Low-cost short-process high-impact and wear-resistant high-speed steel and preparation method

Abstract

The application provides a low-cost short-process high-impact-resistance wear-resistant high-speed steel and a preparation method thereof; the preparation method comprises the following steps: mixing iron-vanadium powder, boron powder and iron powder, wrapping and compacting the iron foil 1, performing electric explosion reaction 1 to obtain alloy 1, mixing titanium dioxide powder, boron carbide powder and aluminum powder, wrapping and compacting the aluminum foil, performing electric explosion reaction 2 to obtain alloy 2; then crushing and mixing the alloys 1 and 2, treating by high-frequency induction plasma method, wrapping with iron foil 2 to obtain a wire containing vanadium boride, titanium carbide and titanium diboride nanoparticles; mixing and melting the wire with high-speed steel refining melt, refining, casting, forging, annealing, rolling, quenching and tempering to obtain the low-cost short-process high-impact-resistance wear-resistant high-speed steel, the impact toughness and wear resistance are simultaneously improved, the unnotched impact toughness is greater than or equal to 25 J / cm 2 , and the volume wear rate is less than or equal to 9.2*10 ‑6 mm 3 / (N*m).

Description

Technical Field

[0001] This invention relates to the field of high-speed steel, specifically to low-cost, short-process, high-impact, and wear-resistant high-speed steel and its preparation method. Background Technology

[0002] High-speed steel is the core material for high-end cutting tools and molds. As the "teeth" of machining, it ensures precision machining and efficient production in industries such as automotive, aerospace, rail transportation, precision molds, and military. Industrial machining requires high-speed steel to have higher impact toughness and wear resistance. However, current technologies show that improving the impact toughness of high-speed steel will reduce its wear resistance, and vice versa. Therefore, in the context of green and low-cost manufacturing, achieving both high impact toughness and high wear resistance of high-speed steel under short-process and low-cost conditions is of great significance.

[0003] The wear resistance of high-speed steel mainly depends on the content and distribution of hard carbides (such as WC, MoC, VC, Cr7C3, etc.) in its microstructure. Typically, increasing the content of carbon and alloying elements such as W, Mo, and V generates sufficient hard carbides, improving the matrix hardness and wear resistance. However, excessive carbon and alloying elements can lead to coarse, network-like, intergranular continuous precipitation of carbides, forming a brittle phase. This also increases the risk of inclusions, porosity, and carbide segregation within the material, significantly reducing the toughness of the high-speed steel. This reduces its impact resistance, making it prone to chipping and unable to withstand complex conditions such as intermittent cutting and impact loads. Conversely, reducing the carbon and alloying element content, while refining grains and purifying grain boundaries to reduce brittleness and improve impact toughness, results in insufficient hard carbide content and decreased matrix hardness. This significantly reduces the wear resistance of the high-speed steel, making it susceptible to abrasive wear and adhesive wear, shortening the product's service life. Furthermore, while surface strengthening technologies (such as PVD / CVD coatings and nitriding) can improve surface wear resistance, if the coating and substrate have poor adhesion or the substrate itself lacks toughness, problems such as coating peeling and substrate cracking can easily occur under impact loads, failing to fundamentally solve the pain point of the difficulty in simultaneously improving both wear resistance and toughness. From the perspective of manufacturing processes, traditional casting and forging processes are prone to producing coarse eutectic carbide segregation, resulting in uneven microstructure. Even with processes such as vacuum smelting and electroslag remelting, it is difficult to completely eliminate carbide segregation, making it impossible to simultaneously improve wear resistance and toughness.

[0004] In summary, current technologies cannot simultaneously achieve a balance between high impact resistance, high wear resistance, and low-cost, short-process manufacturing of high-speed steel. Relying on composition design, surface strengthening treatment, and complex preparation processes can only optimize one specific property, failing to solve the challenge of simultaneously improving high impact resistance and high wear resistance. Moreover, the addition of precious metals and complex preparation processes such as electroslag remelting increase carbon emissions and manufacturing costs. Therefore, how to reduce or avoid the addition of precious metals, simplify processes, achieve short-process manufacturing, and simultaneously improve the high impact resistance and high wear resistance of high-speed steel, as well as achieve stable industrial production, are urgent technical challenges that need to be addressed. Summary of the Invention

[0005] To address the aforementioned technical challenges, this invention provides a low-cost, short-process, high-impact, wear-resistant high-speed steel, the preparation method of which includes the following steps: (1) At room temperature, iron vanadium powder, boron powder and iron powder are mixed at a mass ratio of 10-35:5-15:50-85 at a speed of 80-180 r / min for 10-25 hours to obtain powder mixture 1; titanium dioxide, boron carbide powder and aluminum powder are mixed at a mass ratio of 12-30:6-16:54-82 at a speed of 60-120 r / min for 5-16 hours to obtain powder mixture 2. The iron-vanadium powder, by mass percentage, consists of 75 wt% vanadium and 25 wt% iron, with a particle size of 10-260 micrometers. The particle sizes of the boron powder, iron powder, titanium dioxide powder, boron carbide powder, and aluminum powder are 15-95 micrometers, 16-96 micrometers, 20-120 micrometers, 25-220 micrometers, and 50-300 micrometers, respectively. (2) After wrapping the powder mixture 1 obtained in step (1) with iron foil 1, it is compacted 1 and then subjected to an electro-explosion reaction 1 to obtain an alloy 1 containing micron-sized ceramic particles; after wrapping the powder mixture 2 obtained in step (1) with aluminum foil, it is compacted 2 and then subjected to an electro-explosion reaction 2 to obtain an alloy 2 containing micron-sized ceramic particles. The compaction treatment 1 described above: pressure 311-817 MPa, holding time 7-17 min; The aforementioned electro-explosion reaction treatment 1: under argon protection, pressure 0.015-0.065 MPa, current density 2.7×10⁻⁶ MPa. 5 Up to 8.5×10 6 A / mm 2 Voltage 11-31kV; The mass ratio of the iron foil 1 to the mixture 1 is 0.008-0.018:1; The compaction treatment 2 described above: pressure 328-835 MPa, holding time 4-16 min; The aforementioned electro-explosion reaction treatment 2: under argon protection, pressure 0.03-0.08 MPa, current density 2.6×10⁻⁶ MPa. 5 Up to 8.1×10 6 A / mm 2 Voltage 17-36kV; The mass ratio of the aluminum foil to mixture 2 is 0.006-0.016:1; (3) Alloy 1 and Alloy 2 obtained in step (2) are crushed and then mixed at a speed of 30-80 r / min for 0.2-4.5 hours according to a mass ratio of 2-5:1-6 to obtain mixture 3; mixture 3 is treated by high frequency induction plasma method to obtain powder containing nano-ceramic particles; powder containing nano-ceramic particles is wrapped with iron foil 2 to obtain wire containing nano-ceramic particles. The wire containing nano-ceramic particles contains nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles, with the mass percentage of the above three types of particles being 6-50%. The high-frequency induction plasma method is carried out under argon protection, with a pressure of 0.01-0.15 MPa, a temperature of 2000-5000℃, a power supply operating frequency of 1-15 MHz, and an output power of 20-100 kW. The particle sizes of the nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles range from 100-800 nanometers, 50-550 nanometers, and 75-650 nanometers, respectively. The mass ratio of the iron foil 2 to the powder containing nano-ceramic particles is 0.002-0.016:1; (4) Under argon protection, the high-speed steel is melted at 1420-1950℃ and held for 35-115 minutes, refined, and then the wire obtained in step (3) is added for melting, refined under vacuum, cast at room temperature, forged, isothermal annealed, rolled, quenched and tempered to obtain low-cost short-process high impact-resistant and wear-resistant high-speed steel. The refining process involves: a temperature of 1480-1700℃, a refining time of 10-100 minutes, and stirring with argon gas at a flow rate of 0.2-0.6 m³ / min. 3 / h; The mass ratio of the wire obtained in step (3) to the high-speed steel is 0.006-0.35%:1; The forging process is described as follows: the forging temperature is 1050-1200℃, and the forging ratio is 2-5:1. The isothermal annealing process involves holding the temperature at 815-885℃ for 1-6 hours. The rolling process is as follows: roughing rolling starts at 1059-1189℃ and finishes at 915-1015℃, with 5-13 passes, each pass having a different reduction rate of 3-31%, for a total reduction rate of 55-78%, and a speed of 3-8 m / s; finishing rolling starts at 882-959℃ and finishes at 815-881℃, with 6-12 passes, each pass having a different reduction rate of 3.5-30%, for a total reduction rate of 78-93%, and a speed of 15-29 m / s. The quenching treatment is described as follows: oil quenching at 1160-1250℃; The tempering treatment described herein consists of 1-4 tempering treatments, each of which involves holding at 545-615℃ for 40-200 minutes. The high-speed steel described herein, by mass percentage, has the following composition: C: 0.80-0.95; W: 5.50-7.00; Mo: 4.60-5.50; Cr: 3.50-4.50; V: 1.70-2.25; Co: 4.50-5.50; Si: 0.20-0.45; Mn: 0.15-0.40; P: ≤0.030; S: ≤0.030, with the balance being Fe; Compared with existing high-speed steels that undergo electroslag remelting and alloying with high amounts of precious metals, this invention provides a low-cost, short-process, high-impact, and wear-resistant high-speed steel with the following advantages: First, it eliminates the need for electroslag remelting; second, it only adds ≤0.35 wt% of wire containing nano-ceramic particles, which does not contain precious metal elements, significantly reducing raw material production costs and improving the uniformity of the high-speed steel's microstructure. Therefore, under the same testing conditions as existing technologies, it exhibits better stability in impact toughness and wear resistance, simultaneously improving both. Specifically, the unnotched impact toughness is ≥25 J / cm. 2 Compared with existing technologies, it improves wear rate by ≥40%; it achieves significant reduction in wear rate under both room temperature and high temperature conditions, with volumetric wear rate ≤9.2×10⁻⁶. -6 mm 3 / (N·m), compared with the prior art, the volumetric wear rate is reduced by ≥15%; among which, under a rotation speed of 900 r / min for 300 min and a load of 30-50 N, the volumetric wear rate at room temperature, 200℃ and 400℃ is ≤7.6×10. -6 mm 3 / (N·m), ≤9.2×10 -6 mm 3 / (N·m), ≤6.5×10 -6 mm 3 / (N·m). Meanwhile, the surface roughness and height difference between peaks and valleys of the wear surface obtained under both room temperature and high temperature conditions are far less than the relevant values ​​obtained by existing technologies. The lower these values, the better the wear resistance. In summary, the low-cost, short-process, high-impact, and wear-resistant high-speed steel obtained by this invention exhibits excellent wear resistance.

