Micro-nanoparticle reinforced m35 high speed steel with excellent wear resistance and preparation method thereof

Abstract

The application provides trace nano-particle reinforced M35 high-speed steel with excellent wear resistance and a preparation method, and the preparation method comprises the following steps: mixing titanium-aluminum alloy powder, BN powder and C powder through ball milling, and then obtaining wire rod A through aluminum strip coating and drawing; heating the wire rod A to obtain a metal melt, mixing the metal melt with pure aluminum liquid, and then obtaining second mixed particles through mechanical stirring, ultrasonic treatment, casting and rolling and crushing; mixing aluminum-niobium alloy powder and B4C powder through ball milling, and then obtaining fourth mixed particles through press forming and electric explosion reaction treatment; mixing the second mixed particles and the fourth mixed particles, and then obtaining wire rod B through stainless steel strip coating and drawing; melting and refining M35 high-speed steel, adding the wire rod B, and then performing casting, forging, isothermal annealing, rolling, quenching and tempering treatment; the application adds Nb-TiC and Nb-TiB2 nano ceramic particles, significantly refines carbides and makes the carbides disperse and distribute; the volume wear rate at room temperature is 6.9*10 ‑6 -7.5*10 ‑6 mm 3 / (N*m), the volume wear rate at 200 DEG C is 8.8*10 ‑6 -9.5*10 ‑6 mm 3 / (N*m), the wear surface furrow is narrow, the cutting trace is shallow, and the overall wear resistance is excellent.

Description

Technical Field

[0001] This invention belongs to the field of high-speed steel material technology, specifically relating to M35 high-speed steel reinforced with micro-nano particles with excellent wear resistance and its preparation method. Background Technology

[0002] In the manufacturing of various cutting tools, molds, and wear-resistant parts (such as cold work die steel and tools for machining titanium alloys), M35 high-speed steel has become an indispensable material for manufacturing complex cutting tools due to its excellent hardness and wear resistance. However, with the increasing application of high-speed cutting, dry cutting, and difficult-to-machine materials such as titanium alloys and high-temperature alloys, the wear resistance of M35 high-speed steel has gradually become insufficient to meet the higher requirements of modern manufacturing for tool life and machining efficiency. To improve the wear resistance of M35 high-speed steel, existing technologies mainly add precious metal elements such as cerium, lanthanum, and yttrium, with an addition amount of approximately 0.03%-0.06%, leading to a significant increase in raw material costs. Simultaneously, complex processes such as electroslag remelting and pulsed current treatment are required, placing stringent demands on equipment. Although these high-cost and complex processes improve the wear resistance and toughness of M35 high-speed steel to some extent, the overall cost is high due to the combined effects of raw materials, processes, and equipment, limiting its economic viability and promotional value in a wider range of industrial applications. Furthermore, high pressure or high temperature conditions will cause a decrease in the wear resistance of high-speed steel. Therefore, how to ensure the high wear resistance of M35 high-speed steel while reducing the addition of precious metal elements, simplifying the process, and reducing costs is an urgent problem to be solved. Summary of the Invention

[0003] To address the aforementioned technical challenges, this invention provides a micro-nano-particle-reinforced M35 high-speed steel with excellent wear resistance, the preparation method of which includes the following steps: (1) Titanium aluminum alloy powder, BN powder and C powder are ball-milled at a speed of 25-55 r / min for 8-23 hours at a mass ratio of 55-85:10-20:10-20 to obtain uniform first mixed particles; the first mixed particles are coated with pure aluminum strip, and the mass ratio of pure aluminum strip to first mixed particles is 1.7-2.7:1. Then, after 2-7 drawing processes, wire A is finally obtained; wherein, the particle size of titanium aluminum alloy powder is 30-80 μm, the particle size of BN powder is 50-120 μm, and the particle size range of C powder is 30-60 μm; the drawing process of each pass is: temperature of 200-250℃, speed of 10-17 m / min; (2) The wire A obtained in step (1) is heated to 730-760℃ to obtain a molten metal. The molten metal is then thoroughly mixed with pure aluminum liquid at a mass ratio of 1-10:15-60. After mixing, the mixture is subjected to mechanical stirring, ultrasonic treatment, casting and rolling, and mechanical crushing in sequence to obtain a second mixed particle. The mechanical stirring is performed at a stirring speed of 300-800 rpm for 5-15 minutes. The ultrasonic treatment is performed at an ultrasonic power of 2-10 kW, a frequency of 20-30 kHz, and a treatment time of 1-5 minutes. The casting and rolling process is performed at a temperature of 300-450℃, a speed of 10-30 m / min, and a cooling water flow rate of 10-50 L / min. The mechanical crushing process is performed at a rotation speed of 2300-3800 rpm for 7-22 minutes. (3) Aluminum-niobium alloy powder and B4C powder are ball-milled at a mass ratio of 25-45:5-15 for 4-12 hours at a rotation speed of 25-55 r / min to obtain a third mixed particle; the third mixed particle is then subjected to pressing and electro-explosion reaction treatment to obtain a fourth mixed particle; wherein the particle size of aluminum-niobium alloy powder is 45-110 μm and the particle size of B4C powder is 75-120 μm; the pressing is performed at a pressure of 150-200 MPa and a pressing speed of 15-30 mm / min; the electro-explosion reaction is performed under a low-pressure protective atmosphere, with a controlled pressure of 0.04-0.07 MPa and a pulse current density of 4 × 10⁻⁶. 5 -8×10 5 A / m 2 ; (4) Mix the second mixed particles obtained in step (2) and the fourth mixed particles obtained in step (3) at a mass ratio of 1-3:1. Coat the second and fourth mixed particles with stainless steel strip. The total mass ratio of stainless steel to the second and fourth mixed particles is 1.3-2.7:1. After 10-14 drawing processes, wire B containing stainless steel coated Nb-TiC and Nb-TiB2 nano-ceramic particles is obtained. The drawing process for each pass is: temperature 130-200℃, speed 5-15m / min. (5) After melting M35 high-speed steel at 1520-1620℃ and refining it at 1550-1610℃, wire B obtained in step (4) is added, melted, purified by blowing argon gas, and then vacuum treated at 1550-1610℃ for 50-80 minutes; after casting, forging, isothermal annealing, rolling, quenching and tempering, a micro-nano particle reinforced M35 high-speed steel with excellent wear resistance is obtained; the mass ratio of wire B to M35 is 0.1-0.35%:1; The main components of the M35 high-speed steel, by weight percentage, are: C: 0.87-0.92 wt.%; W: 5.85-6.15 wt.%; Mo: 4.58-5.25 wt.%; Cr: 3.90-4.40 wt.%; V: 1.85-2.05 wt.%; Co: 4.55-4.85 wt.%; Si: 0.28-0.43 wt.%; Mn: 0.23-0.38 wt.%; P: ≤0.022 wt.%; S: ≤0.022 wt.%; the balance is Fe; The casting process is carried out under an argon atmosphere, with the argon protective chamber pressure at 0.025-0.035 MPa, the molten steel temperature controlled at 1430-1480℃, and the molten steel tapping temperature at 1500-1560℃. The forging process is carried out at a temperature of 1100-1170℃ and a forging ratio of 2-5:1. The isothermal annealing process involves holding the temperature at 840-880℃ for 3-6 hours. The rolling process is as follows: roughing rolling begins at 1120-1200℃, finishes at 1000-1050℃, with 5-8 passes, each pass having a different reduction rate of 5-30%, resulting in a total reduction rate of 55-71%, and a speed of 5-10 m / s; finishing rolling begins at 950-1060℃, finishes at 830-910℃, with 6-9 passes, each pass having a different reduction rate of 5-25%, resulting in a total reduction rate of 73-85%, and a speed of 12-22 m / s. The quenching and tempering treatment is as follows: oil quenching at 1200-1230℃ for 8-15 minutes; tempering treatment at 550-590℃ for 2-4 times, each time for 2-3 hours. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance obtained in step (5) contains 0.015-0.035% Nb-TiC and Nb-TiB2 nano-ceramic particles by mass, wherein the average particle size of Nb-TiC nano-ceramic particles is 75-196 nm and the average particle size of Nb-TiB2 nano-ceramic particles is 80-210 nm. From the perspective of microstructure, the addition of nanoparticles can refine the carbides, making the carbides present a fine, dispersed and uniform distribution. The dispersed and fine carbides can effectively inhibit crack initiation and propagation, significantly improving the mechanical properties and wear resistance of the test steel. Compared with the comparative example, the carbide grains of the present invention are finer and the distribution is more dispersed and uniform. In terms of wear performance, when subjected to friction test with high-speed steel with hardness ≥67.2HRC under a load of 40N, the volume wear rate of the micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance obtained in the present invention at room temperature and 200℃ is 6.9×10. -6 -7.5×10 -6 mm3 / (N·m) and 8.8×10 -6 -9.5×10 -6 mm 3 / (N·m); The volumetric wear rate of high-speed steel obtained by existing technology when subjected to friction tests with steel with a hardness ≤60HRC at room temperature and 200℃ is 9.0×10. -6 -22.0×10 -6 mm 3 / (N·m) and 11.0×10 -6 -24.5×10 - 6 mm 3 / (N·m); Compared with the prior art, the volumetric wear rate obtained by the present invention under the same or more stringent test conditions is much smaller than that of the prior art. The volumetric wear rate is the most core quantitative indicator of the wear resistance of high-speed steel, and the smaller the value, the better the wear resistance. It can be seen from the comparison that the volumetric wear rate of the present invention is significantly lower than that of the prior art. Therefore, the wear performance of the present invention is significantly higher than that of the prior art.

