Research on Preparation and Properties of Carbon Fiber Reinforced Zinc-Based Aluminum Rich Alloy Composite

Aiming at the problems of poor bonding between the carbon fiber and the metal matrix and the friction and wear performance of the composite material during the preparation of carbon fiber reinforced zinc-based aluminum rich alloy composites, the carbon fiber surface metallization process was studied. Taking ZA27 as the research object, a new type of zinc-based aluminum rich alloy composite material was prepared by using surface metallized chopped carbon fibers with different contents as reinforcement materials. The microscopic morphology, element distribution and phase composition of the surface metallized carbon fiber and composite materials were characterized, and the hardness and friction and wear properties of the composite materials were tested. The results show that: the surface metallization of carbon fiber effectively reduces the diffusion of carbon elements into the matrix material during the sintering process, and improves the interface bonding between the carbon fiber and the matrix material; Compared with ZA27 alloy, the hardness of 6vt% carbon fiber is increased by 29.6%, and the average friction coefficient and wear rate are reduced by about 18.4% and 96%, respectively, indicating that the carbon fiber reinforced zinc-based aluminum rich alloy composite material optimizes the friction and wear performance of traditional materials.


Introduction
Zinc-based aluminum rich alloy is a new non-ferrous metal material that has been widely used at home and abroad in recent decades [1,2]. Due to its low melting point, low density and excellent mechanical properties [3,4], it is widely used in coal, petroleum, aerospace and other fields [5,6]. With the development of social industry, people' requirements of zinc-based aluminum rich alloy's friction and wear performance are becoming higher and higher. Therefore, in order to further enhance the anti-friction and wear-resistant properties of zinc-based aluminum rich alloys, as anti-friction and wear-resistant materials, the research and development of new zinc-based aluminum rich alloy has important practical significance [7,8]. Compared with the currently widely used copper-based wearresistant alloy, the zinc-based aluminum rich alloy ZA27 which is studied in this paper has higher strength and lower density [9], so it can play a more important role in the lightweight design of parts. In addition, the world has abundant zinc reserves and the price of zinc alloy is only about 1/3 of traditional copper alloys, which means using high aluminum zinc is becoming more economical [10].
In recent years, people have mainly studied the friction and wear properties of zincaluminum alloys from the aspects of alloying, heat treatment and modification treatment [11][12][13]. With the continuous emergence of high-performance materials such as carbon fiber, graphene, and polyethylene fiber, non-metallic materials have strengthened. The research on non-metallic materials reinforced metal matrix composites has received

Experimental Materials
The chemical composition of the new zinc-based aluminum rich alloy composite material and ZA27 alloy material developed in this experiment are shown in Table 1. The metal powder used in the experiment is chemically pure. The particle size of the ZA27 alloy powder is 300 meshes. The TC-35 type 12K carbon fiber is selected as the research object. The basic performance parameters are shown in Table 2. The chopped carbon fiber length is 0.2 mm.

Experimental Method
Due to the poor interfacial bonding between carbon fiber and ZA27 alloy, a nickel layer was plated on the surface of the carbon fiber by electroplating to improve the interfacial bonding between the carbon fiber and the matrix material. The carbon fiber reinforced zincbased aluminum rich alloy was prepared by SPS spark plasma sintering. For composite materials, the experimental process is shown in Figure 1. alloy powder is 300 meshes. The TC-35 type 12K carbon fiber is selected as the research object. The basic performance parameters are shown in Table 2. The chopped carbon fiber length is 0.2 mm.

Experimental Method
Due to the poor interfacial bonding between carbon fiber and ZA27 alloy, a nickel layer was plated on the surface of the carbon fiber by electroplating to improve the interfacial bonding between the carbon fiber and the matrix material. The carbon fiber reinforced zinc-based aluminum rich alloy was prepared by SPS spark plasma sintering. For composite materials, the experimental process is shown in Figure 1.

Pretreatment Process
Surface pretreatment is required before metallization of the carbon fiber surface. First, degumming (hot degreasing + acetone solution immersion): wash the crucible clean with deionized water, dry it in a drying furnace, take it out and add a weighing scale to the crucible put the measured carbon fiber bundle into a DRZ resistance furnace, heat it up to 400 ℃ and burn it for 120 min to burn off the organic binder on the surface, soak it in an acetone solution for 60 min to dissolve the coke, and wash it with deionized water. After being dried, it is ready for use. Its purpose is to remove the epoxy resin covering the surface of commercial carbon fiber. Then roughen the surface: place the degummed carbon fiber bundle in NaOH solution to roughen it, while rotating it on a smart mag-

Pretreatment Process
Surface pretreatment is required before metallization of the carbon fiber surface. First, degumming (hot degreasing + acetone solution immersion): wash the crucible clean with deionized water, dry it in a drying furnace, take it out and add a weighing scale to the crucible put the measured carbon fiber bundle into a DRZ resistance furnace, heat it up to 400°C and burn it for 120 min to burn off the organic binder on the surface, soak it in an acetone solution for 60 min to dissolve the coke, and wash it with deionized water. After being dried, it is ready for use. Its purpose is to remove the epoxy resin covering the surface of commercial carbon fiber. Then roughen the surface: place the degummed carbon fiber bundle in NaOH solution to roughen it, while rotating it on a smart magnetic stirrer and heating it for 15 min, then take out the carbon fiber bundle and rinse it with deionized water until it is neutral, and put it in electric heating drying in a constant temperature drying box in order to increase the surface roughness of the fiber and the polar group, thereby increasing the surface activity, improving the affinity with the metal base, and prepare for the metallization of the carbon fiber surface.

