A carbon steel composite material and its preparation method and application

Abstract

The present invention discloses a carbon steel composite material, its preparation method, and application. The carbon steel composite material comprises a carbon steel substrate and a high-entropy alloy coating disposed on the surface of the carbon steel substrate; the high-entropy alloy coating comprises the following elements: iron, cobalt, chromium, nickel, copper, and boron. The carbon steel composite material provided by the present invention exhibits high friction reduction and wear resistance at both room and high temperatures.

Description

Technical Field

[0001] The present invention relates to the technical field of carbon steel processing, in particular to a carbon steel composite material and a preparation method and application thereof. Background Art

[0002] Carbon steel is the earliest and most widely used basic material in modern industry. It is a carbon structural steel characterized by excellent plasticity, toughness, and resistance to weld cracking. Its low price makes it widely used in buildings, high-voltage transmission towers, vehicles, ships, and other applications. It is also widely used in mechanical components. However, carbon steel's poor wear resistance and friction reduction properties limit its use in moving parts.

[0003] Therefore, it is necessary to develop a carbon steel composite material with better performance. Summary of the Invention

[0004] The present invention aims to solve at least one of the technical problems existing in the prior art. To this end, in a first aspect, the present invention provides a carbon steel composite material that can effectively improve friction reduction and wear resistance at room temperature and high temperature.

[0005] The second aspect of the present invention also provides a method for preparing the carbon steel composite material.

[0006] The third aspect of the present invention further provides an application of a carbon steel composite material.

[0007] According to a first aspect of the present invention, a carbon steel composite material is provided, comprising a carbon steel substrate and a high entropy alloy coating located on a surface of the carbon steel substrate;

[0008] The high entropy alloy coating comprises the following components: iron, cobalt, chromium, nickel, copper and boron.

[0009] The carbon steel composite material according to the embodiment of the present invention has at least the following beneficial effects:

[0010] The carbon steel composite material provided by the present invention has a high friction reduction and wear resistance effect at both room temperature and high temperature. Under the influence of its high structural entropy, high-entropy alloys easily form simple solid solutions between alloying elements rather than intermetallic compounds, thus having good mechanical and tribological properties. Its ability to exhibit excellent wear resistance makes it advantageous in scenarios characterized by severe wear and abrasion.

[0011] Furthermore, boron, as a non-metallic element with a large atomic size difference from Fe, Co, Cr, Ni and Cu, will cause severe lattice distortion when forming a solid solution, increase the dislocation density of the coating, and improve the mechanical properties.

[0012] Furthermore, boron has very high hardness and melting point. At high temperatures, it can form metal borides with other metal or non-metal elements that have high strength, high hardness, high heat resistance, and high corrosion resistance. Borides also have lubricity and can effectively reduce the friction coefficient.

[0013] Furthermore, the oxidation Gibbs free energy of boron element B2O3 is low, it can exist stably, and it has a low melting point. It melts at 510°C to form a low-viscosity liquid, forming a lubricating film that isolates the contact surface and can directly reduce contact and adhesion.

[0014] According to some embodiments of the present invention, the molar ratio of the iron, cobalt, chromium, nickel, copper, and boron elements is 1:1:1:1:1:1:(0.1-0.5). Therefore, when the amount of boron added is too low, the high-temperature friction reduction effect is not significantly improved. When the amount of boron added exceeds 0.5, the improvement in friction reduction performance is limited, and a large amount of boron addition will affect the brittleness and hardness of the coating.

[0015] According to some embodiments of the present invention, the molar ratio of the iron element, the cobalt element, the chromium element, the nickel element, the copper element and the boron element is 1:1:1:1:1:(0.3-0.5).

[0016] According to a second aspect of the present invention, an embodiment provides a method for preparing the carbon steel composite material described above, comprising the following steps:

[0017] S1, mixing iron powder, cobalt powder, chromium powder, nickel powder, copper powder and boron powder, ball milling and drying to obtain a mixed powder;

[0018] S2. Using laser to clad the surface of a carbon steel substrate with the mixed powder to obtain a carbon steel composite material.

[0019] According to some embodiments of the present invention, the laser power of the laser cladding is 1200 W to 2000 W. For example, the laser power is selected from 1200 W, 1400 W, 1600 W, 1800 W, 2000 W, or a range consisting of any two of the above values.

[0020] According to some embodiments of the present invention, the rotation speed of the ball mill is 400 r / min to 800 r / min.