[0006] Further, in step (1): at room temperature, iron vanadium powder, boron powder and iron powder are mixed at a mass ratio of 11-34:6-14:52-83 at a speed of 95-165 r / min for 11-23 hours to obtain powder mixture 1; and titanium dioxide, boron carbide powder and aluminum powder are mixed at a mass ratio of 13-29:7-15:56-80 at a speed of 82-111 r / min for 6.5-14.5 hours to obtain powder mixture 2. The iron-vanadium powder, by mass percentage, consists of 75 wt% vanadium and 25 wt% iron, with a particle size of 25-245 micrometers; The particle sizes of the boron powder, iron powder, titanium dioxide powder, boron carbide powder, and aluminum powder are 25-85 micrometers, 26-86 micrometers, 30-110 micrometers, 35-210 micrometers, and 60-290 micrometers, respectively.

[0007] Furthermore, the compaction treatment 1 described in step (2) has a pressure of 315-813 MPa and a holding time of 8-16 min. The aforementioned electro-explosion reaction treatment 1 is as follows: under argon protection, pressure 0.017-0.062 MPa, current density 3.1×10⁻⁶ MPa. 5 Up to 8.1×10 6 A / mm², voltage 12-30kV; The mass ratio of the iron foil 1 to the mixture 1 is 0.011-0.017:1; The compaction treatment 2 described above: pressure 331-830 MPa, holding time 5-15 min; The aforementioned electro-explosion reaction treatment 2 is performed under argon protection at a pressure of 0.032-0.078 MPa and a current density of 2.7 × 10⁻⁶ MPa. 5 Up to 7.9×10 6 A / mm², voltage 18-35kV; The mass ratio of the aluminum foil to mixture 2 is 0.009-0.015:1.

[0008] Further, in step (3), alloy 1 and alloy 2 are crushed and then mixed at a speed of 45-65 r / min for 0.5-4.2 hours to obtain mixture 3 according to a mass ratio of 3-4:2-5; mixture 3 is treated with high frequency induction plasma method to obtain powder containing nano-ceramic particles; the powder containing nano-ceramic particles is wrapped with iron foil 2 to obtain wire containing nano-ceramic particles. The wire containing nano-ceramic particles contains nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles, with the mass percentage of the above three particles being 9-46%. The high-frequency induction plasma method is carried out under argon protection, with a pressure of 0.02-0.12 MPa, a temperature of 2500-4500℃, a power supply operating frequency of 2-13 MHz, and an output power of 25-85 kW. The particle sizes of the nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles range from 120-780 nanometers, 65-500 nanometers, and 85-600 nanometers, respectively. The mass ratio of the iron foil 2 to the powder containing nano-ceramic particles is 0.0025-0.013:1.

[0009] Further, in step (4), the high-speed steel is melted at 1430-1930℃ under argon protection, held for 40-110 minutes, refined, and then the wire obtained in step (3) is added for melting, refined under vacuum, cast at room temperature, forged, isothermal annealed, rolled, quenched and tempered to obtain low-cost, short-process, high-impact, wear-resistant high-speed steel.

[0010] Furthermore, the refining process described in step (4) involves: a temperature of 1500-1680℃, a refining time of 20-90 minutes, stirring with argon gas, and an argon gas flow rate of 0.3-0.5 m³ / min. 3 / h; The mass ratio of the wire to high-speed steel is 0.008-0.3%:1.

[0011] Furthermore, the forging in step (4) involves a forging temperature of 1090-1160℃ and a forging ratio of 2.2-4.2:1. The isothermal annealing process involves holding the temperature at 820-875℃ for 2-5 hours. The rolling process is as follows: roughing rolling starts at 1065-1182℃ and finishes at 919-1009℃, with 6-11 passes, each pass having a different reduction rate of 3.5-30%, for a total reduction rate of 60-73%, and a speed of 4-7 m / s; finishing rolling starts at 886-955℃ and finishes at 819-876℃, with 7-11 passes, each pass having a different reduction rate of 4-28%, for a total reduction rate of 80-91%, and a speed of 17-27 m / s. The quenching treatment is described as follows: oil quenching at 1180-1240℃; The tempering process involves 2-3 tempering cycles, with each tempering cycle consisting of holding at 555-605℃ for 45-185 minutes.

