Fabrication and Tribological Properties of Copper Matrix Solid Self-Lubricant Composites Reinforced with Ni/NbSe2 Composites

This paper presents a facile and effective method for preparing Ni/NbSe2 composites in order to improve the wettability of NbSe2 and copper matrix, which is helpful in enhancing the friction-reducing and anti-wear properties of copper-based composites. The powder metallurgy (P/M) technique was used to fabricate copper-based composites with different weight fractions of Ni/NbSe2, and tribological properties of composites were evaluated by using a ball-on-disk friction-and-wear tester. Results indicated that tribological properties of copper-based composites were improved by the addition of Ni/NbSe2. In particular, copper-based composites containing 15 wt.% Ni/NbSe2 showed the lowest friction coefficient (0.16) and wear rate (4.1 × 10−5 mm3·N−1·m−1) among all composites.


Introduction
Owing to its low cost, ease of production, and excellent thermal and electrical conductivities, copper and its composites have always attracted considerable interest among all metallic materials [1][2][3][4]. These merits have made copper-based composites become potential materials in industrial applications, such as for automobiles, marines, and machinery. However, especially in the field of tribology, the application of copper and its composites was seriously limited due to their low hardness and strength. Therefore, it is of vital significance to develop the friction-reducing and anti-wear properties of copper-based composites. So far, filling various suitable solid lubricants might be an effective method. Kumar and Kovacik et al. [5,6] found that copper matrix composites exhibit outstanding tribological properties compared with pure copper by the addition of MoS 2 or graphite. However, MoS 2 shows excellent lubricating properties under dry conditions, and graphite is a famous solid lubricant in a non-vacuum environment. Besides, both graphite and MoS 2 could decrease load-carrying capacity and wear rate due to poor mechanical properties [7]. Therefore, the distinct shortcomings of MoS 2 and graphite greatly limit the development of copper-based composites.
The exploration of effective solid lubricants is currently imperative. Transition metal dichalcogenides NbSe 2 possesses a hexagonal laminated structure and outstanding self-lubrication ability, such as that of graphite and MoS 2 [8]. Moreover, the mechanical property of NbSe 2 is higher than that of graphite and MoS 2 , which could further improve the wear resistance of copper-based composites. Therefore, NbSe 2 can be used as the substitute of MoS 2 or graphite. Some researchers, such as Shi et al. [9] found that the friction-reducing and anti-wear properties of copper-based composites with nano-sized NbSe 2 improved compared to those with micro-sized NbSe 2 , and the formation of

Fabrication of Materials
Firstly, NbSe 2 were successfully synthesized by a facile thermal solid-state reaction [14]; then, the as-prepared NbSe 2 was coated with Ni layers by electroless plating [15]. Details of the electroless plating are as follows: NbSe 2 powder was firstly coarsened by ultrasonic treatment in a concentrated H 2 SO 4 solution for 20 min. Then, they were further sensitized and activated by immersion in an aqueous solution containing HCl (20 ml/L) and SnCl 2 (20 g/L), and 0.3% AgNO 3 , respectively. The NbSe 2 was immersed in copper plating solution for 30 min with agitation. (Table 1 exhibits the chemical components of the copper plating solution.) Finally, the copper-coated NbSe 2 was dried in an oven at 100 • C for 12 h. The mixed powders of copper and Ni/NbSe 2 were ball-milled by a planetary high-energy mill machine (QM-SP2, NanDa Instrument Company, Nanjing, China) in a high-purity argon atmosphere for more than 600 min at a rotational speed of 250 rpm. The fraction of Ni/NbSe 2 was selected to be 0, 5 wt.%, 10 wt.%, and 15 wt.% (designed as CNE0, CNE5, CNE10, and CNE15, respectively) for ascertaining the effect of the solid lubricant. Then, the above mixed powders were cold-pressed at 400 MPa and sintered pressurelessly at 800 • C in argon gas for 120 min. The samples were machined and polished before the properties test. For comparison, copper-based composite with 15 wt.% NbSe 2 (denoted as CN15) was fabricated using the same processing parameters.