[0021] According to some embodiments of the present invention, the laser beam output spot of the laser cladding is 1 to 2 mm.

[0022] According to some embodiments of the present invention, the scanning speed of the laser cladding is 4-8 mm / s.

[0023] According to some embodiments of the present invention, the particle sizes of the iron powder, cobalt powder, chromium powder, nickel powder and copper powder are independently selected from 45 μm to 105 μm.

[0024] According to some embodiments of the present invention, the particle size of the boron powder is 15 μm to 45 μm.

[0025] According to some embodiments of the present invention, the surface of the carbon steel substrate is treated to remove impurities.

[0026] According to some embodiments of the present invention, the carbon steel matrix is ​​selected from at least one of Q235 ordinary carbon steel, Q345 high-quality carbon steel, No. 35 high-quality carbon steel, and No. 45 high-quality carbon steel.

[0027] A third aspect of the present invention provides an application of the above-mentioned carbon steel composite material in motion parts.

[0028] Other features and advantages of the present invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the present invention. BRIEF DESCRIPTION OF THE DRAWINGS

[0029] The above and / or additional aspects and advantages of the present invention will become apparent and readily understood from the following description of the embodiments with reference to the accompanying drawings, in which:

[0030] Figure 1 is the XRD pattern of the carbon steel composite material of Examples 1 to 3 of the present invention;

[0031] Figure 2 are cross-sectional microscopic morphologies of the carbon steel composite materials of Examples 1 to 3 of the present invention;

[0032] Figure 3 is a microhardness curve diagram of the carbon steel composite material of Examples 1 to 3 of the present invention;

[0033] Figure 4 Graphs of contact angles and surface energies of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 of the present invention;

[0034] Figure 5 Graphs showing friction coefficients of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 of the present invention;

[0035] Figure 6 is a wear rate graph of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 of the present invention;

[0036] Figure 7 3. The worn surface morphologies of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 of the present invention at room temperature;

[0037] Figure 83. The figure shows the surface morphology of the grinding balls of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 of the present invention at room temperature.

[0038] Figure 9 3 are wear surface morphologies of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 of the present invention at 600° C.

[0039] Figure 10 Surface morphology of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 of the present invention worn by grinding balls at 600°C. DETAILED DESCRIPTION

[0040] The following are specific embodiments of the present invention, and the technical solutions of the present invention are further described in conjunction with the embodiments, but the present invention is not limited to these embodiments.

[0041] Unless otherwise specified, the reagents, methods and equipment used in the present invention are conventional reagents, methods and equipment in the art.

[0042] Example 1

[0043] Example 1 provides a carbon steel composite material comprising a carbon steel substrate and a high-entropy alloy coating disposed on the surface of the carbon steel substrate. The high-entropy alloy coating comprises the following components: iron, cobalt, chromium, nickel, copper, and boron. The molar amounts of each element are shown in Table 1. The preparation method is as follows:

[0044] S1. Weigh the powders according to the molar ratio using an electronic scale and place the mixed powders in a DECO-PBM-V-0.4L ball mill at a speed of 600 r / min for 4 h. Then, dry the mixed powders at a constant temperature of 60°C for 4 h.

[0045] The Q235 ordinary carbon steel substrate was ground using sandpaper of different mesh sizes to remove surface impurities;

[0046] S2, using a fiber laser (YLS-3000) with an output power of 1600W to melt the composite coating in a synchronous powder feeding manner, the laser beam output spot is The scanning speed was 5 mm / s, the defocusing amount was -20 mm, and the powder feeding rate was 10.5 g / min. A multi-channel continuous laser scanning technique was used for preparation with an overlap rate of 50%, and a carbon steel composite material (named B1) was prepared.

[0047] Examples 2-3

[0048] Examples 2 and 3 provide a series of carbon steel composite materials, the components and amounts of which are shown in Table 1, and the preparation method is the same as that of Example 1. The prepared carbon steel composite materials are named B3 and B5 respectively.

[0049] Table 1 Examples 1 to 3

[0050]

[0051] Example 4

[0052] This example provides a carbon steel composite material, the component dosage and preparation method of which are basically the same as those in Example 1, except that the laser power in the preparation method is 1200W.

[0053] Example 5

[0054] This example provides a carbon steel composite material, the component dosage and preparation method of which are basically the same as those in Example 1, except that the laser power in the preparation method is 1400W.

[0055] Example 6

[0056] This example provides a carbon steel composite material, the component dosage and preparation method of which are basically the same as those in Example 1, except that the laser power in the preparation method is 1800W.

