A wear-resistant coating for bearings and TC bearings

Abstract

This invention discloses a bearing wear-resistant coating and a TC bearing, belonging to the technical field of cemented carbide coated bearings. It includes a wear-resistant coating and a wear-resistant transition layer. The wear-resistant coating comprises 10-40% metallic binder phase, 0.3-0.8% rare earth oxides, and the balance being a wear-resistant hard phase. The preparation method of the bearing wear-resistant coating is as follows: S1. Laser cladding the raw materials for the wear-resistant transition layer onto the surface of the bearing steel substrate; S2. Mixing, grinding, pressing, and pre-sintering the raw materials for the wear-resistant coating to obtain a blank, then pulverizing and ball-milling the blank to obtain coating powder; S3. Laser cladding the coating powder onto the surfaces of the cemented carbide block and the wear-resistant transition layer to form the bearing wear-resistant coating. This invention significantly improves the bonding stability between the coating and the bearing substrate and cemented carbide block, reduces damage to the heat-affected zone of the substrate, and the prepared TC bearing has long-term service capability.

Description

Technical Field

[0001] This invention belongs to the field of bearing wear-resistant coating technology, specifically a bearing wear-resistant coating and a TC bearing. Background Technology

[0002] As a core component of mechanical equipment, bearings directly affect the service life, reliability, and operating efficiency of the equipment. Under extreme working conditions such as oil drilling, mining machinery, and metallurgical rolling, bearings are subjected to the combined effects of high loads, strong impacts, severe wear, and corrosive media, which places extremely stringent requirements on surface wear resistance.

[0003] Currently, to directly form a high-wear-resistant coating in the gaps between cemented carbide blocks, existing technology CN118932330A uses composite tungsten carbide and nickel-iron alloy powders with specific compositions, achieving metallurgical bonding through laser cladding. However, this existing technology has a relatively singular wear-resistant phase, mainly relying on tungsten carbide. Although Ni and Co binders are added, it still falls short in terms of high-temperature red hardness and toughness. The mechanical mixing characteristics of the powder are prone to component segregation or dissolution of the hard phase during rapid melting and solidification, affecting the uniformity of the microstructure. At the same time, due to the lack of effective microstructure modification, the grains are coarse and have defects such as micropores, which limit the load-bearing capacity and fatigue life of the coating. Summary of the Invention

[0004] To overcome the aforementioned technical problems, this invention provides a bearing wear-resistant coating and a TC bearing. The ternary wear-resistant system of this invention is combined with a nickel-based alloy binder phase and modified with rare earth oxides and grain growth inhibitors. It is prepared using a process combining pre-sintering powder preparation and laser cladding. The pre-sintering process achieves pre-alloying and composition homogenization of the raw materials, while the laser cladding precisely controls the heat input, forming a dense and uniform coating structure. Simultaneously, it significantly improves the bonding stability between the coating and the bearing substrate and cemented carbide block, reduces damage to the heat-affected zone of the substrate, and the prepared TC bearing possesses long-term service capability.

[0005] The present invention solves the above-mentioned technical problems through the following technical solutions.

[0006] This invention discloses a bearing wear-resistant coating, comprising a wear-resistant coating and a wear-resistant transition layer; The wear-resistant coating comprises the following raw materials by mass percentage: 10-40% metallic binder phase, 0.3-0.8% rare earth oxides, and the balance wear-resistant hard phase; preferably, the bearing wear-resistant coating comprises the following raw materials by mass percentage: 20-30% metallic binder phase, 0.4-0.6% rare earth oxides, and the balance wear-resistant hard phase; The wear-resistant hard phase comprises the following raw materials by mass percentage: 5-20% TiC powder, 5-20% Cr3C2 powder, 0.5-1.5% grain growth inhibitor and balance WC; The raw materials for preparing the wear-resistant transition layer and the metal binder phase are both nickel-based alloy powders; The method for preparing the bearing wear-resistant coating includes the following steps: S1. Laser cladding the raw materials for the wear-resistant transition layer onto the surface of the bearing steel substrate; S2. The raw materials for the preparation of the wear-resistant coating are mixed, ground, pressed and pre-sintered to obtain a blank. The blank is then crushed and ball-milled to obtain the coating powder. S3. The coating powder is laser-fused onto the surface of the cemented carbide block and the wear-resistant transition layer to form a bearing wear-resistant coating.

