Next Article in Journal
Influence of Growth Temperature of the Nucleation Layer on the Growth of InP on Si (001)
Previous Article in Journal
Key Problems Affecting the Anti-Erosion Coating Performance of Aero-Engine Compressor: A Review
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Coatings
Volume 9
Issue 12
10.3390/coatings9120822
coatings-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Microstructure and Tribocorrosion Properties of Ni-Based Composite Coatings in Artificial Seawater

by
Bo Li
1,*,
Cong Li
1,*,
Yimin Gao
1,
Hongjian Guo
2,
Yunchuan Kang
1 and
Siyong Zhao
3
1
State Key Laboratory for Mechanical Behaviour of Materials, School of Materials Science and Engineering, Xi’an Jiaotong University, Xi’an 710049, China
2
State Key Laboratory of Solid Lubrication, Lanzhou Institute of Chemical Physics, Chinese Academy of Sciences, Lanzhou 100864, China
3
Guangxi Great Wall Machineries, Hezhou 542800, China
*
Authors to whom correspondence should be addressed.
Coatings 2019, 9(12), 822; https://doi.org/10.3390/coatings9120822
Submission received: 6 November 2019 / Revised: 25 November 2019 / Accepted: 2 December 2019 / Published: 4 December 2019
(This article belongs to the Section Corrosion, Wear and Erosion)
Browse Figures
Versions Notes

Abstract

:
NiAl matrix composite coatings were prepared using atmospheric plasma spraying (APS). The mechanical and tribocorrosion properties of the NiAl matrix composite coatings, incorporated with Cr2O3 and Mo, were investigated, and the synergistic effect between corrosion and wear was studied in detail. The microhardness of the composite coating improved from 195.1 to 362.2 HV through the addition of Cr2O3 and Mo. Meanwhile, the Cr2O3 and Mo phases were distributed uniformly in the composite coatings. The X-ray diffraction (XRD) peaks of Ni-based solid solution slightly shifted to the right after adding the Mo. This was probably due to the solid solution of Mo into the matrix. The NiAl–Cr2O3–Mo composite coating had the lowest corrosion current density, wear rate and friction coefficient of 9.487 × 10−6 A/cm2, 3.63 × 10−6 mm3/Nm, and 0.18, in all composite coatings as well as showing excellent tribocorrosion properties.

1. Introduction

With the forward depletion of land sources, it is very hard to satisfy the development needs of industry [1,2]. In recent years, the abundance of ocean resources has attracted researchers’ attention [3,4]. Marine equipment has had an important effect on marine exploration, such as ocean wind turbines, vessels and offshore oil platforms. However, ocean equipment easily suffers, not only from direct corrosion, but also the onset of wear, and their combined damage greatly affects the service lives of these kinds of engineering equipment [5,6,7,8,9]. The synergism effect of wear and corrosion is very destructive and usually decided by the reciprocity of chemistry, electrochemistry, mechanics and physics [10,11]. Therefore, corrosion will influence the microstructure, hardness and roughness of worn surfaces, further affecting the wear behavior [12]. In most tribocorrosion situations, the material loss is usually bigger than the simple sum of corrosion and wear [13,14]. The synergetic effects of corrosion and wear reduce the service life, safety and reliability of mechanical parts in seawater environments [15]. Therefore, it is imperative to optimize the corrosion and wear properties of mechanical parts in this environment, and to apply coatings with satisfactory mechanical properties. Tribocorrosion is a promising technology, which may provide good protection in ocean environments.
NiAl intermetallic compounds are considered to be promising materials in marine environments, due to their low density of 5.86 g/cm3, their high thermal conductivity, their high Young’s module of 240 GPa, and their high melting point of 1638 °C, as well as excellent corrosion and oxidation resistance [16,17,18,19,20]. Nevertheless, the practical application of NiAl has been restricted by its inherent poor ductility at ambient temperatures [21,22,23]. Acting as a solution-strengthening phase, Mo could improve the strength of materials effectively [24,25,26]. Meanwhile, Mo could improve the ductility of NiAl intermetallic compounds at ambient temperatures [27,28]. Our previous study on NiAl–Mo2C nanocomposites indicated that the hardness and density of NiAl–Mo2C nanocomposites increased with increasing Mo contents. Meanwhile, the maximum stress and yield strength were all higher than that of NiAl intermetallics [28]. Nevertheless, the NiAl coating has low hardness and suffers severe wear at room temperature [29]. Hence, excellent wear resistant hard phases should be added in the NiAl protective coating [30]. Cr2O3, acting as a strengthening hard phase, could, effectively, improve the wear resistance properties and hardness of materials [31,32,33].
In this work, the mechanical and tribocorrosion properties of NiAl matrix plasma-sprayed composite coatings, incorporated with Cr2O3 and Mo in artificial seawater, were investigated, and the synergistic effect between corrosion and wear was studied in detail.