[0057] Example 7

[0058] This example provides a carbon steel composite material, the component dosage and preparation method of which are basically the same as those in Example 1, except that the laser power in the preparation method is 2000W.

[0059] Comparative Example 1

[0060] Comparative Example 1 provides a carbon steel composite material, the component dosage and preparation method of which are the same as those of Example 1, except that Comparative Example 1 does not contain boron element.

[0061] Performance Testing

[0062] The high entropy alloy coating of the carbon steel composite material prepared in Examples 1 to 3 was subjected to XRD testing, and the results are as follows: Figure 1 As shown, the coating is mainly composed of FCC type solid solution. By selecting the strongest characteristic peak (111) crystal plane family in the spectrum for analysis, as the boron element increases, the intensity of the characteristic peak gradually decreases, and the peak gradually shifts to the left, the FWHM value increases, and the coating grain size decreases. In the coatings in Examples 2 and 3, XRD detected the precipitation of Cr2B, and its PDF card is: ICDD01-089-4876. Cr2B has high hardness and strength, and Cr2B has a high melting point and thermal stability. These properties help the coating improve its tribological properties. In Example 1, due to the low boron content, the detection accuracy of XRD could not be detected.

[0063] Furthermore, the carbon steel composite materials prepared in Examples 1 to 3 were subjected to SEM testing, and the results were as follows: Figure 2 Figures 2a, 2b, and 2c show the microstructures of Examples 1, 2, and 3, respectively. The boron element precipitates along the grain boundaries, forming Cr2B, which forms a network-like distribution and reduces the grain size. A portion of the boron element acts as a solute, forming a solid solution with other metal elements, leading to lattice distortion. The evolution of the microstructure after the introduction of boron indicates that its addition produces grain refinement, dispersion strengthening, and lattice distortion.

[0064] Furthermore, the carbon steel composite materials prepared in Examples 1 to 3 were subjected to hardness tests, and the results are as follows: Figure 3 As shown, from Figure 3 It can be seen that the average microhardness of carbon steel composite materials B1, B3 and B5 are 236.53HV 0.5 、266.29HV 0.5 and 343.98HV 0.5 , about Q235 ordinary carbon steel matrix (175.6HV 0.5 ) is 1.34-1.96 times that of the original material. The hardness of the coating is improved to varying degrees, which can be attributed to the following three aspects: First, fine grain strengthening, the B element can reduce the phase transition temperature, which is conducive to low-temperature rapid sintering, thereby reducing the grain size of the high-entropy alloy, and increasing the density of the grain boundary and the dislocation slip resistance. Second, dispersion strengthening, the boride precipitated after adding the B element has high hardness and high melting point. As a dispersion-strengthened precipitate phase, it can improve the wear resistance and creep resistance of the metal, and its network distribution can hinder the movement of dislocations, thereby improving the hardness and strength of the metal. Third, lattice distortion, because the atomic radius of the B element is much smaller than that of the other five metal elements, when it is used as a solute to form a solid solution, it will cause lattice distortion, increase the difficulty of dislocation slip, and improve the yield strength and tensile strength of the coating.

[0065] Furthermore, the surface energy of the coating was measured by the Owens two-liquid method using a JGW-360B contact angle meter, with deionized water and n-hexadecane (C 16 H 34 ) two liquids, and their properties are listed in Table 2. The test results of contact angle and surface energy of Q235 ordinary carbon steel and B1, B3, B5 carbon steel composite materials are shown in Figure 4 The contact angles of the three high-entropy alloy coatings were all greater than those of Q235 ordinary carbon steel, and their surface energies were all lower than those of Q235 ordinary carbon steel. The periodic lattice structure of a solid is the lowest energy stable state that forms spontaneously, while the surface of the material is equivalent to a two-dimensional defect, resulting in it having higher energy than the interior of the material. Therefore, the surface of a low-surface-energy material tends to reach an internal stable state. Studies have reported that lower surface energy can reduce the occurrence of adhesion, and since friction occurs on the surface of the material, it can improve the material's tribological properties.