[0012] Furthermore, the low-cost, short-process, high-impact, and wear-resistant high-speed steel described in step (4) has the following advantages: firstly, it does not require electroslag remelting; secondly, it only requires the addition of ≤0.30 wt% of wire containing nano-ceramic particles, which does not contain precious metal elements, significantly reducing raw material production costs and improving the uniformity of the high-speed steel structure. Therefore, under the same testing conditions as existing technologies, it exhibits better stability in impact toughness and wear resistance, simultaneously improving both. Specifically, the unnotched impact toughness is 25.5-29.5 J / cm. 2 Compared with existing technologies, it improves efficiency by 40.8-55%; it achieves significant reductions in wear rate under both room temperature and high temperature conditions, with a volumetric wear rate of 4.5×10⁻⁶. -6 -9.1×10 -6 mm 3 / (N·m), the volumetric wear rate is reduced by 16.5%-42% compared with existing technologies. Attached Figure Description

[0013] Figure 1 (a) and (b) are impact fracture diagrams of the low-cost, short-process, high-impact, and wear-resistant high-speed steel 1 prepared in Example 1 of the present invention and the high-speed steel 5 prepared in Comparative Example 2, respectively.

[0014] Figure 2 a and 2b are white light interference diagrams of the room temperature wear surfaces of the low-cost, short-process, high-impact, and wear-resistant high-speed steel 2 prepared in Example 2 of the present invention and the high-speed steel prepared in Comparative Example 3, respectively.

[0015] Figure 3 a and 3b are white light interference diagrams of the 200℃ wear surfaces of the low-cost, short-process, high-impact, and wear-resistant high-speed steel 2 prepared in Example 2 of the present invention and the high-speed steel prepared in Comparative Example 3, respectively. Detailed Implementation

[0016] 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

[0017] The preparation method of low-cost, short-process, high-impact, and wear-resistant high-speed steel 1 includes the following steps: (1) At room temperature, iron vanadium powder, boron powder and iron powder are mixed at a mass ratio of 11:6:83 at a speed of 85 r / min for 23 hours to obtain powder mixture 1; titanium dioxide, boron carbide powder and aluminum powder are mixed at a mass ratio of 29:15:56 at a speed of 110 r / min for 6 hours to obtain powder mixture 2. The iron-vanadium powder, by mass percentage, consists of 75 wt% vanadium and 25 wt% iron, with a particle size of 35 micrometers. The particle sizes of the boron powder, iron powder, titanium dioxide powder, boron carbide powder, and aluminum powder are 25 micrometers, 29 micrometers, 110 micrometers, 195 micrometers, and 275 micrometers, respectively. (2) After wrapping the powder mixture 1 obtained in step (1) with iron foil 1, it is compacted 1 and then subjected to an electro-explosion reaction 1 to obtain an alloy 1 containing micron-sized ceramic particles; after wrapping the powder mixture 2 obtained in step (1) with aluminum foil, it is compacted 2 and then subjected to an electro-explosion reaction 2 to obtain an alloy 2 containing micron-sized ceramic particles. The compaction treatment 1 described above: pressure 320 MPa, holding time 15 min; The aforementioned electro-explosion reaction treatment 1: under argon protection, pressure 0.016 MPa, current density 8.3 × 10⁻⁶ MPa. 6 A / mm², voltage 30kV; The mass ratio of the iron foil 1 to the mixture 1 is 0.009:1; The compaction treatment 2 described above: pressure 330 MPa, holding time 14 min; The aforementioned electro-explosion reaction treatment 2: under argon protection, pressure 0.04 MPa, current density 2.7 × 10⁻⁶. 5 A / mm², voltage 18kV; The mass ratio of the aluminum foil to mixture 2 is 0.007:1; (3) Alloy 1 and Alloy 2 obtained in step (2) are crushed and then mixed at a speed of 35 r / min for 4.3 hours according to a mass ratio of 2:5 to obtain mixture 3; mixture 3 is treated by high frequency induction plasma method to obtain powder containing nano-ceramic particles; the powder containing nano-ceramic particles is wrapped with iron foil 2 to obtain wire containing nano-ceramic particles. The wire containing nano-ceramic particles contains nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles, with the mass percentage of the above three types of particles being 28%. The high-frequency induction plasma method is carried out under argon protection at a pressure of 0.04 MPa, a temperature of 3000℃, a power supply operating frequency of 4 MHz, and an output power of 70 kW. The particle sizes of the nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles range from 100-350 nanometers, 150-450 nanometers, and 205-550 nanometers, respectively. The mass ratio of the iron foil 2 to the powder containing nano-ceramic particles is 0.003:1; (4) Under argon protection, the high-speed steel is melted at 1620℃ and held for 100 min, refined, and then the wire obtained in step (3) is added for melting, refined under vacuum, cast at room temperature, forged, isothermal annealed, rolled, quenched and tempered to obtain low-cost short-process high impact and wear-resistant high-speed steel. The refining process was conducted at a temperature of 1520℃ for 80 minutes, with argon gas stirring at a flow rate of 0.3 m³ / min. 3 / h; The mass ratio of the wire obtained in step (3) to the high-speed steel is 0.05%:1; The forging process is described as follows: the forging temperature is 1090℃, and the forging ratio is 2:1. The isothermal annealing process involves holding the temperature at 825℃ for 5 hours. The rolling process is as follows: roughing mill: starting temperature 1065℃, finishing temperature 920℃, 12 passes, each pass has a different reduction rate of 5-15%, total reduction rate 75%, speed 4m / s; finishing mill: starting temperature 890℃, finishing temperature 820℃, 11 passes, each pass has a different reduction rate of 4-18%, total reduction rate 90%, speed 16m / s; The quenching treatment described above: oil quenching at 1190℃; The tempering process consists of three tempering processes: holding at 580℃ for 50 min, holding at 570℃ for 60 min, and holding at 560℃ for 70 min in sequence. The high-speed steel 1 described herein has the following composition by mass percentage: C: 0.81; W: 5.52; Mo: 4.61; Cr: 3.51; V: 1.72; Co: 4.53; Si: 0.25; Mn: 0.17; P: 0.020; S: 0.010, with the balance being Fe; Compared with existing high-speed steels that undergo electroslag remelting and alloying with high amounts of precious metals, this invention yields a low-cost, short-process, high-impact, and wear-resistant high-speed steel1. Firstly, it eliminates the need for electroslag remelting; secondly, it only incorporates 0.05 wt% of wire containing nano-ceramic particles, which does not contain precious metal elements, significantly reducing raw material production costs and improving the uniformity of the high-speed steel's microstructure. Therefore, under the same testing conditions as existing technologies, it exhibits better stability in impact toughness and wear resistance, simultaneously improving both. Specifically, the unnotched impact toughness is 25.9 J / cm2. 2 Compared with existing technologies, it improves efficiency by 42%, and achieves low cost, short process, high impact resistance, and wear resistance in high-speed steel 1, as shown in the impact fracture surface. Figure 1 As shown in (a), significant toughness characteristics are visible, with no obvious cracks or breakage on the surface; under a rotational speed of 900 r / min for 300 min and a load of 30 N, the volumetric wear rates at room temperature, 200℃, and 400℃ are 7.4 × 10⁻⁶. -6 mm 3 / (N·m), 9.1×10 -6 mm 3 / (N·m) and 6.3×10 -6 mm 3 / (N·m), compared with the prior art, the volumetric wear rate was reduced by 24.5%, 16.5% and 20.0% respectively, and the wear surface roughness ( R a) The values ​​are 0.094, 0.119, and 0.189, respectively, indicating that the wear surface roughness is low. R a) The smaller the value, the better the wear resistance of the material. Example 2

