CN111235484A - High-strength high-hardness low-density steel and preparation method and application thereof - Google Patents

High-strength high-hardness low-density steel and preparation method and application thereof Download PDF

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CN111235484A
CN111235484A CN202010176397.5A CN202010176397A CN111235484A CN 111235484 A CN111235484 A CN 111235484A CN 202010176397 A CN202010176397 A CN 202010176397A CN 111235484 A CN111235484 A CN 111235484A
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treatment
strength
density steel
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CN111235484B (en
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刘日平
王飞
陈博涵
王锁涛
马巍
景勤
张新宇
马明臻
李英梅
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Yanshan University
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/08—Extraction of nitrogen
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/24—Nitriding
    • C23C8/26—Nitriding of ferrous surfaces

Abstract

The invention belongs to the technical field of alloy materials, and particularly relates to high-strength high-hardness low-density steel and a preparation method and application thereof. The high-strength high-hardness low-density steel provided by the invention is obtained by nitriding and denitrating high-strength low-density steel in sequence, and comprises the following components in percentage by mass: 0.7-1.8% of C, 8-12% of Al, 0.3-0.9% of Si, 25-34% of Mn, 0.3-1.2% of Cr, 0.1-0.7% of V, 0.1-0.8% of Ti, 0.7-1.3% of Mo, and the balance of Fe and inevitable impurities. The embodiment results show that the yield strength of the high-strength high-hardness low-density steel obtained by the invention is 870.21-1077.36 MPa, the tensile strength is 950.35-1127.7 MPa, and the hardness is 62-68 HRC; the density is 6.63 to 7.19g/cm3。

Description

High-strength high-hardness low-density steel and preparation method and application thereof
Technical Field
The invention belongs to the technical field of alloy materials, and particularly relates to high-strength high-hardness low-density steel and a preparation method and application thereof.
Background
With the development of national science and technology, the green and high-efficiency become the main melody. In terms of alloy materials, reducing the density of the alloy materials can not only reduce the cost of the alloy materials, but also promote the development of green science and technology. Almost all transmission mechanisms need a shaft part, and under the condition of not changing the size, reducing the density of shaft alloy materials is one of the most effective methods for reducing the weight of shaft parts; the density of the shaft alloy material is reduced, the integral quality of parts can be reduced, and the transmission efficiency of the transmission mechanism can be improved, so that the aim of saving energy is fulfilled. In view of the function of the shaft member, the density is reduced, and at the same time, the strength and hardness of the material need to be ensured, and the existing method for improving the hardness of the alloy material generally forms martensite with higher hardness on the surface of the alloy material through a phase transformation mode so as to improve the hardness of the shaft alloy material and meet the requirement of wear resistance of the surface of the shaft alloy material. However, the Al element added into the low-density steel improves the stacking fault energy of the alloy steel, so that the low-density steel is difficult to have martensitic transformation. How to ensure the strength and the hardness of the alloy steel while reducing the density of the alloy steel is a technical problem which needs to be solved urgently.
Disclosure of Invention
The invention provides high-strength high-hardness low-density steel and a preparation method and application thereof in order to solve the technical problems.
The invention provides high-strength high-hardness low-density steel which is obtained by sequentially nitriding and denitrating the high-strength low-density steel, wherein the high-strength low-density steel comprises the following element components in percentage by mass: 0.7-1.8% of C, 8-12% of Al, 0.3-0.9% of Si, 25-34% of Mn, 0.3-1.2% of Cr, 0.1-0.7% of V, 0.1-0.8% of Ti, 0.7-1.3% of Mo, and the balance of Fe and inevitable impurities.
Preferably, the nitriding treatment temperature is 570-580 ℃, the time is 47-50 h, and the heating rate of heating to the nitriding treatment temperature is 10-20 ℃/min; the temperature of the nitrogen removing treatment is 620-630 ℃, the time is 2-4 h, and the heating rate of the nitrogen removing treatment is 5-10 ℃/min.
The invention also provides a preparation method of the high-strength high-hardness low-density steel, which comprises the following steps:
1) smelting a raw material of high-strength low-density steel to obtain an alloy ingot;
2) carrying out hot forging treatment on the alloy cast ingot to obtain an alloy forging material;
3) carrying out water toughening treatment on the alloy forging material to obtain a water-toughened alloy forging material;
4) sequentially carrying out hot rolling treatment and solid solution treatment on the water-tough alloy forging stock to obtain an alloy plate blank;
5) performing cold rolling treatment on the alloy plate blank to obtain a cold-rolled alloy plate blank;
6) carrying out aging treatment on the cold-rolled alloy plate blank to obtain high-strength low-density steel;
7) and sequentially carrying out nitriding treatment and denitrating treatment on the high-strength low-density steel to obtain the high-strength high-hardness low-density steel.
Preferably, the cold rolling treatment in the step 5) is multi-pass rolling deformation, and the total deformation amount of the cold rolling treatment is 50-60%.
Preferably, the temperature of the hot forging treatment in the step 2) is 1050-1100 ℃, and the time is 20-30 min.
Preferably, the temperature of the water toughening treatment in the step 3) is 1050-1100 ℃, and the time is 25-30 min.
Preferably, the temperature of the hot rolling treatment in the step 4) is 1000-1120 ℃, the hot rolling treatment is multi-pass rolling deformation, and the total deformation amount of the hot rolling treatment is 60-65%.