[0004] Further, in step (1), titanium-aluminum alloy powder, BN powder, and C powder are ball-milled at a speed of 30-50 r / min for 13-20 hours at a mass ratio of 60-80:13-17:13-17 to obtain uniform first mixed particles; pure aluminum strip is used to coat the first mixed particles, and the mass ratio of pure aluminum strip to the first mixed particles is 1.9-2.5:1. Then, after 3-6 drawing processes, wire A is finally obtained; wherein, the particle size of titanium-aluminum alloy powder is 40-70 μm, the particle size of BN powder is 70-100 μm, and the particle size range of C powder is 40-50 μm; the drawing process for each pass is: temperature of 220-240℃, speed of 12-15 m / min.

[0005] Further, in step (2), the wire A obtained in step (1) is heated to 740-750℃ to obtain a molten metal, and the molten metal is thoroughly mixed with pure aluminum liquid at a mass ratio of 3-7:25-45; after mixing, mechanical stirring, ultrasonic treatment, casting and rolling and mechanical crushing are performed in sequence to obtain the second mixed particles; wherein, the mechanical stirring is: stirring speed 450-650rpm, stirring time 7-13 minutes; the ultrasonic treatment is: ultrasonic power 4-8kW, frequency 22-27kHz, treatment time 2-4 minutes; the casting and rolling is: temperature 320-410℃, speed 15-25m / min, cooling water flow rate 20-40L / min; the mechanical crushing is: rotation speed 2500-3500rpm, crushing time 10-20min.

[0006] Further, in step (3), aluminum-niobium alloy powder and B4C powder are ball-milled at a mass ratio of 30-40:7-13 for 6-10 hours at a rotation speed of 30-50 r / min to obtain a third mixed particle; the third mixed particle is then subjected to pressing and electro-explosion reaction treatment to obtain a fourth mixed particle; wherein, the particle size of aluminum-niobium alloy powder is 60-90 μm, and the particle size of B4C powder is 85-110 μm; the pressing is performed at a pressure of 160-190 MPa and a pressing rate of 17-27 mm / min; the electro-explosion reaction is performed under a low-pressure protective atmosphere, with a controlled pressure of 0.05-0.06 MPa and a pulse current density of 5 × 10⁻⁶ MPa. 5 -7×10 5 A / m 2 .

[0007] Further, in step (4), the second mixed particles obtained in step (2) and the fourth mixed particles obtained in step (3) are mixed evenly at a mass ratio of 1.5-2.7:1. The second and fourth mixed particles are coated with stainless steel strip. The total mass ratio of stainless steel to the second and fourth mixed particles is 1.5-2.5:1. After 11-13 drawing processes, wire B containing stainless steel coated Nb-TiC and Nb-TiB2 nano-ceramic particles is obtained. The drawing process for each pass is: temperature 150-180℃, speed 7-13m / min.

[0008] Further, the main components of M35 high-speed steel described in step (5) by mass percentage are: C: 0.88-0.90wt.%; W: 5.90-6.10wt.%; Mo: 4.65-5.20wt.%; Cr: 3.95-4.35wt.%; V: 1.87-2.02wt.%; Co: 4.60-4.80wt.%; Si: 0.30-0.40wt.%; Mn: 0.25-0.35wt.%; P: ≤0.020wt.%; S: ≤0.020wt.%; with the balance being Fe.