[0018] Low-cost, short-process, high-impact, wear-resistant high-speed steel 2, characterized in that its preparation method includes the following steps: (1) At room temperature, iron vanadium powder, boron powder and iron powder are mixed at a mass ratio of 34:14:52 at a speed of 175 r / min for 12 hours to obtain powder mixture 1; titanium dioxide, boron carbide powder and aluminum powder are mixed at a mass ratio of 13:7:80 at a speed of 70 r / min for 15 hours to obtain powder mixture 2. The iron-vanadium powder, by mass percentage, consists of 75 wt% vanadium and 25 wt% iron, with a particle size of 220 micrometers. The particle sizes of the boron powder, iron powder, titanium dioxide powder, boron carbide powder, and aluminum powder are 89 micrometers, 92 micrometers, 35 micrometers, 45 micrometers, and 75 micrometers, respectively. (2) After wrapping the powder mixture 1 obtained in step (1) with iron foil 1, it is compacted 1 and then subjected to an electro-explosion reaction 1 to obtain an alloy 1 containing micron-sized ceramic particles; after wrapping the powder mixture 2 obtained in step (1) with aluminum foil, it is compacted 2 and then subjected to an electro-explosion reaction 2 to obtain an alloy 2 containing micron-sized ceramic particles. The compaction treatment 1 described above: pressure 810 MPa, holding time 8 min; The aforementioned electro-explosion reaction treatment 1: under argon protection, at a pressure of 0.06 MPa and a current density of 2.9 × 10⁻⁶ MPa. 5 A / mm², voltage 12kV; The mass ratio of the iron foil 1 to the mixture 1 is 0.017:1; The compaction treatment 2 described above: pressure 830 MPa, holding time 5 min; The aforementioned electro-explosion reaction treatment 2: under argon protection, pressure 0.07 MPa, current density 8.0 × 10⁻⁶. 5 A / mm², voltage 35 kV; The mass ratio of the aluminum foil to mixture 2 is 0.015:1; (3) Alloy 1 and Alloy 2 obtained in step (2) are crushed and mixed at a speed of 75 r / min for 0.5 hours according to a mass ratio of 5:2 to obtain mixture 3; mixture 3 is treated by high frequency induction plasma method to obtain powder containing nano-ceramic particles; powder containing nano-ceramic particles is wrapped with iron foil 2 to obtain wire containing nano-ceramic particles. The wire containing nano-ceramic particles contains nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles, with the above three types of particles accounting for 34% by mass. The high-frequency induction plasma treatment is carried out under argon protection at a pressure of 0.05 MPa, a temperature of 3200℃, a power supply operating frequency of 5 MHz, and an output power of 65 kW. The particle sizes of the nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles range from 260-580 nanometers, 60-260 nanometers, and 80-350 nanometers, respectively. The mass ratio of the iron foil 2 to the powder containing nano-ceramic particles is 0.015:1; (4) Under argon protection, the high-speed steel is melted at 1790℃ and held for 45 min, refined, and then the wire obtained in step (3) is added to melt, refined under vacuum, cast at room temperature, forged, isothermal annealed, rolled, quenched and tempered to obtain low-cost short-process high impact and wear-resistant high-speed steel. The refining process was carried out at a temperature of 1650℃ for 30 minutes, with argon gas blowing and stirring at a flow rate of 0.5 m³ / min. 3 / h; The mass ratio of the wire obtained in step (3) to the high-speed steel is 0.25%:1; The forging process is described as follows: the forging temperature is 1160℃, and the forging ratio is 4:1. The isothermal annealing process involves holding the temperature at 865℃ for 2 hours. The rolling process is as follows: roughing mill: starting temperature 1085℃, finishing temperature 1010℃, 6 passes, each pass has a different reduction rate, each pass has a reduction rate of 6-16%, the total reduction rate is 70%, and the speed is 7m / s; finishing mill: starting temperature 945℃, finishing temperature 875℃, 7 passes, each pass has a different reduction rate, each pass has a reduction rate of 5-15%, the total reduction rate is 88%, and the speed is 25m / s. The quenching treatment described above involves oil quenching at 1220℃. The tempering process consists of three tempering processes: holding at 590℃ for 55 min, holding at 580℃ for 62 min, and holding at 570℃ for 68 min in sequence. The high-speed steel described herein, by mass percentage, has the following composition: C: 0.85; W: 5.73; Mo: 4.72; Cr: 3.62; V: 1.81; Co: 4.62; Si: 0.23; Mn: 0.16; P: 0.010; S: 0.015, with the balance being Fe; Compared with existing high-speed steels that undergo electroslag remelting and alloying with high amounts of precious metals, this invention yields a low-cost, short-process, high-impact, and wear-resistant high-speed steel 2. Firstly, it eliminates the need for electroslag remelting; secondly, it only incorporates 0.25 wt% of wire containing nano-ceramic particles, which does not contain precious metal elements, significantly reducing raw material production costs and improving the uniformity of the high-speed steel's microstructure. Therefore, under the same testing conditions as existing technologies, it exhibits better stability in impact toughness and wear resistance, simultaneously improving both. Specifically, the unnotched impact toughness is 25.6 J / cm². 2 Compared with existing technologies, this represents a 40.8% improvement; under a rotational speed of 900 r / min for 300 min and a load of 40 N, the volumetric wear rates at room temperature, 200℃, and 400℃ are 7.3 × 10⁻⁶. -6 mm 3 / (N·m), 9.0×10 -6mm 3 / (N·m) and 6.1×10 -6 mm 3 / (N·m), compared with the prior art, the volumetric wear rate was reduced by 20.3%, 19.6% and 29.0% respectively, and the wear surface roughness ( R a) The values ​​are 0.116, 0.119, and 0.199, respectively, indicating a low surface roughness. This demonstrates the white light interference on the worn surface of low-cost, short-process, high-impact, wear-resistant high-speed steel 2 at room temperature and 200℃. Figure 2 As shown in (a) and 3(a), the height differences between peaks and valleys are 857.02 nm and 1032.7 nm, respectively. The height difference between peaks and valleys on the 400℃ wear surface is 3600.4 nm. The surface roughness of the wear surface is ( R a) The smaller the numerical value and the height difference between the peaks and valleys of the wear surface, the better the wear resistance of the material. Example 3