Metallization of Carbon Fiber Surface
The carbon fiber bundle after the above pretreatment is placed in an electroplating device for electroplating. The composition and process parameters of the electroplating solution are shown in Tables 3 and 4. The steps of nickel electroplating in this experiment are as follows: Step 1, weigh the required nickel sulfate, nickel chloride, boric acid and sodium dodecyl sulfate, and dissolve them in an appropriate amount of deionized water, mix them in sequence, and then mix them. Add hydrochloric acid dropwise to the plating solution, adjust the pH of the plating solution to 3, and dilute the volume to 500 mL; Step 2, use sandpaper to remove the oxides on the surface of the high-purity nickel plate, ultrasonically clean for 30 min, and rinse with deionized water; Step 3, the carbon fiber bundle and the high-purity nickel plate are, respectively, fixed to the cathode and anode of the power supply, and placed in the electroplating device as shown in Figure 2, electroplating is carried out by controlling the current, voltage and electroplating time, and then washed with deionized water and dried. netic stirrer and heating it for 15 min, then take out the carbon fiber bundle and rinse it with deionized water until it is neutral, and put it in electric heating drying in a constant temperature drying box in order to increase the surface roughness of the fiber and the polar group, thereby increasing the surface activity, improving the affinity with the metal base, and prepare for the metallization of the carbon fiber surface.

Metallization of Carbon Fiber Surface
The carbon fiber bundle after the above pretreatment is placed in an electroplating device for electroplating. The composition and process parameters of the electroplating solution are shown in Tables 3 and 4. The steps of nickel electroplating in this experiment are as follows: Step 1, weigh the required nickel sulfate, nickel chloride, boric acid and sodium dodecyl sulfate, and dissolve them in an appropriate amount of deionized water, mix them in sequence, and then mix them. Add hydrochloric acid dropwise to the plating solution, adjust the pH of the plating solution to 3, and dilute the volume to 500 mL; Step 2, use sandpaper to remove the oxides on the surface of the high-purity nickel plate, ultrasonically clean for 30 min, and rinse with deionized water; Step 3, the carbon fiber bundle and the high-purity nickel plate are, respectively, fixed to the cathode and anode of the power supply, and placed in the electroplating device as shown in Figure 2, electroplating is carried out by controlling the current, voltage and electroplating time, and then washed with deionized water and dried.

Blending and SPS Spark Plasma Sintering
Use a carbon fiber cutter to cut the metalized carbon fiber bundles into 0.2 mm chopped carbon fibers. Use a V-type blender to evenly disperse the chopped carbon fibers in the matrix powder. Put the mixture into a graphite mold and placed in SPS spark plasma sintering equipment for sintering. Firstly, by adjusting the sintering time of the composite material for 3 min, the sintering temperature is increased from room temperature to 300 °C at 100 °C/min, and the pre-pressurization is 15 kN, and the pressure is

Blending and SPS Spark Plasma Sintering
Use a carbon fiber cutter to cut the metalized carbon fiber bundles into 0.2 mm chopped carbon fibers. Use a V-type blender to evenly disperse the chopped carbon fibers in the matrix powder. Put the mixture into a graphite mold and placed in SPS spark plasma sintering equipment for sintering. Firstly, by adjusting the sintering time of the composite material for 3 min, the sintering temperature is increased from room temperature to 300 • C at 100 • C/min, and the pre-pressurization is 15 kN, and the pressure is maintained for 2 min. Secondly, increase the sintering temperature from 300 • C to 380 • C at a heating rate of 50 • C/min, hold for 10 min, and increase the sintering pressure to 30 kN, and then cool down with the furnace to obtain a carbon fiber reinforced zinc-based aluminum rich alloy composite material. In addition, during the sintering process, the sample is fully loaded to 50 MPa, and the specific SPS spark plasma sintering process curve is shown in Figure 3. maintained for 2 min. Secondly, increase the sintering temperature from 300 °C to 380 °C at a heating rate of 50 °C/min, hold for 10 min, and increase the sintering pressure to 30 kN, and then cool down with the furnace to obtain a carbon fiber reinforced zinc-based aluminum rich alloy composite material. In addition, during the sintering process, the sample is fully loaded to 50 MPa, and the specific SPS spark plasma sintering process curve is shown in Figure 3.

