Tribological behaviour of thermally sprayed silicon carbide coatings
Introduction
Silicon carbide based ceramics have been widely employed in tribological systems for decades due to their high chemical and structural stability. Coatings of SiC have been extensively used in applications requiring low friction and high wear resistance [1]. Some of the applications include, but are not limited to, aerospace moving components [2], metal working tools [3], and protective coatings against corrosion in steel [4]. Most of these coatings are produced via dynamic ion mixing [2], RF magnetron sputtering [3], [4] or chemical vapour deposition [5]. These methods are only able to produce SiC coatings on limited size components and they are considered costly and unsuitable for large-scale machine components [6]. For larger components such as turbine bearings, highly versatile, low-cost techniques, requiring minimum equipment investment and maintenance, and that are relatively easy to perform (i.e. thermal spray) have until now failed in the production of SiC coatings [7]. In the case of thermal spray, this is due to the lack of melting point of SiC. This material tend to decomposes or sublimates at 2500–2600 °C under atmospheric conditions thus limiting their spray-ability [8]. Thermal spray is a technology that uses torches/flames at high temperatures (above 2500 °C) for melting or partially melting a feedstock material that is finally propelled towards a substrate to create a coating layer by layer [9]. Since many years, several researchers had attempted to deposit SiC coating by thermal-spraying methods with different grades of success [8], [10], [11]. In these studies, the key point is always the preparation of SiC feedstock material, which has to be adjusted by introducing metal or ceramic binders that will hinder the decomposition of SiC during spraying. Unfortunately, only limited studies on their tribological performance are available. Bach et al. [8] had performed wear tests on plasma sprayed SiC coatings and showed that the wear resistance of the coatings was about 30 times lower as compared to thermally sprayed WC–Co coating. The low wear resistance of SiC thermally sprayed coating was mainly attributed to the large porosity in the coating and the brittle silicon phase found in the matrix [8]. On the other hand, the tribological performance of bulk silicon carbide materials under various experimental testing conditions has been widely reported in dry and lubricating conditions [1], [12], [13], [14], [15], [16], [17]. These studies found the good performance of SiC self-mated pairs or rubbing against graphite or other ceramics. In most cases friction is very low, in the hydrodynamic regime, and whether the lubricating mechanisms are purely hydrodynamic or boundary lubrication (via tribochemical reaction forming silicon oxide or hydroxide) is still an open topic for discussion.
In the present work, the tribological performance of silicon carbide coatings produced by thermal spraying will be investigated and compared to bulk silicon carbide obtained by liquid phase sintering. High-frequency pulse detonation (HFPD) thermal-spraying technique has been utilised to deposit a modified SiC feedstock powder developed and patented by the authors of this work [18]. The modified SiC feedstock powder consists of nano-films of yttrium aluminium garnet (YAG) acting as matrix binders and deposited on each single SiC particle by co-precipitation technique. The goal of the oxide binders is to limit the interaction of SiC particles with the thermal spray flame, thereby greatly reducing their decomposition. Since this oxide phase is homogenously distributed, it is expected to supply a liquid phase in the SiC particles vicinities upon their melting in the flame during spraying. The oxide liquid phase will bind the SiC particles and will become a matrix of the coating increasing densification and cohesive strength of the thermally sprayed SiC coating. The prospects of thermally sprayed SiC coating in offshore applications, such as wind turbine bearings, will be assessed through reciprocating sliding tests under three different conditions namely dry, 3.5 wt% NaCl solution and PAO lubricated sliding. As comparison, liquid phase sintering (LPS)–SiC bulk material with YAG binder will be also tested. Their friction and wear behaviour under different reciprocating sliding conditions has been the focus of the investigation.
Section snippets
Feedstock and SiC coating preparation
The modified SiC feedstock powder used to produce the thermally sprayed SiC coating contains 30 wt% of nano-film YAG that is delivered onto the SiC particles surface via co-precipitation of aluminium and yttrium salt solution precursor. The mixed salt solution precursor is titrated into α-SiC suspension (Washington Mills AS, Norway, d50=0.60 µm) that contains a weak base precipitator agent. The suspension is heated up to 50 °C and the pH is adjusted above 8.0 to favour the precipitation of
Structural characterisation
The SEM images of the modified SiC feedstock powders prepared in this work are shown in Fig. 1. The powders are agglomerated as illustrated in Fig. 1a. A high magnification image of the cross-sectional view of the modified SiC particles displayed in Fig. 1b reveals a bright colour layer on the surface of SiC particles, which corresponds to the YAG phase. EDS analysis indicated these regions are rich in yttrium, aluminium and oxygen, which correspond to yttrium aluminium garnet (YAG, Y3Al5O12)
Discussion
The lowest friction and wear was found for the SiC coatings tested in dry and PAO conditions, and for the bulk LPS–SiC in PAO. When investigating the wear topography of the wear tracks, smooth surfaces were found although different features could be identified among the samples (Fig. 6). The SiC coating and bulk LPS–SiC samples show a very smooth surface with some pores in the case of the SiC coating under PAO (Fig. 6a and b). In the case of the SiC coating, the tiny pores that were produced
Conclusions
Successful thermally sprayed SiC coatings with good adhesion and mechanical stability have been prepared in this work. The tribological behaviour has been compared to bulk sintered LPS–SiC under three different testing conditions (dry, oil lubricated and NaCl solution). The following conclusions can be drawn:
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The lack of sintering of the coating has not been a drawback for the friction and wear performance of the thermal spray coating. Indeed, the SiC coating has shown low wear and friction in
Acknowledgements
The authors would like to acknowledge the support of TSO Materialer, NTNU (Strategic Area of Materials, NTNU) for funding. Carlos Vaquero, Inaki Fagoaga and Georgii Barykin (TECNALIA, Spain) are also thanked for helping and advising in the production of the coatings.
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