[0009] Furthermore, the casting is carried out under an argon atmosphere, with the argon protective chamber pressure at 0.026-0.033 MPa, the temperature of the molten steel controlled at 1440-1470℃, and the temperature of the molten steel exiting the furnace at 1510-1550℃; Forging is carried out at a temperature of 1130-1150℃ with a forging ratio of 2-4:1. The isothermal annealing process involves holding the temperature at 850-870℃ for 3-5 hours. The rolling process is as follows: roughing rolling begins at 1130-1190℃ and ends at 1010-1040℃, with 6-7 passes, each pass having a different reduction rate of 7-28%, resulting in a total reduction rate of 57-68%, and a speed of 6-9 m / s; finishing rolling begins at 960-1050℃ and ends at 840-900℃, with 7-8 passes, each pass having a different reduction rate of 7-23%, resulting in a total reduction rate of 74-83%, and a speed of 14-20 m / s. The quenching and tempering treatment is as follows: hold at 1205-1220℃ for 9-14 minutes, then oil quench; and perform 3-4 tempering treatments at 555-585℃, holding for 2.5-3 hours each time.

[0010] Furthermore, the volumetric wear rate of the micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance at room temperature and 200°C is 7.0 × 10⁻⁶. -6 -7.4×10 -6 mm 3 / (N·m) and 8.9×10 -6 -9.4×10 -6 mm 3 / (N·m).

[0011] Compared with the prior art, the advantages of the present invention are: Existing technologies improve the wear resistance of M35 high-speed steel to some extent by adding 0.03%-0.06% or more of high-cost metals and rare earth modifiers, or by using complex and costly processes such as electroslag remelting and pulsed current coating. However, these methods generally significantly increase raw material production costs, equipment investment, and production cycles. This invention adds 0.015-0.035% Nb-TiC and Nb-TiB2 nano-ceramic particles to M35 high-speed steel without changing the main matrix composition, and avoids expensive processes such as electroslag remelting, pulsed current treatment, and coating. From a microscopic perspective, the addition of nanoparticles refines the carbides, promoting a fine, dispersed, and uniform distribution, which is significantly better than the coarse and agglomerated carbide distribution in the comparative proportion. The refined and uniformly distributed carbides effectively resist abrasive ploughing, inhibit crack initiation and propagation, avoid stress concentration and large-scale spalling caused by coarse carbide agglomeration, significantly reduce the volumetric wear rate of high-speed steel, and optimize wear resistance. Regarding wear performance, when subjected to friction tests with high-speed steel with a hardness ≥67.2HRC under a load of 40N, the micro-nano-particle-reinforced M35 high-speed steel with excellent wear resistance obtained in this invention exhibits volumetric wear rates of 6.9×10⁻⁶ at room temperature and 200℃. -6 -7.5×10 -6 mm 3 / (N·m) and 8.8×10 -6 -9.5×10 -6mm 3 / (N·m); The volumetric wear rate of high-speed steel obtained by existing technology when subjected to friction tests with steel with a hardness ≤60HRC at room temperature and 200℃ is 9.0×10. -6 -22.0×10 -6 mm 3 / (N·m) and 11.0×10 -6 -24.5×10 -6 mm 3 / (N·m); This invention simultaneously improves the wear resistance of high-speed steel under both room temperature and high temperature conditions, breaking through the technical bottleneck of existing technologies that struggle to maintain high wear resistance simultaneously under these conditions. Volumetric wear rate is the most crucial quantitative indicator of high-speed steel's wear resistance; the smaller the value, the better the wear resistance, meaning this invention exhibits superior wear resistance. This invention, while improving the material's high-pressure and high-temperature performance, significantly simplifies the process, reduces costs, and facilitates large-scale industrial applications. Attached Figure Description

[0012] Figure 1 (a) and (b) are respectively images of the wear surface morphology of the micro-nano-particle-reinforced M35 high-speed steel 1 obtained in Example 1 of the present invention at room temperature and 200°C.

[0013] Figure 2 This is a diagram showing the carbide distribution structure of the micro-nanoparticle-reinforced M35 high-speed steel 1 obtained in Example 1 of the present invention.

[0014] Figure 3 (a) and (b) are respectively images of the wear surface morphology of the micro-nano-particle reinforced M35 high-speed steel 2 obtained in Example 2 of the present invention at room temperature and 200°C.

[0015] Figure 4 This is a diagram showing the carbide distribution structure of the micro-nano-particle-reinforced M35 high-speed steel 2 obtained in Example 2 of the present invention.

[0016] Figure 5 (a) and (b) are respectively images of the wear surface morphology of electroslag remelted M35 high-speed steel 1 obtained in Comparative Example 1 of the present invention at room temperature and 200°C.

[0017] Figure 6 This is a microstructure diagram of the carbide distribution of the electroslag remelted M35 high-speed steel 1 obtained in Comparative Example 1 of the present invention. Detailed Implementation

[0018] The technical solutions in the embodiments of the present invention will be clearly and completely described below. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention. Example 1