Characterization
The morphology of Ni/NbSe 2 was characterized by a field emission scanning electron microscope (FESEM, JSM-7001F, JEOL, Tokyo, Japan) and TEM (Transmission electron microscope) (JEOL-2010, JEOL, Tokyo, Japan). Micro-hardness was measured by a Vickers indenter (MH-5). 500 g and 15 s were a normal load and dwell time, respectively. The densities of composites were measured by using the Archimedes method. A ball-on-disk friction-and-wear tester (TRN) was used to evaluate the tribological properties of the samples. The disks and the counterpart were as-prepared materials and the GCr15 steel ball had a diameter of 4 mm, respectively. The surface of the disks and the counterpart were cleaned with acetone, and then dried in a vacuum before the wear test. Each test was conducted at the condition of 5N-0.00612 m/s for 20 min. The wear rate was expressed as the wear volume divided by the applied load and sliding distance [16]. The morphology and phase compositions on the wear scars of specimens were examined via a field emission scanning electron microscope (FESEM, JSM-7001F) equipped with EDS (Energy Dispersive Spectrometer). Three repeated wear tests were conducted on each sample, and the mean value was shown.

Microstructure of Composites
The morphological and structural characteristics of composites have been characterized in Figure 1. As shown in Figure 1a, NbSe 2 had a mainly hexagonal structure, with the average diameter being about 2 µm and 200 nm in thickness. Figure 1b shows the morphology of Ni/NbSe 2 . The products consisted of a large number of Ni nanoparticles and sheet-like NbSe 2 . It can be clearly seen that Ni nanoparticles with average sizes of about 30 nm in diameter were well-dispersed and attached to NbSe 2 sheets, which was consistent with TEM images in Figure 1d. The morphology of Ni/NbSe2 was characterized by a field emission scanning electron microscope (FESEM, JSM-7001F, JEOL, Tokyo, Japan) and TEM (Transmission electron microscope) (JEOL-2010, JEOL, Tokyo, Japan).
Micro-hardness was measured by a Vickers indenter (MH-5). 500 g and 15 s were a normal load and dwell time, respectively. The densities of composites were measured by using the Archimedes method. A ball-on-disk friction-and-wear tester (TRN) was used to evaluate the tribological properties of the samples. The disks and the counterpart were as-prepared materials and the GCr15 steel ball had a diameter of 4 mm, respectively. The surface of the disks and the counterpart were cleaned with acetone, and then dried in a vacuum before the wear test. Each test was conducted at the condition of 5N-0.00612 m/s for 20 min. The wear rate was expressed as the wear volume divided by the applied load and sliding distance [16]. The morphology and phase compositions on the wear scars of specimens were examined via a field emission scanning electron microscope (FESEM, JSM-7001F) equipped with EDS (Energy Dispersive Spectrometer). Three repeated wear tests were conducted on each sample, and the mean value was shown.