Preferably, the temperature of the solution treatment in the step 4) is 1000-1100 ℃, and the time is 120-180 min.
Preferably, the temperature of the aging treatment in the step 6) is 350-450 ℃, and the time is 6-12 h.
The invention also provides application of the high-strength high-hardness low-density steel in the technical scheme or the high-strength high-hardness low-density steel obtained by the preparation method in the technical scheme in the aspect of preparing shaft components.
The invention provides high-strength high-hardness low-density steel which is obtained by sequentially nitriding and denitrating the high-strength low-density steel, wherein the high-strength low-density steel comprises the following element components in percentage by mass: 0.7-1.8% of C, 8-12% of Al, 0.3-0.9% of Si, 25-34% of Mn, 0.3-1.2% of Cr, 0.1-0.7% of V, 0.1-0.8% of Ti, 0.7-1.3% of Mo, and the balance of Fe and inevitable impurities. The aluminum has lower density, the invention adds a large amount of Al element in the alloy steel to reduce the density of the alloy steel, and the material density is reduced by 0.101g/cm for every 1 percent of Al element3(ii) a Adding Mn element as austenite stabilizing element into alloy steel to promote austeniteThe plasticity of the alloy steel is ensured, the addition of C element also plays a role in stabilizing austenite, and simultaneously improves the plasticity of the alloy steel, and in addition, the density of the alloy steel is reduced by 0.41g/cm for every 1 percent of C element is added3(ii) a The invention reduces the density of the alloy steel under the combined action of the Al, Mn and C with specific contents, and simultaneously improves the plasticity of the alloy steel. The V and Ti elements are added into the alloy steel, so that the grain size can be obviously reduced, and the carbide formed by the vanadium and the titanium has high dissolution temperature due to the strong affinity with carbon; in the heating process, the undissolved carbide small particles increase the nucleation center of austenite and prevent the movement or combination of austenite grain boundaries at high temperature, the austenite grains begin to grow rapidly until the carbide small particles are completely dissolved in a solid solution, the addition of V, Ti element reduces the size of alloy steel grains, and the mechanical property of the material is obviously improved along with the increase of V, Ti; mo element is added into the alloy steel, so that the tempering brittleness is inhibited, and the toughness and the mechanical strength of the alloy steel are improved. The invention improves the strength of the alloy steel while reducing the density of the alloy steel material under the combined action of all the element components; meanwhile, the invention combines nitriding treatment to enable N atoms to permeate into the surface of the material, and the N atoms and aluminum and chromium form aluminum nitride and chromium nitride, so that the surface hardness of the material is greatly improved. The embodiment results show that the yield strength of the high-strength high-hardness low-density steel obtained by the invention is 870.21-1077.36 MPa, the tensile strength is 950.35-1127.7 MPa, and the hardness is 62-68 HRC; the density is 6.63 to 7.19g/cm3。
The invention also provides a preparation method of the high-strength high-hardness low-density steel, which comprises the following steps: smelting a raw material of high-strength low-density steel to obtain an alloy ingot; carrying out hot forging treatment on the alloy cast ingot to obtain an alloy forging material; carrying out water toughening treatment on the alloy forging material to obtain a water-toughened alloy forging material; sequentially carrying out hot rolling treatment and solid solution treatment on the water-tough alloy forging stock to obtain an alloy plate blank; performing cold rolling treatment on the alloy plate blank to obtain a cold-rolled alloy plate blank; carrying out aging treatment on the cold-rolled alloy plate blank to obtain high-strength low-density steel; and sequentially carrying out nitriding treatment and denitrating treatment on the high-strength low-density steel to obtain the high-strength high-hardness low-density steel. According to the invention, a large amount of dislocation tangles can be generated in the steel material through cold rolling treatment, and the tensile strength of the alloy steel material is improved due to the structure of the large amount of dislocation tangles; meanwhile, the invention combines nitriding treatment to enable N atoms to permeate into the surface of the material, and the N atoms and aluminum and chromium form aluminum nitride and chromium nitride, so that the surface hardness of the material is greatly improved.
Drawings
FIG. 1 is a schematic drawing of dimensions of a tensile specimen, wherein the dimensions are in mm;
FIG. 2 is a metallographic optical micrograph of a high-strength, high-hardness, low-density steel obtained in example 1 of the present invention;
FIG. 3 is a metallographic optical micrograph of a comparative 40Cr steel;
FIG. 4 is a scanning image of a nitrided layer of the high strength, high hardness, low density steel obtained in example 1;
FIG. 5 is a line scan of the nitrided layer of the high strength, high hardness, low density steel obtained in example 1.
Detailed Description
The invention provides high-strength high-hardness low-density steel which is obtained by sequentially nitriding and denitrating the high-strength low-density steel, wherein the high-strength low-density steel comprises the following element components in percentage by mass: 0.7-1.8% of C, 8-12% of Al, 0.3-0.9% of Si, 25-34% of Mn, 0.3-1.2% of Cr, 0.1-0.7% of V, 0.1-0.8% of Ti, 0.7-1.3% of Mo, and the balance of Fe and inevitable impurities.
