CN109825756B - Preparation method of high-wear-resistance alloy steel material - Google Patents
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Abstract
The invention discloses a preparation method of a high-wear-resistance alloy steel material, and belongs to the technical field of wear-resistance material preparation. The wear-resistant alloyed medium carbon steel comprises, by mass, 0.25-0.4% of C, 0.15-0.3% of Si, 0.4-0.65% of Mn, 0.7-0.95% of Cr, 0.7-0.95% of Ti, 0.01-0.05% of V, 0.3-0.45% of Mo, 0.5-0.7% of Ni, less than 0.005% of P, less than 0.006% of S and the balance of Fe and residual trace impurities. According to the invention, through component design and subsequent heat treatment, deformation process and relaxation treatment, a large amount of (Ti, Mo) C particles and a small amount of VC carbide particles with small sizes are generated in an alloying medium carbon steel structure, the large-size (Ti, Mo) C particles can effectively resist the micro-cutting effect of abrasive particles, and the small-size VC particles can enhance the yield strength of a matrix, so that the deformation resistance of the matrix is improved, the support effect on the (Ti, Mo) C particles is enhanced, and the wear resistance of the material is obviously improved.
Description
Technical Field
The invention relates to a preparation method of a high-wear-resistance alloy steel material, and belongs to the technical field of wear-resistance material preparation.
Background
Wear is one of the main causes of failure of mechanical parts, and the loss of material and energy due to wear of mechanical parts is quite dramatic; a large amount of wear-resistant materials are applied to the departments of mines, coal, metallurgy, chemical industry and the like, and in the industries, a large amount of economic loss is caused by the wear failure of the materials; the development of wear resistant materials is therefore very advantageous both for technical accumulation and for economic growth.
In recent years, various alloy wear resistant steel materials have been widely used in manufacturing, mining, and metallurgy sectors, including XAR500, NM500, HARDOX500, and the like. In general, the wear resistance of steel materials is proportional to their hardness, and the method of increasing the hardness of steel is often by increasing the carbon or chromium content of the steel. However, higher carbon and chromium contents in steel drastically deteriorate the workability and weldability of the material, while at the same time making it clearThe plasticity and the toughness of the material are obviously reduced. There is therefore a need to improve the wear resistance of steel by other methods without impairing its workability and weldability. Various patents previously disclosed have demonstrated that the wear resistance of materials can be effectively improved by compounding hard particles comprising TiC, WC, NbC, Al on a metal matrix2O3、ZrO3TiN, etc., wherein TiC is widely used as a hard particle in reinforcing steel materials because of its high melting point and hardness and the cost of Ti is lower than that of other strong carbonitride forming elements, and Mo promotes precipitation of TiC in steel, and thus is often added to steel together with Ti. During abrasive wear, the hard (Ti, Mo) C particles may be effective against wear to protect the metal matrix.
The Chinese invention patent CN106544549A discloses a preparation method of a micro-nano dual-scale TiC particle reinforced aluminum matrix composite, which is characterized by comprising the following specific steps: ball-milling and mixing micron-sized TiC powder, C powder and Ti powder, and then pressing into a precast block; smelting aluminum alloy by using a resistance furnace, and pressing the prepared prefabricated block into an aluminum alloy melt by using a graphite bell jar; and pouring the melt into a graphite mold, and solidifying to obtain the dual-scale TiC particle reinforced aluminum matrix composite. The mechanical property and the frictional wear property of the aluminum matrix composite material are improved. The Chinese invention patent CN105622101A discloses a synthesis method of TiC/C composite material, which is characterized by comprising the following specific steps: mixing a titanium source and a carbon material in proportion and ball-milling, vacuumizing a ball-milling tank and filling CO in the ball-milling process2And then heating the powder to 1100-1450 ℃ under the protection of argon, preserving the heat for 2-8 h, and cooling to room temperature to obtain the TiC composite material. Because of the high hardness and stability of TiC, the composite material obtains high wear resistance and corrosion resistance. In summary, the wear resistance of the material can be effectively improved by compounding the TiC hard particles on the metal matrix, but the production processes are relatively complex, the production period is long, the efficiency is low, and the reduction of labor cost and large-scale industrial production are not facilitated.
