Tribological behavior of a shot-peened nickel-based single crystal superalloy at high temperature

doi:10.21203/rs.3.rs-1646603/v1

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Tribological behavior of a shot-peened nickel-based single crystal superalloy at high temperature

https://doi.org/10.21203/rs.3.rs-1646603/v1

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The tribological behavior of a nickel-based single crystal (NBSC) superalloy treated by shot-peening has been investigated. Friction tests under three normal loads and three temperatures were carried out based on the ball-on-disc configuration. The results showed that coefficient of friction (COF) and wear rate of the shot-peened superalloy at room temperature were nearly 2 times and 4 times that at 600 ℃, respectively. However, there were no significant difference in COF and wear rate between the shot-peened NBSC superalloy and the as-received NBSC superalloy, which was ascribed to the competing effects between the increased hardness and the increased roughness of NSBC superalloy after shot-peening. High temperature friction promoted the formation of a glaze-layer on the substrate, which was derived from the sintering and compacting of oxidized wear debris. The formed glaze-layer prevented the direct contact of the friction pair and contributed to the reduced COF and wear rate. The wear mechanism of the SP-NSBC superalloy at high temperature included oxidation, adhesion, and abrasion. With the decreasing normal load and increasing temperature, the adhesive wear weakened. This work provided insights into the effects of shot-peening treatment on the tribological properties of NBSC superalloy.

Shot-peening

nickel-based single crystal

tribological performance

high temperature

glaze-layer

Wear affects the operation of mechanical systems operating at high temperature, such as the bearings and the blade-disk assemblies in aero-engines and gas turbines [1, 2]. High temperature wear causes the deterioration of structural surface and the variation of contact status, which has become one of the life limiting factors of high temperature components [3, 4]. Nickel-based single crystal (NBSC) superalloys were preferred in turbine blades due to their excellent mechanical properties at high temperature [5]. In order to meet the requirement of high-performance aero-engines and gas turbines, the NBSC turbine blades were typically strengthened by shot-peening treatment to improve its anti-fatigue performance, which were attributed to the introduction of favorable compressive residual stress and deep work hard zone [6, 7]. However, the tribological behavior of the shot-peened nickel-based single crystal (SP-NBSC) superalloy have not been investigated at high temperature.

Shot-peening treatment can introduce fine grain microstructure and large surface hardness, but also increase the surface roughness [8]. The change of mechanical properties and surface morphologies caused by shot-peening treatment would have a great influence on the tribological properties of materials. It has been reported that shot-peening treatment can improve the wear resistance and fatigue life mainly by introducing high compressive residual stress and large microhardness in the depth direction [9–11]. Nevertheless, in some cases, shot-peening treatment has no effects or even opposite effects on tribological behaviors of alloys. Zammit et al. [12] found that transformation of microstructure and residual compressive stresses were counteracted, and no improvement of wear resistance of iron was observed. Besides, shot-peening showed no effect on the wear behavior of Ti6Al4V alloy under fretting loading [13]. It can be found that the tribological behavior of materials after shot-peening treatment mainly depended on the surface microstructure, residual stress field, and surface morphology. Moreover, the microstructure and residual stress field were strongly affected by the elevated temperature, which would result in a more complicated effect of shot-peening treatment on the tribological performance [14]. However, the effects of shot peening treatment on tribological behavior of NBSC superalloys at high temperature have not been investigated.

High temperature wear process includes oxidation, creep, fatigue and frictional effects, among which the dramatically change of the physical, chemical, and mechanical properties will directly affect the tribological behavior [15, 16]. During the friction process of nickel-based superalloy at high temperature, it has been found that a thin and physically homogeneous oxide layer was formed on the component surface [17–20]. The formed oxide layer was also known as the glaze-layer, which was reported to contribute to the low coefficient of friction (COF) and wear rate for NBSC superalloys at high temperature [21, 22]. A widely recognized speculation was that the glaze-layer was formed by compacting and sintering the wear particles produced during sliding process with the presence of heat [18, 23, 24]. The glaze-layer prevented the direct metal–metal contact between the friction pair, therefore, the properties of the glaze-layer would directly influence the tribological behaviors of superalloys at high temperature [25]. Moreover, it was reported that the formation of the glaze-layer was affected by the contact load and temperature. On the one hand, the lower contact load could not destroy the surface oxide film, while the larger contact load would break the glaze-layer excessively and prevent it from forming [26]. On the other hand, the glaze-layer formed only when the environmental temperature reached the certain threshold [27].Therefore, it was important to investigate the formation of glaze-layer on the SP-NBSC superalloys to reveal the wear mechanism.