The high-strength high-hardness low-density steel provided by the invention is obtained by sequentially carrying out nitriding and denitrating treatment on the high-strength low-density steel. In the present invention, the atmosphere of the nitriding treatment is preferably ammonia; the temperature of the nitriding treatment is preferably 570-580 ℃, more preferably 575 ℃, the time of the nitriding treatment is preferably 47-50 h, more preferably 48h, and the temperature rise rate of raising the temperature to the nitriding treatment temperature is preferably 10-20 ℃/min, more preferably 15 ℃/min; the preferred atmosphere of the nitrogen removing treatment is ammonia gas, the preferred temperature of the nitrogen removing treatment is 620-630 ℃, the more preferred temperature is 624 ℃, the preferred time of the nitrogen removing treatment is 2-4 h, the more preferred time is 3h, and the heating rate of the temperature rising to the nitrogen removing treatment temperature is 5-10 ℃/min, and the more preferred time is 6 ℃/min. The invention has no special requirements on equipment for nitriding treatment, and the embodiment of the invention adopts a well type nitriding furnace. The nitrogen atoms are permeated into the surface of the alloy steel through nitriding treatment and denitriding treatment and react with aluminum and chromium in the alloy steel material to form aluminum nitride and chromium nitride, so that the hardness of the surface of the alloy steel is improved. The nitriding treatment improves the hardness of the alloy steel and simultaneously improves the brittleness of the alloy steel, and the nitriding treatment can reduce the brittleness of the alloy steel.
In the invention, the high-strength low-density steel comprises 0.7-1.8% of C, preferably 1.4% of C by mass percentage. In the invention, the addition of the element C can play a role in stabilizing austenite and improve the plasticity of the alloy steel; meanwhile, carbon and Fe form a solid solution, the carbon is dissolved in the crystal lattice in a solid manner, the crystal lattice constant is increased, the mass of the alloy steel is unchanged, the density of the alloy steel is reduced, and the density of the material is reduced by 0.41g/cm when 1% of C element is added3。
The high-strength low-density steel comprises 8-12% of Al, and preferably 10% of Al. According to the invention, a large amount of Al element is added into the alloy steel, so that the density of the alloy steel is reduced, and the material density is reduced by 0.101g/cm when 1% of Al is added3。
The high-strength low-density steel comprises 0.3-0.9% of Si, preferably 0.6% by mass. In the invention, the Si generates replacement solid solution strengthening in the steel, causes spherical symmetric distortion of iron, and generates elastic interaction with edge dislocation to stop dislocation movement, thereby remarkably improving the tensile strength of the steel.
The high-strength low-density steel comprises, by mass, 25-34% of Mn, and preferably 30%. According to the invention, Mn is added into the alloy steel to promote the austenite structure, so that the plasticity of the alloy steel is ensured.
The high-strength low-density steel comprises 0.3-1.2% of Cr by mass percentage, and preferably 0.7%.
According to the mass percentage, the high-strength low-density steel comprises 0.1-0.7% of V, and preferably 0.4%.
The high-strength low-density steel comprises 0.1-0.8% of Ti by mass percentage, and preferably 0.5% of Ti by mass percentage.
The V and Ti elements added into the alloy steel have strong affinity with carbon in the alloy steel, and the formed carbide has high dissolution temperature; during heating, the undissolved small carbide particles increase the nucleation center of austenite and prevent the movement or combination of austenite grain boundaries at high temperature, the austenite grains do not begin to grow rapidly until the small carbide particles are completely dissolved in solid solution, the V, Ti element reduces the size of alloy steel grains, and the mechanical property of the material is obviously improved along with the increase of V, Ti.
The high-strength low-density steel comprises 0.7-1.3% of Mo, and preferably 1% of Mo. In the invention, the Mo element can reduce the tempering brittleness of the steel material and improve the mechanical strength of the steel.
According to the mass percentage, the high-strength low-density steel comprises the balance of Fe and inevitable impurities. In the present invention, the impurities include S and P, and the content of S is preferably not more than 0.005%, and the content of P is preferably not more than 0.015%.
The invention limits the content of each element within a specific range, obtains high-strength low-density steel under the combined action of each element, combines nitriding and denitrating treatment to obtain high-strength high-hardness low-density steel, and the density of the high-strength high-hardness low-density steel is 6.63-7.19 g/cm3The yield strength is 870.21-1077.36 MPa, the tensile strength is 950.35-1127.79 MPa, and the hardness is 62-68 HRC.
The invention also provides a preparation method of the high-strength high-hardness low-density steel, which comprises the following steps:
1) smelting a raw material of high-strength low-density steel to obtain an alloy ingot;
2) carrying out hot forging treatment on the alloy cast ingot to obtain an alloy forging material;
3) carrying out water toughening treatment on the alloy forging material to obtain a water-toughened alloy forging material;
4) sequentially carrying out hot rolling treatment and solid solution treatment on the water-tough alloy forging stock to obtain an alloy plate blank;
5) performing cold rolling treatment on the alloy plate blank to obtain a cold-rolled alloy plate blank;
6) carrying out aging treatment on the cold-rolled alloy plate blank to obtain high-strength low-density steel;
7) and sequentially carrying out nitriding treatment and denitrating treatment on the high-strength low-density steel to obtain the high-strength high-hardness low-density steel.
The invention smelts the raw material of the high-strength low-density steel to obtain the alloy cast ingot. In the embodiment of the invention, the raw materials of the high-strength low-density steel are preferably carbon, aluminum, silicon, manganese, chromium, vanadium, titanium, molybdenum and iron, wherein an aluminum source is preferably an aluminum rod with the diameter of 25mm, an iron source is preferably an iron rod with the diameter of 25mm, and other raw materials are all blocky.