2. Materials and Methods

2.1. Material Preparation

The NiAl matrix coatings were produced using atmospheric plasma spraying (APS), and the schematic for the preparation of composite coatings is shown in Figure 1. The spray powders of NiAl, Cr2O3 and Mo were purchased from Sulzer Metco (Winterthur, Switzerland). The mixed feedstock powders were mingled mechanically before spraying. The Inconel 718 substrate was sand-blasted using a sand-blasting machine (Beijing Changkong Sand Blasting Equipment Company Ltd., Beijing, China) with corundum grit before spraying, and then an ultrasonic cleaner (Kunshan Ultrasonic Instruments Company Ltd., Kunshan, China) was used with acetone to clean the residual sand from the composite coating surface. The composition of each composite coating is presented in Table 1. The thickness of the composite coatings was 300 ± 20 μm. The thickness of the composite coatings was measured by the method of microscopically examining the cross-sections. Table 2 presents the spraying parameters. Scanning electron microscopy (FE-SEM, Tescan Mira 3, Bron, Kohoutovice, Czech Republic) was used to characterize the morphologies of the powders and composite coatings. The chemical composition of composite coatings was analyzed using an X’Pert-MRD X-ray diffractometer (Philips, Eindhoven, the Netherlands). A microhardness tester (MH-5-VM, Shanghai Hengyi Science and Technology, Shanghai, China) was used to measure the microhardness of composite coatings. The load was 300 g. The dwell time was 5 s.

2.2. Tribocorrosion Tests

A reciprocating ball-on-disk tribometer (UMT, Karlsruhe, Germany) was used to measure the tribocorrosion properties of the composite coatings in artificial seawater. The artificial seawater was prepared according the ASTM D114-98 standard [8]. To adjust the artificial seawater pH value to 8.2, 0.1 M NaOH was used. Table 3 presents the artificial seawater’s chemical composition. Figure 2 showed the reciprocating ball-on-disc tribometer’s schematic. The solution cell material was polytetrafluoroethylene (PTFE), which presented excellent corrosion resistance and effectively avoided the environmental effect, according to the experiment results. The Al2O3 ceramic ball was used as the counter ball. The diameter of the Al2O3 ceramic ball was 5 mm. Firstly, the composite coatings were polished until the composite coating surface roughness was below 0.5 μm. The tribocorrosion tests have been described in detail elsewhere [34].

3. Results and Discussion

3.1. Microstructure and Microhardness of Composite Coatings

Figure 3 shows the SEM morphologies of spray powders. The NiAl and Mo powders were fabricated by gas-atomization and present the spherical shape. The size of the powders was around 50–100 μm. The feedstock powder of Cr2O3 is fabricated by sintering and crushing and shows an angular shape. The size of the Cr2O3 was 5–53 μm. All feedstock powders are mingled mechanically before spraying, in order to make sure the powders distribute uniformly [35].
Figure 4 gives SEM images of a polished cross-section of NiAl matrix composite coatings. The composite coatings contain many defects (cracks and pores) (Figure 4a), and present the typical lamellar structure. Combining energy disperse spectroscopy (EDS) and X-ray diffraction (XRD) (Figure 5), the black phase is Cr2O3 and the gray phase is Mo in the composite coatings. The Cr2O3 and Mo phases distribute uniformly, and the interface of these two phases has no evident cracks.
Figure 5 presents the XRD patterns of NiAl matrix composite coatings. All composite coatings contain the Ni-based solid solution (JCPDS file no. 04-0850) and NiAl (JCPDS file no. 20-0019). The XRD spectrum of NA1 and NA2 composite coatings contains the diffraction peaks of Cr2O3 (JCPDS file no. 38-1479) and single-phase Mo (JCPDS file no. 42-1120). It is surprising that the diffraction peaks of Ni-based solid solution slightly shift to the right after addition of the Mo, which may be due to the partial solid solution of Mo in the matrix [36].
Table 4 gives the microhardness of composite coatings. The microhardness of composite coatings increased with the addition of Cr2O3 and Mo. The addition of Cr2O3 makes the microhardness of the composite coating increase from 195.1 to 290.5 HV. The Cr2O3 often acts as a strengthening hard phase, which could effectively enhance the hardness of materials [37,38]. So, the microhardness of the composite coating is obviously improved. The NA2 composite coating has the highest microhardness, of 362.2 HV in all composite coatings. The Mo could act as the solution-strengthening phase, to greatly increase the microhardness of the composite coatings [39].