At present, the microalloying technology combined with the controlled rolling and controlled cooling process is one of effective ways for developing low-cost high-strength steel, and the controlled rolling and controlled cooling technology can enable dispersed large-size hard TiC particles to be generated in situ in a Ti alloy steel structure, effectively block the micro-cutting effect of abrasive particles in the abrasion process of an abrasive, and greatly improve the abrasion resistance of steel on the premise of ensuring the weldability and the machinability of the steel. However, at present, the content research on the wear resistance of Ti alloying controlled rolling and cooling steel is less, so that the development of the high-wear-resistance alloy steel based on the controlled rolling and cooling technology has huge economic benefits and wide market application prospects.
Disclosure of Invention
The invention aims to provide a preparation method of a high-wear-resistance alloy steel material, which is characterized in that (Ti, Mo) C particles and fine VC carbide particles are generated in a carbon steel structure in an alloy through the design of alloy elements and the combination of smelting and subsequent processing processes; the method specifically comprises the following steps:
(1) vacuum smelting: weighing pure iron, ferromanganese, ferrochrome, ferrotitanium, ferrosilicon, ferromolybdenum, vanadium particles, a nickel plate and a graphite electrode block according to the design components, carrying out vacuum melting to obtain a metal ingot, heating the demoulded metal ingot to 950 +/-20 ℃, preserving heat for 30-40 min, and forging the metal ingot into an ingot after the heat preservation is finished.
(2) Controlled rolling and controlled cooling treatment: heating the cast ingot to 1200-1250 ℃ at the speed of 5 ℃/s, preserving heat for 40-60 min, cooling to the rolling temperature range of 980-850 ℃ at the speed of 10 ℃/s, preserving heat for 5s, and then performing three-pass rolling, wherein the strain rate of the first pass rolling is 0.5-1 s-1Carrying out second pass rolling after the deformation is 25% and the interval is 60-180 s, wherein the strain rate of the second pass rolling is 0.5-1 s-1The deformation is 30%, the third rolling is carried out after the interval of 60-180 s, and the strain rate of the third rolling is 0.5-1 s-1The deformation amount is 25%; the initial rolling temperature is 960-980 ℃, and the final rolling temperature is 870-850 ℃; then carrying out relaxation treatment for 300-600 s; and then cooling to 610 +/-20 ℃ at a cooling speed of 30-40 ℃/s, preserving heat for 15-20 min, and cooling to room temperature after heat preservation is finished.
The alloy steel comprises, by mass, 0.25-0.4% of C, 0.15-0.3% of Si, 0.4-0.65% of Mn, 0.7-0.95% of Cr, 0.7-0.95% of Ti, 0.01-0.05% of V, 0.3-0.45% of Mo, 0.5-0.7% of Ni, less than 0.005% of P, less than 0.006% of S and the balance of Fe and residual trace impurities.
Preferably, the vacuum melting in step (1) of the present invention comprises the following specific processes: filling pure iron and a graphite electrode block into a pre-dried built-in crucible, vacuumizing a vacuum induction furnace to 10-20 Pa, starting smelting until the pure iron is completely melted, and keeping the temperature of molten steel at 1490-1540 ℃; argon is blown from the bottom of the vacuum furnace for protection until the vacuum degree reaches 2800-3200 Pa, ferrochromium, ferromanganese, ferromolybdenum and ferrosilicon are sequentially added for smelting for 10-15 min, after furnace burden is uniformly melted, an aluminum block is added for deoxidation, ferrotitanium and ferrovanadium are sequentially added after 1-2 min, the temperature of the molten metal is kept at 1530-1580 ℃, the molten metal is sampled and subjected to chemical direct-reading spectral analysis, and the chemical components of the molten metal are adjusted to the range of designed components according to the analysis result; after the molten metal reaches the preset chemical composition, the power supply of the smelting furnace is turned off, and the molten metal is cooled along with the furnace for 3-4 hours; and removing the bottom plate of the furnace, separating the built-in crucible from the furnace shell, breaking the crucible, taking out the metal ingot, and removing the oxidized skin to obtain the metal ingot.
Preferably, the built-in crucible in the vacuum melting furnace is a magnesia crucible.
Preferably, the purity of the vanadium particles in step (1) of the present invention is not less than 99.97 wt.%.
Preferably, in the invention, the thickness of the cast ingot forged in the step (1) is 40-80 mm.