[0007] Preferably, the wear-resistant hard phase comprises the following raw materials by mass percentage: 8-18% TiC powder, 10-18% Cr3C2 powder, 0.8-1.2% grain growth inhibitor, and the balance WC; wherein, WC provides basic hardness and wear resistance; TiC has extremely high hardness, which can significantly improve the red hardness and high-temperature wear resistance of the coating, and can refine the WC grains; Cr3C2 has good oxidation resistance and corrosion resistance, and at the same time, it has good wettability with the nickel-based binder phase.

[0008] According to some embodiments of the present invention, the grain growth inhibitor is TaC and / or NbC.

[0009] According to some embodiments of the present invention, the rare earth oxide is at least one of Y2O3 powder and La2O3 powder; the rare earth oxide is used to alleviate the thermal stress of laser cladding and reduce the risk of cracking.

[0010] According to some embodiments of the present invention, the average particle size of the raw material for preparing the wear-resistant hard phase is 10~150μm, preferably 30~80μm.

[0011] According to some embodiments of the present invention, the average particle size of the rare earth oxide is 0.2~1μm, preferably 0.3~0.6μm.

[0012] According to some embodiments of the present invention, the nickel-based alloy powder comprises the following chemical composition by mass percentage: 10-20% Cr, 1.5-3.5% B, 2-4.5% Si, 0-10% Fe, and the balance Ni; preferably, the nickel-based alloy powder comprises the following chemical composition by mass percentage: 14-18% Cr, 2-3% B, 2.5-4% Si, 0-5% Fe, and the balance Ni. Cr improves oxidation and corrosion resistance; B and Si significantly lower the alloy melting point and improve fluidity; Fe element improves compatibility with the steel matrix.

[0013] According to some embodiments of the present invention, the average particle size of the nickel-based alloy powder is 50~100μm, preferably 60~80μm.

[0014] In S1, the protective gas flow rate is 12~16L / min and the powder feeding gas flow rate is 6~8L / min during the laser cladding process; In S1, the power of the laser cladding is 1.0~1.5kW, preferably 1.0~1.3kW; In S1, the diameter of the laser cladding spot is 2.5~4.0mm, preferably 3.0~3.5mm; In S1, the scanning speed of the laser cladding is 12~20 mm / s, preferably 14~18 mm / s; In S1, the overlap rate of the laser cladding is 35-45%; In S1, the powder feeding rate of the laser cladding is 8~18 g / min, preferably 10~15 g / min.

[0015] In S2, the grinding is carried out by mixing and grinding in a planetary ball mill for 2 to 4 hours, with a ball-to-material ratio of 8:1 to 10:1 and a rotation speed of 200 to 250 rpm, and then passing the grinding through a 150-mesh sieve. In S2, the pressing pressure is 150~250MPa, preferably 180~220MPa.

[0016] In S2, the pre-sintering is carried out in an inert gas atmosphere by heating to 1100-1200°C at a heating rate of 5-8°C / min and holding at that temperature for 2-3 hours. In S2, the crushing is performed by a jaw crusher to crush the particles to a size ≤5mm; In S2, the ball milling is carried out in a planetary ball mill for 2-4 hours, with a ball-to-material ratio of 8:1-10:1 and a rotation speed of 200-250 rpm. After ball milling, the material is passed through a 120-mesh sieve.

[0017] In S3, the protective gas flow rate is 15~20L / min and the powder feeding gas flow rate is 8~10L / min during the laser cladding process.

[0018] In S3, the power of the laser cladding is 1.0~2.0kW, preferably 1.3~1.8kW.

[0019] In S3, the diameter of the laser cladding spot is 3~5mm, preferably 3.5~4.5mm.

[0020] In S3, the scanning speed of the laser cladding is 8~15mm / s, preferably 10~12mm / s.

[0021] In S3, the overlap rate of the laser cladding is 45-55%, preferably 50-55%.