Microstructure of Composites
The morphological and structural characteristics of composites have been characterized in Figure 1. As shown in Figure 1a, NbSe2 had a mainly hexagonal structure, with the average diameter being about 2 µm and 200 nm in thickness. Figure 1b shows the morphology of Ni/NbSe2. The products consisted of a large number of Ni nanoparticles and sheet-like NbSe2. It can be clearly seen that Ni nanoparticles with average sizes of about 30 nm in diameter were well-dispersed and attached to NbSe2 sheets, which was consistent with TEM images in Figure 1d.   Figure 2 shows the microstructure of sintered CN15 and CNE15, which was characterized by optical micrographs after metallographic preparation. It can also be observed that the microstructure of specimen CNE15 was more homogeneous than that of specimen CN15. Figure 3 indicates the compactness of Cu/Ni/NbSe 2 composites. It can clearly be seen that the compactness of specimen CN15 is lower than that of specimen CNE15. According to Figures 2 and 3, it can be concluded that Ni-coated NbSe 2 does not benefit the uniform dispersion of NbSe 2 in the copper matrix, but further enhances the interfacial combination [16,17]. For specimen CN15, it can be seen that the NbSe 2 phases have some agglomeration in the copper matrix, significantly deteriorating the physical and tribological properties of the composites [18].  Figure 2 shows the microstructure of sintered CN15 and CNE15, which was characterized by optical micrographs after metallographic preparation. It can also be observed that the microstructure of specimen CNE15 was more homogeneous than that of specimen CN15. Figure 3 indicates the compactness of Cu/Ni/NbSe2 composites. It can clearly be seen that the compactness of specimen CN15 is lower than that of specimen CNE15. According to Figure 2 and Figure 3, it can be concluded that Ni-coated NbSe2 does not benefit the uniform dispersion of NbSe2 in the copper matrix, but further enhances the interfacial combination [16,17]. For specimen CN15, it can be seen that the NbSe2 phases have some agglomeration in the copper matrix, significantly deteriorating the physical and tribological properties of the composites [18].   Table 2 lists the compositions, densities, and hardness of composites. The densities of specimen CNE5, CNE10, CNE15, and CNE0 were 7.1 g·cm −3 , 6.9 g·cm −3 , 6.7 g·cm −3 , and 7.3 g·cm −3 , respectively. Compared with specimen CNE0, specimen CNE5, CNE10, and CNE15 showed lower densities for the addition of low-density NbSe2 [19]. Besides, the hardness of specimen CNE5, CNE10, CNE15, and CNE0 were 90 HV, 95 HV, 108 HV, and 75 HV, respectively. Specimen CNE5, CNE10, and CNE15 exhibited higher hardness than specimen CNE0 due to the dispersion strengthening effect of Ni/NbSe2. However, specimen CN15 possessed lower hardness than specimen CNE15. The presence of Ni with high hardness enhanced the mechanical properties of composites [20].  Figure 2 shows the microstructure of sintered CN15 and CNE15, which was characterized by optical micrographs after metallographic preparation. It can also be observed that the microstructure of specimen CNE15 was more homogeneous than that of specimen CN15. Figure 3 indicates the compactness of Cu/Ni/NbSe2 composites. It can clearly be seen that the compactness of specimen CN15 is lower than that of specimen CNE15. According to Figure 2 and Figure 3, it can be concluded that Ni-coated NbSe2 does not benefit the uniform dispersion of NbSe2 in the copper matrix, but further enhances the interfacial combination [16,17]. For specimen CN15, it can be seen that the NbSe2 phases have some agglomeration in the copper matrix, significantly deteriorating the physical and tribological properties of the composites [18].   Table 2 lists the compositions, densities, and hardness of composites. The densities of specimen CNE5, CNE10, CNE15, and CNE0 were 7.1 g·cm −3 , 6.9 g·cm −3 , 6.7 g·cm −3 , and 7.3 g·cm −3 , respectively. Compared with specimen CNE0, specimen CNE5, CNE10, and CNE15 showed lower densities for the addition of low-density NbSe2 [19]. Besides, the hardness of specimen CNE5, CNE10, CNE15, and CNE0 were 90 HV, 95 HV, 108 HV, and 75 HV, respectively. Specimen CNE5, CNE10, and CNE15 exhibited higher hardness than specimen CNE0 due to the dispersion strengthening effect of Ni/NbSe2. However, specimen CN15 possessed lower hardness than specimen CNE15. The presence of Ni with high hardness enhanced the mechanical properties of composites [20].  Table 2 lists the compositions, densities, and hardness of composites. The densities of specimen CNE5, CNE10, CNE15, and CNE0 were 7.1 g·cm −3 , 6.9 g·cm −3 , 6.7 g·cm −3 , and 7.3 g·cm −3 , respectively. Compared with specimen CNE0, specimen CNE5, CNE10, and CNE15 showed lower densities for the addition of low-density NbSe 2 [19]. Besides, the hardness of specimen CNE5, CNE10, CNE15, and CNE0 were 90 HV, 95 HV, 108 HV, and 75 HV, respectively. Specimen CNE5, CNE10, and CNE15 exhibited higher hardness than specimen CNE0 due to the dispersion strengthening effect of Ni/NbSe 2 . However, specimen CN15 possessed lower hardness than specimen CNE15. The presence of Ni with high hardness enhanced the mechanical properties of composites [20].