3.2. Electrochemical Behavior of Composite Coatings

Figure 6 shows the open circuit potential (OCP) evolution before, during and after the tribocorrosion of composite coatings in artificial seawater. During the first half hour, the composite coatings were immersed in artificial seawater before sliding. The initial highest OCP value, before sliding, was for NA1. When the counter ball of Al2O3 started sliding on the sample surface, the OCP of all composite coatings shifted rapidly to the negative. The OCP of the NA coating is more negative than that of the NA1 and NA2 coatings. After adding the element Mo, the Mo partially dissolved in the matrix, resulting the effect of solid solution-strengthening in the composite coating. It is very helpful if the coating forms a dense rust layer on the composite coating surface during the first half hour of immersion in artificial seawater [12]. This dense rust layer is very difficult to destroy in the sliding process. So, the OCP of the NA2 coating is the most positive in the process of sliding. The OCP values of all the composite coatings start to gradually increase when the sliding stops, which plays the main role in deciding the OCP value. The addition of Mo makes it easier for NA2 to form a dense, passive film, leading the OCP of this sample having the highest value after sliding.
Figure 7 presents the potentiodynamic polarization curves of composite coatings sliding in artificial seawater. Basic parameters (corrosion current density (icorr), corrosion potential (Ecorr), anodic and cathodic Tafel slopes (βa and βc) of the composite coatings are listed in Table 5, measured from Figure 7, using the Tafel extrapolation method. The polarization resistance value (Rp) is calculated using the Stern–Geary equation:
R P = β a × β c 2.303 i corr ( β a + β c )
The results show that the corrosion potential (Ecorr) of the NA2 composite coating is −0.490 V (vs. saturated calomel electrode (SCE)) and obviously higher than that of the NA and NA1 composite coatings of −0.583 V (vs. SCE) and −0.552 V (vs. SCE). The NA2 composite coating has the highest corrosion potential value of all composite coatings. Still, the corrosion current density (icorr) of the NA2 composite coating, at 9.487 × 10−6 A/cm2, is lower than that of NA and NA1 composite coatings, at 8.896 × 10−5 and 4.624 × 10−5 A/cm2, respectively, indicating that the NA2 composite coating presents the best corrosion resistance and is very difficult to corrode. Generally speaking, corrosion current density is an important criterion in valuing the corrosion resistance of materials [8,40]. So, the NA2 composite coating presents lower corrosion rates than those of the NA and NA1 composite coatings, and may be very hard to corrode. At the same time, the NA2 composite coating has the highest Rp of 9.003 × 102 Ω, which further illustrates that the NA2 composite coating presents very strong corrosion resistance under artificial seawater. In general, the βa is higher than βc of the material [4,7,11,41]. In this test result, the βa of all composite coatings are higher than the βc. This kind of phenomenon is related to the fact that the cathodic part exchange-current density value is higher than that of the anodic part. The entire kinetics of the corrosion of all composite coatings are decided by the anodic part [11]. That is to say, the anodic dissolution rate is slower than that of the cathodic reaction.