[0022] In S3, the powder feeding rate of the laser cladding is 20~35g / min, preferably 25~30g / min.

[0023] In step S3, the laser cladding process further includes a stress annealing step, wherein the stress annealing is performed at 150~400℃ for 1~3 hours; preferably, the stress annealing is performed at 200~300℃ for 1.5~2.5 hours.

[0024] According to some embodiments of the present invention, the thickness of the wear-resistant transition layer is 0.8~1.6mm, preferably 1.2~1.5mm.

[0025] According to some embodiments of the present invention, the Vickers hardness HV0.5 of the wear-resistant coating is ≥1040 HV, preferably 1040~1150 HV.

[0026] This invention discloses a TC bearing, comprising a bearing base, a cemented carbide block, and the aforementioned bearing wear-resistant coating.

[0027] According to some embodiments of the present invention, the material of the bearing base is 42CrMo, 40Cr, 40CrMo, 4145 or 4330V.

[0028] According to some embodiments of the present invention, the cemented carbide block is a YG-type tungsten-cobalt cemented carbide, preferably a YG6, YG8, or YG10-type tungsten-cobalt cemented carbide.

[0029] According to some embodiments of the present invention, the depth of the heat-affected zone below the coating area of ​​the bearing substrate is ≤0.9mm, preferably 0.6~0.8mm.

[0030] According to some embodiments of the present invention, the shear bond strength between the bearing wear-resistant coating and the bearing substrate is ≥320MPa, preferably 330~350MPa.

[0031] Based on common knowledge in the field, the above-mentioned preferred conditions can be combined arbitrarily to obtain various preferred embodiments of the present invention.

[0032] Compared with the prior art, the beneficial effects of the present invention are: 1. This invention employs a ternary wear-resistant phase. WC provides basic hardness, TiC enhances the red hardness of the coating, and Cr3C2 optimizes the wettability with the nickel-based binder phase, while simultaneously improving the coating's oxidation resistance and corrosion resistance, preventing oxidation failure at high temperatures. This triple wear-resistant structure can resist abrasive wear of different scales. The metallic binder phase is a key factor in the interface strengthening mechanism. Cr in the nickel-based alloy powder enhances the coating's oxidation resistance and corrosion resistance, preventing binder phase failure under harsh working conditions. B and Si lower the alloy's melting point, improve cladding fluidity, and ensure coating density. Fe optimizes compatibility with the bearing steel substrate, improving the metallurgical bonding effect. Laser cladding causes elemental interdiffusion between the binder phase and the matrix, forming a metallurgical bond.

[0033] 2. This invention, through mixing, pressing, and pre-sintering the raw materials, allows elements such as Ni and Co to penetrate into the WC grain boundaries in advance, solving the compositional segregation problem caused by traditional direct powder mixing. The pre-alloyed powder melts rapidly under laser irradiation, forming a uniform molten pool. The ternary wear-resistant phase is uniformly dispersed in the binder phase, preventing the hard phase from agglomerating or dissolving, thus ensuring microstructure uniformity. Compared to direct powder mixing and laser cladding, this method ensures both compositional uniformity and controls the heat-affected zone, achieving advantages in uniformity and low damage.

[0034] 3. A wear-resistant transition layer with excellent toughness and compatibility with the bearing substrate is first formed through low-heat-input laser cladding. A high-hardness wear-resistant coating is then clad onto this transition layer, achieving thermal input stress gradient buffering. The transition layer composition matches the thermal expansion coefficient of the bearing substrate, significantly mitigating the thermal shock and internal stress concentration caused by directly cladding the high-hardness wear-resistant coating. This avoids problems such as localized overheating, grain coarsening, and substrate softening caused by direct contact between the wear-resistant coating and the steel substrate. Without reducing the interfacial bonding strength, the depth of the heat-affected zone of the substrate is significantly reduced, protecting the original strength and toughness of the bearing substrate. This makes the bearing less prone to substrate fatigue deformation and coating cracking under heavy load, high speed, and impact conditions, significantly improving its overall service life.