[0019] Low-cost, short-process, high-impact, wear-resistant high-speed steel 3 is characterized by its preparation method comprising the following steps: (1) At room temperature, iron vanadium powder, boron powder and iron powder are mixed at a mass ratio of 22:10:68 at a speed of 130 r / min for 17 hours to obtain powder mixture 1; titanium dioxide, boron carbide powder and aluminum powder are mixed at a mass ratio of 21:11:68 at a speed of 90 r / min for 11 hours to obtain powder mixture 2. The iron-vanadium powder, by mass percentage, consists of 75 wt% vanadium and 25 wt% iron, with a particle size of 110 micrometers. The particle sizes of the boron powder, iron powder, titanium dioxide powder, boron carbide powder, and aluminum powder are 55 micrometers, 58 micrometers, 70 micrometers, 125 micrometers, and 175 micrometers, respectively. (2) After wrapping the powder mixture 1 obtained in step (1) with iron foil 1, it is compacted 1 and then subjected to an electro-explosion reaction 1 to obtain an alloy 1 containing micron-sized ceramic particles; after wrapping the powder mixture 2 obtained in step (1) with aluminum foil, it is compacted 2 and then subjected to an electro-explosion reaction 2 to obtain an alloy 2 containing micron-sized ceramic particles. The compaction treatment 1 described above: pressure 513 MPa, holding time 12 min; The aforementioned electro-explosion reaction treatment 1: under argon protection, pressure 0.04 MPa, current density 4.2 × 10⁻⁶. 6 A / mm², voltage 21kV; The mass ratio of the iron foil 1 to the mixture 1 is 0.013:1; The compaction treatment 2 described above: pressure 578 MPa, holding time 10 min; The aforementioned electro-explosion reaction treatment 2: under argon protection, pressure 0.055 MPa, current density 4.1 × 10⁻⁶. 6 A / mm², voltage 26kV; The mass ratio of the aluminum foil to mixture 2 is 0.011:1; (3) Alloy 1 and Alloy 2 obtained in step (2) are crushed and then mixed at a speed of 55 r / min for 2.3 hours according to a mass ratio of 3:4 to obtain mixture 3; mixture 3 is treated by high frequency induction plasma method to obtain powder containing nano-ceramic particles; powder containing nano-ceramic particles is wrapped with iron foil 2 to obtain wire containing nano-ceramic particles. The wire containing nano-ceramic particles contains nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles, with the mass percentage of the above three types of particles being 30%. The high-frequency induction plasma treatment is carried out under argon protection at a pressure of 0.07 MPa, a temperature of 3400℃, a power supply operating frequency of 8 MHz, and an output power of 55 kW. The particle sizes of the nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles range from 130-410 nm, 88-350 nm, and 95-430 nm, respectively. The mass ratio of the iron foil 2 to the powder containing nano-ceramic particles is 0.009:1; (4) Under argon protection, the high-speed steel is melted at 1685℃ and held for 75 min, refined, and then the wire obtained in step (3) is added to melt, refined under vacuum, cast at room temperature, forged, isothermal annealed, rolled, quenched and tempered to obtain low-cost short-process high impact and wear-resistant high-speed steel. The refining process was conducted at a temperature of 1590℃ for 55 minutes, with argon gas stirring at a flow rate of 0.4 m³ / min. 3 / h; The mass ratio of the wire obtained in step (3) to the high-speed steel is 0.1%:1; The forging process is described as follows: forging temperature is 1125℃, and forging ratio is 3:1. The isothermal annealing process involves holding the temperature at 850℃ for 3.5 hours. The rolling process is as follows: roughing mill: starting temperature 1150℃, finishing temperature 990℃, 7 passes, each pass has a different reduction rate, each pass has a reduction rate of 6-13%, the total reduction rate is 65%, and the speed is 5m / s; finishing mill: starting temperature 925℃, finishing temperature 845℃, 9 passes, each pass has a different reduction rate, each pass has a reduction rate of 5-17%, the total reduction rate is 82%, and the speed is 21m / s. The quenching treatment described above involves oil quenching at 1200℃. The tempering process consists of three tempering processes: holding at 585℃ for 60 minutes, holding at 575℃ for 65 minutes, and holding at 565℃ for 70 minutes in sequence. The high-speed steel described herein, by mass percentage, has the following composition: C: 0.89; W: 5.79; Mo: 4.81; Cr: 3.58; V: 1.78; Co: 4.59; Si: 0.29; Mn: 0.19; P: 0.008; S: 0.012, with the balance being Fe; Compared with existing high-speed steels that undergo electroslag remelting and alloying with high amounts of precious metals, the high-speed steel obtained by this invention is a low-cost, short-process, high-impact, and wear-resistant high-speed steel 3 with the following advantages: First, it eliminates the need for electroslag remelting; second, it only requires the addition of 0.1 wt% wire containing nano-ceramic particles, which does not contain precious metal elements, significantly reducing raw material production costs and improving the uniformity of the high-speed steel's microstructure. Therefore, under the same testing conditions as existing technologies, it exhibits better stability in impact toughness and wear resistance, simultaneously improving both. Specifically, the unnotched impact toughness is 26.3 J / cm². 2 Compared with existing technologies, this represents a 46% improvement. Under a continuous rotational speed of 900 r / min for 300 min and a load of 50 N, the volumetric wear rates at room temperature, 200℃, and 400℃ are 7.5 × 10⁻⁶. -6 mm 3 / (N·m), 8.9×10 -6 mm 3 / (N·m) and 6.4×10 -6 mm 3 / (N·m), compared with the prior art, the volumetric wear rate was reduced by 18.5%, 19.1% and 21.9% respectively, and the wear surface roughness ( R a) The values ​​are 0.347, 0.548, and 0.784 respectively, indicating that the wear surface roughness is low. R a) The smaller the value, the better the wear resistance of the material. Comparative Example 1

[0020] High-speed steel 4, characterized in that its preparation method includes the following steps: (1) At room temperature, iron vanadium powder, boron powder and iron powder are mixed at a mass ratio of 9:4:87 at a speed of 70 r / min for 26 hours to obtain powder mixture 1; titanium dioxide, boron carbide powder and aluminum powder are mixed at a mass ratio of 32:17:51 at a speed of 125 r / min for 4 hours to obtain powder mixture 2. The iron-vanadium powder, by mass percentage, consists of 75 wt% vanadium and 25 wt% iron, with a particle size of 8 micrometers. The particle sizes of the boron powder, iron powder, titanium dioxide powder, boron carbide powder, and aluminum powder are 12 micrometers, 13 micrometers, 125 micrometers, 225 micrometers, and 310 micrometers, respectively. (2) After wrapping the powder mixture 1 obtained in step (1) with iron foil 1, it is compacted 1 and then subjected to an electro-explosion reaction 1 to obtain an alloy 1 containing micron-sized ceramic particles; after wrapping the powder mixture 2 obtained in step (1) with aluminum foil, it is compacted 2 and then subjected to an electro-explosion reaction 2 to obtain an alloy 2 containing micron-sized ceramic particles. The compaction treatment 1 described above: pressure 820 MPa, holding time 5 min; The aforementioned electro-explosion reaction treatment 1: under argon protection, pressure: 0.012 MPa, current density: 2.3 × 10⁻⁶ 5 A / mm², voltage 10kV; The mass ratio of the iron foil 1 to the mixture 1 is 0.007:1; The compaction treatment 2 described above: pressure 320 MPa, holding time 20 min; The aforementioned electro-explosion reaction treatment 2: under argon protection, pressure: 0.02 MPa, current density 8.3 × 10⁻⁶. 6 A / mm², voltage 38kV; The mass ratio of the aluminum foil to mixture 2 is 0.018:1; (3) Alloy 1 and Alloy 2 obtained in step (2) are crushed and mixed at a speed of 25 r / min for 0.15 hours according to a mass ratio of 1:6 to obtain mixture 3; mixture 3 is treated by high frequency induction plasma method to obtain powder; the powder is wrapped with iron foil 2 to obtain wire; No nano-ceramic particles were found in the wire. The high-frequency induction plasma treatment is carried out under argon protection at a pressure of 0.2 MPa, a temperature of 1800℃, a power supply operating frequency of 0.8 MHz, and an output power of 18 kW. The mass ratio of the iron foil 2 to the powder containing nano-ceramic particles is 0.001:1; (4) Under argon protection, the high-speed steel is melted at 1410℃ and held for 125 minutes, refined, and then the wire obtained in step (3) is added for melting, refined under vacuum, cast at room temperature, forged, isothermal annealed, rolled, quenched and tempered to obtain low-cost short-process high impact and wear-resistant high-speed steel. The refining process was conducted at a temperature of 1450℃ for 110 minutes, with argon gas stirring at a flow rate of 0.1 m³ / min. 3 / h; The mass ratio of the wire obtained in step (3) to the high-speed steel is 0.005%:1; The forging process is described as follows: the forging temperature is 1030℃, and the forging ratio is 1.5:1. The isothermal annealing process involves holding the temperature at 805℃ for 6.5 hours. The rolling process is as follows: roughing mill: starting temperature 1045℃, finishing temperature 910℃, 15 passes, each pass has a different reduction rate, each pass has a reduction rate of 1-12%, the total reduction rate is 50%, and the speed is 2m / s; finishing mill: starting temperature 860℃, finishing temperature 810℃, 5 passes, each pass has a different reduction rate, each pass has a reduction rate of 2-15%, the total reduction rate is 70%, and the speed is 12m / s. The quenching treatment described above: oil quenching at 1150℃; The tempering process consists of three tempering processes: holding at 543℃ for 205 min, holding at 540℃ for 205 min, and holding at 535℃ for 205 min in sequence. The high-speed steel described herein, by mass percentage, has the following composition: C: 0.75; W: 5.32; Mo: 4.51; Cr: 3.43; V: 1.62; Co: 4.42; Si: 0.18; Mn: 0.13; P: 0.032; S: 0.035, with the balance being Fe; The obtained high-speed steel 4 has an unnotched impact toughness of 12.5 J / cm. 2 Under a rotational speed of 900 r / min for 300 min and a load of 40 N, the volumetric wear rates at room temperature, 200℃, and 400℃ were 2.92 × 10⁻⁶. -5 mm 3 / (N·m), 3.89×10 -5 mm 3 / (N·m) and 4.81×10 -5 mm 3 / (N·m), wear surface roughness ( R a) The values ​​are 0.501, 0.770, and 1.899, respectively.