[0019] The preparation method of M35 high-speed steel reinforced with micro-nanoparticles is as follows: (1) Titanium aluminum alloy powder, BN powder and C powder were ball-milled at a speed of 40 r / min for 16 hours at a mass ratio of 75:16:16 to obtain uniform first mixed particles; the first mixed particles were coated with pure aluminum strip, and the mass ratio of pure aluminum strip to the first mixed particles was 2:1. Then, after 4 drawing processes, wire A was finally obtained; wherein, the particle size of titanium aluminum alloy powder was 40-70 μm, the particle size of BN powder was 70-100 μm, and the particle size range of C powder was 40-50 μm; the drawing process of each pass was: temperature 210℃, speed 13 m / min; (2) The wire A obtained in step (1) is heated to 740°C to obtain a molten metal. The molten metal is then thoroughly mixed with pure aluminum liquid at a mass ratio of 3:40. After mixing, the mixture is subjected to mechanical stirring, ultrasonic treatment, casting and rolling, and mechanical crushing in sequence to obtain a second mixed particle. The mechanical stirring is performed at a stirring speed of 600 rpm for 10 minutes. The ultrasonic treatment is performed at an ultrasonic power of 6 kW, a frequency of 25 kHz, and a treatment time of 3 minutes. The casting and rolling process is performed at a temperature of 410°C, a speed of 23 m / min, and a cooling water flow rate of 30 L / min. The mechanical crushing process is performed at a rotation speed of 3000 rpm for 15 minutes. (3) Aluminum-niobium alloy powder and B4C powder were ball-milled at a mass ratio of 34:10 for 8 hours at a rotation speed of 45 r / min to obtain a third mixed particle; the third mixed particle was then subjected to pressing and electro-explosion reaction treatment to obtain a fourth mixed particle; wherein the particle size of the aluminum-niobium alloy powder was 60-90 μm and the particle size of the B4C powder was 85-110 μm; the pressing was performed at a pressure of 180 MPa and a pressing rate of 21 mm / min; the electro-explosion reaction was performed under a low-pressure protective atmosphere, with a controlled pressure of 0.05 MPa and a pulse current density of 6.5 × 10⁻⁶. 5 A / m 2 ; (4) The second mixed particles obtained in step (2) and the fourth mixed particles obtained in step (3) are mixed evenly at a mass ratio of 2.3:1. The second and fourth mixed particles are coated with stainless steel strip. The total mass ratio of stainless steel to the second and fourth mixed particles is 1.8:1. After 11 drawing processes, wire B containing stainless steel coated Nb-TiC and Nb-TiB2 nano-ceramic particles is obtained. The drawing process for each process is: temperature 160℃, speed 11m / min. (5) After melting M35 high-speed steel at 1600℃ and refining it at 1580℃, wire B obtained in step (4) is added, melted, purified by blowing argon gas, and then vacuum treated at 1600℃ for 70 minutes; after casting, forging, isothermal annealing, rolling, quenching and tempering, a micro-nano particle reinforced M35 high-speed steel with excellent wear resistance is obtained; the mass ratio of wire B to M35 is 0.32%:1; The main components of the M35 high-speed steel, by weight percentage, are: C: 0.90 wt.%; W: 5.93 wt.%; Mo: 4.97 wt.%; Cr: 3.95 wt.%; V: 1.91 wt.%; Co: 4.61 wt.%; Si: 0.33 wt.%; Mn: 0.31 wt.%; P: 0.019 wt.%; S: 0.019 wt.%; with the balance being Fe. The casting process is carried out under an argon atmosphere, with the argon protective chamber pressure at 0.031 MPa, the molten steel temperature controlled at 1460℃, and the molten steel tapping temperature at 1540℃. The forging process is as follows: temperature is 1140℃, and forging ratio is 3:1; The isothermal annealing is described as follows: holding at 860℃ for 4 hours; The rolling process is as follows: roughing milling starts at 1152℃ and finishes at 1015℃, with 7 passes. The reduction rate for each pass is distributed in descending order: 18%, 17%, 16%, 15%, 14%, 10%, and 7%, for a total reduction rate of 65% and a speed of 7 m / s. Finishing milling starts at 1032℃ and finishes at 876℃, with 8 passes. The reduction rate for each pass is distributed in descending order: 23%, 22%, 21%, 20%, 18%, 15%, 12%, and 8%, for a total reduction rate of 78.5% and a speed of 18 m / s. The quenching and tempering treatment is as follows: oil quenching at 1210℃ for 10 minutes; and tempering at 580℃ three times, each time for 2.5 hours. The micro-nanoparticle-reinforced M35 high-speed steel 1 prepared in this embodiment contains 0.027% Nb-TiC and Nb-TiB2 nano-ceramic particles by mass, wherein the average particle size of the Nb-TiC nano-ceramic particles is 81-190 nm and the average particle size of the Nb-TiB2 nano-ceramic particles is 87-203 nm, and no electroslag remelting or pulsed current treatment process was used. Regarding wear performance, when subjected to friction tests with high-speed steel of hardness 67.8 HRC under a 40 N load, the volumetric wear rate of the micro-nanoparticle-reinforced M35 high-speed steel 1 at room temperature and 200 °C is 7.3 × 10⁻⁶. -6 mm 3 / (N·m) and 9.0×10 -6 mm 3 / (N·m); its wear surface morphology at room temperature and 200℃ are as follows: Figure 1 As shown in (a) and (b), the wear surface has narrower furrows, less cutting marks, and less wear debris; from a microscopic perspective, the carbide distribution of the micro-nano-particle-reinforced M35 high-speed steel 1 is as follows. Figure 2 As shown, the addition of nanoparticles can refine carbides, promoting their fine, dispersed, and uniform distribution. The finely dispersed carbides can effectively inhibit crack initiation and propagation, significantly improving wear resistance. Example 2

[0020] The preparation method of M35 high-speed steel reinforced with micro-nano particles is as follows: (1) Titanium aluminum alloy powder, BN powder and C powder were ball-milled at a speed of 45 r / min for 14 hours at a mass ratio of 78:14:14 to obtain uniform first mixed particles; the first mixed particles were coated with pure aluminum strip, and the mass ratio of pure aluminum strip to first mixed particles was 1.9:1. Then, after 5 drawing processes, wire A was finally obtained; wherein, the particle size of titanium aluminum alloy powder was 40-70 μm, the particle size of BN powder was 70-100 μm, and the particle size range of C powder was 40-50 μm; the drawing process of each pass was: temperature 225℃, speed 12 m / min; (2) The wire A obtained in step (1) is heated to 745°C to obtain a molten metal. The molten metal is then thoroughly mixed with pure aluminum liquid at a mass ratio of 2:30. After mixing, the mixture is subjected to mechanical stirring, ultrasonic treatment, casting and rolling, and mechanical crushing in sequence to obtain a second mixed particle. The mechanical stirring is performed at a stirring speed of 620 rpm for 11 minutes. The ultrasonic treatment is performed at an ultrasonic power of 7 kW, a frequency of 23 kHz, and a treatment time of 3.5 minutes. The casting and rolling is performed at a temperature of 420°C, a speed of 20 m / min, and a cooling water flow rate of 35 L / min. The mechanical crushing is performed at a rotation speed of 3100 rpm for 16 minutes. (3) Aluminum-niobium alloy powder and B4C powder were ball-milled at a mass ratio of 33:8 for 9 hours at a rotation speed of 40 r / min to obtain a third mixed particle; the third mixed particle was subjected to pressing and electro-explosion reaction treatment to obtain a fourth mixed particle; wherein the particle size of aluminum-niobium alloy powder was 60-90 μm and the particle size of B4C powder was 85-110 μm; the pressing was performed at a pressure of 185 MPa and a pressing speed of 22 mm / min; the electro-explosion reaction was performed under a low-pressure protective atmosphere, with a controlled pressure of 0.06 MPa and a pulse current density of 7 × 10⁻⁶. 5 A / m 2 ; (4) The second mixed particles obtained in step (2) and the fourth mixed particles obtained in step (3) are mixed evenly at a mass ratio of 2.1:1. The second and fourth mixed particles are coated with stainless steel strip. The total mass ratio of stainless steel to the second and fourth mixed particles is 2.3:1. After 12 drawing processes, wire B containing stainless steel coated Nb-TiC and Nb-TiB2 nano-ceramic particles is obtained. The drawing process for each pass is: temperature 165℃, speed 12m / min. (5) After melting M35 high-speed steel at 1580℃ and refining it at 1590℃, wire B obtained in step (4) is added, melted, purified by blowing argon gas, and then vacuum treated at 1580℃ for 75 minutes; after casting, forging, isothermal annealing, rolling, quenching and tempering, a micro-nano particle reinforced M35 high-speed steel with excellent wear resistance is obtained; the mass ratio of wire B to M35 is 0.25%:1; The main components of the M35 high-speed steel, by weight percentage, are: C: 0.89 wt.%; W: 5.94 wt.%; Mo: 4.98 wt.%; Cr: 3.97 wt.%; V: 1.92 wt.%; Co: 4.63 wt.%; Si: 0.32 wt.%; Mn: 0.32 wt.%; P: 0.018 wt.%; S: 0.018 wt.%; balance Fe; The casting process is carried out under an argon atmosphere, with the argon protective chamber pressure at 0.029 MPa, the molten steel temperature controlled at 1465℃, and the molten steel tapping temperature at 1545℃. The forging process is as follows: temperature is 1150℃, and forging ratio is 4:1; The isothermal annealing is described as follows: holding at 870℃ for 5 hours; The rolling process is as follows: roughing milling starts at 1189℃ and finishes at 1042℃, with 5 passes. The reduction rate for each pass is distributed in descending order: 30%, 28%, 24%, 15%, and 6%, for a total reduction rate of 69.4% and a speed of 5 m / s. Finishing milling starts at 1051℃ and finishes at 895℃, with 9 passes. The reduction rate for each pass is distributed in descending order: 25%, 24%, 22%, 20%, 17%, 15%, 11%, 8%, and 5%, for a total reduction rate of 80.5% and a speed of 16 m / s. The quenching and tempering treatment is as follows: oil quenching at 1220℃ for 9 minutes; and tempering at 570℃ three times, each time for 2 hours. The micro-nanoparticle-reinforced M35 high-speed steel 2 prepared in this embodiment contains 0.020% Nb-TiC and Nb-TiB2 nano-ceramic particles by mass, wherein the average particle size of the Nb-TiC nano-ceramic particles is 83-191 nm and the average particle size of the Nb-TiB2 nano-ceramic particles is 88-201 nm, and no electroslag remelting or pulsed current treatment process was used. Regarding wear performance, when subjected to friction tests with high-speed steel of hardness 67.9 HRC under a 40 N load, the wear surface morphologies at room temperature and 200 °C are as follows: Figure 3 As shown in (a) and (b), the wear surface has narrower furrows, less cutting marks, and less wear debris; the volumetric wear rate of the micro-nano-particle reinforced M35 high-speed steel 2 at room temperature and 200℃ is 7.1×10⁻⁶. -6 mm 3 / (N·m) and 9.1×10 -6 mm 3 / (N·m); From a microscopic perspective, the distribution of carbides in the microstructure of the M35 high-speed steel reinforced with trace nanoparticles is as follows: Figure 4 As shown, the addition of nanoparticles can refine carbides, promoting their fine, dispersed, and uniform distribution. The finely dispersed carbides can effectively inhibit crack initiation and propagation, significantly improving wear resistance. Comparative Example 1