[0035] 4. Rare earth oxides can alleviate the thermal stress generated by laser cladding and reduce the risk of cracking through the lattice distortion effect of rare earth atoms. Grain inhibitors further suppress WC grain ripening, ensuring the stability of the fine-grained structure. In addition to the addition of rare earth oxides to avoid stress concentration, this invention also reduces the risk of cracking by releasing internal stress through a stress-relief annealing process. Attached Figure Description

[0036] To facilitate understanding by those skilled in the art, the present invention will be further described below with reference to the accompanying drawings.

[0037] Figure 1 This is a cross-sectional view of the bearing wear-resistant coating prepared in Example 1.

[0038] Figure 2 This is a cross-sectional view of the bearing wear-resistant coating prepared in Example 7.

[0039] Figure 3 This is a cross-sectional view of the bearing wear-resistant coating prepared in Comparative Example 1. Detailed Implementation

[0040] To facilitate understanding of the present invention, the present invention will be described more fully and in detail below with reference to preferred embodiments, but the scope of protection of the present invention is not limited to the following specific embodiments.

[0041] Unless otherwise defined, all technical terms used herein have the same meaning as commonly understood by those skilled in the art. The technical terms used herein are for the purpose of describing particular embodiments only and are not intended to limit the scope of the invention.

[0042] Example 1 The bearing wear-resistant coating in this embodiment consists of a wear-resistant coating and a wear-resistant transition layer; The raw materials for preparing the wear-resistant coating consist of 25% metallic binder phase (nickel-based alloy powder, average particle size 80 μm), 0.5% rare earth oxide (Y2O3 powder, average particle size 0.6 μm) and the balance wear-resistant hard phase (average particle size 50 μm). The wear-resistant hard phase is composed of the following raw materials in mass percentage: 16.3% TiC powder, 9.8% Cr3C2 powder, 1.0% grain growth inhibitors (0.5% TaC and 0.5% NbC) and balance WC; The raw material for preparing the wear-resistant transition layer is nickel-based alloy powder; The nickel-based alloy powder is composed of the following chemical composition: 16wt%Cr, 2.5wt%B, 3.2wt%Si, 3wt%Fe and balance Ni.

[0043] The method for preparing the bearing wear-resistant coating in this embodiment is as follows: S0. Preprocessing The surface of 42CrMo steel (outer diameter Φ100mm, inner diameter Φ70mm, length 125mm) is cleaned and finely ground; YG8 tungsten cobalt cemented carbide is fitted and assembled with the bearing base friction surface, and the surface roughness Ra of the cladding surface is 0.05μm. S1. Laser-clad wear-resistant transition layer The aforementioned nickel-based alloy powder was used to clad the bearing substrate surface. A protective gas was used throughout the cladding process. Specific process parameters were as follows: argon flow rate for protective gas 13 L / min, argon flow rate for powder feeding gas 7 L / min; laser cladding power 1.1 kW, spot diameter 3.2 mm, scanning speed 15 mm / s, overlap rate 42%, powder feeding rate 13 g / min; maximum cladding layer thickness 1.35 ± 0.01 mm. S2. Preparation of coating powder The raw materials for the above-mentioned wear-resistant coating were put into a planetary ball mill with a ball-to-material ratio of 9:1 and a rotation speed of 230 rpm. The mixture was ground for 3 hours and passed through a 150-mesh sieve. Then, a hydraulic press was used to cold press the material under a pressure of 200 MPa to obtain a blank with a diameter of 50 mm and a thickness of 20 mm. The billet is placed in a vacuum sintering furnace, and argon (an inert gas) is introduced as a protective gas. The temperature is raised to 1150°C at a rate of 6.5°C / min and held for 2.5 hours. After sintering, the billet is cooled to room temperature with the furnace to obtain a pre-sintered billet. The pre-sintered billet is crushed to a particle size of ≤5mm by a jaw crusher, and then fed into a planetary ball mill with a ball-to-material ratio of 9:1 and a rotation speed of 230rpm for 3 hours. After ball milling, it is passed through a 120-mesh sieve to obtain the coating powder. S3. Laser-clad wear-resistant coating The coating powder obtained in step S2 is transported to the cladding area via a powder feeder using a laser cladding machine. A protective gas is used throughout the cladding process. Specific process parameters are as follows: argon flow rate for protective gas 17 L / min, argon flow rate for powder feeding gas 9 L / min; laser cladding power 1.5 kW, spot diameter 4.2 mm, scanning speed 11 mm / s, overlap rate 52%, powder feeding rate 28 g / min; maximum cladding layer thickness 1.5 ± 0.1 mm. The laser-clad bearing substrate and cemented carbide block were placed in a vacuum annealing furnace, protected by argon gas, and heated to 300°C at a rate of 5°C / min. The temperature was held for 2 hours and then allowed to cool naturally to room temperature.