Compound Representation
In this experiment, the ZEISS Gemini 300 scanning electron microscope was used to observe and analyze the surface morphology and cross-sectional morphology of the carbon fiber before and after the nickel coating, and the carbon fiber reinforced zinc-based aluminum rich alloy composite material was mapped and scanned to obtain the element distribution of the composite material figure, characterize the phase of the composite material with an x-ray diffractometer. At the same time, the HVS-1000Z digital micro-hardness tester (HV0.1 = 100 MPa, 10 s) is used to test the hardness of the composite material. A sample with a thickness of 7 mm and a diameter of 30 mm is ground and polished to obtain a smooth and flat surface. The test is carried out with a diamond spherical indenter, the test force is 9.807 N, the holding time is 15 s, 6 points are selected for each sample to be tested and the average value is taken. The dry sliding friction and wear test was carried out by the pin-disc wear tester UMT-3. The friction pair was a GCr15 alloy steel ball with a diameter of 6 mm. Before the test, the two parallel surfaces of the sample were polished and polished with 2000 grit sandpaper. The following applications were applied test parameters: At room temperature, the applied load is 8 N, the friction stroke is 5 mm, the friction frequency is 2 Hz, and the wear test cycle is 30 min. After the sliding test, each sample was cleaned with ethanol to remove potential contaminants, and the wear surface and wear volume of the sample were characterized by scanning electron microscope and MicroXAM-800 non-contact optical profiler. Figure 4a is the surface morphology of carbon fiber before electroplating. It can be clearly seen that there is no colloidal substance on the surface of carbon fiber after being roughened by NaOH solution, and there are obvious longitudinal grooves, and the surface roughness has increased. At the same time, the surface of carbon fiber has no obvi-