[0021] The preparation method of electroslag remelted M35 high-speed steel 1 is as follows: M35 high-speed steel was melted at 1600℃, refined at 1580℃ with simultaneous argon blowing for purification, and then vacuum-treated at 1600℃ for 70 minutes. Following casting, electroslag remelting, forging, isothermal annealing, rolling, quenching, and tempering, electroslag remelted M35 high-speed steel 1 was obtained. The main components of the M35 high-speed steel, by weight percentage, are: C: 0.90 wt.%; W: 5.93 wt.%; Mo: 4.97 wt.%; Cr: 3.95 wt.%; V: 1.91 wt.%; Co: 4.61 wt.%; Si: 0.33 wt.%; Mn: 0.31 wt.%; P: 0.019 wt.%; S: 0.019 wt.%; with the balance being Fe. The casting process is carried out under an argon atmosphere, with the argon protective chamber pressure at 0.031 MPa, the molten steel temperature controlled at 1460℃, and the molten steel tapping temperature at 1540℃. The electroslag remelting is performed with the following parameters: current 5900A, voltage 45V, and molten pool temperature 1565℃. The forging process is as follows: temperature is 1140℃, and forging ratio is 3:1; The isothermal annealing is described as follows: holding at 860℃ for 4 hours; The rolling process is as follows: roughing milling starts at 1152℃ and finishes at 1015℃, with 7 passes. The reduction rate for each pass is distributed in descending order: 18%, 17%, 16%, 15%, 14%, 10%, and 7%, for a total reduction rate of 65% and a speed of 7 m / s. Finishing milling starts at 1032℃ and finishes at 876℃, with 8 passes. The reduction rate for each pass is distributed in descending order: 23%, 22%, 21%, 20%, 18%, 15%, 12%, and 8%, for a total reduction rate of 78.5% and a speed of 18 m / s. The quenching and tempering treatment is as follows: oil quenching at 1210℃ for 10 minutes; and tempering at 580℃ three times, each time for 2.5 hours. In terms of wear performance, Comparative Example 1, when subjected to friction tests with high-speed steel of hardness 67.8 HRC under a load of 40 N, showed volumetric wear rates of 9.3 × 10⁻⁶ at room temperature and 200 °C. -6 mm 3 / (N·m) and 11.2×10 -6 mm 3 / (N·m); its wear surface morphology at room temperature and 200℃ are as follows: Figure 5 As shown in (a) and (b), the carbide distribution structure is as follows: Figure 6 As shown, the carbides are coarse and agglomerated; the difference between Examples 1-2 of the present invention and Comparative Example 1 is that: Compared with the electroslag remelted M35 high-speed steel 1 obtained in Comparative Example 1, the trace nanoparticle-reinforced M35 high-speed steel 1 obtained in Example 1 of this invention has the same M35 high-speed steel matrix alloy composition and various preparation process parameters. The main difference is that: in terms of raw materials, the electroslag remelted M35 high-speed steel 1 prepared in Comparative Example 1 did not contain nano-ceramic particles, while Examples 1 and 2 added 0.015-0.035% of Nb-TiC and Nb-TiB2 trace nano-ceramic particles; in terms of process, Comparative Example 1 used the costly and complex electroslag remelting process in its preparation process, while Examples 1 and 2 do not require this process, which can significantly simplify the preparation process and reduce production costs; in terms of wear performance, when Example 1 was subjected to friction tests with high-speed steel with a hardness of 67.8 HRC under a load of 40 N, the volumetric wear rate at room temperature and 200 °C was 7.3 × 10⁻⁶. -6 mm 3 / (N·m) and 9.0×10 -6 mm 3 / (N·m); while in Comparative Example 1, under a load of 40N, when subjected to friction tests with high-speed steel with a hardness of 67.8HRC, the volumetric wear rates at room temperature and 200℃ were 9.3×10⁻⁶ (N·m); -6 mm 3 / (N·m) and 11.2×10 -6 mm 3 / (N·m); A comparison shows that, with the same M35 high-speed steel matrix alloy composition and all preparation process parameters, Example 1, by introducing trace amounts of Nb-TiC and Nb-TiB2 nano-ceramic particles, improved wear resistance by approximately 21.5% and 19.6% at room temperature and 200℃, respectively. Compared to Comparative Example 1, Example 2, after adjusting the content of introduced nanoparticles and all process parameters, showed improved wear resistance of approximately 23.7% and 18.8% at room temperature and 200℃ under a 40N load when subjected to friction tests with high-speed steel with a hardness of 67.9 HRC. The wear surface morphologies at room temperature and 200℃ compared to Comparative Example 1 are as follows: Figure 5 As shown in (a) and (b), compared to Comparative Example 1-2, the wear surface furrows are narrower, the cutting marks are less pronounced, and the amount of wear debris generated is significantly reduced; from a microstructure perspective, compared to Comparative Example 1, the carbide distribution structure is significantly improved. Figure 6 As shown, compared with the control example, the addition of nanoparticles in Examples 1-2 can refine the carbides, promoting their fine, dispersed, and uniform distribution, which is significantly better than the control example; the finely dispersed carbides can inhibit the initiation and propagation of cracks, and significantly improve the mechanical properties and wear resistance of the test steel. Comparative Example 2