[0021] Compared with Examples 1-3, Comparative Example 1 uses component ratios and process parameter ranges that are not within the protection scope of claim 1 of this invention. Therefore, the impact and wear resistance obtained in Comparative Example 1 are lower than the minimum performance (notched impact toughness 25 J / cm) obtained in claim 1 of this invention. 2 Volumetric wear rate: 9.2 × 10⁻⁶ -6 mm 3 / (N·m) ). Comparative Example 2

[0022] The high-speed steel 5, which has undergone electroslag remelting, is characterized in that its preparation method includes the following steps: (1) Under argon protection, high-speed steel was melted at 1620℃ and held for 100 min, refined, refined under vacuum, cast at room temperature, electroslag remelted, forged, isothermal annealed, rolled, quenched and tempered to obtain high-speed steel 5 after electroslag remelting. The refining process was conducted at a temperature of 1520℃ for 80 minutes, with argon gas blowing and stirring at a flow rate of 0.3 m³ / min. 3 / h; The electroslag remelting process described above: under argon protection, power 145 kW, current density 7 A / mm². 2 The melting time was 43 minutes, and the molten pool temperature was 1515℃. The forging process is described as follows: the forging temperature is 1090℃, and the forging ratio is 2:1. The isothermal annealing process involves holding the temperature at 825℃ for 5 hours. The rolling process is as follows: roughing mill: starting temperature 1065℃, finishing temperature 920℃, 12 passes, each pass has a different reduction rate of 5-15%, total reduction rate 75%, speed 4m / s; finishing mill: starting temperature 890℃, finishing temperature 820℃, 11 passes, each pass has a different reduction rate of 4-18%, total reduction rate 90%, speed 16m / s; The quenching treatment described is: oil quenching at 1190℃; The tempering process consists of three tempering processes: holding at 580℃ for 50 min, holding at 570℃ for 60 min, and holding at 560℃ for 70 min in sequence. The high-speed steel described herein, by mass percentage, has the following composition: C: 0.81; W: 5.52; Mo: 4.61; Cr: 3.51; V: 1.72; Co: 4.53; Si: 0.25; Mn: 0.17; P: 0.02; S: 0.010, with the balance being Fe; The high-speed steel 5 obtained after electroslag remelting has an unnotched impact toughness of 13.8 J / cm. 2 The impact fracture surface of high-speed steel 5 after electroslag remelting is as follows: Figure 1 As shown in (b), surface cracks and breakage are visible; under a rotational speed of 900 r / min for 300 min and a load of 30 N, the volumetric wear rates at room temperature, 200℃, and 400℃ are 2.84 × 10⁻⁶. -6 mm 5 / (N·m), 2.88×10 -5 mm 3 / (N·m) and 3.81×10 -5 mm 3 / (N·m), wear surface roughness ( Ra) The values ​​are 0.452, 0.691, and 1.612, respectively.

[0023] Compared with Examples 1-3, Comparative Example 2 did not add the wire containing nano-ceramic particles of the present invention, and added electroslag remelting treatment. All other component ratios and process parameters were within the range of claim 1. However, the unnotched impact toughness and volumetric wear resistance of Comparative Example 2 were far lower than the minimum performance of claim 1 (unnotched impact toughness 25 J / cm). 2 Volumetric wear rate: 9.2 × 10⁻⁶ -6 mm 3 / (N·m)). Comparative Example 3

[0024] In his master's thesis, "Microstructure and Property Regulation of High-Speed ​​Steel Based on Pulsed Current Treatment," published in June 2024, Chen Dihui demonstrated that, based on commercially available high-speed steel that had undergone electroslag remelting in a hot-rolled annealed state, a notched impact toughness of ~16.0 J / cm² was achieved after one electropulse austenitization followed by quenching and three electropulse tempering processes. 2 The performance and the extent of performance improvement are far lower than the impact resistance (unnotched impact toughness ≥25J / cm) of the low-cost, short-process, high-impact, wear-resistant high-speed steel of this invention. 2 (The increase is ≥40%).

[0025] The volumetric wear rates of high-speed steel reported in Comparative Example 3, after being subjected to a rotational speed of 150 r / min for 20 min and a load of 40 N, and after quenching following a single electrical pulse austenitization and after tempering following three electrical pulses at room temperature, 200℃, and 400℃, were 2.15 × 10⁻⁶. -5 2.41×10 -5 and 3.52×10 -5 mm 3 N -1 m -1 Wear surface roughness ( R a) The white light interference patterns of the worn surfaces of this high-speed steel at room temperature and 200℃ are 1.16, 2.387, and 4.682, respectively. Figure 2 As shown in (b) and 3(b), the average depths are 15.69 μm and 16.98 μm, respectively. At 400℃, the average depth of the wear surface increases to 25.21 μm. The peak-valley depth of the wear surface obtained by this invention is at the nanometer level, while existing technologies reach tens of micrometers or more. At a temperature of 400℃ and loads of 30 N, 40 N, and 50 N, the volumetric wear rates are 2.7 × 10⁻⁶. -5 3.52×10 -5 and 4.17×10 -5 mm 3 N -1 m -1This invention utilizes a low-cost, short-process, high-impact, wear-resistant high-speed steel. Under conditions of 900 r / min for 300 min and a load of 30-50 N, the volumetric wear rate is ≤7.6 × 10⁻⁶ at room temperature, 200℃, and 400℃. -6 mm 3 / (N·m), ≤9.2×10 -6 mm 3 / (N·m), ≤6.5×10 -6 mm 3 / (N·m), surface roughness ( R a) ≤0.347, ≤0.548, ≤0.784. Therefore, compared with Comparative Example 3, the wear rate of high-speed steel obtained by the present invention is significantly reduced, the wear resistance rate is increased by 64.6% or more, the roughness of the wear surface is lower, and the height difference between the peaks and valleys of the wear surface is smaller. The wear resistance performance obtained by the present invention is significantly better than that of Comparative Example 3.