According to the invention, the raw materials are preferably cleaned before smelting, the cleaning preferably comprises acetone washing and alcohol washing which are sequentially carried out, and the acetone washing and the alcohol washing are preferably carried out in an ultrasonic cleaning mode; the acetone washing can remove oil contamination impurities on the surface of the raw material, the alcohol washing can remove residual acetone solution on the surface of the raw material, and the dried raw material is obtained by alcohol volatilization; in the present invention, the alcohol is preferably industrial alcohol.
In the invention, the smelting is preferably carried out in a vacuum induction furnace, the magnesia crucible in the vacuum induction smelting furnace is preferably cleaned before the smelting, and the invention has no special requirement on the cleaning mode as long as the residue in the magnesia crucible can be cleaned. In the present invention, the smelting preferably comprises the steps of:
putting Al, Mn, Fe and Si in the raw materials into a magnesia crucible in a vacuum induction furnace, and putting V, Ti, Cr, C and Mo in the raw materials into a secondary hopper of the vacuum induction furnace;
vacuumizing the vacuum induction furnace until the vacuum degree is 0.009-0.02 MPa, and then filling protective gas into the vacuum induction furnace until the vacuum degree is 0.04-0.06 MPa;
setting the power of the vacuum induction furnace to 5kW, and heating for 5-10 min;
setting the power of the vacuum induction furnace to 10kW, and heating for 5-10 min;
setting the power of the vacuum induction furnace to be 20kW, heating for 10-15 min, and pouring the raw materials in the secondary charging hopper into a magnesia crucible;
setting the power of the vacuum induction furnace to 40kW, and heating for 20-30 min to obtain molten steel.
In the present invention, the protective gas is preferably high-purity argon gas, and the purity of the high-purity argon gas is preferably 99.9%. In the invention, in the heating process of the vacuum induction furnace, the molten metal can be stirred along one direction, so that all components in the molten steel are more uniform.
After the molten steel is obtained, the molten steel is preferably poured into a mold and naturally cooled to room temperature, so that the alloy ingot is obtained.
The method preferably cleans the magnesia crucible in the vacuum induction melting furnace before melting, has no special requirements on the cleaning mode, and only needs to clean the residues in the magnesia crucible.
After the alloy ingot is obtained by smelting, the alloy ingot is subjected to hot forging treatment to obtain the alloy forging material. In the invention, the hot forging treatment is preferably carried out in a muffle furnace, the invention has no special requirements on the type and the source of the muffle furnace, and in the embodiment of the invention, the muffle furnace is a muffle furnace with the type of KL-13 produced by Kai constant electro-thermal technology Limited of Tianjin. In the invention, the temperature of the hot forging treatment is preferably 1050-1100 ℃, more preferably 1080 ℃, the time of the hot forging treatment is preferably 20-30 min, more preferably 25min, and the heating rate of heating to the temperature of the hot forging treatment is preferably 5-10 ℃/min.
In the present invention, the hot forging treatment is preferably performed by using a 150kg hammer, and the number of times of the hot forging treatment is preferably 5 to 6, and may be specifically 5 or 6. The invention has no special requirements on the shape of the alloy forging material, and in the embodiment of the invention, the alloy forging material is a round bar with the diameter of 70 mm.
After the alloy forging material is obtained, the invention carries out water toughening treatment on the alloy forging material to obtain the water-toughened alloy forging material. In the invention, the temperature of the water toughening treatment is 1050-1100 ℃, more preferably 1090 ℃, and the time is preferably 25-30 min, more preferably 28 min. The specific operation of the water toughening treatment is not particularly limited, and a person skilled in the art can carry out the water toughening treatment according to the conventional operation, in the embodiment of the invention, the specific step of the water toughening treatment is preferably to heat the alloy forging material to 1050-1100 ℃, keep the temperature for 25-30 min, and then quench the alloy forging material in water, and the quenching water is preferably normal temperature water.
After the water-tough alloy forging stock is obtained, the water-tough alloy forging stock is subjected to hot rolling treatment and solution treatment in sequence to obtain an alloy plate blank. In the invention, the water-tough alloy forging is preferably cut into steel blocks of 50 (length) × 30 (width) × 20 (thickness) mm before hot rolling treatment; the temperature of the hot rolling treatment is preferably 1000-1120 ℃, and more preferably 1070 ℃; the heating rate of heating to the hot rolling treatment temperature is preferably 10-20 ℃/min; after heating to the hot rolling treatment temperature, the alloy ingot is preferably subjected to heat preservation treatment at the hot rolling treatment temperature so as to make the temperature of each part of the alloy ingot uniform, and the time of the heat preservation treatment is preferably 2 hours. In the invention, the heating and temperature rise are preferably carried out in a muffle furnace, the source and the model of the muffle furnace are not particularly limited, and the muffle furnace known by the person skilled in the art can be adopted; in the embodiment of the invention, the muffle furnace is preferably a muffle furnace with a model number of KL-13, which is manufactured by Kai constant electro-thermal technology of Tianjin. According to the invention, the alloy ingot after heat preservation treatment is preferably taken out quickly for hot rolling treatment, so that the temperature drop of the sample after the sample is separated from the muffle furnace is avoided, and in the invention, the temperature drop is preferably 10-20 ℃, and more preferably 12-15 ℃.