NBSC superalloys contained many doping elements, such as chromium, cobalt and tungsten etc., which resulted in complex tribo-reaction during friction process at high temperature. For the nickel-based alloys, it was found that friction promoted the formation of NiO phase, which was an effective lubricous binary oxide [28, 29]. Chromium can easily react with oxygen and form Cr₂O₃, which was known for its favorable tribological characteristics due to the excellent resistance to particles fracture and micro-cracks [18, 30]. In comparison with nickel oxides and chromium oxides, cobalt oxides have been reported to have the lower friction and wear, and they preferred to form a continuous solid film instead of being worn off [22, 31]. However, not all metal oxides are beneficial for reducing friction and wear. WO₃ with a high content will make the glaze-layer porous, that was inconducive for wear reduction [30]. Al₂O₃ owned strong ionic/covalent bonds that were difficult to shear [29]. Generally, friction induced glaze-layer at high temperature comprised different kinds of oxides, analyzing the composition of the glaze-layer would be conducive to further analysis of the tribological behavior of SP-NBSC superalloy.

In the present study, the tribological behavior of a SP-NBSC superalloy has been investigated. Friction tests under different temperatures and normal loads were carried out to study the evolution of COF and wear rate. The morphologies and chemical compositions of the wear track on the SP-NBSC superalloy were characterized to study the wear damage and the formation of the glaze-layer. Furthermore, the cross-section morphologies were also analyzed to further reveal the characteristics of the formed glaze-layer between the friction pairs. Based on the analysis results, the wear mechanism of the SP-NBSC superalloy was proposed, which provided support for understanding the tribological behavior of NBSC superalloys after shot peening.

2.1 Materials and specimen

An NBSC superalloy DD6, which was typically applied in aero-engine turbine blades, was treated by shot-peening for the further friction tests. The microstructure of the NBSC superalloy consisted of a large volume fraction of L12 ordered γ′ precipitates coherently embedded in a faced centered cubic γ matrix (Fig. 1). NBSC superalloy contained a variety of metal elements, and the major chemical compositions of the DD6 superalloy were shown in Table 1. The NBSC specimen was processed into the square plate (20 ×20 ×4 mm³) by using wire electrical discharge machining, and the surface roughness was about 0.8 µm after polishing. The [001] crystal orientation of the NBSC superalloy was in consistence with the thickness direction of the specimen. Cast steel ball with a 0.3 mm diameter was used as the projectile to shot the specimen surface, and the shot-peening intensity was about 0.165 mmA, which can effectively improve the fatigue resistance of NBSC superalloy.

Table 1

The chemical composition and element percentage of the NBSC superalloy (wt. %)
Element	C	Cr	Co	W	Mo	Al	Re	Ta	Ni
wt.%	≤ 0.04	3.8–4.8	8.5 − 0.05	7.0–9.0	1.5–2.5	5.2–6.2	1.6–2.4	6.0-8.5	Bal.

2.2 Friction test

In order to investigate the tribological behavior of the SP-NBSC superalloy at high temperature, friction tests were performed using a high temperature tribometer (HT-100) with a rotation mode of ball-on-plate configuration (Fig. 2). The upper balls were Si₃N₄ with a diameter of 6 mm, which had high hardness and excellent wear resistance [32]. Besides, the property of Si₃N₄ was table at high temperature that will not affect the evolution of NBSC superalloy during the friction process [33]. Before each test, the NBSC superalloy specimen and the Si₃N₄ ball were supersonically cleaned with acetone and alcohol in sequence for 30 mins to remove the surface contamination. The rotational angular velocity of the NBSC specimen was 560 rpm with a constant rotation radius of 5 mm. Friction tests with three different normal loads varying from 10 to 20 N were carried out to study the effects of normal load on tribological behavior of SP-NBSC superalloy (the corresponding maximum Hertz contact stress varied from 1.27 to 1.60 GPa). Besides, three representative temperatures (25, 600 and 700 ℃) were selected, which corresponded to the actual operation condition of the blade-disk assembly [26]. During the high temperature friction test, the furnace was heated to the preset temperature and hold for 20 mins to ensure the uniformity of test temperature. The friction tests under different loading conditions were repeated twice to ensure the accuracy, and each test was carried out for 120 minutes.