Compound Representation
In this experiment, the ZEISS Gemini 300 scanning electron microscope was used to observe and analyze the surface morphology and cross-sectional morphology of the carbon fiber before and after the nickel coating, and the carbon fiber reinforced zinc-based aluminum rich alloy composite material was mapped and scanned to obtain the element distribution of the composite material figure, characterize the phase of the composite material with an x-ray diffractometer. At the same time, the HVS-1000Z digital microhardness tester (HV0.1 = 100 MPa, 10 s) is used to test the hardness of the composite material. A sample with a thickness of 7 mm and a diameter of 30 mm is ground and polished to obtain a smooth and flat surface. The test is carried out with a diamond spherical indenter, the test force is 9.807 N, the holding time is 15 s, 6 points are selected for each sample to be tested and the average value is taken. The dry sliding friction and wear test was carried out by the pin-disc wear tester UMT-3. The friction pair was a GCr15 alloy steel ball with a diameter of 6 mm. Before the test, the two parallel surfaces of the sample were polished and polished with 2000 grit sandpaper. The following applications were applied test parameters: At room temperature, the applied load is 8 N, the friction stroke is 5 mm, the friction frequency is 2 Hz, and the wear test cycle is 30 min. After the sliding test, each sample was cleaned with ethanol to remove potential contaminants, and the wear surface and wear volume of the sample were characterized by scanning electron microscope and MicroXAM-800 non-contact optical profiler. Figure 4a is the surface morphology of carbon fiber before electroplating. It can be clearly seen that there is no colloidal substance on the surface of carbon fiber after being roughened by NaOH solution, and there are obvious longitudinal grooves, and the surface roughness has increased. At the same time, the surface of carbon fiber has no obvious damages such as splits and fractures, and longitudinal grooves can increase the contact area and interface bonding force between the carbon fiber and the nickel layer. Figure 4b shows the micro-morphology of the nickel-plated carbon fiber surface at a bath temperature of 25 • C, a plating time of 20 min, a current of 2.3 A, and a voltage of 0.05 V. It can be seen that the nickel layer completely covers the carbon fiber, and the surface is plated. The particles of the nickel layer are dense and uniform as a whole, and there is no obvious drop-off and other defects. According to the observation in Figure 4c, there are some round cell-shaped protrusions on the plating layer, which are caused by the growth method of the nickel layer. It is a relatively complicated process involving the nucleation and nucleation of crystals and the catalytic deposition of nickel particles. When electroplating has just been carried out, the bottom of the groove on the carbon fiber surface is likely to preferentially deposit nickel particles to form nickel nuclei. As the electroplating process progresses, the carbon fiber protrusions and groove sides that are not conducive to nucleation will also be nickel nuclei appear, and then over time the entire carbon fiber surface will be covered with nickel nuclei and grow up at the same time. As the electroplating time increases, the crystal nuclei initially formed at the bottom of the groove on the surface of the carbon fiber and the incomplete structure gradually grow up, and the small particle nuclei continue to gather into large particles, and finally form a continuous and uniform nickel layer. Furthermore, a round cell-shaped protrusion is formed on the surface [25]. These protrusions had increased the surface roughness of the fiber, which is conducive to the combination of the fiber and the aluminum matrix. EDS quantitative analysis of part of the coating in the frame of Figure 4b obtains the weight percentage and atomic percentage of the elements. From the energy spectrum of Figure 4d and the data in the table, it can be seen that the coating contains nickel and carbon. It shows that there aren't any new impurity elements are involved in the electroplating process, and the spectral peak corresponding to nickel is the highest. The weight percentages of nickel and carbon are 96.31% and 3.69%, and the atomic content is 84.22% and 15.78%, respectively. ous damages such as splits and fractures, and longitudinal grooves can increase the contact area and interface bonding force between the carbon fiber and the nickel layer. Figure 4b shows the micro-morphology of the nickel-plated carbon fiber surface at a bath temperature of 25 °C, a plating time of 20 min, a current of 2.3 A, and a voltage of 0.05 V. It can be seen that the nickel layer completely covers the carbon fiber, and the surface is plated. The particles of the nickel layer are dense and uniform as a whole, and there is no obvious drop-off and other defects. According to the observation in Figure 4c, there are some round cell-shaped protrusions on the plating layer, which are caused by the growth method of the nickel layer. It is a relatively complicated process involving the nucleation and nucleation of crystals and the catalytic deposition of nickel particles. When electroplating has just been carried out, the bottom of the groove on the carbon fiber surface is likely to preferentially deposit nickel particles to form nickel nuclei. As the electroplating process progresses, the carbon fiber protrusions and groove sides that are not conducive to nucleation will also be nickel nuclei appear, and then over time the entire carbon fiber surface will be covered with nickel nuclei and grow up at the same time. As the electroplating time increases, the crystal nuclei initially formed at the bottom of the groove on the surface of the carbon fiber and the incomplete structure gradually grow up, and the small particle nuclei continue to gather into large particles, and finally form a continuous and uniform nickel layer. Furthermore, a round cell-shaped protrusion is formed on the surface [25]. These protrusions had increased the surface roughness of the fiber, which is conducive to the combination of the fiber and the aluminum matrix. EDS quantitative analysis of part of the coating in the frame of Figure 4b obtains the weight percentage and atomic percentage of the elements. From the energy spectrum of Figure 4d and the data in the table, it can be seen that the coating contains nickel and carbon. It shows that there aren't any new impurity elements are involved in the electroplating process, and the spectral peak corresponding to nickel is the highest. The weight percentages of nickel and carbon are 96.31% and 3.69%, and the atomic content is 84.22% and 15.78%, respectively.    Figure 5a is a cross-sectional morphology of nickel-plated carbon fiber. It can be seen that the plated nickel layer is evenly distributed and surrounds the carbon fiber, and it is tightly attached to the surface of the carbon fiber. The average thickness of the nickel layer is about 817.4 nm. Since the left side of the carbon fiber is close to the anode nickel plate, and the right side is farther from the anode nickel plate. Thus, the atom movement distance is too far, which means it cannot be attached to the right side of the carbon fiber in time, which may result in uneven coating thickness [26]. Figure 5b is a scan of the plated carbon fiber. It is observed that the nickel element is uniformly distributed on the surface of the carbon fiber, indicating that the nickel-plating layer completely wraps the carbon fiber and forms the structure of the shell. layer is about 817.4 nm. Since the left side of the carbon fiber is close to the anode nickel plate, and the right side is farther from the anode nickel plate. Thus, the atom movement distance is too far, which means it cannot be attached to the right side of the carbon fiber in time, which may result in uneven coating thickness [26]. Figure 5b is a scan of the plated carbon fiber. It is observed that the nickel element is uniformly distributed on the surface of the carbon fiber, indicating that the nickel-plating layer completely wraps the carbon fiber and forms the structure of the shell.  Figure 6 is the actual distribution of carbon fiber content of 0vt%, 3vt%, 6vt%, and 9vt% in the composite material under the scanning electron microscope. It can be seen from the above figures that the carbon fiber in the composite material is basically evenly distributed, and the overall carbon fiber is short in the rod shape, some of the carbon fibers are concentrated and then appear as dots. The nickel-plated carbon fibers may be broken due to the different arrangement of the carbon fibers or the high pressure during the pressing process. The high content of carbon fiber with a volume fraction of 9vt% leads to obvious local agglomeration. The agglomeration of carbon fiber blocks the diffusion of the matrix material, which has caused the carbon fiber and the matrix material could not be tightly combined during the sintering process. Therefore, the holes have occurred.  Figure 6 is the actual distribution of carbon fiber content of 0vt%, 3vt%, 6vt%, and 9vt% in the composite material under the scanning electron microscope. It can be seen from the above figures that the carbon fiber in the composite material is basically evenly distributed, and the overall carbon fiber is short in the rod shape, some of the carbon fibers are concentrated and then appear as dots. The nickel-plated carbon fibers may be broken due to the different arrangement of the carbon fibers or the high pressure during the pressing process. The high content of carbon fiber with a volume fraction of 9vt% leads to obvious local agglomeration. The agglomeration of carbon fiber blocks the diffusion of the matrix material, which has caused the carbon fiber and the matrix material could not be tightly combined during the sintering process. Therefore, the holes have occurred.