In the invention, the hot rolling treatment is preferably multi-pass rolling deformation, and the pass reduction in the multi-pass rolling deformation process is preferably 1-3 mm, and more preferably 1.6-2.0 mm; after each pass of rolling, the product after the previous pass of rolling is preferably put into a muffle furnace again to be heated to the hot rolling treatment temperature, the temperature is kept at the hot rolling treatment temperature for 10min, and then the next rolling is carried out. In the present invention, the total deformation amount of the hot rolling treatment is preferably 60 to 65%. In the present invention, the multi-pass rolling deformation is preferably performed on a double-roller mill, and the source and the type of the double-roller mill are not particularly limited in the present invention, and a double-roller mill known to those skilled in the art can be used. In the invention, the number of times of the multi-pass rolling deformation is preferably 4 to 8, and may be 4, 5, 6, 7 or 8.
In the present invention, the solution treatment is preferably performed on the hot-rolled product after the end of the last pass of rolling, and the solution treatment preferably includes the steps of: heating the final hot rolling treatment product to 1000-1100 ℃, preserving the heat for 120-180 min, and then performing water quenching; the temperature of the water for water quenching is preferably room temperature.
After the alloy plate blank is obtained, the cold rolling treatment is carried out on the alloy plate blank to obtain the cold-rolled alloy plate blank. In the present invention, the cold rolling treatment is preferably performed at room temperature, and the present invention has no particular requirement on the equipment for the cold rolling treatment, and a cold rolling mill well known to those skilled in the art may be used, and a twin rolling mill is used in the embodiment of the present invention.
In the invention, the cold rolling treatment is preferably multi-pass and multi-pass rolling deformation, and the pass reduction in the multi-pass rolling deformation process is preferably 0.07-0.09 mm; in the present invention, the total deformation amount of the cold rolling treatment is preferably 50 to 60%. In the present invention, the multi-pass rolling deformation is preferably performed on a double-roller mill, the source and type of the double-roller mill are not particularly limited, and a double-roller mill known to those skilled in the art may be used, and the number of the multi-pass rolling deformation is preferably 40 to 80, more preferably 44 to 47, and most preferably 46.
In the invention, the cold rolling treatment generates a large amount of dislocation tangle in the cold-rolled alloy plate blank, and the large amount of dislocation prevents the slip from proceeding, thereby improving the tensile strength of the cold-rolled alloy plate blank.
After the cold-rolled alloy plate blank is obtained, the invention carries out aging treatment on the cold-rolled alloy plate blank to obtain the high-strength low-density steel. In the invention, the aging treatment is preferably carried out in a muffle furnace, the invention has no special requirements on the type and the source of the muffle furnace, and in the embodiment of the invention, the muffle furnace is a muffle furnace with the type of KL-13 produced by Kai constant electro-thermal technology Limited of Tianjin. In the invention, the temperature of the aging treatment is preferably 350-450 ℃, and more preferably 430 ℃; the time of the aging treatment is preferably 6-12 h, and more preferably 10 h; the heating rate of the temperature rise to the aging treatment temperature is preferably 5-10 ℃/min.
After the high-strength low-density steel is obtained, nitriding treatment and denitrating treatment are sequentially carried out on the high-strength low-density steel, and the high-strength high-hardness low-density steel is obtained. According to the invention, before nitriding treatment, high-strength low-density steel is preferably cut into circular plates with the diameter of 50mm by using linear cutting, and the circular plates are respectively ground on No. 150-No. 800 SiC abrasive paper until the surfaces are smooth and have no obvious scratches. In the present invention, the nitriding and denitrating operations are as described above and will not be described herein.
The invention also provides application of the high-strength high-hardness low-density steel in the technical scheme or the high-strength high-hardness low-density steel obtained by the preparation method in the technical scheme in the aspect of preparing shaft components.
In order to further illustrate the present invention, the following detailed description of a high strength, high hardness and low density steel provided by the present invention, its preparation method and application are provided in conjunction with the accompanying drawings and examples, which should not be construed as limiting the scope of the present invention.
Example 1
According to the mass percentage, 0.7 percent of carbon, 25 percent of manganese, 8 percent of aluminum rod with the diameter of 25mm, 0.3 percent of silicon, 0.3 percent of chromium, 0.1 percent of vanadium, 0.1 percent of titanium, 0.7 percent of molybdenum and the balance of iron rod with the diameter of 25mm are taken.
After the raw materials are subjected to ultrasonic cleaning treatment in acetone and alcohol in sequence, putting aluminum, manganese, iron and silicon into a magnesia crucible in a vacuum induction furnace, and putting vanadium, titanium, chromium, carbon and molybdenum in the raw materials into a secondary hopper of the vacuum induction furnace; vacuumizing the vacuum induction furnace to the vacuum degree of 0.02MPa, and then filling high-purity argon into the vacuum induction furnace to the vacuum degree of 0.04 MPa; setting the power of the vacuum induction furnace to 5kW, and heating for 5 min; setting the power of the vacuum induction furnace to 10kW, and heating for 5 min; setting the power of the vacuum induction furnace to be 20kW, heating for 10min, and pouring the raw materials in the secondary charging hopper into a magnesia crucible; setting the power of the vacuum induction furnace to 40kW, heating for 30min to obtain molten steel, and then pouring the molten steel into a mold to naturally cool to room temperature to obtain an alloy ingot;
placing the alloy cast ingot in a muffle furnace, heating to 1050 ℃ at a heating rate of 10 ℃/min, preserving heat for 20min, forging by using a 150kg forging hammer, and forging for 5 times to obtain a round bar with the diameter of 70 mm;
and (3) placing the round bar with the diameter of 70mm in a muffle furnace at 1050 ℃ for heat preservation for 25min, and then cooling to room temperature by water to obtain the water-tough alloy forging material.