[0066] Table 2 Surface energy determination liquid properties

[0067]

[0068] Furthermore, in order to test the tribological properties of the carbon steel composite materials of Examples 1 to 3 and Comparative Example 1, the present invention uses a ball-disc high-temperature friction and wear tester (HT-1000) to perform tribological performance tests, and the test parameters are shown in Table 3. The obtained friction factor curve is shown in Figure 5 As shown, 5a is the friction coefficient at room temperature, and 5b is the friction coefficient at 600°C; detailed friction factor data are shown in Table 4. At room temperature, compared to Q235 ordinary carbon steel, although Comparative Example 1 has certain friction reduction performance, it is not obvious. However, the addition of element B has a significant friction reduction effect. The B5 coating with obvious friction reduction effect has a friction coefficient reduced by 46.89% compared to Q235 ordinary carbon steel. When element B is present in the alloy, it can form a lubricating film on the surface of the alloy, which can reduce friction and wear between metal surfaces. This self-lubricity is due to the good lubrication properties of the compounds or oxides formed by element B and the metal surface, which can effectively reduce the friction coefficient. In addition, after the three strengthening mechanisms introduced by the addition of element B, the hardness of the coating is significantly increased. The increase in hardness will make the surface smoother and the surface roughness smaller, which makes the contact area relatively small during the friction process, reduces the possibility of adhesion, and reduces the relative sliding resistance between the friction pairs. At 600°C, the friction coefficient curve is more stable than that at room temperature. This is because the oxidation reaction is intensified, which causes a lubricating oxide film to be generated quickly and in large quantities. This not only reduces the friction coefficient but also slows down wear. The friction factors of the coating containing element B are lower than those of Comparative Example 1.

[0069] Table 3 Friction and wear parameters

[0070]

[0071] Table 4 Average friction coefficients of Q235 ordinary carbon steel and three high entropy alloy coatings

[0072]

[0073] The wear surface profile and wear volume of the carbon steel composite materials of Examples 1 to 3 and Comparative Example 1 were measured using an M-500 probe wear scar measuring instrument. The wear rate values ​​calculated by the formula are shown in Table 5, and the comparison diagram is shown in Figure 6 ( Where W is the wear rate (mm 3 / N·m), F is the load (N), d is the sliding distance (m), and V is the wear volume (mm 3)). Experimental results show that the wear resistance of the coating improves significantly with increasing boron content. Changes in the wear resistance of the high-entropy alloy coating are closely related to the evolution of the microstructure. The precipitated boride plays an important role in the microstructure, firstly improving the alloy's microstructure. Secondly, the borides precipitated at the grain boundaries not only have high hardness themselves but also effectively hinder the movement of dislocations, thereby increasing the alloy's strength and hardness. The addition of boron significantly improves the wear resistance of the high-entropy alloy coating.

[0074] Table 5 Wear rate of substrate and composite coating (×10 -5 mm 3 / N·m)

[0075]

[0076] At room temperature, the wear surface morphology of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 is as follows: Figure 7As shown (a1 to a3 are Q235 ordinary carbon steel; b1 to b3 are B1; c1 to c3 are B3; and d1 to d3 are B5), the wear surface of Q235 ordinary carbon steel has a large amount of morphology formed by the peeling of coating surface material after cold welding. The dark area is the oxide film, and the white fine powdery debris is mainly caused by oxidation wear and fatigue wear. Small scratches caused by micro-cutting can also be observed. The wear mechanism is more complex at room temperature, and the characteristics of multiple wear mechanisms appear. There is a small-sized oxide film and blocky debris on the wear surface of the B1 coating. In the area where there is no oxide film, there are obvious plowing grooves and small scratches caused by micro-cutting. This is the wear morphology caused by the abrasive wear mechanism. There are a large number of cracks on the wear scar surface. When the material is subjected to cyclic loads or stresses, cracks form and expand on the surface or subsurface, leading to material spalling and the generation of abrasive particles. These cracks will expand with the increase in the number of cycles, eventually leading to material damage and wear. It can be inferred that the B1 coating has a certain degree of fatigue wear. Therefore, the main wear mechanism of the B1 coating is abrasive wear and fatigue wear. There is material spalling caused by adhesive wear on the wear scar of the B3 coating, and the oxide film has undergone layered spalling. There are scratches caused by cutting on the unflaked oxide film. That is, the main wear mechanism of the B3 coating is adhesive wear and slight abrasive wear. The wear scar width of the B5 coating is the smallest, and there is a discontinuous oxide film on the wear scar surface. The EDS results show that it is consistent with the B3 coating, and the B element content in the oxide film is enriched. The Gibbs free energy of the most stable oxides of Fe, Co, Cr, Ni, Cu, and B at room temperature is as follows: Fe2O3 (-742.5 kJ / mol), Co3O4 (-784.2 kJ / mol), Cr2O3 (-1041.0 kJ / mol), Ni3O4 (-763.6 kJ / mol), CuO (-129.7 kJ / mol), and B2O3 (-833 kJ / mol). Cr2O3 has the lowest Gibbs free energy, indicating that it is the most stable oxide, followed by B2O3. Cr2O3 and B2O3 can form oxide films with low friction coefficients during friction. Both Cr2O3 and B2O3 are high-temperature solid lubricants. Through thermal reaction or mechanical mixing at the friction interface, they can form composite oxide films with metals or other oxides. These films have a low friction coefficient, excellent wear resistance, and can effectively reduce the generation and conduction of frictional heat, thereby achieving a self-lubricating effect. The B5 coating also exhibits cracks in characteristic areas due to cyclic loads or stresses, and micro-cutting caused by abrasive particles. The main wear mechanisms of the B5 coating are slight abrasive wear and fatigue wear.