Tribological Properties
The variation of friction coefficients and wear rates of all five materials at the condition of 5N-0.00612m/s are illustrated in Figure 4. In Figure 4a, it can be seen that specimen CNE0 shows the highest and most unstable friction coefficient value of around 0.42, whereas with Ni/NbSe 2 composites added, the composites exhibit a relatively low and stable friction coefficient value. In particular, composites show the lowest and most stable friction coefficient of about 0.16 as the Ni/NbSe 2 increases to 15 wt.%. Besides, specimen CN15 shows a lower friction coefficient of about 0.27 than specimen CNE0, but it is higher than specimen CNE15.

Tribological Properties
The variation of friction coefficients and wear rates of all five materials at the condition of 5N-0.00612m/s are illustrated in Figure 4. In Figure 4a, it can be seen that specimen CNE0 shows the highest and most unstable friction coefficient value of around 0.42, whereas with Ni/NbSe2 composites added, the composites exhibit a relatively low and stable friction coefficient value. In particular, composites show the lowest and most stable friction coefficient of about 0.16 as the Ni/NbSe2 increases to 15 wt.%. Besides, specimen CN15 shows a lower friction coefficient of about 0.27 than specimen CNE0, but it is higher than specimen CNE15.
As can be seen in Figure 4b, the wear rate of composites obviously decrease due to the addition of Ni/NbSe2. It can be clearly seen that the wear rate falls from 7.3 × 10 −3 mm 3 ·N −1 ·m −1 to the lowest value of 4.1 × 10 −5 mm 3 ·N −1 ·m −1 as the Ni/NbSe2 content increases to 15 wt.%. However, the wear rate of specimen CN15 is about 2.3 × 10 −3 mm 3 ·N −1 ·m −1 , which is higher than that of specimen CNE15. Therefore, specimen CNE15 possessed the lowest wear rate, which decreased by more than 99% and 98% in comparison with specimens CNE0 and CN15, respectively. Thus, according to the above experimental results, Ni/NbSe2 showed better friction reduction and wear resistance than NbSe2 during the rubbing process. Specimen CNE15 with the lowest friction coefficient and wear rate among all specimens was also proved by non-contact, three-dimensional cross-section images of wear tracks. As can be seen in Figure 5, the wear width of copper-based composites decrease with the addition of Ni/NbSe2. The wear width of specimen CNE5 is around 1.6 mm, which clearly decreased by 20% compared with that of specimen CNE0. In particular, specimen CNE15 possessed minimal wear width of about 0.45 mm, decreasing by 77%, 72%, and 52% compared with that of specimens CNE0, CNE5, and CN15, respectively.
Besides, the changing trend of wear width of composites was consistent with that of the wear depth. Therefore, the results were consistent with Figure 4b. As can be seen in Figure 4b, the wear rate of composites obviously decrease due to the addition of Ni/NbSe 2 . It can be clearly seen that the wear rate falls from 7.3 × 10 −3 mm 3 ·N −1 ·m −1 to the lowest value of 4.1 × 10 −5 mm 3 ·N −1 ·m −1 as the Ni/NbSe 2 content increases to 15 wt.%. However, the wear rate of specimen CN15 is about 2.3 × 10 −3 mm 3 ·N −1 ·m −1 , which is higher than that of specimen CNE15. Therefore, specimen CNE15 possessed the lowest wear rate, which decreased by more than 99% and 98% in comparison with specimens CNE0 and CN15, respectively. Thus, according to the above experimental results, Ni/NbSe 2 showed better friction reduction and wear resistance than NbSe 2 during the rubbing process.
Specimen CNE15 with the lowest friction coefficient and wear rate among all specimens was also proved by non-contact, three-dimensional cross-section images of wear tracks. As can be seen in Figure 5, the wear width of copper-based composites decrease with the addition of Ni/NbSe 2. The wear width of specimen CNE5 is around 1.6 mm, which clearly decreased by 20% compared with that of specimen CNE0. In particular, specimen CNE15 possessed minimal wear width of about 0.45 mm, decreasing by 77%, 72%, and 52% compared with that of specimens CNE0, CNE5, and CN15, respectively.

Worn Surface Morphologies
The worn surfaces of specimens CNE0, CNE5, CNE15, and CN15 after wear tests are shown in Figure 6. Figure 6a shows the worn surface morphologies of specimen CNE0. Furrows, plastic Besides, the changing trend of wear width of composites was consistent with that of the wear depth. Therefore, the results were consistent with Figure 4b.

Worn Surface Morphologies
The worn surfaces of specimens CNE0, CNE5, CNE15, and CN15 after wear tests are shown in Figure 6. Figure 6a shows the worn surface morphologies of specimen CNE0. Furrows, plastic deformation, and clear adhesive took place on the worn surface of specimen CNE0, which was attributed to severe plastic deformation and adhesive wear [12,21]. This was consistent with the result of pure copper possessing the highest wear rate. In Figure 6b, grooves and wear debris can be observed on the worn surface of specimen CNE5, suggesting that the wear mechanism was dominant by micro-cutting and micro-ploughing, which meant that the addition of Ni/NbSe 2 obviously changed the worn morphologies [10]. Besides, the grooves were indeed alleviated by the addition of Ni/NbSe 2 .
Materials 2018, 11, x FOR PEER REVIEW 7 of 11 deformation, and clear adhesive took place on the worn surface of specimen CNE0, which was attributed to severe plastic deformation and adhesive wear [12,21]. This was consistent with the result of pure copper possessing the highest wear rate. In Figure 6b, grooves and wear debris can be observed on the worn surface of specimen CNE5, suggesting that the wear mechanism was dominant by micro-cutting and micro-ploughing, which meant that the addition of Ni/NbSe2 obviously changed the worn morphologies [10]. Besides, the grooves were indeed alleviated by the addition of Ni/NbSe2. As can be seen in Figure 6c, there is slight plastic deformation and micro-scuffing on the worn surface of specimen CNE15. There is also the presence of a smooth, complete, and dense tribo-film, which helped to lower the friction coefficient and wear rate of specimen CNE15. However, the shape of the wear grove is not regular (Figure 5c) and its width and depth is not constant, indicating that the contact area and friction force oscillated and could have influenced the tribo-film. Figure 6d exhibits the worn surface of specimen CN15. It can be seen that the worn surface is covered by the discontinuous tribo-film, which was responsible for increased friction coefficient of wear rate.

Phase Composition of Worn Surface
The corresponding EDS of the worn surface on the specimens is illustrated in Table 3. The elemental mapping revealed that Cu and O, as well as a small amount of Fe were distributed uniformly on the worn surface, showing that some oxides of copper and iron were formed on the worn surface of specimen CNE15 during the sliding process, and the Fe element was transferred from the counterpart of the GCr15 steel ball. This means that severe oxidative wear could be found on the worn surface of Cu-based composites during the sliding process. As can be seen in Figure 6c, there is slight plastic deformation and micro-scuffing on the worn surface of specimen CNE15. There is also the presence of a smooth, complete, and dense tribo-film, which helped to lower the friction coefficient and wear rate of specimen CNE15. However, the shape of the wear grove is not regular (Figure 5c) and its width and depth is not constant, indicating that the contact area and friction force oscillated and could have influenced the tribo-film. Figure 6d exhibits the worn surface of specimen CN15. It can be seen that the worn surface is covered by the discontinuous tribo-film, which was responsible for increased friction coefficient of wear rate.