Cutting the water-tough alloy forging stock into steel blocks with the thickness of 50 (length) × 30 (width) × 20 (thickness), then putting the steel blocks into a muffle furnace, heating to 1000 ℃ at the heating rate of 10 ℃/min, preserving heat for 2h, and then quickly taking out the material for first hot rolling; and after the first rolling is finished, putting the product subjected to the first rolling into a muffle furnace, reheating to 1000 ℃, preserving heat for 10min, performing second hot rolling, and repeating the operation for 6 times to obtain a hot rolling treatment product with the thickness of 8mm, wherein the pass reduction is 2mm, and the total deformation of the hot rolling treatment reaches 60%. And after the final pass rolling, carrying out solid solution treatment, carrying out heat preservation for 120min at the temperature of 1000 ℃, then carrying out water quenching, and taking out after cooling to normal temperature to obtain the alloy plate blank.
And (3) carrying out cold rolling treatment on the alloy plate blank on a double-roller mill for 44 times to obtain a cold-rolled alloy plate blank with the thickness of 4mm, wherein the total deformation of the cold rolling treatment is 50%, and the pass reduction is 0.09 mm.
Placing the cold-rolled alloy plate blank into a muffle furnace, heating to 350 ℃ at the heating rate of 10 ℃/min, preserving heat for 6 hours, and cooling to room temperature in an air cooling mode to obtain high-strength low-density steel;
cutting the high-strength low-density steel into circular plates with the diameter of 50mm by utilizing linear cutting, respectively grinding the circular plates on No. 150-800 # SiC water-grinding abrasive paper until the surfaces are smooth and have no obvious scratches, putting the ground circular plates of the high-strength low-density steel into a well-type nitriding furnace with the atmosphere of ammonia, heating to 570 ℃ at the heating rate of 10 ℃/min, preserving heat for 47 hours, heating to 620 ℃ at the heating rate of 5 ℃/min, preserving heat for 2 hours, and cooling to room temperature along with the furnace to obtain the high-strength high-hardness low-density steel.
Example 2
According to the mass percentage, 1.4 percent of carbon, 30 percent of manganese, 10 percent of aluminum rod with the diameter of 25mm, 0.6 percent of silicon, 0.7 percent of chromium, 0.4 percent of vanadium, 0.5 percent of titanium, 1 percent of molybdenum and the balance of iron rod with the diameter of 25mm are taken.
After the raw materials are subjected to ultrasonic cleaning treatment in acetone and alcohol in sequence, putting aluminum, manganese, iron and silicon into a magnesia crucible in a vacuum induction furnace, and putting vanadium, titanium, chromium, carbon and molybdenum in the raw materials into a secondary hopper of the vacuum induction furnace; vacuumizing the vacuum induction furnace to the vacuum degree of 0.02MPa, and then filling high-purity argon into the vacuum induction furnace to the vacuum degree of 0.04 MPa; setting the power of the vacuum induction furnace to 5kW, and heating for 7 min; setting the power of the vacuum induction furnace to 10kW, and heating for 7 min; setting the power of the vacuum induction furnace to be 20kW, heating for 10min, and pouring the raw materials in the secondary charging hopper into a magnesia crucible; setting the power of the vacuum induction furnace to 40kW, heating for 20min to obtain molten steel, and then pouring the molten steel into a mold to naturally cool to room temperature to obtain an alloy ingot;
placing the alloy cast ingot in a muffle furnace, heating to 1080 ℃ at a heating rate of 10 ℃/min, preserving heat for 25min, forging by adopting a 150kg forging hammer, and forging for 5 times to obtain a round bar with the diameter of 70 mm;
and (3) placing the round bar with the diameter of 70mm in a muffle furnace with the temperature of over 1090 ℃ for heat preservation for 28min, and then cooling the round bar to room temperature by water to obtain the water-tough alloy forging material.
Cutting the water-tough alloy forging stock into steel blocks with the thickness of 50 (length) × 30 (width) × 20 (thickness), then putting the steel blocks into a muffle furnace, heating to 1070 ℃ at the heating rate of 10 ℃/min, preserving heat for 2h, and then quickly taking out the material for first hot rolling; and after the first rolling is finished, putting the product subjected to the first rolling into a muffle furnace, reheating to 1070 ℃ and preserving heat for 10min, carrying out second hot rolling, and repeating the operation for 8 times to obtain a hot rolling treatment product with the thickness of 7.2mm, wherein the pass reduction is 1.6mm, and the total deformation of the hot rolling treatment is 64%. And after the final pass rolling, carrying out solid solution treatment, carrying out heat preservation for 150min at 1050 ℃, then carrying out water quenching, and taking out after cooling to normal temperature to obtain the alloy plate blank.
And (3) carrying out cold rolling treatment on the alloy plate blank on a double-roller mill for 46 times to obtain a cold-rolled alloy plate blank with the thickness of 3.1mm, wherein the total deformation of the cold rolling treatment is 57%, and the pass reduction is 0.09 mm.