Microscopic Morphology and Phase Analysis of Carbon Fiber Reinforced Zinc-Based Aluminum Rich Alloy Composites
layer is about 817.4 nm. Since the left side of the carbon fiber is close to the anode nickel plate, and the right side is farther from the anode nickel plate. Thus, the atom movement distance is too far, which means it cannot be attached to the right side of the carbon fiber in time, which may result in uneven coating thickness [26]. Figure 5b is a scan of the plated carbon fiber. It is observed that the nickel element is uniformly distributed on the surface of the carbon fiber, indicating that the nickel-plating layer completely wraps the carbon fiber and forms the structure of the shell.  Figure 6 is the actual distribution of carbon fiber content of 0vt%, 3vt%, 6vt%, and 9vt% in the composite material under the scanning electron microscope. It can be seen from the above figures that the carbon fiber in the composite material is basically evenly distributed, and the overall carbon fiber is short in the rod shape, some of the carbon fibers are concentrated and then appear as dots. The nickel-plated carbon fibers may be broken due to the different arrangement of the carbon fibers or the high pressure during the pressing process. The high content of carbon fiber with a volume fraction of 9vt% leads to obvious local agglomeration. The agglomeration of carbon fiber blocks the diffusion of the matrix material, which has caused the carbon fiber and the matrix material could not be tightly combined during the sintering process. Therefore, the holes have occurred. four elements distribution is relatively uniform. It can be seen in Figure 7f,g, carbon and nickel element has a concentration and whole are dispersed in the matrix, and to distinguish clearly, it shows that the surface plating nickel short carbon fiber dispersed uniformly in the matrix, the basic no reunion phenomenon, while the distribution of carbon and nickel elements are basically identical, but the part of the nickel elements have obvious diffusion phenomenon, in sintering process of nickel coating on the surface of the carbon fiber, may spread to the substrate [27]. For 6vt% composites of carbon fiber content mapping scanning, composite material distribution of each element, from Figure 7b-e it can be seen that carbon fiber reinforced zinc-based aluminum rich alloy composite material of zinc, copper, magnesium, aluminum four elements distribution is relatively uniform. It can be seen in Figure 7f,g, carbon and nickel element has a concentration and whole are dispersed in the matrix, and to distinguish clearly, it shows that the surface plating nickel short carbon fiber dispersed uniformly in the matrix, the basic no reunion phenomenon, while the distribution of carbon and nickel elements are basically identical, but the part of the nickel elements have obvious diffusion phenomenon, in sintering process of nickel coating on the surface of the carbon fiber, may spread to the substrate [27].   Figure 8b shows that the nickel-plated short carbon fiber and the matrix material is tightly bonded, and the matrix material is completely covered on the surface of the nickel-plated carbon fiber, forming a dense microstructure, and no obvious pores or carbon fiber damage are observed. The nickel-plating layer is highly reliable and it has excellent oxidation resistance, so when it is compounded with the matrix material at high temperatures, it can effectively prevent the carbon fibers from being damaged, and prevent the direct contact and agglomeration between the carbon fibers. However, there is no clear nickel-plating profile in Figure 8b which means that the nickel plating around the carbon fiber may partially disappear. It can be verified from the scanning results of Figure 8c,d, in Figure 8b spot1 it can be seen in Figure 8c that most of the elements in the bonding site are carbon elements, and contain less nickel, zinc and aluminum. Compare the scan results of spot2 in Figure 8b-d, it is found that the nickel content in the area far from the joint is significantly increased compared to the joint. The weight percentage of nickel increases from 12.51% at spot1 to 39.68% at spot2, indicating that the nickel-plating layer is gradually moving towards the substrate during the sintering process. In the diffusion, and the formation of intermetallic compounds. Figure 9 shows the XRD diffraction pattern of the composite material，compared with ZA27, it can be seen that the Ni coating on the carbon fiber surface in the composite material gradually diffuses into the matrix, and reacts with ZA27 to form Al3Ni phase, which is distributed near the carbon fiber, the Al3Ni phase is generated with the carbon fiber as the nucleation   Figure 8b shows that the nickel-plated short carbon fiber and the matrix material is tightly bonded, and the matrix material is completely covered on the surface of the nickel-plated carbon fiber, forming a dense microstructure, and no obvious pores or carbon fiber damage are observed. The nickel-plating layer is highly reliable and it has excellent oxidation resistance, so when it is compounded with the matrix material at high temperatures, it can effectively prevent the carbon fibers from being damaged, and prevent the direct contact and agglomeration between the carbon fibers. However, there is no clear nickel-plating profile in Figure 8b which means that the nickel plating around the carbon fiber may partially disappear. It can be verified from the scanning results of Figure 8c,d, in Figure 8b spot1 it can be seen in Figure 8c that most of the elements in the bonding site are carbon elements, and contain less nickel, zinc and aluminum. Compare the scan results of spot2 in Figure 8b-d, it is found that the nickel content in the area far from the joint is significantly increased compared to the joint. The weight percentage of nickel increases from 12.51% at spot1 to 39.68% at spot2, indicating that the nickel-plating layer is gradually moving towards the substrate during the sintering process. In the diffusion, and the formation of intermetallic compounds. Figure 9 shows the XRD diffraction pattern of the composite material, compared with ZA27, it can be seen that the Ni coating on the carbon fiber surface in the composite material gradually diffuses into the matrix, and reacts with ZA27 to form Al 3 Ni phase, which is distributed near the carbon fiber, the Al 3 Ni phase is generated with the carbon fiber as the nucleation center and grows at the interface of the carbon fiber. At the interface between the carbon fiber and the substrate, a nickel-rich area is formed in the contact area with the coating, and a nickel-poor area is formed in the area away from the coating. Such a concentration gradient change can indicate that the nickel coating has diffused. In the XRD diffraction pattern detection results of Figure 9, in addition to the reaction of Ni coating and ZA27 to form Al 3 Ni phase, a small amount of Al 4 C 3 , brittle phase is formed between ZA27 and carbon fiber, which may be due to the fact that both ends of chopped carbon fiber are not covered by nickel layer and the matrix is in contact Generated, At the same time, in Figure 8b, the carbon content at spot2 is significantly lower than that at spot1, and its weight percentage decreases from 79.54% at spot1 to 4.35% at spot2, indicating that the intermetallic compound formed between the nickel coating and the substrate can It can effectively inhibit the diffusion of carbon fibers during the sintering process, thereby inhibiting the formation of a large number of brittle carbides Al 4 C 3 , and improving the interface bonding between carbon fibers and matrix materials.