3.3. Tribological Behavior of NiAl Matrix Composite Coatings

Figure 8 shows the friction curves and wear rate of the NiAl matrix composite coatings in artificial seawater. Obviously, the friction coefficient and wear rate of the NA2 composite coating, of 0.18 and 3.63 × 10−6 mm3/Nm, respectively, are the lowest of all the composite coatings. This result is probably due to the way Cr2O3 acts as a strengthening hard phase, to enhance the hardness and wear resistance properties of composite coatings effectively. Meanwhile, the Mo could dissolve in the matrix and has a solid solution-strengthening effect in the NA2 composite coating. These are very useful in helping form the dense rust layer on the worn surface of the NA2 composite coating, which effectively reduces the corrosion rate, friction coefficient and wear rate of the NA2 composite coating.
In order to further investigate the tribocorrosion behavior of NiAl matrix composite coatings in artificial seawater, a color 3D laser scanning microscope was used. Figure 9 gives the 3D profiles of worn surfaces of NiAl matrix composite coatings after being tested in artificial seawater. The NA2 composite coating worn track is, at 118.9 μm, narrower than the NA and NA1 composite coatings, at 189.6 and 136.3 μm, respectively. This observation is in accordance with the friction coefficient and wear rate results of NiAl matrix composite coatings (Figure 8). Meanwhile, the worn surface of the NA coating suffered very severe corrosion. However, the worn surfaces of NA1 and NA2 composite coatings display slight corrosion. This result is similar with that of the corrosion current densities of the composite coatings (Table 5). Corrosion could aggravate the wear rate of the NiAl matrix composite coatings. So, the NA coating presents the highest wear rate and the NA2 coating has the lowest wear rate (Figure 8). It further illustrates that, in artificial seawater, the NA2 composite coating presents excellent tribocorrosion properties.
Figure 10 presents the SEM morphologies of composite coating worn surfaces during sliding. The NA coating displayed poor corrosion performance at cracks and pores (Figure 10a). The coating with the addition of Cr2O3 and Mo had visibly less corrosion than those of any other coatings (Figure 10c). It is probably due to the way Mo acts as a solution-strengthening phase, which could enhance the strength of materials [24,25,26].

4. Conclusions

In this study, composite coatings were fabricated using APS. The mechanical and tribocorrosion properties of composite coatings incorporated with Cr2O3 and Mo in artificial seawater were investigated, and the synergistic effect between corrosion and wear were investigated in detail. The main conclusions are given as follows:
  • Upon adding Cr2O3 and Mo, the microhardness of the composite coatings improves from 195.1 to 362.2 HV. Meanwhile, the Cr2O3 and Mo phases distribute uniformly and the interface of these two phases has no evident cracks.
  • The Ni-based solid solution diffraction peaks slightly shift to the right after the addition of Mo, which is maybe due to the partial solid solution of the element Mo into the matrix.
  • The NiAl–Cr2O3–Mo composite coating has the lowest corrosion current density, friction coefficient and wear rate of 9.487 × 10−6 A/cm2, 0.18 and 3.63 × 10−6 mm3/Nm in all composite coatings.
  • The NiAl–Cr2O3–Mo composite coating shows excellent tribocorrosion properties in artificial seawater.

Author Contributions

Writing—original draft preparation, B.L.; writing—review and editing, C.L.; project administration, Y.G.; visualization, H.G.; data curation, Y.K.; formal analysis, S.Z.

Funding

This research was funded by the National Natural Science Foundation of China (Grant Nos. 51805408, 51665026), the Natural Science Foundation of Shaanxi Province (Grant No. 2019JQ-283), the China Postdoctoral Science Foundation (Grant No. 2019M653597), the Shaanxi Province Postdoctoral Science Foundation, the Fundamental Research Funds for Central Universities (Grant Nos. xzy012019010, xtr0118008), the Guangxi Innovation Driven Development Project (Grant No. GUIKEAA18242001) and the Guangdong Province Key Area R&D Program (Grant No. 2019B010942001).