Placing the cold-rolled alloy plate blank into a muffle furnace, heating to 430 ℃ at a heating rate of 10 ℃/min, preserving heat for 10h, and cooling to room temperature in an air cooling mode to obtain high-strength low-density steel;
cutting the high-strength low-density steel into circular plates with the diameter of 50mm by utilizing linear cutting, respectively grinding the circular plates on No. 150-800 # SiC water grinding abrasive paper until the surfaces are smooth and have no obvious scratches, putting the ground circular plates of the high-strength low-density steel into a well-type nitriding furnace with the atmosphere of ammonia, heating to 575 ℃ at the heating rate of 15 ℃/min, preserving heat for 48 hours, heating to 624 ℃ at the heating rate of 6 ℃/min, preserving heat for 3 hours, and cooling to room temperature along with the furnace to obtain the high-strength high-hardness low-density steel.
Example 3
According to the mass percentage, 1.8 percent of carbon, 34 percent of manganese, 12 percent of aluminum rod with the diameter of 25mm, 0.9 percent of silicon, 1.2 percent of chromium, 0.7 percent of vanadium, 0.8 percent of titanium, 1.3 percent of molybdenum and the balance of iron rod with the diameter of 25mm are taken.
After the raw materials are subjected to ultrasonic cleaning treatment in acetone and alcohol in sequence, putting aluminum, manganese, iron and silicon into a magnesia crucible in a vacuum induction furnace, and putting vanadium, titanium, chromium, carbon and molybdenum in the raw materials into a secondary hopper of the vacuum induction furnace; vacuumizing the vacuum induction furnace until the vacuum degree is 0.009MPa, and then filling high-purity argon into the vacuum induction furnace until the vacuum degree is 0.05 MPa; setting the power of the vacuum induction furnace to 5kW, and heating for 7 min; setting the power of the vacuum induction furnace to 10kW, and heating for 7 min; setting the power of the vacuum induction furnace to be 20kW, heating for 13min, and pouring the raw materials in the secondary charging hopper into a magnesia crucible; setting the power of the vacuum induction furnace to 40kW, heating for 25min to obtain molten steel, and then pouring the molten steel into a mold to naturally cool to room temperature to obtain an alloy ingot; magnetic stirring is accompanied in the heating process;
placing the alloy cast ingot in a muffle furnace, heating to 1100 ℃ at a heating rate of 10 ℃/min, preserving heat for 30min, forging by adopting a 150kg forging hammer, and forging for 5 times to obtain a round bar with the diameter of 70 mm;
and (3) placing the round bar with the diameter of 70mm in a muffle furnace at the temperature of 1100 ℃ for heat preservation for 30min, and then cooling the round bar to room temperature by water to obtain the water-tough alloy forging material.
Cutting the water-tough alloy forging stock into steel blocks with the thickness of 50 (length) × 30 (width) × 20 (thickness), then putting the steel blocks into a muffle furnace, heating to 1120 ℃ at the heating rate of 10 ℃/min, preserving heat for 2h, and then quickly taking out the material for first hot rolling; and after the first rolling is finished, putting the product subjected to the first rolling into a muffle furnace, reheating to 1120 ℃, preserving heat for 10min, carrying out second hot rolling, and repeating the operation for 8 times to obtain a hot rolling treatment product with the thickness of 7mm, wherein the pass reduction is 1.625mm, and the total deformation of the hot rolling treatment is 65%. And after the final pass rolling, carrying out solid solution treatment, carrying out heat preservation for 180min at the temperature of 1050 ℃, then carrying out water quenching, and taking out after cooling to normal temperature to obtain the alloy plate blank.
And (3) carrying out cold rolling treatment on the alloy plate blank on a double-roller mill for 47 times to obtain a cold-rolled alloy plate blank with the thickness of 2.8mm, wherein the total deformation of the cold rolling treatment is 60%, and the pass reduction is 0.089 mm.
Placing the cold-rolled alloy plate blank into a muffle furnace, heating to 450 ℃ at a heating rate of 10 ℃/min, preserving heat for 12h, and cooling to room temperature in an air cooling mode to obtain high-strength low-density steel;
cutting the high-strength low-density steel into circular plates with the diameter of 50mm by utilizing linear cutting, respectively grinding the circular plates on No. 150-800 # SiC water-grinding abrasive paper until the surfaces are smooth and have no obvious scratches, putting the ground circular plates of the high-strength low-density steel into a well-type nitriding furnace with the atmosphere of ammonia, heating to 580 ℃ at the heating rate of 10 ℃/min, preserving heat for 50h, heating to 630 ℃ at the heating rate of 10 ℃/min, preserving heat for 4h, and cooling to room temperature along with the furnace to obtain the high-strength high-hardness low-density steel.
Three tensile samples shown in fig. 1 were cut out of the high-strength low-density steels and the comparative material 40Cr steels in examples 1 to 3 by wire cutting, and uniaxial tensile tests were performed on an Instron5982 universal material testing machine according to GBT228-2002, and the test results are shown in table 1 by taking the average values.
Three rectangular parallelepipeds of 10 × 2mm were cut out by wire cutting at different positions of the high-strength low-density steels and the comparative 40Cr steels in examples 1 to 3, respectively, and the densities thereof were measured by archimedes' principle, and the average values thereof were obtained, and the results thereof are shown in table 1.