The principle of the invention is as follows: according to the invention, by designing the components of the Ti-Mo-V medium carbon alloy steel and adopting the process flows of vacuum melting, controlled rolling and controlled cooling, a large amount of large-size (Ti, Mo) C hard particles and a small amount of small-size VC carbide particles are generated in the finally obtained alloy steel structure. The rolling process of three passes is adopted in the controlled rolling and cooling stage, each pass adopts rolling parameters of large reduction and slow strain rate, a period of time is arranged between each pass, the slow strain rate and the large reduction can ensure the continuous accumulation of deformation energy storage in steel, certain thermodynamic conditions are provided for the precipitation and the precipitation of (Ti, Mo) C hard particles in the steel, and the precipitation of the (Ti, Mo) C hard particles in the steel are promoted; a certain dynamic condition can be provided for precipitation and precipitation of the (Ti, Mo) C hard particles at intervals of one time, the precipitation and precipitation quantity of the (Ti, Mo) C hard particles is increased, and the precipitation process is promoted to be carried out fully; after the rolling process is finished, relaxation treatment is carried out to promote a large amount of deformation induced precipitation (Ti, Mo) C hard particles generated in the rolling process to coarsen and grow up, C and alloy elements in steel can be fully diffused due to the fact that the structure temperature is high at the moment, and the (Ti, Mo) C hard particles continuously grow up along with the extension of relaxation time. Carbide hard particles precipitated in steel during rolling and relaxation treatment mainly consist of (Ti, Mo) C hard particles, because Ti has a low equilibrium solid solubility product and is easy to precipitate in steel, and VC has a high equilibrium solid solubility product and is often precipitated in a lower temperature range. Cooling to 610 +/-20 ℃ at a cooling speed of 30-40 ℃/s after relaxation treatment and preserving heat, and aims to increase the supercooling degree in steel through rapid cooling, promote precipitation of VC particles, prevent VC precipitated in the cooling process from coarsening, and increase the precipitation amount of the VC particles through isothermal cooling. During the abrasion process of the abrasive, the large-size (Ti, Mo) C hard particles can resist the micro-cutting action of the abrasive particles and prevent the abrasive particles from being embedded into a matrix; when abrasive grains are embedded somewhere in the matrix and sliding cutting occurs, (Ti, Mo) C hard particles may hinder sliding cutting of abrasive grains; the small-size VC particles can enhance the yield strength of the matrix, improve the deformation resistance of the matrix, provide better supporting effect for the (Ti, Mo) C hard particles and prevent the large-size hard particles from falling off when continuously subjected to the action of external force.
The invention has the beneficial effects that:
(1) the method of the invention takes the premise of not damaging the machinability and weldability of the steel in the component design and subsequent treatment processes, fully considers the simplicity of the production process and the economy of the production cost, and improves the wear resistance of the steel by generating a large amount of large-size (Ti, Mo) C hard particles and small-size VC particles in the alloy steel structure.
(2) The method is mature and reliable, has simple flow and lower cost, and is beneficial to large-scale industrial production; a large amount of (Ti, Mo) C hard particles and VC particles are obtained in a finally obtained steel structure through three-pass rolling process, relaxation treatment, rapid cooling and isothermal treatment, wherein the (Ti, Mo) C particles can resist the micro-cutting effect of abrasive particles, and the VC particles can play a role in reinforcing a matrix, so that the wear resistance of the steel is greatly improved.
(3) The alloy steel has the main alloy element of Ti, and because the titanium ore resources are rich and the reserves are large in China, the production cost is greatly reduced; meanwhile, Ti is a strong carbonitride forming element in steel, so that hard carbide particles with larger size and uniform distribution are easy to generate, and the production difficulty is reduced.
Drawings
FIG. 1 is a process flow diagram of the present invention.
Fig. 2 is a schematic view of the principle of the resistance of alloyed medium carbon steel and plain medium carbon steel prepared by the present invention to abrasive wear during abrasive wear.
FIG. 3 is an SEM photograph of (Ti, Mo) C precipitate particles in the alloyed medium carbon steel structure of example 1.
FIG. 4 is a TEM image of VC precipitate particles in the alloyed medium carbon steel structure in example 1.
Detailed Description
The invention is described in further detail below with reference to the figures and the embodiments, but the scope of the invention is not limited to the description.
