, W.Z.; project administration, W.Z.; funding acquisition, W.Z. and S.C.T. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the National Research Foundation of Singapore, Rolls-Royce Singapore Pte. Ltd., and Nanyang Technological University through grants #002123-00002 and #002124-00002.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Not applicable.

Acknowledgments

This study was supported under the RIE2020 Industry Alignment Fund—Industry Collaboration Projects (IAF-ICP) Funding Initiative, as well as cash and in-kind contributions from Rolls-Royce Singapore Pte. Ltd.

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. SEM micrographs of CoNiCrAlY powder feedstock showing (a) surface morphology and (b) cross-section microstructure. (c) Size distribution of CoNiCrAlY particles.
Figure 1. SEM micrographs of CoNiCrAlY powder feedstock showing (a) surface morphology and (b) cross-section microstructure. (c) Size distribution of CoNiCrAlY particles.
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Figure 2. Experimental setup of induction heating of the cold sprayed samples.
Figure 2. Experimental setup of induction heating of the cold sprayed samples.
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Figure 3. Optical microscope observation of the cross-sections of the cold sprayed samples: (a) as-sprayed, (b) 800 °C, (c) 900 °C, (d) 1000 °C and (e) 1100 °C. (f) Porosity percentage of cold sprayed samples depending on the induction heating temperature. The red ellipses indicate areas with interfacial debonding.
Figure 3. Optical microscope observation of the cross-sections of the cold sprayed samples: (a) as-sprayed, (b) 800 °C, (c) 900 °C, (d) 1000 °C and (e) 1100 °C. (f) Porosity percentage of cold sprayed samples depending on the induction heating temperature. The red ellipses indicate areas with interfacial debonding.
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Figure 4. SEM images of the surface morphologies of cold sprayed CoNiCrAlY coatings: (a) as-sprayed, (b) induction heating at 800 °C and (c) induction heating at 1100 °C. The red and yellow ellipses indicate areas with poor and good inter-particle bonding, respectively.
Figure 4. SEM images of the surface morphologies of cold sprayed CoNiCrAlY coatings: (a) as-sprayed, (b) induction heating at 800 °C and (c) induction heating at 1100 °C. The red and yellow ellipses indicate areas with poor and good inter-particle bonding, respectively.
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Figure 5. Backscattered electron micrographs showing the microstructures of the cold sprayed coatings: (a,b) as-sprayed, (c,d) 800 °C, (e,f) 900 °C, (g,h) 1000 °C and (i,j) 1100 °C.
Figure 5. Backscattered electron micrographs showing the microstructures of the cold sprayed coatings: (a,b) as-sprayed, (c,d) 800 °C, (e,f) 900 °C, (g,h) 1000 °C and (i,j) 1100 °C.
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Figure 6. IPF maps of the cold sprayed CoNiCrAlY coatings: (a) 800 °C, (b) 900 °C, (c) 1000 °C and (d) 1100 °C. (e) Grain size of the deposited coatings after induction heating.
Figure 6. IPF maps of the cold sprayed CoNiCrAlY coatings: (a) 800 °C, (b) 900 °C, (c) 1000 °C and (d) 1100 °C. (e) Grain size of the deposited coatings after induction heating.
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Figure 7. Schematic graph of the preferential heating induced pore closure by induction heating.
Figure 7. Schematic graph of the preferential heating induced pore closure by induction heating.
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Figure 8. Effect of induction heating temperature on the microhardness of the cold sprayed CoNiCrAlY coatings.
Figure 8. Effect of induction heating temperature on the microhardness of the cold sprayed CoNiCrAlY coatings.
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Figure 9. Variation of the microhardness of the cold sprayed coatings at different locations from the substrate–coating interface.
Figure 9. Variation of the microhardness of the cold sprayed coatings at different locations from the substrate–coating interface.
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Table
Table 1. Chemical composition of the materials used in this study.
Table 1. Chemical composition of the materials used in this study.
MaterialsChemical Composition (wt%)
CoNi CrAlFeYMoNbTi
CoNiCrAlY38.431.921.08.0-0.5---
Inconel 7180.3152.918.30.5218.5-3.065.060.98
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Yang, Y.; Aprilia, A.; Wu, K.; Tan, S.C.; Zhou, W. Post-Processing of Cold Sprayed CoNiCrAlY Coatings on Inconel 718 by Rapid Induction Heating. Metals 2022, 12, 396. https://doi.org/10.3390/met12030396

AMA Style

Yang Y, Aprilia A, Wu K, Tan SC, Zhou W. Post-Processing of Cold Sprayed CoNiCrAlY Coatings on Inconel 718 by Rapid Induction Heating. Metals. 2022; 12(3):396. https://doi.org/10.3390/met12030396

Chicago/Turabian Style

Yang, Yongjing, Aprilia Aprilia, Kaiqiang Wu, Sung Chyn Tan, and Wei Zhou. 2022. "Post-Processing of Cold Sprayed CoNiCrAlY Coatings on Inconel 718 by Rapid Induction Heating" Metals 12, no. 3: 396. https://doi.org/10.3390/met12030396

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