[0044] Figure 1 The cross-sectional view of the bearing wear-resistant coating shows that the coating is highly dense, without cladding or bonding defects, and has fine and uniform grains.

[0045] Example 2 The difference between this embodiment and Embodiment 1 is as follows: The wear-resistant hard phase is composed of the following raw materials by mass percentage: 5.7% TiC powder, 16.4% Cr3C2 powder, 1.0% grain growth inhibitor and balance WC; The other raw materials, steps and parameters are the same as in Example 1.

[0046] Example 3 The difference between this embodiment and Embodiment 1 is as follows: The wear-resistant hard phase is composed of the following raw materials in mass percentage: 17.9% TiC powder, 6.8% Cr3C2 powder, 1.0% grain growth inhibitor and balance WC; The other raw materials, steps and parameters are the same as in Example 1.

[0047] Example 4 The difference between this embodiment and Embodiment 1 is as follows: The nickel-based alloy powder is composed of the following chemical composition by weight percentage: 18wt% Cr, 3wt% B, 4.5wt% Si, 5wt% Fe and balance Ni; The other raw materials, steps and parameters are the same as in Example 1.

[0048] Example 5 The difference between this embodiment and Embodiment 1 is as follows: The nickel-based alloy powder is composed of the following chemical composition by weight percentage: 10 wt% Cr, 1.5 wt% B, 2.0 wt% Si and balance Ni; The other raw materials, steps and parameters are the same as in Example 1.

[0049] Example 6 The difference between this embodiment and Embodiment 1 is as follows: The S1 laser cladding power was adjusted to 0.9kW and the scanning speed to 18mm / s; The other raw materials, steps and parameters are the same as in Example 1.

[0050] Example 7 The difference between this embodiment and Embodiment 1 is as follows: The S3 laser cladding power was adjusted to 2.0kW and the scanning speed to 15mm / s; The other raw materials, steps and parameters are the same as in Example 1.

[0051] Figure 2 In the cross-sectional view of the bearing wear-resistant coating, the high temperature during the cladding of the wear-resistant layer is transmitted downwards, causing a secondary thermal shock to the already formed transition layer, resulting in fine stress textures at the interface between the transition layer and the substrate.

[0052] Comparative Example 1 The difference between this comparative example and Example 1 is as follows: In S2, the raw materials for preparing the wear-resistant coating are ground and then directly subjected to the S2 process without pressing or pre-sintering. The other raw materials, steps and parameters are the same as in Example 1.

[0053] Figure 3 In the cross-sectional view of the bearing wear-resistant coating, the wear-resistant coating has local hard aggregates and uneven dispersion, and there are many cracks and pores in both the wear-resistant coating and the wear-resistant transition layer. This is because the melting and spreading behavior is out of control during laser cladding, and the stability of the molten pool decreases significantly. At the same time, the heat input is disordered, local overheating is severe, and high temperature fluctuations are transmitted downwards, damaging the already formed wear-resistant transition layer.

[0054] Comparative Example 2 The difference between this comparative example and Example 1 is as follows: The bearing wear-resistant coating consists of 30% metallic binder phase (nickel-based alloy powder) and the balance wear-resistant hard phase; The other raw materials, steps and parameters are the same as in Example 1.