Microscopic Morphology and Phase Analysis of Carbon Fiber Reinforced Zinc-Based Aluminum Rich Alloy Composites
center and grows at the interface of the carbon fiber. At the interface between the carbon fiber and the substrate, a nickel-rich area is formed in the contact area with the coating, and a nickel-poor area is formed in the area away from the coating. Such a concentration gradient change can indicate that the nickel coating has diffused. In the XRD diffraction pattern detection results of Figure 9, in addition to the reaction of Ni coating and ZA27 to form Al3Ni phase, a small amount of Al4C3, brittle phase is formed between ZA27 and carbon fiber, which may be due to the fact that both ends of chopped carbon fiber are not covered by nickel layer and the matrix is in contact Generated, At the same time, in Figure 8b, the carbon content at spot2 is significantly lower than that at spot1, and its weight percentage decreases from 79.54% at spot1 to 4.35% at spot2, indicating that the intermetallic compound formed between the nickel coating and the substrate can It can effectively inhibit the diffusion of carbon fibers during the sintering process, thereby inhibiting the formation of a large number of brittle carbides Al4C3, and improving the interface bonding between carbon fibers and matrix materials.  center and grows at the interface of the carbon fiber. At the interface between the carbon fiber and the substrate, a nickel-rich area is formed in the contact area with the coating, and a nickel-poor area is formed in the area away from the coating. Such a concentration gradient change can indicate that the nickel coating has diffused. In the XRD diffraction pattern detection results of Figure 9, in addition to the reaction of Ni coating and ZA27 to form Al3Ni phase, a small amount of Al4C3, brittle phase is formed between ZA27 and carbon fiber, which may be due to the fact that both ends of chopped carbon fiber are not covered by nickel layer and the matrix is in contact Generated, At the same time, in Figure 8b, the carbon content at spot2 is significantly lower than that at spot1, and its weight percentage decreases from 79.54% at spot1 to 4.35% at spot2, indicating that the intermetallic compound formed between the nickel coating and the substrate can It can effectively inhibit the diffusion of carbon fibers during the sintering process, thereby inhibiting the formation of a large number of brittle carbides Al4C3, and improving the interface bonding between carbon fibers and matrix materials.

Hardness of Composite Materials
At least 6 hardness measurements were performed on different positions of each sample, and the average of these measurements was reported as the Vickers hardness of the sample. As shown in Figure 10, the ZA27 matrix sample has the lowest hardness of 89.22 HV among all samples. The hardness of the sample increases with the increase of carbon fiber content. The average hardness is 114.11 HV, 115.715 HV, 132.766 HV. It can be observed that the hardness of ZA27 can be increased to 27.9% by incorporating 3vt% carbon fiber, 6vt% carbon fiber can be increased to 29.6%, and 9vt% carbon fiber can be incorporated. It can be increased to 49.4%. The increase in hardness is due to the fact that the carbon fiber itself is harder than the matrix material, and at the same time, the carbon fiber has a higher strength. The addition of ZA27 plays a role in the second phase strengthening. The increase in the hardness value of the composite material is also affected by the slightly increased carbide in these materials [28].

Hardness of Composite Materials
At least 6 hardness measurements were performed on different positions of each sample, and the average of these measurements was reported as the Vickers hardness of the sample. As shown in Figure 10, the ZA27 matrix sample has the lowest hardness of 89.22 HV among all samples. The hardness of the sample increases with the increase of carbon fiber content. The average hardness is 114.11 HV, 115.715 HV, 132.766 HV. It can be observed that the hardness of ZA27 can be increased to 27.9% by incorporating 3vt% carbon fiber, 6vt% carbon fiber can be increased to 29.6%, and 9vt% carbon fiber can be incorporated. It can be increased to 49.4%. The increase in hardness is due to the fact that the carbon fiber itself is harder than the matrix material, and at the same time, the carbon fiber has a higher strength. The addition of ZA27 plays a role in the second phase strengthening. The increase in the hardness value of the composite material is also affected by the slightly increased carbide in these materials [28].

Friction and Wear Properties of Composite Materials
At room temperature, the test parameters are as follows: when the friction frequency is 2 Hz, the friction length is 5 mm, the applied load is 8 N, and the friction time is 30 min, the carbon fiber content increases to 0vt%, 3vt%, 6vt%, 9vt%, The obtained Figure 11 shows the change trend graph of the friction coefficient and the average friction coefficient of different content carbon fiber reinforced zinc-based aluminum rich alloy composites, and Figure 12 shows the three-dimensional profile of wear volume and the change trend graph of wear rate of different content carbon fiber reinforced zinc-based aluminum rich alloy composites. As can be seen from Figure 11, When the addition of carbon fiber is 0vt%, the average friction coefficient of the ZA27 alloy matrix is 0.445. With the increase of the carbon fiber content of the reinforcement, the friction coefficient of the composite material gradually decreases. When the addition of the reinforcement is 3vt%, the average friction coefficient drops to 0.38, which is 14.4% lower than the friction coefficient of the ZA27 alloy matrix. When the carbon fiber content is increased to 6vt%, the average friction coefficient is further reduced to 0.367, which is 18.4% lower than the friction coefficient of the ZA27 alloy matrix, and the carbon fiber content increases at 9vt%, the average friction coefficient is 0.366, which is basically as same as the friction coefficient when the content is 6vt%. Figure 12 shows the effect of carbon fiber volume fraction on the wear volume and wear rate of composite materials. Figure 12a-d shows