[0077] The wear morphology of the grinding balls of Q235 ordinary carbon steel and the carbon steel composite materials of Examples 1 to 3 at room temperature is as follows: Figure 8As shown in the figures ((a) Q235 ordinary carbon steel; (b) B1; (c) B3; (d) B5), as the molar ratio of element B increases, the wear area of ​​the grinding balls decreases significantly, indicating that the wear resistance of the coatings has improved. A large amount of material that migrated from the B1 coating adheres to the grinding balls corresponding to the B1 coating. This material migration is significantly reduced in the B3 and B5 coatings, resulting in less coating material on the grinding balls. The B3 and B5 coatings are more stable during the friction process, and the wear on the grinding balls is less. This is related to the precipitation of boride in the microstructure of the B3 and B5 coatings, which makes it difficult for the grinding balls to press the coatings into the grinding balls, thereby reducing the contact area between the friction pairs. As a result, less material is sheared and exfoliated by shear force, improving the overall wear resistance of the friction pairs. The addition of element B can effectively inhibit adhesive wear, reduce the friction coefficient, enhance the overall wear resistance and friction reduction performance of the friction pairs, and extend the overall service life of the friction pairs.

[0078] Figure 9The wear surface morphology of Q235 ordinary carbon steel and the carbon steel composite material of Examples 1 to 3 at 600°C (((a1 to a3) is Q235 ordinary carbon steel; (b1 to b3) is B1; (c1 to c3) is B3; (d1 to d3) is B5)). According to the results in the figure, it can be seen that compared with the wear morphology at room temperature, the wear scar surface is covered by a thicker oxide film. The wear scar surface is basically covered by oxides. The wear surface of Q235 ordinary carbon steel is covered by a continuous large-area oxide film, but due to the effect of thermal expansion and the influence of internal stress, cracks appear on the surface of the oxide film, and there are obvious plowing grooves on the wear scar surface. This is caused by the cutting action of the hard abrasive particles formed by the shedding of the oxide particles of the coating itself during the wear process when they move on the coating surface, and are then filled with the peeled-off fine oxide chips. Its main wear mechanisms are abrasive wear, adhesive wear and oxidative wear. The B1 coating exhibits fine white debris scattered across its smooth oxide film, a result of oxidative wear. Small scratches are observed in characteristic areas. At the initial stage of friction, the various elements in the B1 coating spontaneously undergo oxidation reactions at high temperatures to form an oxide film. Under the crushing action of the grinding balls, the lower-hardness oxides are first broken and ground to powder by the grinding balls, while the other hard oxides participate in the friction process, causing three-body abrasive wear and resulting in small scratches on the oxide film. The primary wear mechanisms of the B1 coating are oxidative wear and abrasive wear. The wear morphology of the B3 coating is strikingly different from that of B1. The worn surface remains fully covered by the oxide film, but the area of ​​the broken oxide film is significantly larger, and the amount of powdered debris increases significantly. Severe cracks are present at the edges of the oxide film, which flakes off to form flaky fragments, while microcutting is significantly slowed. At the beginning of wear, the B3 coating's hardness increases due to the addition of element B, but this also leads to increased brittleness and reduced fatigue strength, making it more susceptible to brittle peeling. When the friction pair continues to slide relative to each other, the cyclic stress generated in the contact area exceeds the fatigue strength of the material, and cracks appear on the surface. The cracks then gradually expand, and then continue to crack and peel, forming flaky wear debris. The wear mechanism of the B3 coating changes from that of the B1 coating to oxidation wear and fatigue wear. The wear scar surface of the B5 coating is covered by a smooth and dense oxide film, and the fragmentation of the oxide film and the fine wear scars are significantly alleviated. Although the addition of element B can lead to a decrease in fatigue strength, the B content in the oxide film also increases significantly with the increase in the molar ratio of element B. The Gibbs free energy of the most stable oxides of Fe, Co, Cr, Ni, Cu and B elements at 600°C are: Fe2O3 (-1177.9 kJ / mol), Co3O4 (-1209.8 kJ / mol), Cr2O3 (-1568.0 kJ / mol), Ni3O4 (-1188.4 kJ / mol), CuO (-426.6 kJ / mol), and B2O3 (-1960.0 kJ / mol).B2O3 has the lowest Gibbs free energy, indicating that it is the most stable oxide and can be used as a high-temperature lubricant. The melting point of B2O3 is 510°C. At 600°C, B2O3 melts into a low-viscosity liquid, forming a lubricating film that isolates the contact surfaces and reduces direct contact and adhesion. The B2O3 liquid film has high fluidity and self-repairing ability, and can adjust to changes in the friction surface to maintain lubrication. It can also absorb and transfer some frictional heat, reducing the temperature of the friction surface and delaying the onset of oxidation and thermal fatigue. Therefore, the B5 coating's oxidation wear and fatigue wear are significantly suppressed at 600°C, and its main wear mechanisms are mild abrasive wear and fatigue wear.