The hardness of the high-strength, high-hardness and low-density steel obtained in examples 1 to 3 and the 40Cr steel as a comparative material were tested by using a conventional rockwell hardness tester, the hardness test end of the sample to be tested was polished to be bright by using 150# to 2000# sandpaper and polished on a polishing machine before the test, and the opposite side of the test end was polished by using 150# sandpaper until the surface had no oxide layer, so as to reduce the influence of the oxide layer on the hardness of the material itself, and the obtained results are listed in table 1.
TABLE 1 Performance test results for inventive examples 1-3 and comparative materials
Figure BDA0002410968300000131
The results in the table 1 show that the high-strength high-hardness low-density steel provided by the invention has lower density, and the density is reduced by 12.73-23.64% compared with the density of 40Cr of a comparative material; the high-strength high-hardness low-density steel provided by the invention has higher mechanical properties, the yield strength of the steel is 1077.36MPa, and the yield strength of the steel is improved by 10.85-37.24% compared with that of a contrast material 40 Cr; the tensile strength of the material is 1127.79MPa, and is improved by 21.03-39.23% compared with the tensile strength of a contrast material 40 Cr.
Metallographic structure observation is carried out on the high-strength low-density steel and the comparative material 40Cr steel in the embodiment 1 to obtain figures 2 and 3, it can be known from figures 2 and 3 that the metallographic phase of the high-strength low-density steel obtained by the invention is mainly an austenite phase, compared with the comparative material 40Cr, crystal grains have an obvious refining trend, and according to a Hall-Petch formula, the tensile strength of the steel material is enhanced along with the refining of the crystal grains.
The scanning pattern of the nitrided layer and the line scanning pattern of the nitrided layer obtained by scanning the high-strength, high-hardness and low-density steel obtained in example 1 by using a Hitachi S-3400 scanning electron microscope are shown in FIGS. 4 and 5. From fig. 4 and 5, it can be seen that a nitrided layer is formed in the steel material after the nitriding treatment, and the nitrogen element in the nitrided layer and the aluminum and the chromium in the steel material form aluminum nitride and chromium nitride, which significantly improves the surface hardness of the steel material.
Although the present invention has been described in detail with reference to the above embodiments, it is only a part of the embodiments of the present invention, not all of the embodiments, and other embodiments can be obtained without inventive step according to the embodiments, and the embodiments are within the scope of the present invention.

Claims (10)

1. The high-strength high-hardness low-density steel is obtained by sequentially carrying out nitriding and denitrating treatment on high-strength low-density steel, and comprises the following element components in percentage by mass: 0.7-1.8% of C, 8-12% of Al, 0.3-0.9% of Si, 25-34% of Mn, 0.3-1.2% of Cr, 0.1-0.7% of V, 0.1-0.8% of Ti, 0.7-1.3% of Mo, and the balance of Fe and inevitable impurities.
2. The high-strength high-hardness low-density steel according to claim 1, wherein the nitriding treatment temperature is 570-580 ℃, the time is 47-50 hours, and the temperature rise rate of the nitriding treatment temperature is 10-20 ℃/min; the temperature of the nitrogen removing treatment is 620-630 ℃, the time is 2-4 h, and the heating rate of the nitrogen removing treatment is 5-10 ℃/min.
3. A method for producing a high-strength high-hardness low-density steel as claimed in claim 1 or 2, comprising the steps of:
1) smelting a raw material of high-strength low-density steel to obtain an alloy ingot;
2) carrying out hot forging treatment on the alloy cast ingot to obtain an alloy forging material;
3) carrying out water toughening treatment on the alloy forging material to obtain a water-toughened alloy forging material;
4) sequentially carrying out hot rolling treatment and solid solution treatment on the water-tough alloy forging stock to obtain an alloy plate blank;
5) performing cold rolling treatment on the alloy plate blank to obtain a cold-rolled alloy plate blank;
6) carrying out aging treatment on the cold-rolled alloy plate blank to obtain high-strength low-density steel;
7) and sequentially carrying out nitriding treatment and denitrating treatment on the high-strength low-density steel to obtain the high-strength high-hardness low-density steel.
4. The method for preparing the high-strength high-hardness low-density steel according to claim 3, wherein the cold rolling treatment in the step 5) is multi-pass rolling deformation, and the total deformation amount of the cold rolling treatment is 50-60%.
5. The method for preparing the high-strength high-hardness low-density steel according to claim 3, wherein the temperature of the hot forging treatment in the step 2) is 1050-1100 ℃ and the time is 20-30 min.
6. The method for preparing the high-strength high-hardness low-density steel according to claim 3, wherein the temperature of the water toughening treatment in the step 3) is 1050-1100 ℃ and the time is 25-30 min.
7. The method for preparing the high-strength high-hardness low-density steel according to claim 3, wherein the temperature of the hot rolling treatment in the step 4) is 1000 to 1120 ℃, the hot rolling treatment is multi-pass rolling deformation, and the total deformation amount of the hot rolling treatment is 60 to 65 percent.
8. The method for preparing high-strength high-hardness low-density steel according to claim 3, wherein the temperature of the solution treatment in the step 4) is 1000 to 1100 ℃ and the time is 120 to 180 min.
9. The method for preparing the high-strength high-hardness low-density steel according to claim 3, wherein the temperature of the aging treatment in the step 6) is 350-450 ℃ and the time is 6-12 hours.
10. Use of the high-strength high-hardness low-density steel according to any one of claims 1 to 2 or the high-strength high-hardness low-density steel obtained by the preparation method according to any one of claims 3 to 9 in the preparation of shaft components.
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