2.3 Characterization

A three-dimensional integral microscopy with enhanced resolution and depth of field (KEYENCE, VHX-700FC) was used to observe the surface morphologies of the SP-NBSC superalloy before and after the friction tests. The surface hardnesses of the SP-NBSC superalloy and the as-received nickel-based single crystal (AS-NBSC) superalloy were measured by using a microhardness tester (Qness Q60A+). A Raman spectrometer (Thermo Scientific DXR2) with a laser wavelength of 532 nm was used to identify the chemical compositions of the worn regions. Besides, a scanning electron microscopy (SEM) (FEI, Verios G4) equipped with an energy dispersive X-ray (EDS) was applied to investigate the microstructures and chemical compositions of the wear tracks on the SP-NBSC superalloy. The cross-sectional morphology of the shot-peened regions of the NBSC superalloy was observed by using a high-resolution transmission electron microscopy (HRTEM, 2100plus, Jeol, Japan)

Wear rate was an important factor to evaluate the tribological performance of the moving assembly, which can be quantified as the volume of material removed by the counterpart normalized by the load and the traveled distance [29]. After the friction test, the wear volume was calculated as the product of the averaged cross-sectional area and circumference of the wear track, as shown in Eq. (1):

$$\begin{array}{c}\text{V}\text{=}\text{2}\text{π}\text{R}\text{S}, \#\text{(}\text{1}\text{)}\end{array}$$

where $\text{R}$ was the rotation radius and $\text{S}$ was the averaged cross-sectional area of the wear track, which was obtained by using the three-dimensional integral microscopy. The wear rate can be calculated as follows:

$$\begin{array}{c}{\text{W}}_{\text{r}}\text{=}\frac{\text{V}}{\text{FL}}\text{,}\text{ }\#\text{(}\text{2}\text{)}\end{array}$$

where ${\text{W}}_{\text{r}}$ indicated the wear rate, $\text{V}$ was the wear volume, $\text{F}$ and $\text{L}$ were the applied normal load and the sliding distance, respectively.

3.1 Characterization of the SP-NBSC superalloy

Shot-peening treatment caused the change of microstructure and surface morphology. The surface morphology of the SP-NBSC superalloy was observed by the three-dimensional integral microscopy (Fig. 3a). It can be found that many impact pits were distributed on the specimen surface induced by the steel ball with high speed. The enlarged morphology showed that the impact pits seemed like irregular circles with the averaged depth about 20 µm (Fig. 3b). The surface roughness of the SP-NBSC superalloy was about 9.35 µm, which was more than ten times that of the AS-NBSC superalloy. The increased surface roughness indicated that the serious plastic deformation occurred on the specimen surface. Moreover, the microstructure of the cross-sectional region near the shot-peened surface showed that shot-peening treatment introduced dislocation bands and dislocation networks beneath the surface (Fig. 3c). Shot-peening treatment improved the surface hardness of the NBSC superalloy from 370 Hv to 551 Hv, the improvement of the surface harness was mainly attributed to the severe plastic deformation and strain hardening [34].

3.2 Tribological performance

In order to investigate the tribological performance of the SP-NBSC superalloy, the friction tests under different temperatures and normal loads were carried out. It can be observed that the COF evolutions under different test temperatures exhibited dramatical differences (Fig. 4a). At room temperature (about 25 ℃), the initial COF reached to about 0.7 and lasted for about 60 mins, then it decreased to about 0.6. When the temperature increased to 600 and 700 ℃, the COFs were more stable and about half of that at room temperature, it can be deduced that high temperature promoted the tribo-chemical reaction that was beneficial to friction reduction. Besides, the averaged COFs during the steady wear period decreased with the increase of test temperature, but there was little difference in COF when the test temperatures were 600 and 700 ℃ (Fig. 4c). However, the evolution of COF showed great difference under different normal loads at 600 ℃ (Fig. 4b). It can be observed that when the normal load was 15 N, the COF increased to about 0.65 rapidly and lasted for about 30 mins, then it decreased to about 0.4 sharply. The larger COF during the running-in period at 15 N may be resulted from the instability of the formed glaze-layer under lower normal load. With the continuous sliding, the COF would decreased finally, which might indicate that the stable glaze-layer formed. Similarly, when the normal load was 10 N, the evolution of COF also exhibited the characteristics of piecewise decline. It can be deduced that larger normal load promoted the formation of stable tribo-layer. Moreover, the averaged COF increased from 0.3 to 0.4 when the normal load decreased from 20 N to 10 N (Fig. 4d). Therefore, it can conclude that both temperature and normal load have a great influence on COF. Besides, the averaged COFs of the SP-NBSC superalloy under different loading condition showed no great differences compared with those of the AS-NBSC superalloy, which may be due to the competing effects between hardness and roughness.