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Aribo, S.; Fakorede, A.; Ige, O.; Olubambi, P. Erosion-corrosion behaviour of aluminum alloy 6063 hybrid composite. Wear 2017, 376–377, 608–614. [Google Scholar] [CrossRef]
  2. Babu, P.; Sen, D.; Jyothirmayi, A.; Krishna, L.; Rao, D. Influence of microstructure on the wear and corrosion behavior of detonation sprayed Cr2O3–Al2O3 and plasma sprayed Cr2O3 coatings. Ceram. Int. 2018, 44, 2351–2357. [Google Scholar] [CrossRef]
  3. Bai, W.; Xie, Y.; Li, L.; Wang, X.; Gu, C.; Tu, J. Tribological and corrosion behaviors of Zr-doped graphite-like carbon nanostructured coatings on Ti6Al4V alloy. Surf. Coat. Technol. 2017, 320, 235–239. [Google Scholar] [CrossRef]
  4. Castillejo, F.; Marulanda, D.; Olaya, J.; Alfonso, J. Wear and corrosion resistance of niobium-chromium carbide coatings on AISI D2 produced through TRD. Surf. Coat. Technol. 2014, 254, 104–111. [Google Scholar] [CrossRef] [Green Version]
  5. Dehghanghadikolaei, A.; Ibrahim, H.; Amerinatanzi, A.; Hashemi, M.; Moghaddam, N.; Elahinia, M. Improving corrosion resistance of additively manufactured nickel-titanium biomedical devices by micro-arc oxidation process. J. Mater. Sci. 2019, 54, 7333–7355. [Google Scholar] [CrossRef]
  6. Dalibón, E.; Escalada, L.; Simison, S.; Forsich, C.; Heim, D.; Bruhl, S. Mechanical and corrosion behavior of thick and soft DLC coatings. Surf. Coat. Technol. 2017, 312, 101–109. [Google Scholar] [CrossRef]
  7. Fotovvati, B.; Namdari, N.; Dehghanghadikolaei, A. On coating techniques for surface protection: A review. J. Manuf. Mater. Process. 2019, 3, 28. [Google Scholar] [CrossRef] [Green Version]
  8. Liu, X.; Zhao, X.; An, Y.; Hou, G.; Li, S.; Deng, W.; Zhou, H.; Chen, J. Effects of loads on corrosion-wear synergism of NiCoCrAlYTa coating in artificial seawater. Tribol. Int. 2018, 118, 421–431. [Google Scholar] [CrossRef]
  9. Dun, Y.; Zhao, X.; Tang, Y.; Dino, S.; Zuo, Y. Microstructure and corrosion resistance of a fluorosilane modified silane-graphene film on 2024 aluminum alloy. Appl. Surf. Sci. 2018, 437, 152–160. [Google Scholar] [CrossRef]
  10. Silva, R.; Nogueira, R.; Bastos, I. Tribocorrosion of UNS S32750 in chloride medium: Effect of the load level. Electrochim. Acta 2011, 56, 8839–8845. [Google Scholar] [CrossRef]
  11. Liu, X.; An, Y.; Li, S.; Zhao, X.; Hou, G.; Zhou, H.; Chen, J. An assessment of tribological performance on NiCoCrAlYTa coating under corrosive environments. Tribol. Int. 2017, 115, 35–44. [Google Scholar] [CrossRef]
  12. Ma, F.; Li, J.; Zeng, Z.; Gao, Y. Structural, mechanical and tribocorrosion behaviour in artificial seawater of CrN/AlN nano-multilayer coatings on F690 steel substrates. Appl. Surf. Sci. 2018, 428, 404–414. [Google Scholar] [CrossRef]
  13. Buciumeanu, M.; Bagheri, A.; Souza, J.; Silva, F.; Henriques, B. Tribocorrosion behavior of hot pressed CoCrMo alloys in artificial saliva. Tribol. Int. 2016, 97, 423–430. [Google Scholar] [CrossRef]
  14. Mischler, S. Triboelectrochemical techniques and interpretation methods in tribocorrosion: A comparative evaluation. Tribol. Int. 2008, 41, 573–583. [Google Scholar] [CrossRef]
  15. Chen, Q.; Xie, Z.; Chen, T.; Gong, F. Tribocorrosion failure mechanism of TiN/SiOx duplex coating deposited on AISI304 stainless steel. Materials 2016, 9, 963. [Google Scholar] [CrossRef] [Green Version]