Example 1
The preparation method of the wear-resistant alloyed medium carbon steel comprises the following chemical components in percentage by mass: 0.31 percent of C, 0.24 percent of Si, 0.55 percent of Mn, 0.76 percent of Cr, 0.83 percent of Ti, 0.04 percent of V, 0.36 percent of Mo, 0.58 percent of Ni, less than 0.004 percent of P, less than 0.005 percent of S, and the balance of Fe and residual trace impurities. The alloy steel forging has the size of 800mm multiplied by 50mm multiplied by 60mm, and referring to fig. 1, the specific process flow comprises the following steps:
(1) vacuum smelting: preparing materials by adopting a 100kg vacuum induction furnace: weighing pure iron, ferromanganese, ferrochrome, ferrotitanium, ferrosilicon, ferromolybdenum, vanadium particles, a nickel plate and a graphite electrode block according to design components; melting: filling pure iron and graphite electrode blocks into a pre-dried built-in crucible, vacuumizing a vacuum induction furnace to 15Pa, and starting smelting until the pure iron is completely melted, wherein the temperature range of the measured molten steel reaches 1510 ℃; alloying: argon is blown from the bottom of the vacuum furnace for protection until the vacuum degree reaches 3000Pa, ferrochromium, ferromanganese, ferromolybdenum and ferrosilicon are sequentially added, smelting is carried out for 12min, after furnace burden is melted uniformly, an aluminum block is added for deoxidation, ferrotitanium and ferrovanadium are sequentially added after 2min, and at the moment, the temperature of the metal liquid reaches 1550 ℃; chemical analysis: sampling the metal liquid, carrying out chemical direct-reading spectral analysis on the sample, and properly adjusting the chemical components of the metal liquid to the range of designed components according to the analysis result; and (3) solidification: after the molten metal reaches the preset chemical composition, the power supply of the smelting furnace is turned off, and the molten metal is cooled along with the furnace for 3 hours; demolding: removing the furnace bottom plate, separating the built-in crucible from the furnace shell, breaking the crucible, taking out the metal ingot and removing the oxidized skin; forging: heating the demoulded metal ingot to 950 ℃ and preserving heat for 30min, and forging the metal ingot into a cast ingot of 800mm multiplied by 50mm multiplied by 60mm after the heat preservation is finished.
(2) Controlled rolling and controlled cooling treatment: heating the forging to 1210 ℃ at a speed of 5 ℃/s, preserving heat for 40min, cooling to a rolling temperature range (980-850 ℃) at a speed of 10 ℃/s, preserving heat for 5s, and then performing three-pass rolling, wherein the strain rate of the first pass rolling is 0.5s-1The deformation is 25 percent, the second pass rolling is carried out after the interval of 120s, and the strain rate of the second pass rolling is 0.5s-1The deformation is 30 percent, the third rolling is carried out after the interval of 120s, and the strain rate of the third rolling is 0.5s-1The deformation amount is 25%; the initial rolling temperature is 980 ℃, and the final rolling temperature is 850 ℃; then carrying out relaxation treatment with the relaxation time of 600 s; then cooling to 610 ℃ at the cooling speed of 30 ℃/s, preserving the heat for 20min, and cooling to room temperature after the heat preservation is finished.
Analysis of an SEM image (figure 3) shows that a large number of (Ti, Mo) C precipitate particles with the size ranging from a few microns to tens of microns are distributed in a matrix of the alloy steel workpiece prepared by the embodiment of the invention; the shape of the abrasive is irregular block, and the abrasive is high in hardness and large in size and is dispersed on the surface of the whole matrix, so that the micro-cutting effect of abrasive particles can be effectively resisted in the abrasive wear process, the direct contact between the matrix and sharp abrasive particles is isolated, and the wear resistance of the material is improved. Analysis of a TEM bright field image (figure 4) shows that VC precipitate particles with the size range of about 100-200 nm are also distributed in the alloy steel workpiece matrix prepared by the embodiment of the invention, the alloy steel workpiece matrix is mainly irregular block-shaped and spherical, and the alloy steel workpiece matrix is mainly produced in the rapid cooling isothermal process; the nanoscale VC particles can improve the yield strength of a metal matrix through the action of hindering dislocation motion, enhance the capacity of the matrix for resisting plastic deformation, provide a better supporting action for large-size (Ti, Mo) C hard particles, and further improve the wear resistance of steel.