[0022] The preparation method of pulsed current treatment for M35 high-speed steel 1 is as follows: In his 2024 Master's thesis at Jilin University, "Microstructure and Property Control of M35 High-Speed ​​Steel Based on Pulsed Current Treatment," Chen Dihui systematically studied the influence of pulsed current treatment on wear performance. M35 steel was produced from rolled and annealed bar stock. A pulsed current heat treatment process was used, employing a TL1600 tube furnace with argon protection. The temperature was increased sequentially from 50℃ to 650℃ (holding for 8 min), 850℃ (holding for 6 min), and 1050℃ (holding for 3 min) at a rate of 10℃ / min. Finally, the temperature was raised to 1195℃ and held for 5 min, followed by hot water quenching to 50℃. After quenching, the steel was tempered at 550℃ for 2 hours and then furnace-cooled to 50℃. This tempering process was repeated three times. The pulsed current process involved first applying a 5V, 480ms pulsed current to complete austenitization and quenching, followed by a 5V, 200ms pulsed tempering. This tempering process was repeated three times, with an average pulsed austenite current density of 8.8 × 10⁻⁶. 3 kA / m 2 The average current density during pulse tempering is 8.2 × 10⁻⁶. 3 kA / m 2 ; The composition of M35 high-speed steel, by mass percentage: C: 0.98 wt.%; W: 5.95 wt.%; Mo: 4.86 wt.%; Cr: 4.01 wt.%; V: 1.91 wt.%; Co: 5.1 wt.%; Si: 0.35 wt.%; Mn: 0.4 wt.%, with the remainder being Fe matrix. Comparative Example 2, under a load of 40 N, underwent friction testing with ASTM 5150 steel with a hardness of 60 HRC; the volumetric wear rates at room temperature and 200 °C were 21.5 × 10⁻⁶ and 21.5 × 10⁻⁶, respectively. -6 mm 3 / (N·m) and 24.1×10 -6 mm 3 / (N·m); The difference between Embodiments 1-2 of the present invention and Comparative Example 2 is as follows: In terms of raw materials, the pulsed current treated M35 high-speed steel 1 prepared in Comparative Example 2 did not contain any nano-ceramic particles, while Examples 1 and 2 contained 0.015-0.035% Nb-TiC and Nb-TiB2 trace nano-ceramic particles. Regarding the process, Comparative Example 2 used high-cost, high-precision pulsed current treatment equipment, resulting in high energy consumption. In contrast, Examples 1 and 2 do not require this process, significantly simplifying the preparation process and reducing production costs. In terms of wear performance, Comparative Example 2, under a 40N load, underwent friction tests with ASTM 5150 steel with a hardness of 60HRC; the volumetric wear rates at room temperature and 200℃ were 21.5 × 10⁻⁶. -6 mm 3 / (N·m) and 24.1×10 -6 mm3 / (N·m); This invention was tested under a 40N load with high-speed steel with a hardness of 67.6-68.0 HRC. Compared with the prior art, this invention uses high-speed steel with higher hardness for friction testing, and the test conditions are more stringent than the comparative example. However, under the more stringent test conditions of the comparative example, this invention achieves a lower volumetric wear rate at room temperature or high temperature. The volumetric wear rate of this invention at room temperature is only 6.9 × 10⁻⁶. -6 -7.5×10 - 6 mm 3 / (N·m), the volumetric wear rate at 200℃ is 8.8×10 -6 -9.5×10 -6 mm 3 / (N·m), since the volumetric wear rate of the present invention is lower, the wear performance of the present invention is superior to that of Comparative Example 2; compared with the pulse current treatment of M35 high-speed steel 1 in Comparative Example 2, the wear resistance of Example 1 is improved by about 66.1% and 62.7% at room temperature and 200°C, respectively; compared with the pulse current treatment of M35 high-speed steel 1 in Comparative Example 2, the wear resistance of Example 2 is improved by about 67.0% and 62.2% at room temperature and 200°C, respectively; therefore, the wear performance of the present invention is more superior.

[0023] Table 1. Comparison of room temperature volumetric wear rate values ​​of M35 high-speed steel in the comparative examples and various embodiments.

[0024] Table 2. Comparison of volumetric wear rate at 200℃ for M35 high-speed steel in the comparative examples and various embodiments.

[0025] This invention effectively refines the carbides in M35 high-speed steel, resulting in a dispersed and uniform distribution of carbides. Under a 40N load, the room temperature volumetric wear rate of the M35 high-speed steel prepared by this invention is 6.9 × 10⁻⁶. -6 -7.5×10 -6 mm 3 / (N·m), the volumetric wear rate at 200℃ is 8.8×10 -6 -9.5×10 -6 mm 3 / (N·m); Volumetric wear rate is the most crucial quantitative indicator of the wear resistance of high-speed steel; the smaller the value, the better the wear resistance. The comparative sample exhibited coarse and aggregated carbides. Under a 40N load, its volumetric wear rates at room temperature and 200℃ were 9.0×10⁻⁶. -6 -22.0×10 -6 mm 3 / (N·m) and 11.0×10 -6-24.5×10 -6 mm 3 / (N·m); As can be seen from the comparison, the sample of the present invention not only has a finer and more uniform carbide structure, but also a significantly lower volume wear rate than the comparative example, showing obvious comprehensive performance advantages.