[0026] Table 1. Comparison of high-speed steel performance in comparative examples and various embodiments.

[0027] Although the method reported in Comparative Example 3 can improve the impact toughness and wear performance of high-speed steel, the impact toughness and wear performance achieved in the comparative example are far lower than those of the low-cost, short-process, high-impact, and wear-resistant high-speed steel obtained in the embodiments of the present invention. Moreover, Comparative Example 3 requires a more complex preparation process and a proprietary electric pulse device, which is not suitable for the industrialization of large-scale products. It can only be used for small laboratory samples, and the process production cost is higher than that of the present invention.

[0028] The composition of the high-speed steel in Comparative Example 3 is as follows: 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: 0.40 wt%; with the balance being Fe. The content of C, Mn, and precious metals such as Mo and Co is higher than in all embodiments of this invention, but the performance is far lower than in all embodiments of this invention.

[0029] This invention eliminates the need for electroslag remelting, saving 2500-3000 RMB / ton of steel in electroslag costs, conserving energy and precious alloy resources such as Mo and V, while reducing carbon emissions. It adds only ≤0.35 wt% nanoparticles (costing 300-400 RMB / ton of steel), achieving a simultaneous and significant improvement in the impact toughness and wear resistance of high-speed steel. This breaks through the technical bottleneck of existing high-cost raw materials and complex processes that make it difficult to simultaneously improve impact toughness and wear resistance. Furthermore, this invention improves carbide segregation, microstructure uniformity, formability, and product qualification rate, achieving a synergistic improvement in performance and formability, and balancing high-performance, high-quality forming and short-process green manufacturing. Therefore, this invention has significant cost advantages, performance advantages, and short-process manufacturing advantages.

[0030] From Comparative Examples 1-3 and each embodiment of the present invention, it can be seen that: firstly, the process parameters of Comparative Example 1 are not within the scope of protection of claim 1 of the present invention; secondly, Comparative Example 2 does not add the wire containing nano-ceramic particles of the present invention and adds electroslag remelting treatment; thirdly, the proportions and process parameters of each embodiment of the present invention are different, but the results are that the performance of each embodiment is different. In addition, the wear resistance and impact resistance of Comparative Examples 1-3 are lower than the minimum performance of claim 1 of the present invention. This shows that the present invention has achieved the best effect that is significantly superior to the prior art. Furthermore, the best technical effect obtained by the present invention is not determined by a certain component, proportion, process, or process parameter, but is achieved by the interaction of components, proportion, process, and synergistic regulation of process parameters. Moreover, the significantly improved technical effect can only be achieved within the scope of claim 1 of the present invention.

Claims

1. Low-cost, short-process, high-impact, wear-resistant high-speed steel, characterized by: Its preparation method includes the following steps: (1) At room temperature, iron vanadium powder, boron powder and iron powder are mixed at a mass ratio of 10-35:5-15:50-85 at a speed of 80-180 r / min for 10-25 hours to obtain powder mixture 1; titanium dioxide, boron carbide powder and aluminum powder are mixed at a mass ratio of 12-30:6-16:54-82 at a speed of 60-120 r / min for 5-16 hours to obtain powder mixture 2. The iron-vanadium powder, by mass percentage, consists of 75 wt% vanadium and 25 wt% iron, with a particle size of 10-260 micrometers. The particle sizes of the boron powder, iron powder, titanium dioxide powder, boron carbide powder, and aluminum powder are 15-95 micrometers, 16-96 micrometers, 20-120 micrometers, 25-220 micrometers, and 50-300 micrometers, respectively. (2) After wrapping the powder mixture 1 obtained in step (1) with iron foil 1, it is compacted 1 and then subjected to an electro-explosion reaction 1 to obtain an alloy 1 containing micron-sized ceramic particles; after wrapping the powder mixture 2 obtained in step (1) with aluminum foil, it is compacted 2 and then subjected to an electro-explosion reaction 2 to obtain an alloy 2 containing micron-sized ceramic particles. The compaction treatment 1 described above: pressure 311-817 MPa, holding time 7-17 min; The aforementioned electro-explosion reaction treatment 1: under argon protection, pressure 0.015-0.065 MPa, current density 2.7×10⁻⁶ MPa. 5 Up to 8.5×10 6 A / mm 2 Voltage 11-31kV; The mass ratio of the iron foil 1 to the mixture 1 is 0.008-0.018:1; The compaction treatment 2 described above: pressure 328-835 MPa, holding time 4-16 min; The aforementioned electro-explosion reaction treatment 2: under argon protection, pressure 0.03-0.08 MPa, current density 2.6×10⁻⁶ MPa. 5 Up to 8.1×10 6 A / mm 2 Voltage 17-36kV; The mass ratio of the aluminum foil to mixture 2 is 0.006-0.016:1; (3) Alloy 1 and Alloy 2 obtained in step (2) are crushed and then mixed at a speed of 30-80 r / min for 0.2-4.5 hours according to a mass ratio of 2-5:1-6 to obtain mixture 3; mixture 3 is treated by high frequency induction plasma method to obtain powder containing nano-ceramic particles; powder containing nano-ceramic particles is wrapped with iron foil 2 to obtain wire containing nano-ceramic particles. The wire containing nano-ceramic particles contains nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles, with the mass percentage of the above three types of particles being 6-50%. The high-frequency induction plasma method is carried out under argon protection, with a pressure of 0.01-0.15 MPa, a temperature of 2000-5000℃, a power supply operating frequency of 1-15 MHz, and an output power of 20-100 kW. The particle sizes of the nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles range from 100-800 nanometers, 50-550 nanometers, and 75-650 nanometers, respectively. The mass ratio of the iron foil 2 to the powder containing nano-ceramic particles is 0.002-0.016:1; (4) Under argon protection, the high-speed steel is melted at 1420-1950℃ and held for 35-115 minutes, refined, and then the wire obtained in step (3) is added for melting, refined under vacuum, cast at room temperature, forged, isothermal annealed, rolled, quenched and tempered to obtain low-cost short-process high impact-resistant and wear-resistant high-speed steel. The refining process involves: a temperature of 1480-1700℃, a refining time of 10-100 minutes, and stirring with argon gas at a flow rate of 0.2-0.6 m³ / min. 3 / h; The mass ratio of the wire obtained in step (3) to the high-speed steel is 0.006-0.35%:1; The forging process is described as follows: the forging temperature is 1050-1200℃, and the forging ratio is 2-5:

1. The isothermal annealing process involves holding the temperature at 815-885℃ for 1-6 hours. The rolling process is as follows: roughing rolling starts at 1059-1189℃, finishes at 915-10℃, with 5-13 passes, each pass having a different reduction rate of 3-31%, for a total reduction rate of 55-78%, and a speed of 3-8 m / s; finishing rolling starts at 882-959℃, finishes at 815-881℃, with 6-12 passes, each pass having a different reduction rate of 3.5-30%, for a total reduction rate of 78-93%, and a speed of 15-29 m / s. The quenching treatment is described as follows: oil quenching at 1160-1250℃; The tempering treatment described herein consists of 1-4 tempering treatments, each of which involves holding at 545-615℃ for 40-200 minutes. The high-speed steel described herein, by mass percentage, has the following composition: C: 0.80-0.95; W：5.50-7.00； Mo: 4.60-5.50; Cr: 3.50-4.50; V: 1.70-2.25; Co: 4.50-5.50; Si: 0.20-0.45; Mn: 0.15-0.40; P: ≤0.030; S ≤0.030, balance is Fe; Compared with existing high-speed steels that undergo electroslag remelting and alloying with high amounts of precious metals, this invention provides a low-cost, short-process, high-impact, and wear-resistant high-speed steel with the following advantages: First, it eliminates the need for electroslag remelting; second, it only adds ≤0.35 wt% of wire containing nano-ceramic particles, which does not contain precious metal elements, significantly reducing raw material production costs and improving the uniformity of the high-speed steel's microstructure. Therefore, under the same testing conditions as existing technologies, it exhibits better stability in impact toughness and wear resistance, simultaneously improving both. Specifically, the unnotched impact toughness is ≥25 J / cm. 2 Compared with existing technologies, it improves wear rate by ≥40%; it achieves significant reduction in wear rate under both room temperature and high temperature conditions, with volumetric wear rate ≤9.2×10⁻⁶. -6 mm 3 / (N·m), compared with the prior art, the volumetric wear rate is reduced by ≥15%; among which, under a rotation speed of 900 r / min for 300 min and a load of 30-50 N, the volumetric wear rate at room temperature, 200℃ and 400℃ is ≤7.6×10. -6 mm 3 / (N·m), ≤9.2×10 -6 mm 3 / (N·m), ≤6.5×10 -6 mm 3 / (N·m); Meanwhile, the wear surface roughness and the height difference between the peaks and valleys of the wear surface obtained under room temperature and high temperature conditions are much smaller than the relevant values ​​obtained by the prior art. The lower the above values, the better the wear resistance performance. In summary, the low-cost, short-process, high-impact, and wear-resistant high-speed steel obtained by the present invention has excellent wear resistance performance.

2. The low-cost, short-process, high-impact, wear-resistant high-speed steel according to claim 1, characterized in that, Step (1) describes the following: At room temperature, iron vanadium powder, boron powder and iron powder are mixed at a mass ratio of 11-34:6-14:52-83 at a speed of 95-165 r / min for 11-23 hours to obtain powder mixture 1; titanium dioxide, boron carbide powder and aluminum powder are mixed at a mass ratio of 13-29:7-15:56-80 at a speed of 82-111 r / min for 6.5-14.5 hours to obtain powder mixture 2. The iron-vanadium powder, by mass percentage, consists of 75 wt% vanadium and 25 wt% iron, with a particle size of 25-245 micrometers; The particle sizes of the boron powder, iron powder, titanium dioxide powder, boron carbide powder, and aluminum powder are 25-85 micrometers, 26-86 micrometers, 30-110 micrometers, 35-210 micrometers, and 60-290 micrometers, respectively.

3. The low-cost, short-process, high-impact, wear-resistant high-speed steel according to claim 1, characterized in that, The compaction treatment 1 described in step (2) is as follows: pressure 315-813 MPa, holding time 8-16 min; The aforementioned electro-explosion reaction treatment 1 is as follows: under argon protection, pressure 0.017-0.062 MPa, current density 3.1×10⁻⁶ MPa. 5 Up to 8.1×10 6 A / mm 2 Voltage 12-30kV; The mass ratio of the iron foil 1 to the mixture 1 is: 0.011-0.017:1； The compaction treatment 2 described above: pressure 331-830 MPa, holding time 5-15 min; The aforementioned electro-explosion reaction treatment 2 is performed under argon protection at a pressure of 0.032-0.078 MPa and a current density of 2.7 × 10⁻⁶ MPa. 5 Up to 7.9×10 6 A / mm 2 Voltage 18-35kV; The mass ratio of the aluminum foil to mixture 2 is 0.009-0.015:

1.

4. The low-cost, short-process, high-impact, wear-resistant high-speed steel according to claim 1, characterized in that, In step (3), alloy 1 and alloy 2 are crushed and mixed at a speed of 45-65 r / min for 0.5-4.2 hours to obtain mixture 3. The mixture 3 is then treated with high-frequency induction plasma to obtain powder containing nano-ceramic particles. The powder containing nano-ceramic particles is wrapped with iron foil 2 to obtain wire containing nano-ceramic particles. The wire containing nano-ceramic particles contains nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles, with the mass percentage of the above three types of particles being 9%-46%. The high-frequency induction plasma method is carried out under argon protection, with a pressure of 0.02-0.12 MPa, a temperature of 2500-4500℃, a power supply operating frequency of 2-13 MHz, and an output power of 25-85 kW. The particle sizes of the nano-vanadium boride, nano-titanium carbide, and nano-titanium diboride particles range from 120-780 nanometers, 65-500 nanometers, and 85-600 nanometers, respectively. The mass ratio of the iron foil 2 to the powder containing nano-ceramic particles is 0.0025-0.013:

1.

5. The low-cost, short-process, high-impact, wear-resistant high-speed steel according to claim 1, characterized in that, Step (4) describes the process of melting high-speed steel at 1430-1930℃ under argon protection, holding it at that temperature for 40-110 minutes, refining it, then adding the wire obtained in step (3) for melting, refining it under vacuum, casting it at room temperature, forging it, isothermal annealing it, rolling it, quenching it and tempering it to obtain low-cost, short-process, high-impact, wear-resistant high-speed steel.

6. The low-cost, short-process, high-impact, wear-resistant high-speed steel according to claim 1, characterized in that, The refining process described in step (4) involves: a temperature of 1500-1680℃, a refining time of 20-90 minutes, and stirring with argon gas at a flow rate of 0.3-0.5 m³ / min. 3 / h; The mass ratio of the wire to high-speed steel is 0.008-0.3%:

1.

7. The low-cost, short-process, high-impact, wear-resistant high-speed steel according to claim 1, characterized in that, The forging described in step (4) is as follows: the forging temperature is 1090-1160℃, and the forging ratio is 2.2-4.2:1; The isothermal annealing process involves holding the temperature at 820-875℃ for 2-5 hours. The rolling process is as follows: roughing rolling starts at 1065-1182℃ and finishes at 919-1009℃, with 6-11 passes, each pass having a different reduction rate of 3.5-30%, for a total reduction rate of 60-73%, and a speed of 4-7 m / s; finishing rolling starts at 886-955℃ and finishes at 819-876℃, with 7-11 passes, each pass having a different reduction rate of 4-28%, for a total reduction rate of 80-91%, and a speed of 17-27 m / s. The quenching treatment is described as follows: oil quenching at 1180-1240℃; The tempering process involves 2-3 tempering cycles, with each tempering cycle consisting of holding at 555-605℃ for 45-185 minutes.

8. The low-cost, short-process, high-impact, wear-resistant high-speed steel according to claim 1, characterized in that, The low-cost, short-process, high-impact, and wear-resistant high-speed steel described in step (4) has the following advantages: First, it does not require electroslag remelting; second, it only requires the addition of ≤0.30 wt% of wire containing nano-ceramic particles, which does not contain precious metal elements, significantly reducing raw material production costs and improving the uniformity of the high-speed steel structure. Therefore, under the same testing conditions as existing technologies, it exhibits better stability in impact toughness and wear resistance, simultaneously improving both. Specifically, the unnotched impact toughness is 25.5-29.5 J / cm. 2 Compared with existing technologies, it improves efficiency by 40.8-55%; it achieves significant reductions in wear rate under both room temperature and high temperature conditions, with a volumetric wear rate of 4.5×10⁻⁶. -6 -9.1×10 -6 mm 3 / (N·m), the volumetric wear rate is reduced by 16.5-42% compared with existing technologies.

Images