After the friction tests, the morphologies of the wear track on the SP-NBSC superalloy were analyzed. The macroscopic morphology of a representative wear scar showed that an annular trace formed on the specimen surface after the friction test (Fig. 5a). In order to analyze the characteristics of wear tracks quantitatively, the cross-sectional morphologies were measured by using the three-dimensional integral microscopy at eight different locations (marked in Fig. 5a). The cross-sectional morphology at a representative location was shown in Fig. 5b, the circular profile was ascribed to the uneven distribution of contact stresses according to Hertz theory. When the normal load was 20 N, both the widths and depths of the wear tracks were lower at 600 and 700 ℃ compared with those at room temperature, which indicated that high temperature promoted the wear reduction (Fig. 5c). Besides, the depths of the wear tracks increased when the normal load increased from 10 N to 15 N at 600 ℃, but the widths of the wear tracks did not change too much when the normal load varied from 15 N to 20 N (Fig. 5d). For all the friction tests, the depths of the wear scar were all greater than 35 µm, which were larger than the thickness of the plastic layer induced by shot-peening treatment. Therefore, it can be inferred that the shot-peening induced plastic layer has been completely worn out after two hours of friction tests.

The wear rates of the SP-NBSC superalloy under different loading conditions were calculated to further investigate its tribological performance. It could be observed that the wear rate of the SP-NBSC superalloy was about 11.21 × 10^− 8 mm³/(N·mm) at room temperature, which was almost three times that at 600 ℃ and 700 ℃. Besides, the wear rate of the SP-NBSC superalloy at 700 ℃ was about 20% higher than that at 600 ℃, which may be due to the deterioration of the mechanical properties at higher temperature. Moreover, the wear rates showed little difference when the normal load varied from 10 N to 15 N, but the wear rate increased as the normal load increased to 20 N, which was consistent with the results of the AS-NBSC superalloy [26]. In summary, although shot-peening treatment resulted in the increased surface roughness, the wear rate of the SP-NBSC superalloy showed little difference in comparison with the AS-NBSC superalloy, and the decreased wear rate at high temperature was may be ascribed to the formed glaze-layer during the friction test.

3.3 Analysis of the wear scar

The tribological behavior of the SP-NBSC superalloy showed great difference under different test conditions, which could lead to distinguished wear damage. To explore the effects of temperatures and loads on the wear damage, the morphologies of the wear tracks on the SP-NBSC plate were investigated by using SEM. It could be found that some micro cracks were distributed on the surface of NBSC after the friction test at room temperature (Fig. 6a), and severe surface peeling occurred due to the large contact stress. Besides, there were many flake-like wear debris attached to the specimen surface, and some deep furrows were generated. It can be inferred that adhesive and abrasive wear was the main wear mechanism for the SP-NBSC superalloy at room temperature. As the test temperature increased to 600 ℃, the surface material was heavily oxidized, parts of the oxides were worn off and crushed into fine wear debris (Fig. 6b). The wear track was smoother compared with that at room temperature, which exhibited the typical characteristic of glaze-layer [35]. Besides, some mild scratches were also distributed on the specimen surface. It can be deduced that the SP-NBSC superalloy underwent more severe abrasive wear at 600 ℃ than room temperature. When the test temperature was 700 ℃, the surface morphologies of the wear track showed different characteristics, which was smoother than that at room temperature and 600 ℃ (Fig. 6c). The formed oxides on the specimen surface seemed dense, and mild scratches were formed on the specimen surface with little granular wear debris attache. Therefore, the abrasive wear was the main wear mechanism when the temperature increased to 700 ℃.

Furthermore, the effects of normal loads on the wear damage of SP-NBSC superalloy at 600 ℃ were also investigated. When the normal load was 15 N, some spalling pits can be observed on the wear track, which was mainly induced by the large frictional stress (Fig. 7a). Then the materials removed from the surface will be crushed into fine wear debris under the action of large contact stress. After the friction test, it can be found that some flake-like wear debris were retained on the worn region. As the normal load decreased to 10 N, many shallow furrows were observed on the wear track, the direction of the furrows was consistent with the sliding direction (Fig. 7b). Besides, there were some elongated spalling pits near the furrows. It can be deduced that the abrasive wear became the main wear mechanism when the normal load decreased from 20 N to 10 N.