Example 2
The preparation method of the wear-resistant alloyed medium carbon steel comprises the following chemical components in percentage by mass: 0.37 percent of C, 0.28 percent of Si, 0.52 percent of Mn, 0.81 percent of Cr, 0.92 percent of Ti, 0.03 percent of V, 0.32 percent of Mo, 0.62 percent of Ni, less than 0.005 percent of P, less than 0.006 percent of S, and the balance of Fe and residual trace impurities; the alloy steel forging size is 600mm multiplied by 40mm multiplied by 50mm, referring to fig. 1, the specific process flow comprises the following steps:
(1) vacuum smelting: preparing materials by adopting a 100kg vacuum induction furnace: weighing pure iron, ferromanganese, ferrochrome, ferrotitanium, ferrosilicon, ferromolybdenum, vanadium particles, a nickel plate and a graphite electrode block according to design components; melting: putting pure iron and a graphite electrode block into a pre-dried built-in crucible, vacuumizing the vacuum induction furnace to 20Pa, and starting smelting until the pure iron is completely melted, wherein the temperature range of the measured molten steel reaches 1530 ℃; alloying: argon is blown from the bottom of the vacuum furnace for protection until the vacuum degree reaches 3200Pa, ferrochromium, ferromanganese, ferromolybdenum and ferrosilicon are sequentially added, smelting is carried out for 10min, after furnace burden is melted uniformly, an aluminum block is added for deoxidation, ferrotitanium and ferrovanadium are sequentially added after 1min, and the temperature of the metal liquid reaches 1530 ℃; chemical analysis: sampling the metal liquid, carrying out chemical direct-reading spectral analysis on the sample, and properly adjusting the chemical components of the metal liquid to the range of designed components according to the analysis result; and (3) solidification: after the molten metal reaches the preset chemical composition, the power supply of the smelting furnace is turned off, and the molten metal is cooled along with the furnace for 4 hours; demolding: removing the bottom plate of the furnace, separating the built-in crucible from the furnace shell, breaking the crucible, taking out the metal ingot and removing the oxidized skin. Forging: and heating the demoulded metal ingot to 960 ℃, preserving heat for 32min, and forging the metal ingot into a casting ingot of 600mm multiplied by 40mm multiplied by 50mm after the heat preservation is finished.
(2) Controlled rolling and controlled cooling treatment: heating the forge piece to 1220 ℃ at the speed of 5 ℃/s, preserving heat for 45min, cooling to a rolling temperature range (980-850 ℃) at the speed of 10 ℃/s, preserving heat for 5s, and then carrying out three-pass rolling, wherein the strain rate of the first pass rolling is 0.65s-1The deformation is 25%, the second pass rolling is carried out after the interval of 100s, and the strain rate of the second pass rolling is 0.65s-1The deformation is 30 percent, the third rolling is carried out after the interval of 100s, and the strain rate of the third rolling is 0.65s-1The deformation amount is 25%; the initial rolling temperature is 980 ℃, and the final rolling temperature is 850 ℃; then carrying out relaxation treatment, wherein the relaxation time is 500 s; cooling to 590 ℃ at a cooling rate of 34 ℃/s, preserving heat for 16min, and then air-cooling to room temperature after the heat preservation is finished
The structure of the alloy medium carbon steel workpiece prepared by the embodiment of the invention is similar to that of the embodiment 1.
Example 3
The preparation method of the wear-resistant alloyed medium carbon steel comprises the following chemical components in percentage by mass: 0.29 percent of C, 0.21 percent of Si, 0.43 percent of Mn, 0.91 percent of Cr, 0.72 percent of Ti, 0.02 percent of V, 0.41 percent of Mo, 0.64 percent of Ni, less than 0.004 percent of P, less than 0.004 percent of S, and the balance of Fe and residual trace impurities. The alloy steel forging has the size of 1000mm multiplied by 40mm, referring to fig. 1, and the specific process flow comprises the following steps:
(1) vacuum smelting: preparing materials by adopting a 100kg vacuum induction furnace: weighing pure iron, ferromanganese, ferrochrome, ferrotitanium, ferrosilicon, ferromolybdenum, vanadium particles, a nickel plate and a graphite electrode block according to design components; melting: filling pure iron and a graphite electrode block into a pre-dried built-in crucible, vacuumizing a vacuum induction furnace to 10Pa, starting smelting until the pure iron is completely melted, and measuring the temperature range of molten steel to 1500 ℃; alloying: argon is blown into the furnace bottom of the vacuum furnace for protection until the vacuum degree reaches 2900Pa, ferrochromium, ferromanganese, ferromolybdenum and ferrosilicon are sequentially added, smelting is carried out for 14min, after furnace materials are uniformly melted, an aluminum block is added for deoxidation, ferrotitanium and ferrovanadium are sequentially added after 1min, and the temperature of the metal liquid reaches 1540 ℃; chemical analysis: sampling the metal liquid, carrying out chemical direct-reading spectral analysis on the sample, and properly adjusting the chemical components of the metal liquid to the range of designed components according to the analysis result; and (3) solidification: after the molten metal reaches the preset chemical composition, the power supply of the smelting furnace is turned off, and the molten metal is cooled along with the furnace for 3.5 hours; demolding: removing the bottom plate of the furnace, separating the built-in crucible from the furnace shell, breaking the crucible, taking out the metal ingot and removing the oxidized skin. Forging: and heating the demoulded metal ingot to 970 ℃, preserving the heat for 36min, and forging the metal ingot into a cast ingot of 1000mm multiplied by 40mm after the heat preservation is finished.