Friction and Wear Properties of Composite Materials
At room temperature, the test parameters are as follows: when the friction frequency is 2 Hz, the friction length is 5 mm, the applied load is 8 N, and the friction time is 30 min, the carbon fiber content increases to 0vt%, 3vt%, 6vt%, 9vt%, The obtained Figure 11 shows the change trend graph of the friction coefficient and the average friction coefficient of different content carbon fiber reinforced zinc-based aluminum rich alloy composites, and Figure 12 shows the three-dimensional profile of wear volume and the change trend graph of wear rate of different content carbon fiber reinforced zinc-based aluminum rich alloy composites. As can be seen from Figure 11, When the addition of carbon fiber is 0vt%, the average friction coefficient of the ZA27 alloy matrix is 0.445. With the increase of the carbon fiber content of the reinforcement, the friction coefficient of the composite material gradually decreases. When the addition of the reinforcement is 3vt%, the average friction coefficient drops to 0.38, which is 14.4% lower than the friction coefficient of the ZA27 alloy matrix. When the carbon fiber content is increased to 6vt%, the average friction coefficient is further reduced to 0.367, which is 18.4% lower than the friction coefficient of the ZA27 alloy matrix, and the carbon fiber content increases at 9vt%, the average friction coefficient is 0.366, which is basically as same as the friction coefficient when the content is 6vt%. Figure 12 shows the effect of carbon fiber volume fraction on the wear volume and wear rate of composite materials. Figure 12a-d shows that the addition of carbon fiber is 0vt%, 3vt%, 6vt%, 9vt% at this time, the wear volumes of the composite materials were 3.69 × 10 8 µm 3 , 0.188 × 10 8 µm 3 , 0.15 × 10 8 µm 3 , and 0.148 × 10 8 µm 3 . The wear rate is calculated by the following (1): where ω s is the wear rate, l is the sliding distance, v is the wear volume of the sample, and p is the normal load. As the volume fraction of carbon fiber increases, the wear rate of the composite material decreases significantly. It is showed in Figure 12e. When the reinforcement addition is 0vt%, the wear rate of the ZA27 alloy matrix is 9.225 mm 3 N −1 m −1 , and when the reinforcement addition is 3vt%, the wear rate drops to 0.471 mm 3 N −1 m −1 , which is 95% lower than the wear rate of the alloy matrix. When the carbon fiber content is increased to 6vt%, the wear rate is further reduced to 0.376 mm 3 N −1 m −1 , which is 96% lower than the wear rate of the alloy matrix. The carbon fiber content when it is increased to 9vt%, the wear rate is 0.371 mm 3 N −1 m −1 . At this time, the wear rate remains basically unchanged with the increase of the carbon fiber content, and this trend is consistent with the change of the friction coefficient. From Figure 11a, it can be found that the friction coefficient of the ZA27 alloy substrate has obvious up and down fluctuations. This may be due to the mutual contact and friction between the surface of the ZA27 alloy material and the bearing steel GCr15 in the experiment, which has caused the surface of the substrate material to deform. Particles of different sizes are constantly falling off, which plays a part of the role of rolling friction between the friction pairs. The friction coefficient curves of 3vt%, 6vt%, and 9vt% in Figure 11a are relatively stable as a whole and are also significantly lower than the friction coefficient of the ZA27 alloy base material. This is due to the cyclic load generated during the wear process. The surface of the sample is plastically deformed. It can be seen from Figure 13a that the carbon fiber is exposed to the surface due to the removal of the surface layer. Under the action of the contact force, the carbon fiber is partially ground into fine carbon particles. As the volume fraction of carbon fibers in the composite increases, more carbon fibers are exposed to the surface, resulting in more carbon fibers being ground into fine carbon particles, a solid lubricant, which forms a thin film on the wear surface of the sample. Due to the existence of this film, it prevents the metal-to-metal contact between the composite material and its counterpart during the friction process, so that the friction coefficient of the composite material is reduced and reduced the wear rate of the composite material [29]. The enhancement of the friction and wear properties of composites is also affected by their hardness. In general, the harder the material, the better the friction and wear properties, because higher hardness materials are better at resisting plastic deformation or failure, resulting in more wear-resistant materials. The experimental results also show that adding carbon fiber can improve the hardness of ZA27 alloy, so the increased hardness by adding carbon fiber helps to improve the wear resistance of the composite material. The SEM micrograph and EDS spectrum of the wear surface of ZA27 alloy material and 6vt% carbon fiber reinforced zinc-based aluminum rich alloy composite material is shown in Figure 13. The wear surface of ZA27 alloy material is mainly composed of grooves and a large amount of wear debris, as shown in Figure 13a, the wear surface is damaged due to plastic deformation. Some of the sheared matrix material fragments are peeled off into flakes and ground and adhered to the surface of the material by the friction pair. The adhesion effect hinders the movement between the matrix material and the friction pair, adhesive wear has occurred with the base material. It can be seen from Figure 13c that the presence of oxygen on the worn surface also indicates that oxidative wear has occurred. As shown in Figure 13d, the wear surface of the 6vt% carbon fiber composite material has wider and shallower grooves than the ZA27 alloy material. The wear surface is smoother than the base material and there is no adhesion of debris. At the same time, due to shear the part where the force acts on the carbon fiber is also exposed on the surface of the material. Obviously, the addition of carbon fiber hinders the deformation of the matrix, which means that the wear rate is reduced. As shown in Figure 13f, the oxygen content on the surface is increased to 21.58wt% relative to the ZA27 alloy, and the carbon content is also increased to 1.72wt%. This indicates that there is a carbon-rich film in the area doped with carbon fiber on the surface of the 6vt% carbon fiber composite material. Since the carbon content is relatively low, the carbon film should only exist around the carbon fiber and not diffuse to the entire wear surface. At this time, the wear mechanism it is oxidative wear. As the load time continues to increase, the friction temperature also increases. If the heat generated by the friction cannot be dissipated in time, the temperature rise will change the surface properties of the friction contact surface. Another reason that carbon fiber reinforced zinc-based aluminum rich alloy composites exhibit better friction properties than ZA27 is to improve the thermal conductivity of the composites. Carbon fiber is an inorganic polymer fiber with a carbon content of more than 90%. The microstructure is similar to artificial graphite, it is a chaotic layer graphite structure, and its thermal conductivity is generally 0.025-0.09 W/(m·K). Due to its excellent thermal conductivity, the thermal conductivity of carbon fiber is higher than that of the alloy matrix. Therefore, the presence of carbon fiber can cause friction. The heat is dissipated in time to prevent the surface temperature from continuously increasing during the friction process, thereby optimizing the friction performance of the material.
material. Obviously, the addition of carbon fiber hinders the deformation of the matrix, which means that the wear rate is reduced. As shown in Figure 13f, the oxygen content on the surface is increased to 21.58wt% relative to the ZA27 alloy, and the carbon content is also increased to 1.72wt%. This indicates that there is a carbon-rich film in the area doped with carbon fiber on the surface of the 6vt% carbon fiber composite material. Since the carbon content is relatively low, the carbon film should only exist around the carbon fiber and not diffuse to the entire wear surface. At this time, the wear mechanism it is oxidative wear. As the load time continues to increase, the friction temperature also increases. If the heat generated by the friction cannot be dissipated in time, the temperature rise will change the surface properties of the friction contact surface. Another reason that carbon fiber reinforced zinc-based aluminum rich alloy composites exhibit better friction properties than ZA27 is to improve the thermal conductivity of the composites. Carbon fiber is an inorganic polymer fiber with a carbon content of more than 90%. The microstructure is similar to artificial graphite, it is a chaotic layer graphite structure, and its thermal conductivity is generally 0.025-0.09 W/(m·K). Due to its excellent thermal conductivity, the thermal conductivity of carbon fiber is higher than that of the alloy matrix. Therefore, the presence of carbon fiber can cause friction. The heat is dissipated in time to prevent the surface temperature from continuously increasing during the friction process, thereby optimizing the friction performance of the material.