It has been reported that the formed glaze-layer during high temperature friction process promoted the reduction of COF and wear rate. Therefore, the chemical composition of the glaze-layer under different test conditions were investigated by using EDS, and the element percentage in the wear track were shown in Table 2. It can be found that the contents of oxygen were almost 20% when the test temperature was 600 ℃ and 700 ℃, while the content of oxygen was 4.34% after the friction test at room temperature. It can be deduced that both the friction induced heat and the high temperature environment promoted the surface oxidation during the high temperature friction process. The composition of the formed oxides had a great influence on the tribological performance of SP-NSBC superalloy. In order to further analyze the material composition of the glaze-layer, Raman spectra analysis under different test conditions were performed, as shown in Fig. 8. There were nearly five different peaks located at 360 cm^− 1, 550 cm^− 1, 680 cm^− 1, 830 cm^− 1 and 1060 cm^− 1, respectively. The strongest peak appeared at around 830 cm^− 1 corresponded to Cr_xO_y and WO_x[36, 37]. The peak at around 1060 cm^− 1 referred to (Ni,Co)O [38, 39], and the peak of 680 cm^− 1 appeared at elevated temperature indicated the existence of Co₃O₄ and NiCrO₄ [38, 40]. The peaks Cr_xO_y also appeared at 360 cm^− 1, 550 cm^− 1 [38, 41]. It can conclude that different kinds of metal oxides (including Ni, Cr, Co, and W) were generated at elevated temperature, that contributed to the reduction of friction and wear [18, 22, 42]. Although friction induced heat at room temperature also cause the surface oxidation, the amount of the oxides was too small to improve the tribological performance of the SP-NBSC superalloy. Moreover, the formation of Co₃O₄ and NiCrO₄ at high temperature also played an important role in the improvement of its tribological performance.

Table 2

The chemical composition and element percentage of the wear scar under different test conditions (w.t.%)
Test condition F / T	C	O	Al	Cr	Co	Ni	W
20 N / 25 ℃	10.76	4.34	5.21	6.41	9.52	59.21	4.55
20 N / 600 ℃	6.41	19.93	4.54	5.54	8.00	49.68	5.90
20 N / 700 ℃	4.27	19.94	5.05	6.13	8.86	49.90	5.85
15 N / 600 ℃	2.95	21.10	4.84	5.47	10.67	51.58	3.39
10 N / 600 ℃	3.45	18.98	4.95	5.26	9.25	55.51	2.60

3.4 Cross-sectional morphology

According to the above analyses, high temperature promoted the formation of glaze-layer, which was composed of different metallic oxides and contributed to the prominent tribological behavior of SP-NBSC. The cross-sectional morphology beneath the wear track was analyzed by using SEM to investigate the microstructure of the glaze-layer, as shown in Fig. 9. It can be observed that the two-layer structure formed after the high temperature friction test, a plastic deformation layer was generated, the γ/γ’ microstructures of which were seriously distorted due to the large contact stress. Above the deformation layer, there was a glaze-layer formed, which was originated from the compacting and sintering of wear debris. The glaze-layer can prevent the direct contact between the friction pair, and contribute to the low COF and wear rate due to the low shear strength of the metal oxides. However, no glaze-layer was formed at room temperature, it was because that the weak oxidation cannot provide enough oxides to form a continuous film, and the initially formed film will be continuously destroyed by the large frictional stress (Fig. 9a). In contrast, the tribofilm formed at elevated temperature was dense, and the thicker tribofilm could effectively protect the substrate (Fig. 9b-9e). The γ/γ’ microstructure beneath the glaze-layer was more distorted at 700 ℃ than that at 600 ℃, which may be induced by the degradation of mechanical properties at higher temperature. When the test temperature was 600 ℃, both the thickness of glaze-layer and plastic layer increased with the increase of normal load. On the one hand, large load resulted in high contact stress and promoted the plastic deformation of substrate. On the other hand, wear debris was easy to wear off and compact on the specimen surface, which will promote the formation of the thicker glaze-layer.

3.5 Wear mechanism

According to the above analyses, the wear mechanism of SP-NBSC superalloy at high temperature was proposed (Fig. 10). The wear process of SP-NBSC superalloy can be divided into two periods, i.e., the running-in period and stable wear period. During in the running-in period, multiple rough peaks of the specimen surface were in contact with the Si₃N₄ ball, the actual stress will be higher compared with the AS-NBSC superalloy due to the increased surface roughness of the SP-NBSC superalloy. The surface material was worn off due to the large frictional stress and then formed wear debris (Fig. 10a). At the same time, the friction induced heat and high temperature environment caused the surface oxidation. With the continuous friction, the surface oxidation and wear intensified, and a part of the wear debris accumulated and be trapped between the friction pair. The trapped wear debris would be sintered and compacted on the surface and formed a glaze-layer (Fig. 10b). The glaze-layer was composed of different kinds of metal oxides (including Ni, Cr, Co, and W), which prevented the direct contact of the friction pair. Furthermore, these oxides had good anti-wear and anti-friction properties, thereby improving the tribological performance under high temperature conditions [15, 29, 31, 42].