[0026] In summary, compared to existing technologies for preparing M35 high-speed steel, this invention employs a technique involving the addition of 0.015-0.035% trace nanoparticles, replacing the high-cost and complex preparation process. By effectively controlling raw material costs and simplifying the production process, it achieves refined and uniformly dispersed carbides, significantly improving the material's wear resistance. Microstructural analysis shows that the M35 high-speed steel matrix obtained by this invention contains uniformly distributed Nb-TiC nanoceramic particles with an average particle size of 75-196 nm and Nb-TiB2 nanoceramic particles with an average particle size of 80-210 nm. Ultimately, the M35 high-speed steel prepared by this invention is less prone to wear and detachment under actual service conditions, better maintaining shape accuracy, surface quality, and integrity, significantly extending its service life, and improving forming accuracy and plasticity. Furthermore, the M35 high-speed steel obtained by this invention exhibits a more dispersed and finer uniform carbide distribution, with volumetric wear rates of 6.9 × 10⁻⁶ at room temperature and 200°C. -6 -7.5×10 -6 mm 3 / (N·m) and 8.8×10 -6 -9.5×10 -6 mm 3 / (N·m). Different embodiments of the present invention employ different component ratios and process parameters, resulting in significantly different technical effects. This indicates that the superior effects of the present invention are not determined by a single component, ratio, or process parameter, but rather depend on the interaction between alloying elements and the synergistic control of component ratios and process parameters. Only within the scope of protection of the claims of this invention can the aforementioned significant performance improvements be achieved, thereby overcoming the technical bottleneck in the prior art where wear resistance and strength / plasticity are difficult to improve simultaneously.

Claims

1. A micro-nano-particle-reinforced M35 high-speed steel with excellent wear resistance, characterized in that, Its preparation method includes the following steps: (1) Titanium aluminum alloy powder, BN powder and C powder are ball-milled at a speed of 25-55 r / min for 8-23 hours at a mass ratio of 55-85:10-20:10-20 to obtain uniform first mixed particles; pure aluminum strip is used to coat the first mixed particles, and the mass ratio of pure aluminum strip to the first mixed particles is 1.7-2.7:

1. Then, after 2-7 drawing processes, wire A is finally obtained; wherein, the particle size of titanium aluminum alloy powder is 30-80 μm, the particle size of BN powder is 50-120 μm, and the particle size range of C powder is 30-60 μm; the drawing process of each pass is: temperature of 200-250℃, speed of 10-17 m / min; (2) The wire A obtained in step (1) is heated at 730-760℃ to obtain a molten metal. The molten metal is then thoroughly mixed with pure aluminum liquid at a mass ratio of 1-10:15-60. After mixing, the mixture is mechanically stirred, ultrasonically treated, cast and rolled, and mechanically crushed in sequence to obtain a second mixed particle. The mechanical stirring is performed at a stirring speed of 300-800 rpm for 5-15 minutes. The ultrasonic treatment is performed at an ultrasonic power of 2-10 kW, a frequency of 20-30 kHz, and a treatment time of 1-5 minutes. The casting and rolling process is performed at a temperature of 300-450℃, a speed of 10-30 m / min, and a cooling water flow rate of 10-50 L / min. The mechanical crushing process is performed at a rotation speed of 2300-3800 rpm for 7-22 minutes. (3) Aluminum-niobium alloy powder and B4C powder are ball-milled at a mass ratio of 25-45:5-15 for 4-12 hours at a rotation speed of 25-55 r / min to obtain a third mixed particle; the third mixed particle is then subjected to pressing and electro-explosion reaction treatment to obtain a fourth mixed particle; wherein the particle size of aluminum-niobium alloy powder is 45-110 μm and the particle size of B4C powder is 75-120 μm; the pressing is performed at a pressure of 150-200 MPa and a pressing rate of 15-30 mm / min; the electro-explosion reaction is performed under a low-pressure protective atmosphere, with a controlled pressure of 0.04-0.07 MPa and a pulse current density of 4 × 10⁻⁶. 5 -8×10 5 A / m 2 ; (4) Mix the second mixed particles obtained in step (2) and the fourth mixed particles obtained in step (3) evenly at a mass ratio of 1-3:

1. Coat the second and fourth mixed particles with stainless steel strip. The total mass ratio of stainless steel to the second and fourth mixed particles is 1.3-2.7:

1. After 10-14 drawing processes, wire B containing stainless steel coated Nb-TiC and Nb-TiB2 nano-ceramic particles is obtained. The drawing process for each pass is: temperature 130-200℃, speed 5-15m / min. (5) After melting M35 high-speed steel at 1520-1620℃ and refining it at 1550-1610℃, wire B obtained in step (4) is added, melted, purified by blowing argon gas, and then vacuum treated at 1550-1610℃ for 50-80 minutes; after casting, forging, isothermal annealing, rolling, quenching and tempering, a micro-nano particle reinforced M35 high-speed steel with excellent wear resistance is obtained; the mass ratio of wire B to M35 is 0.1-0.35%:1; The main components of the M35 high-speed steel, by weight percentage, are: C: 0.87-0.92 wt.%; W: 5.85-6.15 wt.%; Mo: 4.58-5.25 wt.%; Cr: 3.90-4.40 wt.%; V: 1.85-2.05 wt.%; Co: 4.55-4.85 wt.%; Si: 0.28-0.43 wt.%; Mn: 0.23-0.38 wt.%; P: ≤0.022 wt.%; S: ≤0.022 wt.%; the balance is Fe; The casting process is carried out under an argon atmosphere, with the pressure of the argon protective chamber being 0.025-0.035 MPa, the temperature of the molten steel being controlled at 1430-1480℃, and the temperature of the molten steel exiting the furnace being 1500-1560℃. The forging process is carried out at a temperature of 1100-1170℃ and a forging ratio of 2-5:

1. The isothermal annealing is performed by holding the temperature at 840-880℃ for 3-6 hours. The rolling process is as follows: roughing rolling starts at 1120-1200℃ and finishes at 1000-1050℃, with 5-8 passes, each pass having a different reduction rate of 5-30%, for a total reduction rate of 55-71%, and a speed of 5-10 m / s; finishing rolling starts at 950-1060℃ and finishes at 830-910℃, with 6-9 passes, each pass having a different reduction rate of 5-25%, for a total reduction rate of 73-85%, and a speed of 12-22 m / s. The quenching and tempering treatment is as follows: holding at 1200-1230℃ for 8-15 minutes, followed by oil quenching; and tempering at 550-590℃ for 2-4 times, each time holding for 2-3 hours. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance obtained in step (5) contains 0.015-0.035% Nb-TiC and Nb-TiB2 nano-ceramic particles by mass, wherein the average particle size of Nb-TiC nano-ceramic particles is 75-196 nm and the average particle size of Nb-TiB2 nano-ceramic particles is 80-210 nm. From the perspective of microstructure, the addition of nanoparticles can refine the carbides, making the carbides present a fine, dispersed and uniform distribution. The dispersed and fine carbides can effectively inhibit crack initiation and propagation, significantly improving the mechanical properties and wear resistance of the test steel. Compared with the comparative example, the carbide grains of the present invention are finer and the distribution is more dispersed and uniform. In terms of wear performance, when subjected to friction tests with high-speed steel with a hardness ≥67.2 HRC under a load of 40 N, the volume wear rate of the micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance obtained in the present invention at room temperature and 200 °C is 6.9 × 10⁻⁶. -6 -7.5×10 -6 mm 3 / (N·m) and 8.8×10 -6 -9.5×10 -6 mm 3 / (N·m); The volumetric wear rate of high-speed steel obtained by existing technology, when subjected to friction tests with steel with a hardness ≤60HRC, is 9.0×10⁻⁶ at room temperature and 200℃. -6 -22.0×10 -6 mm 3 / (N·m) and 11.0×10 -6 -24.5×10 - 6 mm 3 / (N·m); Compared with the prior art, under the same or more stringent test conditions, the volumetric wear rate obtained by the present invention is much smaller than that of the prior art. The volumetric wear rate is the most core quantitative indicator of the wear resistance of high-speed steel, and the smaller the value, the better the wear resistance. It can be seen from the comparison that the volumetric wear rate of the present invention is significantly lower than that of the prior art. Therefore, the wear performance of the present invention is significantly higher than that of the prior art.

2. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance according to claim 1, characterized in that, In step (1), titanium-aluminum alloy powder, BN powder, and C powder are ball-milled at a speed of 30-50 r / min for 13-20 hours at a mass ratio of 60-80:13-17:13-17 to obtain uniform first mixed particles. The first mixed particles are coated with pure aluminum strip, and the mass ratio of pure aluminum strip to the first mixed particles is 1.9-2.5:

1. Then, after 3-6 drawing processes, wire A is finally obtained. The particle size of titanium-aluminum alloy powder is 40-70 μm, the particle size of BN powder is 70-100 μm, and the particle size range of C powder is 40-50 μm. The drawing process for each pass is: temperature 220-240℃, speed 12-15 m / min.

3. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance according to claim 1, characterized in that, Step (2) involves heating the wire A obtained in step (1) at 740-750℃ to obtain a molten metal. The molten metal is then thoroughly mixed with pure aluminum liquid at a mass ratio of 3-7:25-45. After mixing, the mixture is subjected to mechanical stirring, ultrasonic treatment, casting and rolling, and mechanical crushing in sequence to obtain a second mixed particle. The mechanical stirring is performed at a stirring speed of 450-650 rpm for 7-13 minutes. The ultrasonic treatment is performed at an ultrasonic power of 4-8 kW, a frequency of 22-27 kHz, and a treatment time of 2-4 minutes. The casting and rolling process is performed at a temperature of 320-410℃, a speed of 15-25 m / min, and a cooling water flow rate of 20-40 L / min. The mechanical crushing process is performed at a rotation speed of 2500-3500 rpm for 10-20 minutes.

4. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance according to claim 1, characterized in that, In step (3), aluminum-niobium alloy powder and B4C powder are ball-milled at a mass ratio of 30-40:7-13 for 6-10 hours at a speed of 30-50 r / min to obtain third mixed particles. The third mixed particles are then subjected to pressing and electro-explosion reaction treatment to obtain fourth mixed particles. The particle size of the aluminum-niobium alloy powder is 60-90 μm, and the particle size of the B4C powder is 85-110 μm. The pressing is performed at a pressure of 160-190 MPa and a pressing rate of 17-27 mm / min. The electro-explosion reaction is performed under a low-pressure protective atmosphere, with a controlled pressure of 0.05-0.06 MPa and a pulse current density of 5 × 10⁻⁶ MPa. 5 -7×10 5 A / m 2 .

5. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance according to claim 1, characterized in that, In step (4), the second mixed particles obtained in step (2) and the fourth mixed particles obtained in step (3) are mixed evenly at a mass ratio of 1.5-2.7:

1. The second and fourth mixed particles are coated with stainless steel strip. The total mass ratio of stainless steel to the second and fourth mixed particles is 1.5-2.5:

1. After 11-13 drawing processes, wire B containing stainless steel coated Nb-TiC and Nb-TiB2 nano-ceramic particles is obtained. The drawing process for each pass is: temperature 150-180℃, speed 7-13m / min.

6. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance according to claim 1, characterized in that, The main components of the M35 high-speed steel mentioned in step (5) by mass percentage are: C: 0.88-0.90 wt.%; W: 5.90-6.10 wt.%; Mo: 4.65-5.20 wt.%; Cr: 3.95-4.35 wt.%; V: 1.87-2.02 wt.%; Co: 4.60-4.80 wt.%; Si: 0.30-0.40 wt.%; Mn: 0.25-0.35 wt.%; P: ≤0.020 wt.%; S: ≤0.020 wt.%; the balance is Fe.

7. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance according to claim 1, characterized in that, The casting process is carried out under an argon atmosphere, with the pressure in the argon protective chamber being 0.026-0.033 MPa, the temperature of the molten steel being controlled at 1440-1470℃, and the temperature of the molten steel exiting the furnace being 1510-1550℃. Forging is carried out at a temperature of 1130-1150℃ with a forging ratio of 2-4:

1. The isothermal annealing is performed by holding the temperature at 850-870℃ for 3-5 hours. The rolling process is as follows: roughing rolling starts at 1130-1190℃ and finishes at 1010-1040℃, with 6-7 passes, each pass having a different reduction rate of 7-28%, a total reduction rate of 57-68%, and a speed of 6-9 m / s; finishing rolling starts at 960-1050℃ and finishes at 840-900℃, with 7-8 passes, each pass having a different reduction rate of 7-23%, a total reduction rate of 74-83%, and a speed of 14-20 m / s. The quenching and tempering treatment is as follows: hold at 1205-1220℃ for 9-14 minutes, then oil quench; and perform 3-4 tempering treatments at 555-585℃, holding for 2.5-3 hours each time.

8. The micro-nanoparticle-reinforced M35 high-speed steel with excellent wear resistance according to claim 1, characterized in that, The micro-nanoparticle reinforced M35 high-speed steel with excellent wear resistance has a volumetric wear rate of 7.0 × 10⁻⁶ at room temperature and 200°C. -6 -7.4×10 -6 mm 3 / (N·m) and 8.9×10 -6 -9.4×10 -6 mm 3 / (N·m).

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