  16. Adabi, M.; Amadeh, A. Formation mechanisms of Ni–Al intermetallics during heat treatment of Ni coating on 6061 Al substrate. Trans. Nonferrous Met. Soc. China 2015, 25, 3959–3966. [Google Scholar] [CrossRef]
  17. Ameri, S.; Sadeghian, Z.; Kazeminezhad, I. Effect of CNT addition approach on the microstructure and properties of NiAl-CNT nanocomposites produced by mechanical alloying and spark plasma sintering. Intermetallics 2016, 76, 41–48. [Google Scholar] [CrossRef]
  18. Beyhaghi, M.; Kashefi, M.; Kiani-Rashid, A.; Khaki, J.; Jonsson, S. In-situ synthesis of nanostructured NiAl-Al2O3 composite coatings on cast iron substrates by spark plasma sintering of mechanically activated powders. Surf. Coat. Technol. 2015, 272, 254–267. [Google Scholar] [CrossRef]
  19. Li, B.; Jia, J.; Gao, Y.; Han, M.; Wang, W. Microstructural and tribological characterization of NiAl matrix self-lubricating composite coatings by atmospheric plasma spraying. Tribol. Int. 2017, 109, 563–570. [Google Scholar] [CrossRef]
  20. Liu, E.; Bai, Y.; Gao, Y.; Yi, G.; Jia, J. Tribological properties of NiAl-based composites containing Ag3VO4 nanoparticles at elevated temperatures. Tribol. Int. 2014, 80, 25–33. [Google Scholar] [CrossRef]
  21. Geist, D.; Gammer, C.; Rentenberger, C.; Karnthaler, H. Sessile dislocations by reactions in NiAl severely deformed at room temperature. J. Alloy. Compd. 2015, 621, 371–377. [Google Scholar] [CrossRef] [PubMed] [Green Version]
  22. Hsiao, W.; Su, C.; Huang, T.; Liao, W. The microstructural characteristics and mechanical properties of Ni–Al/h-BN coatings deposited using plasma spraying. J. Alloy. Compd. 2011, 509, 8239–8245. [Google Scholar] [CrossRef]
  23. Liu, E.; Jia, J.; Bai, Y.; Wang, W.; Gao, Y. Study on preparation and mechanical property of nanocrystalline NiAl intermetallic. Mater. Des. 2014, 53, 596–601. [Google Scholar] [CrossRef]
  24. Guo, X.; Niu, Y.; Huang, L.; Ji, H.; Zheng, X. Microstructure and tribological property of TiC–Mo composite coating prepared by vacuum plasma spraying. J. Therm. Spray Technol. 2012, 21, 1083–1090. [Google Scholar] [CrossRef]
  25. Klimashin, F.; Euchner, H.; Mayrhofer, P. Computational and experimental studies on structure and mechanical properties of Mo–Al–N. Acta Mater. 2016, 107, 273–278. [Google Scholar] [CrossRef] [Green Version]
  26. Kong, L.; Bi, Q.; Zhu, S.; Qiao, Z.; Yang, J.; Liu, W. Effect of CuO on self-lubricating properties of ZrO2(Y2O3)–Mo composites at high temperatures. J. Eur. Ceram. Soc. 2014, 34, 1289–1296. [Google Scholar] [CrossRef]
  27. Liu, E.; Gao, Y.; Bai, Y.; Yi, G.; Wang, W.; Zeng, Z.; Jia, J. Tribological properties of self-lubricating NiAl/Mo-based composites containing AgVO3 nanowires. Mater. Charact. 2014, 97, 116–124. [Google Scholar] [CrossRef]
  28. Liu, E.; Gao, Y.; Jia, J.; Bai, Y.; Wang, W. Microstructure and mechanical properties of in situ NiAl–Mo2C nanocomposites prepared by hot-pressing sintering. Mater. Sci. Eng. A 2014, 592, 201–206. [Google Scholar] [CrossRef]
  29. Zhu, S.; Bi, Q.; Niu, M.; Yang, J.; Liu, W. Tribological behavior of NiAl matrix composites with addition of oxides at high temperatures. Wear 2012, 274, 423–434. [Google Scholar] [CrossRef]
  30. Navas, C.; Cadenas, M.; Cuetos, J.; Damborenea, J. Microstructure and sliding wear behaviour of Tribaloy T-800 coatings deposited by laser cladding. Wear 2006, 260, 838–846. [Google Scholar] [CrossRef]