The tribological performances of SP-NBSC superalloy depended on the applied normal load and test temperature during the friction process, which led to the difference in wear mechanism. At room temperature, there was weak oxidation in the contact region, and no glaze-layer was formed to protect the substrate, the main wear mechanism was adhesion and abrasion. When the test temperature increased to 600 ℃ and above, severe oxidative wear occurred, and a glaze-layer was formed on the surface of SP-NBSC superalloy due to the sintering and compacting of wear debris. The formed glaze-layer could avoid the direct contact of the friction pair and effectively reduce friction and wear. However, the wear mechanism under high temperature conditions was not exactly the same. At 600 ℃, both adhesive wear and abrasive wear existed during the friction process, but the abrasive wear became prominent with the decreased normal load. When the test temperature increased to 700 ℃, the main wear mechanism was abrasive wear and oxidative wear, which may be attributed to the different composition of the formed glaze-layer.

The tribological behavior of SP-NBSC superalloy has been investigated when sliding against the Si₃N₄ ball. The effects of temperature and applied normal loads on friction and wear were investigated, and the wear mechanism of SP-NBSC superalloy has also been revealed by analyzing the morphology and chemical composition of the wear track. The main conclusions of this work can be summarized as follows:

1) Shot-peening treatment increased the surface hardness of NBSC superalloy by about 48.9%, and the surface roughness was more than ten times that of the AS-NBSC superalloy. Since the competing effects of hardness and roughness on the tribological behavior, there were no significant differences in COF and wear rate between SP-NBSC superalloy and AS-NBSC superalloy.

2) The averaged COF of SP-NBSC superalloy was about 0.62, which was almost twice that at 600 ℃ (COF = 0.34) and 700 ℃ (COF = 0.33). The wear rate showed a similar trend with temperature, which decreased drastically from 11.21 × 10^− 8 mm³/(N·mm) at room temperature to 3.07 × 10^− 8 mm³/(N·mm) at 600 ℃ and 3.24 × 10^− 8 mm³/(N·mm) at 700 ℃. In addition, the larger normal load was beneficial to reduce COF, and the averaged COF decreased from 0.44 to 0.33 when the applied normal load varied from 10 to 20 N. However, the wear rates did not change significantly, which were 2.90 and 2.85 × 10^− 8 mm³/(N·mm) when the applied normal load were 10, 15 N, respectively.

3) Friction induced heat and high temperature environment promoted the surface oxidation during the friction process. Under the action of large contact stress and frictional stress, severe wear was occurred and a large amount of wear debris were generated, which will be sintered and compacted to form a glaze layer on the surface. The glaze-layer was mainly composted of metal oxides of nickel, chromium, cobalt and tungsten, which contributed to the low COF and wear rate.

Declarations

The authors declare that we have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

Acknowledgements

National Natural Science Foundation of China (Grant No. 52105154 and 51975471), National Science and Technology Major Project (2017-VIII-0003-0114), and Natural Science Foundation of Shanghai (21ZR1469300) support this work.