[0079] Figure 10 Figure 3 shows the surface morphology of the wear surface of the grinding balls of Q235 plain carbon steel and the carbon steel composites of Examples 1-3 at 600°C ((a) Q235 plain carbon steel; (b) B1; (c) B3; (d) B5)). Compared to room temperature, the wear area of ​​the grinding balls increases significantly, but also decreases with increasing molar ratio of the element B. From the perspective of material migration, the wear surface of the grinding balls corresponding to the B1 coating is likely covered by material migrated from the B1 coating, indicating significant adhesion between the B1 coating and the grinding balls. However, the wear morphology after the coating wears away is relatively smooth, lacking obvious signs of adhesive wear. This is because the oxide film formed is relatively thin in the initial wear stage, making it difficult to provide friction reduction and wear resistance. However, at 600°C, the coating softens at high temperatures and is more susceptible to adhesive wear. As the friction test progresses, the oxidation rate increases, gradually forming a stable friction layer composed of a dense oxide film. As the molar ratio of element B increases, its hardness increases. Furthermore, the friction pair, isolated by the liquid B2O3 high-temperature lubricant, reduces direct contact, effectively suppressing adhesion. This is reflected in a decrease in the area of ​​the wear surface of the corresponding grinding balls in the B3 and B5 coatings covered by the migrated material from the coating. Element B can effectively improve the friction compatibility of the friction pair.

[0080] The above is a detailed description of the embodiments of the present invention, but the present invention is not limited to the above embodiments. Various changes can be made within the knowledge of ordinary technicians in the relevant technical field without departing from the scope of the present invention.

Claims

1. A carbon steel composite material, characterized in that: It includes a carbon steel substrate and a high entropy alloy coating on the surface of the carbon steel substrate; The high entropy alloy coating is composed of the following components: iron, cobalt, chromium, nickel, copper and boron; The molar ratio of the iron element, the cobalt element, the chromium element, the nickel element, the copper element and the boron element is 1:1:1:1:1:0.5; The carbon steel composite material is prepared by the following method: S1, mixing iron powder, cobalt powder, chromium powder, nickel powder, copper powder and boron powder, ball milling and drying to obtain a mixed powder; S2, cladding the surface of a carbon steel substrate with the mixed powder by laser to obtain a carbon steel composite material; The laser power of the laser cladding is 1200W to 2000W.

2. The carbon steel composite material according to claim 1, characterized in that: The rotation speed of the ball mill is 400 r / min to 800 r / min.

3. The carbon steel composite material according to claim 1, characterized in that: The laser beam output spot of the laser cladding is 1 to 2 mm.

4. The carbon steel composite material according to claim 1, characterized in that: The particle sizes of the iron powder, cobalt powder, chromium powder, nickel powder and copper powder are independently selected from 45 μm to 105 μm.

5. The carbon steel composite material according to claim 1, characterized in that: The particle size of the boron powder is 15 μm to 45 μm.

6. The carbon steel composite material according to claim 1, characterized in that: The surface of the carbon steel substrate is treated to remove impurities.

7. Use of the carbon steel composite material according to any one of claims 1 to 6 in sports parts.

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