[0055] The bearing wear-resistant coatings of the TC bearings prepared in the above embodiments and comparative examples were subjected to the following tests: Test Example 1—Coating Hardness and Coating-Substrate Shear Bond Strength Test Hardness was tested using a Vickers hardness tester (HV0.5, 4.903N); shear bond strength was determined by the annular indentation shear method using an electronic universal testing machine and a polycrystalline diamond annular indenter (outer diameter 5mm, inner diameter 3mm). During the test, the indenter applied pressure to the coating surface at a rate of 0.5mm / min until shear peeling occurred, and the maximum load F was recorded. The shear bond strength was calculated using the formula τ=F / A, where A is the cross-sectional area of ​​the annular indenter; the test results are shown in Table 1.

[0056]

[0057] Referring to Table 1, it is important to note that: Comparative Example 1 directly used the raw materials for preparing the wear-resistant coating for laser cladding, resulting in component segregation, a large number of unmelted particles, and high internal stress, ultimately leading to a decrease in hardness and bonding strength. Comparative Example 2 lacked rare earth oxides, making the grains more prone to coarsening, especially with the addition of multiple wear-resistant phases, ultimately resulting in a significant decrease in both hardness and bonding strength.

[0058] Test Example 2—Depth and Hardness of Heat-Affected Zone Heat-affected zone depth: Metallographic corrosion test (4% nitric acid alcohol). Using the metallographically corroded sample, observe the area where the coating-substrate interface to the interior of the substrate shows a significant change in microstructure under a metallographic microscope. Measure the vertical distance of this area, which is the depth of the heat-affected zone. Randomly select three fields of view and take the average value. Heat-affected zone hardness: Select five test points evenly within the heat-affected zone (areas of different depths) and use a Vickers hardness tester (HV). 0.5 The hardness was tested at 4.903 N, and the range of hardness variation was recorded to determine whether the matrix had overheated and softened. The test results are shown in Table 2.

[0059]

[0060] Referring to Table 2, it should be noted that: Example 6, due to its low cladding power, fastest speed, and smallest heat input, has the narrowest heat-affected zone and the highest hardness. Example 7 has a slightly higher heat input, a slightly wider heat-affected zone, and slightly lower hardness. Comparative Example 1, lacking the pressing and pre-sintering process of the raw materials, suffers from uneven melting of the coating powder and disordered heat conduction, leading to a significantly wider heat-affected zone and softening of the substrate during laser cladding. Comparative Example 2, lacking rare earth oxides, experiences stress concentration in the wear-resistant coating, increased interfacial thermal resistance, and ultimately a wider heat-affected zone and decreased hardness.

[0061] Test Example 3—Bearing Rotational Fatigue Life Test The test was conducted in accordance with GB / T 307.3, and the bearings prepared in Example 1 were selected as the test group. A bearing rotational fatigue life tester was used, and the test conditions were: radial load 40kN (heavy load), speed 3000r / min (high speed), room temperature 25℃, and grease lubrication. The time when the vibration value suddenly increased, the temperature suddenly increased (>80℃), or the bearing jammed was recorded continuously. This time was the bearing fatigue life. The rated fatigue life (L10, reliability 90%) was calculated according to GB / T 307.3. A 42CrMo bearing of the same model without a wear-resistant transition layer but only containing a wear-resistant coating was used as the control group (the preparation process was the same as in Example 1 except for the lack of step S1). The life was tested simultaneously for comparison. The test results are shown in Table 3.

[0062]

[0063] Unless otherwise specified, all raw materials, reagents, instruments, and equipment used in this invention can be purchased commercially or prepared using existing methods. The specific embodiments described above further illustrate the purpose, technical solution, and beneficial effects of this invention. It should be understood that the above descriptions are merely specific embodiments of this invention and are not intended to limit the invention. Any modifications, equivalent substitutions, or improvements made within the spirit and principles of this invention should be included within the scope of protection of this invention.