  31. Du, L.; Zhang, W.; Zhang, W.; Zhang, T.; Lan, H.; Huang, C. Tribological and oxidation behaviors of the plasma sprayed NiCoCrAlY–Cr2O3–AgVO3 coating. Surf. Coat. Technol. 2016, 298, 7–14. [Google Scholar] [CrossRef]
  32. Kim, G.; Choi, H.; Han, C.; Uhm, S.; Lee, C. Characterization of atmospheric plasma spray NiCr–Cr2O3–Ag–CaF2/BaF2 coatings. Surf. Coat. Technol. 2005, 195, 107–115. [Google Scholar] [CrossRef]
  33. Ramazani, M.; Ashrafizadeh, F.; Mozaffarinia, R. The influence of temperature on frictional behavior of plasma-sprayed NiAl–Cr2O3 based self-adaptive nanocomposite coatings. J. Therm. Spray Technol. 2013, 22, 1120–1132. [Google Scholar] [CrossRef]
  34. Li, B.; Li, C.; Gao, Y.; Guo, H.; Kang, Y.; Zhao, S. Tribological performance of a Ni-based composite coating in artificial seawater. Coatings 2019, 7, 747. [Google Scholar] [CrossRef] [Green Version]
  35. Li, B.; Gao, Y.; Jia, J.; Han, M.; Guo, H.; Wang, W. Influence of heat treatments on the microstructure as well as mechanical and tribological properties of NiCrAlY–Mo–Ag coatings. J. Alloy. Compd. 2016, 686, 503–510. [Google Scholar] [CrossRef]
  36. Li, B.; Jia, J.; Han, M.; Gao, Y.; Wang, W.; Li, C. Microstructure, mechanical and tribological properties of plasma-sprayed NiCrAlY–Mo–Ag coatings from conventional and nanostructured powders. Surf. Coat. Technol. 2017, 324, 552–559. [Google Scholar] [CrossRef]
  37. Zhang, T.; Lan, H.; Huang, C.; Du, L.; Zhang, W. Formation mechanism of the lubrication film on the plasma sprayed NiCoCrAlY–Cr2O3–AgMo coating at high temperatures. Surf. Coat. Technol. 2017, 319, 47–54. [Google Scholar] [CrossRef]
  38. Yang, H.; Lee, C.; Hwang, S. The effect of nano-sized Cr2O3 addition on the characteristics of NiCr–Cr2O3–Ag–BaF2/CaF2 coating. Surf. Coat. Technol. 2006, 201, 38–44. [Google Scholar] [CrossRef]
  39. Tian, J.; Yao, S.; Luo, X.; Li, C.; Li, C. An effective approach for creating metallurgical self-bonding in plasma-spraying of NiCr–Mo coating by designing shell-core-structured powders. Acta Mater. 2016, 110, 19–30. [Google Scholar] [CrossRef]
  40. Zhang, R.; Wang, H.; Xing, X.; Yuan, Z.; Yang, S.; Han, Z.; Yuan, G. Effects of Ni addition on tribocorrosion property of TiCu alloy. Tribol. Int. 2017, 107, 39–47. [Google Scholar] [CrossRef]
  41. Kannan, A.; Muralidharan, S.; Sarangapani, K.; Balaramachandran, V.; Kapali, V. Corrosion and anodic behaviour of zinc and its ternary alloys in alkaline battery electrolytes. J. Powder Sources 1995, 57, 93–98. [Google Scholar] [CrossRef]
Coatings 09 00822 g001 550
Figure 1. Schematic of the preparation of composite coatings.
Figure 1. Schematic of the preparation of composite coatings.
Coatings 09 00822 g001
Coatings 09 00822 g002 550
Figure 2. Reciprocating ball-on-disc tribometer’s schematic.
Figure 2. Reciprocating ball-on-disc tribometer’s schematic.
Coatings 09 00822 g002
Coatings 09 00822 g003 550
Figure 3. SEM morphologies of spray powders: (a) NiAl, (b) Cr2O3 and (c) Mo.
Figure 3. SEM morphologies of spray powders: (a) NiAl, (b) Cr2O3 and (c) Mo.
Coatings 09 00822 g003
Coatings 09 00822 g004 550
Figure 4. SEM images of polished cross-section of NiAl matrix composite coatings: (a) NA, (b) NA1 and (c) NA2.
Figure 4. SEM images of polished cross-section of NiAl matrix composite coatings: (a) NA, (b) NA1 and (c) NA2.
Coatings 09 00822 g004
Coatings 09 00822 g005 550