Conclusions
(1) The nickel layer is plated on the surface of the carbon fiber by electroplating process. The nickel layer grows and distributes on the surface of the carbon fiber. The carbon fiber is completely covered without obvious fall off; Carbon fiber-reinforced zincbased aluminum rich alloy composite materials with contents of 0vt%, 3vt%, 6vt%, and 9vt% were prepared by the SPS sintering method; nickel-plated carbon fiber is tightly combined with the matrix material and dispersed in the matrix material as a whole. Nickel plated carbon fiber is closely combined with the matrix material and dispersed into the matrix material as a whole. The intermetallic compound Al 3 Ni formed between the nickel coating and the matrix effectively inhibits the diffusion of carbon fiber in the sintering process, indicating that the nickel coating improves the interfacial adhesion between carbon fiber and matrix. (2) The average hardness of carbon fiber composites with content of 0vt%, 3vt%, 6vt% and 9vt% are 89.22 HV, 114.11 HV, 115.72 HV and 132.77 HV, respectively. Compared with the ZA27 alloy matrix, 6vt% is added. The hardness of carbon fiber increased by 29.6%. With the increase of carbon fiber content, the friction coefficient and wear rate of the composite material gradually decrease. When the carbon fiber content increases to 6vt%, the friction coefficient and wear amount remain basically unchanged. At this time, the corresponding friction coefficient is 0.367 and the wear amount is 0.376 mm 3 N −1 m −1 , compared with the average coefficient of friction and wear rate of the matrix material, they are reduced by about 18.4% and 96%, respectively. These improvements can be attributed to the addition of carbon fiber, which enhances the hardness of the composite, improves the ability of the material to resist plastic deformation, reduces the metal-to-metal contact between the composite and its counterpart in the friction process, hinders the deformation of the matrix, and optimizes the friction and wear properties of the material.