Claims

1. A bearing wear-resistant coating, characterized in that, Includes wear-resistant coating and wear-resistant transition layer; The wear-resistant coating comprises the following raw materials by mass percentage: 10-40% metallic binder phase, 0.3-0.8% rare earth oxides, and the balance wear-resistant hard phase; the wear-resistant hard phase comprises the following raw materials by mass percentage: 5-20% TiC powder, 5-20% Cr3C2 powder, 0.5-1.5% grain growth inhibitor, and the balance WC; The raw materials for preparing the wear-resistant transition layer and the metal binder phase are both nickel-based alloy powders; the preparation method of the bearing wear-resistant coating includes the following steps: S1. Laser cladding the raw materials for the wear-resistant transition layer onto the surface of the bearing steel substrate; S2. The raw materials for the preparation of the wear-resistant coating are mixed, ground, pressed and pre-sintered to obtain a blank. The blank is then crushed and ball-milled to obtain the coating powder. S3. The coating powder is laser-fused onto the surface of the cemented carbide block and the wear-resistant transition layer to form a bearing wear-resistant coating.

2. The bearing wear-resistant coating as described in claim 1, characterized in that, The grain growth inhibitor is TaC and / or NbC; And / or, the rare earth oxide is at least one of Y2O3 powder and La2O3 powder; And / or, the average particle size of the raw material for preparing the wear-resistant hard phase is 10~150μm; And / or, the average particle size of the rare earth oxide is 0.2~1μm.

3. The bearing wear-resistant coating as described in claim 1, characterized in that, The nickel-based alloy powder comprises the following chemical composition by mass percentage: 10-20% Cr, 1.5-3.5% B, 2-4.5% Si, 0-10% Fe and balance Ni; And / or, the average particle size of the nickel-based alloy powder is 50~100μm.

4. The bearing wear-resistant coating as described in claim 1, characterized in that, In S1, the protective gas flow rate is 12~16L / min and the powder feeding gas flow rate is 6~8L / min during the laser cladding process; And / or, in S1, the power of the laser cladding is 1.0~1.5kW; And / or, in S1, the diameter of the laser cladding spot is 2.5~4.0 mm; And / or, in S1, the scanning speed of the laser cladding is 12~20mm / s; And / or, in S1, the overlap rate of the laser cladding is 35-45%; And / or, in S1, the powder feeding rate of the laser cladding is 8~18 g / min.

5. The bearing wear-resistant coating as described in claim 1, characterized in that, The pressing pressure is 150~250MPa; And / or, the pre-sintering is carried out in an inert gas atmosphere by heating to 1100-1200°C at a heating rate of 5-8°C / min and holding at that temperature for 2-3 hours. And / or, the crushing is performed by a jaw crusher to a particle size ≤5mm; And / or, the ball milling is performed in a planetary ball mill for 2-4 hours, with a ball-to-material ratio of 8:1-10:1 and a rotation speed of 200-250 rpm, and the ball milled material is then passed through a 120-mesh sieve.

6. The bearing wear-resistant coating as described in claim 1, characterized in that, In S3, the protective gas flow rate is 15~20L / min and the powder feeding gas flow rate is 8~10L / min during the laser cladding process; And / or, in S3, the power of the laser cladding is 1.0~2.0kW; And / or, in S3, the diameter of the laser cladding spot is 3~5mm; And / or, in S3, the scanning speed of the laser cladding is 8~15mm / s; And / or, in S3, the overlap rate of the laser cladding is 45-55%; And / or, in S3, the powder feeding rate of the laser cladding is 20~35g / min; The laser cladding process also includes a stress annealing step, which involves holding the product at 150-400°C for 1-3 hours.

7. The bearing wear-resistant coating as described in claim 1, characterized in that, The thickness of the wear-resistant transition layer is 0.8~1.6mm.

8. The bearing wear-resistant coating as described in claim 1, characterized in that, The wear-resistant coating has a Vickers hardness of ≥1040HV0.

5.

9. A TC bearing, characterized in that, Includes a bearing substrate, a cemented carbide block, and a bearing wear-resistant coating as described in any one of claims 1 to 6; And / or, the material of the bearing base is 42CrMo, 40Cr, 40CrMo, 4145 or 4330V; And / or, the cemented carbide block is a YG-type tungsten-cobalt cemented carbide.

10. The TC bearing as described in claim 9, characterized in that, The depth of the heat-affected zone below the coating area in the bearing substrate is ≤0.9mm; And / or, the shear bond strength between the bearing wear-resistant coating and the bearing substrate is ≥320MPa.

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