(2) Controlled rolling and controlled cooling treatment: heating the forge piece to 1230 ℃ at a speed of 5 ℃/s, preserving heat for 55min, cooling to a rolling temperature range (980-850 ℃) at a speed of 10 ℃/s, preserving heat for 5s, and then performing three-pass rolling, wherein the strain rate of the first pass rolling is 0.75s-1The deformation is 25%, the second pass rolling is carried out after the interval of 150s, and the strain rate of the second pass rolling is 0.75s-1The deformation is 30 percent, the third rolling is carried out after the interval of 150s, and the strain rate of the third rolling is 0.75s-1The deformation amount is 25%; the initial rolling temperature is 980 ℃, and the final rolling temperature is 850 ℃; then carrying out relaxation treatment with the relaxation time of 450 s; then cooling to 600 ℃ at the cooling speed of 37 ℃/s, preserving the heat for 18min, and cooling to room temperature after the heat preservation is finished.
The structure of the alloy medium carbon steel workpiece prepared by the embodiment of the invention is similar to that of the embodiment 1.
The alloying medium carbon steel matrix structure prepared by the method is dispersed with a large amount of (Ti, Mo) C and a small amount of VC carbide particles with small size, so that the wear resistance of steel is obviously enhanced, and the surface hardness is not obviously improved. The carbon steel sample in the alloy prepared in the example is subjected to an abrasive wear test on a dry sand rubber wheel wear tester, wherein the abrasive particles are quartz sand (300-500 mu m), the load is 45N, the sliding distance is 2000m, and the abrasion loss and the initial hardness are shown in table 1:
TABLE 1
Claims (3)
1. A preparation method of a high wear-resistant alloy steel material is characterized by comprising the following steps: through the design of alloy elements and the combination of smelting and subsequent processing processes, the (Ti, Mo) C particles and fine VC particles are generated in the alloy steel structure; the method specifically comprises the following steps:
(1) vacuum smelting: weighing pure iron, ferromanganese, ferrochrome, ferrotitanium, ferrosilicon, ferromolybdenum, vanadium particles, a nickel plate and a graphite electrode block according to design components, carrying out vacuum melting to obtain an alloy ingot, heating the demoulded alloy ingot to 950 +/-20 ℃, preserving heat for 30-40 min, and forging the alloy ingot into an ingot after the heat preservation is finished;
(2) controlled rolling and controlled cooling treatment: heating the cast ingot to 1200-1250 ℃ at the speed of 5 ℃/s, preserving heat for 40-60 min, cooling to the rolling temperature range of 980-850 ℃ at the speed of 10 ℃/s, preserving heat for 5s, and then performing three-pass rolling, wherein the strain rate of the first pass rolling is 0.5-1 s-1Carrying out second pass rolling after the deformation is 25% and the interval is 60-180 s, wherein the strain rate of the second pass rolling is 0.5-1 s-1The deformation is 30%, the third rolling is carried out after the interval of 60-180 s, and the strain rate of the third rolling is 0.5-1 s-1The deformation amount is 25%; the initial rolling temperature is 960-980 ℃, and the final rolling temperature is 870-850 ℃; then carrying out relaxation treatment for 300-600 s; then cooling to 610 +/-20 ℃ at a cooling rate of 30-40 ℃/s, preserving heat for 15-20 min, and cooling to room temperature after heat preservation is finished;
the alloy steel comprises, by mass, 0.25-0.4% of C, 0.15-0.3% of Si, 0.4-0.65% of Mn, 0.7-0.95% of Cr, 0.7-0.95% of Ti, 0.01-0.05% of V, 0.3-0.45% of Mo, 0.5-0.7% of Ni, less than 0.005% of P, less than 0.006% of S and the balance of Fe and residual trace impurities.
2. The preparation method of the high wear-resistant alloy steel material according to claim 1, characterized in that: the purity of the vanadium particles in the step (1) is not less than 99.97 wt.%.
3. The preparation method of the high wear-resistant alloy steel material according to claim 1, characterized in that: the thickness of the cast ingot forged in the step (1) is 40-80 mm.
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