Figure 5. XRD patterns of NiAl matrix composite coatings.
Figure 5. XRD patterns of NiAl matrix composite coatings.
Coatings 09 00822 g005
Coatings 09 00822 g006 550
Figure 6. OCP evolution before, during and after tribocorrosion of composite coatings in artificial seawater.
Figure 6. OCP evolution before, during and after tribocorrosion of composite coatings in artificial seawater.
Coatings 09 00822 g006
Coatings 09 00822 g007 550
Figure 7. Potentiodynamic polarization curves of composite coatings sliding in artificial seawater.
Figure 7. Potentiodynamic polarization curves of composite coatings sliding in artificial seawater.
Coatings 09 00822 g007
Coatings 09 00822 g008 550
Figure 8. Friction curves (a) and wear rate (b) of NiAl matrix composite coatings.
Figure 8. Friction curves (a) and wear rate (b) of NiAl matrix composite coatings.
Coatings 09 00822 g008
Coatings 09 00822 g009 550
Figure 9. 3D profiles of worn surfaces of NiAl matrix composite coatings: (a) NA, (b) NA1 and (c) NA2.
Figure 9. 3D profiles of worn surfaces of NiAl matrix composite coatings: (a) NA, (b) NA1 and (c) NA2.
Coatings 09 00822 g009
Coatings 09 00822 g010 550
Figure 10. SEM morphologies of composite coating worn surfaces: (a) NA, (b) NA1 and (c) NA2.
Figure 10. SEM morphologies of composite coating worn surfaces: (a) NA, (b) NA1 and (c) NA2.
Coatings 09 00822 g010
Table
Table 1. Composition of NiAl matrix composite coatings.
Table 1. Composition of NiAl matrix composite coatings.
Composite CoatingNiAl (wt.%)Cr2O3 (wt.%)Mo (wt.%)
NA10000
NA180200
NA2702010
Table
Table 2. Spraying parameters.
Table 2. Spraying parameters.
ParameterValue
Plasma gas flow Ar, L/min40
Secondary gas flow H2, L/min5
Spraying angle90°
Powder feed rate, g/min40
Current, A500
Voltage, V60
Spray distance, mm110
Table
Table 3. Artificial seawater’s chemical composition.
Table 3. Artificial seawater’s chemical composition.
ConstituentConcentration (g/L)
NaCl24.530
Na2SO44.090
CaCl21.160
MgCl2·6H2O11.110
KCl0.695
NaHCO30.201
KBr0.100
H3BO30.027
SrCl2·6H2O0.042
NaF0.003
Table
Table 4. Microhardness of composite coatings.
Table 4. Microhardness of composite coatings.
CoatingsNANA1NA2
Vickers hardness (HV)195.1 ± 13.6290.5 ± 15.8362.2 ± 16.9
Table
Table 5. Corrosion parameters of composite coatings from potentiodynamic polarization curves.
Table 5. Corrosion parameters of composite coatings from potentiodynamic polarization curves.
CoatingsEcorr (V, vs. SCE)icorr (A/cm2)βa (V/dec)−βc (V/dec)Rp (Ω)
NA−0.5838.896 × 10−50.0590.0461.262 × 102
NA1−0.5524.624 × 10−50.0500.0422.143 × 102
NA2−0.4909.487 × 10−60.0420.0379.003 × 102

Share and Cite

MDPI and ACS Style

Li, B.; Li, C.; Gao, Y.; Guo, H.; Kang, Y.; Zhao, S. Microstructure and Tribocorrosion Properties of Ni-Based Composite Coatings in Artificial Seawater. Coatings 2019, 9, 822. https://doi.org/10.3390/coatings9120822

AMA Style

Li B, Li C, Gao Y, Guo H, Kang Y, Zhao S. Microstructure and Tribocorrosion Properties of Ni-Based Composite Coatings in Artificial Seawater. Coatings. 2019; 9(12):822. https://doi.org/10.3390/coatings9120822

Chicago/Turabian Style

Li, Bo, Cong Li, Yimin Gao, Hongjian Guo, Yunchuan Kang, and Siyong Zhao. 2019. "Microstructure and Tribocorrosion Properties of Ni-Based Composite Coatings in Artificial Seawater" Coatings 9, no. 12: 822. https://doi.org/10.3390/coatings9120822

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop