3.2. Microstructure
Figure 2 shows the SEM images of the whole and bonding region of the laser cladding coating. In
Figure 2a, the whole layer was smooth and had no crack, which had a good quality, however, it can also be seen that there were some holes. The bonding region between the cladding layer and substrate was obvious. In
Figure 2b, it can be seen that the layer was connected with the substrate, which had a metallurgical bonding. The layer also had some smaller crystals than the bonding and substrate. Some dendrite crystals appeared at the bottom of layer as shown at the location of the arrows, because the cooling rate was smaller than that of the upper layer; therefore, the crystals had more time to grow.
Figure 3 shows the SEM images in the middle and bonding region of the laser cladding coating. In
Figure 3a, it can be seen that there were many cellular crystals and a few dendrites. Because the overcooling degree and temperature gradient became smaller in the middle of laser cladding coating, the direction of crystal growth was not obvious. Meanwhile, the decomposed ceramic particles WC and TiC also needed some laser energy, which hindered the crystal growth and formed some small compounds. So there were more cellular crystals in the middle of the laser cladding coating. When the cooling rate was small, a few dendrites can also appear in the middle of the laser cladding coating. In
Figure 3b, it can be seen that the crystals in the bonding region were bigger than those in the middle of the laser cladding coating. The reason was that the bonding region had a long time to be liquid, which offered the crystal enough time to grow. On the other hand, the molten pool in the bonding region included more of the Fe element, which formed more Fe and Ni solid solution. There were a few ceramic particles to form crystal nuclei in the bonding region. Therefore, a lot of big crystals appeared in the bonding region.
Figure 4 shows the SEM images and elemental distribution of W, Ti, C, Fe and Ni. In
Figure 4a, it can be seen that there were some particles in the background. The size of the particles was in the range of 0.5 μm to 3 μm. In order to investigate these particles and background, an elemental distribution was obtained. In
Figure 4b–d, the particles included more W, Ti, and C elements. It can be known that those were WC and TiC particles combined with analysis of the main phases. The WC and TiC ceramic particles appeared in the crystals and boundary. Some carbides were smaller than 1 μm, which had the function of fine grain strengthening. In
Figure 4e,f, the background area had more Fe and Ni elements, and they formed the Fe and Ni solid solution. Therefore, the crystal took the Fe and Ni solid solution as the background, and the carbides were uniformly distributed in the interior and boundary of the crystal. The combination of those phases was helpful in improving the properties of laser cladding coating.
Figure 5 shows the SEM images and points 1 and 2 inside the cellular crystal. It can be seen that the crystals were basically cellular crystals. In order to investigate the elemental distribution inside the cellular crystals, points 1 and 2 were selected in
Figure 5a,b. In
Figure 5a, point 1 was in the cellular crystal, but point 2 was the white particle in the cellular crystal.
Table 3 includes the percentage of elemental distribution at point 1 and 2 inside the cellular crystal. Point 1 had the Fe element of 67.0 wt.% and the Ni element of 14.8 wt.%; meanwhile, there were some Cr, W, and Si elements. So, the main phase was γ~(Fe, Ni) in the cellular crystal. Some white particles appeared inside the cellular crystal as shown with point 2. From
Table 3, it can be known that point 2 had the Fe element of 41.6wt.% and the Ni element of 5.2 wt.%, and there were less than those of point 1. The reason was that the Cr and C elements increased. Therefore, the white particle may be some carbide, such Cr
23C
6 and WC.
Figure 6 shows the SEM images and points 3 and 4 inside the cellular crystal. It can be seen that the crystals were cellular and dendrite crystals. In order to investigate the elemental distribution around the crystals, points 3 and 4 were selected in
Figure 6a,b. In
Figure 6a, point 3 was selected around the boundary of cellular crystal and point 4 was selected around the boundary of dendrite crystal.
Table 4 includes the percentage of elemental distribution at point 3 and 4 around the boundary of cellular and dendrite crystals. Point 3 had the Fe element of 50.2 wt.%, the Cr element of 29.0 wt.%, and the Ni element of 5.3 wt.%; meanwhile, there were some C, W, and Si elements. Compared with point 1, the boundary had less Fe and Ni elements and more Cr and W elements. It means that the carbides appeared more around the boundary. Point 4 had the Fe element of 46.7 wt.%, the Cr element of 21.5 wt.%, and the Ni element of 9.6 wt.%; meanwhile, there were some C, W, and Si elements. Compared with point 3, the amount of the C element was more than that of point 3. It demonstrates that there were more carbides formed during the formation of dendrite crystals. Because the process of the dendrite formation was a long time compared to cellular crystals, the carbides had more time to form.
Figure 7 shows the SEM images and points 5 and 6 of the white particles around the boundary. It can be seen that the white particles were usually around the boundary of crystals. There were also some white particles inside the crystals. Points 5 and 6 were selected from different positions around the boundary of crystals. In order to investigate the white particles, the element distribution was detected.
Table 5 includes the percentage of the elemental distribution at points 5 and 6 of white particles around the boundary. Point 5 had the Fe element of 27.3 wt.% and the Ni element of 4.6 wt.% Fe and the amounts of C, Si, Cr, and W elements were 11.9, 6.1, 9.6 and 40.5 wt.%, respectively. The W element had the maximum weight compared with the other elements. It means that the main carbides were WC phase. Point 6 had the Fe element of 29.6 wt.% and the Ni element of 4.8 wt.% and the amounts of C, Si, Cr and W elements were 25.5, 16.7, 18.4 and 5.0 wt.%, respectively. Compared with point 5, point 6 of the white particles around the boundary included more Si and C elements. On the one hand, the white particles were from some carbides, such as WC and Cr
23C
6 phases. On the other hand, the segregation of the Si element appeared around the boundary of crystal.
3.4. Friction and Wear Resistance
The GCr15 ball was used for the friction and wear test. The ball radius was 6.5 mm. The length and width of the friction trace on the surface of the coating and substrate were measured and are included in
Table 6. The length and width of the friction trace on the surface of substrate were 5.58 and 2.48 mm, respectively. The length and width of the friction trace on the surface of the Ni-based coating were 5.23 and 1.35 mm, which were less than those of substrate.
In order to investigate the wear and friction, the wear volume was also calculated [
30].
Figure 9 shows the wear volume of the 45 steel substrate and Ni-based coating for 20 min. It can be seen that the wear volume of the Ni-based coating (0.16 mm
3) was less than that of the 45 steel substrate (1.1 mm
3). The wear volume of the Ni-based coating was only 14.5% of the substrate’s wear volume, which had a better wear resistance. The main reason was that the Ni-based alloy powder could form some reinforced phases, such as γ~(Fe, Ni) and Cr
23C
6, and the added WC and TiC ceramic particles formed some Cr
2Ti phases. There were still some small WC and TiC particles in the crystals. These phases increased the wear resistance of the Ni-based coating.
Figure 10 shows the friction coefficient of the substrate and Ni-based coating for 20 min. The friction coefficient of the 45 steel substrate was in the range of 0.16–0.49, and it was usually around 0.3. This friction coefficient became stable after 30 s. The friction coefficient of the Ni-based alloy coating was in the range of 0.02–0.19, and it was usually around 0.1. After 10 s, the friction coefficient became stable. It can be seen that the Ni-based coating had a smaller coefficient and more stable fluctuations. The reinforced phases and small crystals made the friction and coefficient between GCr15 ball and Ni-based alloy coating smaller.
Figure 11 shows the microscopic morphology on the sliding surface of the substrate and Ni-based coating. In
Figure 11a, it can be seen that there were some spalling zones with the large area and deep furrows on the sliding surface of the substrate. The main wear mechanism of the substrate was abrasive and adhesive wear. In
Figure 11b, there were some spalling zones with the small area and shallow furrows on the sliding surface of the cladding coating. The main wear mechanism of the cladding coating was adhesive wear. The added WC and TiC ceramic particles provided more hard particles and changed the wear mechanism. Therefore, the ceramic particles not only increase the microhardness of the cladding coating, but also offer a good wear resistance.