Lewis, R., Dwyer-Joyce, R.: Combating Automotive Engine Valve Recession.Tribology and Lubrication Technology. ;59. (2003)
F, P.P., Duraiselvam, M., Balamurugan, S.N.: Effect of laser surface texturing on wear resistance of nickel based superalloy. Industrial Lubrication and Tribology. 71, 842–850 (2019)
Sun, S., Li, L., He, K., Yue, Z., Yang, W., Yu, Z.: Fretting fatigue damage mechanism of Nickel-based single crystal superalloys at high temperature. Int. J. Mech. Sci. 186, 105894 (2020)
Sun, S., Li, L., Yue, Z., Yang, W., He, K., Li, S.: Fretting fatigue failure behavior of Nickel-based single crystal superalloy dovetail specimen in contact with powder metallurgy pads at high temperature. Tribol. Int. 142, 105986 (2020)
Tan, Z.H., Wang, X.G., Du, Y.L., Duan, T.F., Yang, Y.H., Liu, J.L., et al.: Temperature dependence on tensile deformation mechanisms in a novel Nickel-based single crystal superalloy. Mater. Sci. Engineering: A. 776, 138997 (2020)
Chen, Y., Jiang, C.: Effect of Shot Peening on Surface Characteristics of Ni-Based Single-Crystal Superalloy. Mater. Trans. 54, 1894–1897 (2013)
Wang, X., Xu, C., Hu, D., Li, C., Liu, C., Tang, Z.: Effect of ultrasonic shot peening on surface integrity and fatigue performance of single-crystal superalloy.Journal of Materials Processing Technology. ;296. (2021)
Yan, W., Fang, L., Sun, K., Xu, Y.: Effect of surface work hardening on wear behavior of Hadfield steel. Mater. Sci. Engineering: A. 460–461, 542–549 (2007)
Kubler, R., Berveiller, S., Bouscaud, D., Guiheux, R., Patoor, E., Puydt, Q.: Shot peening of TRIP780 steel: Experimental analysis and numerical simulation.Journal of Materials Processing Technology. ;270. (2019)
Mitrovic, S., Adamovic, D., Zivic, F., Dzunic, D., Pantic, M.: Friction and wear behavior of shot peened surfaces of 36CrNiMo4 and 36NiCrMo16 alloyed steels under dry and lubricated contact conditions. Appl. Surf. Sci. 290, 223–232 (2014)
Dancer, C.E.J., Yahya, N.A., Berndt, T., Todd, R.I., de Portu, G.: Effect of residual compressive surface stress on severe wear of alumina–silicon carbide two-layered composites. Tribol. Int. 74, 87–92 (2014)
Zammit, A., Abela, S., Wagner, L., Mhaede, M., Grech, M.: Tribological behaviour of shot peened Cu–Ni austempered ductile iron. Wear. 302, 829–836 (2013)
Fridrici, V., Fouvry, S., Kapsa, P.: Effect of shot peening on the fretting wear of Ti–6Al–4V. Wear. 250, 642–649 (2001)
Tong, Z.P., Ren, X.D., Zhou, W.F., Adu-Gyamfi, S., Chen, L., Ye, Y.X., et al.: Effect of laser shock peening on wear behaviors of TC11 alloy at elevated temperature. Opt. Laser Technol. 109, 139–148 (2019)
Rynio, C., Hattendorf, H., Klöwer, J., Eggeler, G.: The evolution of tribolayers during high temperature sliding wear. Wear. 315, 1–10 (2014)
Meng, Y., Xu, J., Jin, Z., Prakash, B., Hu, Y.: A review of recent advances in tribology. Friction. 8, 221–300 (2020)
Stott, F.H.: High-temperature sliding wear of metals. Tribol. Int. 35, 489–495 (2002)
Stott, F.H., Lin, D.S., Wood, G.C.: The structure and mechanism of formation of the ‘glaze’ oxide layers produced on nickel-based alloys during wear at high temperatures. Corros. Sci. 13, 449–469 (1973)
Jiang, J., Stott, F.H., Stack, M.M.: The effect of partial pressure of oxygen on the tribological behaviour of a nickel-based alloy, N80A, at elevated temperatures.Wear. ;203–204:615 – 25. (1997)
Bayata, F., Alpas, A.T.: The high temperature wear mechanisms of iron-nickel steel (NCF 3015) and nickel based superalloy (inconel 751) engine valves.Wear. ;480–481. (2021)
Lawen, J.L. Jr., Calabrese, S.J., Dinc, O.S.: Wear Resistance of Super Alloys at Elevated Temperatures. J. Tribol. 120, 339–344 (1998)
Stoyanov, P., Dawag, L., Goberman, D.G., Shah, D.: Friction and Wear Characteristics of Single Crystal Ni-Based Superalloys at Elevated Temperatures.Tribology Letters. ;66. (2018)
Rynio, C., Hattendorf, H., Klöwer, J., Eggeler, G.: On the physical nature of tribolayers and wear debris after sliding wear in a superalloy/steel tribosystem at 25 and 300°C. Wear. 317, 26–38 (2014)
Wood, P.D., Evans, H.E., Ponton, C.B.: Investigation into the wear behaviour of Tribaloy 400C during rotation as an unlubricated bearing at 600°C. Wear. 269, 763–769 (2010)