Phase Composition of Worn Surface
The corresponding EDS of the worn surface on the specimens is illustrated in Table 3. The elemental mapping revealed that Cu and O, as well as a small amount of Fe were distributed uniformly on the worn surface, showing that some oxides of copper and iron were formed on the worn surface of specimen CNE15 during the sliding process, and the Fe element was transferred from the counterpart of the GCr15 steel ball. This means that severe oxidative wear could be found on the worn surface of Cu-based composites during the sliding process. Besides, the elements Ni, Nb, and Se were evenly distributed on the worn surface except for the elements of Cu, Fe, and O, indicating that the tribo-film and oxide layer were formed on the worn surface of specimen CNE15, which remarkably improved the tribological properties of copper-based composites [19]. Besides, as can be seen in Table 2, the content of the O element decreased with the addition of Ni/NbSe 2 compared with specimen CNE0. It can thus be concluded that a massive amount of Ni were squeezed out of the matrix to spread out on the wear scar, which hindered the oxidation reaction rate and lowered the oxide forming rate, leading to the decrease in O content [22].
In Figure 7, the micro-Raman analyzer gives better insight into the local phase constitutes of the worn and unworn surfaces of specimen CNE15. By comparing the Raman spectrum of the tested and un-tested areas, NbSe 2 , Fe 2 O 3 , and CuO were found on the worn surface, and the intensity of NbSe 2 was the strongest among all phases. In contrast, only relatively weak peak centering of about 230 cm −1 of NbSe 2 was observed on the unworn surface. CuO was formed by the oxidation of metallic copper, and Fe 2 O 3 was transferred from the counterpart GCr15 steel. The results were consistent with the EDS analysis. Besides, the elements Ni, Nb, and Se were evenly distributed on the worn surface except for the elements of Cu, Fe, and O, indicating that the tribo-film and oxide layer were formed on the worn surface of specimen CNE15, which remarkably improved the tribological properties of copper-based composites [19]. Besides, as can be seen in Table 2, the content of the O element decreased with the addition of Ni/NbSe2 compared with specimen CNE0. It can thus be concluded that a massive amount of Ni were squeezed out of the matrix to spread out on the wear scar, which hindered the oxidation reaction rate and lowered the oxide forming rate, leading to the decrease in O content [22].
In Figure 7, the micro-Raman analyzer gives better insight into the local phase constitutes of the worn and unworn surfaces of specimen CNE15. By comparing the Raman spectrum of the tested and un-tested areas, NbSe2, Fe2O3, and CuO were found on the worn surface, and the intensity of NbSe2 was the strongest among all phases. In contrast, only relatively weak peak centering of about 230 cm −1 of NbSe2 was observed on the unworn surface. CuO was formed by the oxidation of metallic copper, and Fe2O3 was transferred from the counterpart GCr15 steel. The results were consistent with the EDS analysis.  Thus, it can be concluded that NbSe2 was the predominant phase in the worn surface, and the presence of NbSe2 was responsible for the improvement of tribological properties [23][24][25][26][27]. However, Ni could not be detected by the micro-Raman, meaning that it could not be observed on the worn surface.
The wear mechanism of composites with NbSe2 and Ni/NbSe2 are shown in Figure 8. For Thus, it can be concluded that NbSe 2 was the predominant phase in the worn surface, and the presence of NbSe 2 was responsible for the improvement of tribological properties [23][24][25][26][27]. However, Ni could not be detected by the micro-Raman, meaning that it could not be observed on the worn surface.
The wear mechanism of composites with NbSe 2 and Ni/NbSe 2 are shown in Figure 8. For specimen CN15, NbSe 2 squeezed out from the matrix due to the combined action of load extrusion and frictional heat were easily sheared to form the protective tribo-layer on the worn surface during the rubbing process, which avoided the direct contact between the substrate and friction pair. Besides, NbSe 2 could continuously repair the tribo-layer under the load. However, the wettability between NbSe 2 and substrate was poor, and some NbSe 2 had a certain degree of agglomeration in the matrix, which led to a decrease in the mechanical properties of specimen CN15. Therefore, the formed tribo-layer was not tightly bonded to the substrate, and was easily broken and peeled off by the friction pair wear, resulting in serious wear of the composite. and frictional heat were easily sheared to form the protective tribo-layer on the worn surface during the rubbing process, which avoided the direct contact between the substrate and friction pair. Besides, NbSe2 could continuously repair the tribo-layer under the load. However, the wettability between NbSe2 and substrate was poor, and some NbSe2 had a certain degree of agglomeration in the matrix, which led to a decrease in the mechanical properties of specimen CN15. Therefore, the formed tribolayer was not tightly bonded to the substrate, and was easily broken and peeled off by the friction pair wear, resulting in serious wear of the composite. For specimen CNE15, Ni/NbSe2 is tightly bound to the matrix and evenly distributed. During the rubbing process, Ni/NbSe2 was squeezed out from the matrix under the action of load extrusion and frictional heat. Due to the tight interface between the Ni-coated NbSe2 and copper matrix, the formed tribo-layer adhered tightly to the worn surface. The tribo-layer subjected to the shearing force of friction pair was easy to slip without breaking or falling off, thereby effectively improving the antifriction and wear resistance of Cu-based composites. Besides, Ni nanoparticles with high hardness acting as micro-bearings could further decrease the friction coefficient and wear rate of composites. Therefore, the synergism of Ni and NbSe2 exhibited superior friction-reducing and anti-wear properties of Cu-based composites. Moreover, Ni/NbSe2 possessed better oxidation resistance than NbSe2, which could further reduce the oxidative wear of composites.

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Ni/NbSe2 composites were successfully prepared by electroless plating. Ni nanoparticles with a particle size of 30 nm were uniformly coated on the surface of NbSe2.

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Copper-based composites exhibited lower friction coefficients and wear rates with the addition of Ni/NbSe2, which was attributed to the formation of the tribo-layer on the worn surface during the sliding process. Friction-reducing and anti-wear properties of Cu-based composites were improved significantly, which was attributed to a good interfacial combination between the NbSe2 and copper matrix, as well as the synergism of Ni and NbSe2. Moreover, Ni/NbSe2 possessed better oxidation resistance than NbSe2, which could further reduce the oxidative wear of composites.
Funding: This work was financially supported by National Natural Science Foundation of China (51275213, 51302112), the Jiangsu National Nature Science Foundation (BK2011534, BK2011480), the Scientific and For specimen CNE15, Ni/NbSe 2 is tightly bound to the matrix and evenly distributed. During the rubbing process, Ni/NbSe 2 was squeezed out from the matrix under the action of load extrusion and frictional heat. Due to the tight interface between the Ni-coated NbSe 2 and copper matrix, the formed tribo-layer adhered tightly to the worn surface. The tribo-layer subjected to the shearing force of friction pair was easy to slip without breaking or falling off, thereby effectively improving the anti-friction and wear resistance of Cu-based composites. Besides, Ni nanoparticles with high hardness acting as micro-bearings could further decrease the friction coefficient and wear rate of composites. Therefore, the synergism of Ni and NbSe 2 exhibited superior friction-reducing and anti-wear properties of Cu-based composites. Moreover, Ni/NbSe 2 possessed better oxidation resistance than NbSe 2 , which could further reduce the oxidative wear of composites.

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Ni/NbSe 2 composites were successfully prepared by electroless plating. Ni nanoparticles with a particle size of 30 nm were uniformly coated on the surface of NbSe 2 .

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Copper-based composites exhibited lower friction coefficients and wear rates with the addition of Ni/NbSe 2 , which was attributed to the formation of the tribo-layer on the worn surface during the sliding process. Friction-reducing and anti-wear properties of Cu-based composites were improved significantly, which was attributed to a good interfacial combination between the NbSe 2 and copper matrix, as well as the synergism of Ni and NbSe 2 . Moreover, Ni/NbSe 2 possessed better oxidation resistance than NbSe 2 , which could further reduce the oxidative wear of composites.