Blau, P.J.: Elevated-temperature tribology of metallic materials. Tribol. Int. 43, 1203–1208 (2010)
Li, L., He, K., Sun, S., Yang, W., Yue, Z., Wan, H.: High-temperature friction and wear features of Nickel-based single crystal superalloy.Tribology Letters. ;68. (2020)
Dreano, A., Fouvry, S., Sao-Joao, S., Galipaud, J., Guillonneau, G.: The formation of a cobalt-based glaze layer at high temperature: A layered structure.Wear. ;440–441. (2019)
Hager, C.H., Sanders, J., Sharma, S., Voevodin, A., Segall, A.: The effect of temperature on gross slip fretting wear of cold-sprayed nickel coatings on Ti6Al4V interfaces. Tribol. Int. 42, 491–502 (2009)
Aouadi, S.M., Gao, H., Martini, A., Scharf, T.W., Muratore, C.: Lubricious oxide coatings for extreme temperature applications: A review. Surf. Coat. Technol. 257, 266–277 (2014)
Korashy, A., Attia, H., Thomson, V., Oskooei, S.: Fretting wear behavior of cobalt - Based superalloys at high temperature – A comparative study.Tribology International. ;145. (2020)
Viat, A., Dreano, A., Fouvry, S., De Barros Bouchet, M.-I., Henne, J.-F.: Fretting wear of pure cobalt chromium and nickel to identify the distinct roles of HS25 alloying elements in high temperature glaze layer formation. Wear. 376–377, 1043–1054 (2017)
Huang, C., Zou, B., Liu, Y., Zhang, S., Huang, C., Li, S.: Study on friction characterization and wear-resistance properties of Si3N4 ceramic sliding against different high-temperature alloys. Ceram. Int. 42, 17210–17221 (2016)
Feng, K., Shao, T.: The evolution mechanism of tribo-oxide layer during high temperature dry sliding wear for nickel-based superalloy.Wear. ;476. (2021)
Unal, O., Varol, R.: Surface severe plastic deformation of AISI 304 via conventional shot peening, severe shot peening and repeening. Appl. Surf. Sci. 351, 289–295 (2015)
Lai, P., Gao, X., Tang, L., Guo, X., Zhang, L.: Effect of temperature on fretting wear behavior and mechanism of alloy 690 in water. Nucl. Eng. Des. 327, 51–60 (2018)
Chua, Y.T., Stair, P.C., Wachs, I.E.: A Comparison of Ultraviolet and Visible Raman Spectra of Supported Metal Oxide Catalysts. J. Phys. Chem. B. 105, 8600–8606 (2001)
Ozkan, E., Lee, S.-H., Tracy, C.E., Pitts, J.R., Deb, S.K.: Comparison of electrochromic amorphous and crystalline tungsten oxide films. Sol. Energy Mater. Sol. Cells. 79, 439–448 (2003)
Kim, J.H., Hwang, I.S.: Development of an in situ Raman spectroscopic system for surface oxide films on metals and alloys in high temperature water. Nucl. Eng. Des. 235, 1029–1040 (2005)
Mironova-Ulmane, N., Kuzmin, A., Steins, I., Grabis, J., Sildos, I., Pärs, M.: Raman scattering in nanosized nickel oxide NiO. Journal of Physics: Conference Series. ;93. (2007)
Rashad, M., Rüsing, M., Berth, G., Lischka, K., Pawlis, A.: CuO and Co3O4Nanoparticles: Synthesis, Characterizations, and Raman Spectroscopy. J. Nanomaterials. 2013, 1–6 (2013)
Monnereau, O., Tortet, L., Grigorescu, C., Savastru, D., Iordanescu, C., Guinneton, F., et al.: Chromium oxides mixtures in PLD films investigated by Raman spectroscopy. J. Optoelectron. Adv. Mater. 12, 1752 (2010)
Hamdy, M.M., Waterhouse, R.B.: The fretting wear of Ti-6Al-4v and aged inconel 718 at elevated temperatures. Wear. 71, 237–248 (1981)

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Editorial decision: Major Revisions Needed
26 Jun, 2022
Reviews received at journal
16 May, 2022
Reviewers invited by journal
16 May, 2022
Editor assigned by journal
14 May, 2022
First submitted to journal
11 May, 2022

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Tribological behavior of a shot-peened nickel-based single crystal superalloy at high temperature

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Abstract

Figures

1. Introduction

2. Materials and method

2.1 Materials and specimen

2.2 Friction test

2.3 Characterization

3. Results and discussion

3.1 Characterization of the SP-NBSC superalloy

3.2 Tribological performance

3.3 Analysis of the wear scar

3.4 Cross-sectional morphology

3.5 Wear mechanism

4. Conclusion

Declarations

Declarations

Acknowledgements

References

Status:

Version 1