CN116179943A - Nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel and preparation method thereof - Google Patents

Nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel and preparation method thereof Download PDF

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CN116179943A
CN116179943A CN202211682701.9A CN202211682701A CN116179943A CN 116179943 A CN116179943 A CN 116179943A CN 202211682701 A CN202211682701 A CN 202211682701A CN 116179943 A CN116179943 A CN 116179943A
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steel
equal
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迟宏宵
马党参
周健
樊译
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Central Iron and Steel Research Institute
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    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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    • C21D2211/00—Microstructure comprising significant phases
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    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
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    • Y02P10/20—Recycling

Abstract

The invention discloses nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel and a preparation method thereof, belongs to the technical field of tool and die steel, and solves the problem that the hardness, corrosion resistance and wear resistance of corrosion-resistant plastic die steel cannot be simultaneously considered in the prior art. The nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistance steel comprises the following components in percentage by mass: c:0.25 to 0.50 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:15.0 to 20.0 percent of Ni:0.005% -2.0%, mo:0.9 to 3.0 percent, V: less than or equal to 0.20 percent, N:0.35 to 0.60 percent, and the balance of Fe and unavoidable impurities. The nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel has excellent mechanical properties and corrosion resistance.

Description

Nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel and preparation method thereof
Technical Field
The invention belongs to the field of tool and die steel, and particularly relates to corrosion-resistant steel with high hardness, high wear resistance and excellent comprehensive performance through Cr-Ni-Mo-N composite alloying and nitrogen distribution type strengthening and a preparation method thereof.
Background
The corrosion-resistant plastic die steel is used as a high-end product in the die steel, is mainly used for forming special engineering plastics with higher temperature and plastics containing flame retardants, and can decompose and generate a large amount of corrosive gases such as hydrogen chloride, hydrogen fluoride, sulfur dioxide and the like in a molten state to generate corrosion action on a used plastic die cavity, so that the service life of the die is reduced. Therefore, such a mold should have a certain corrosion resistance. As the beneficial effect of inexpensive nitrogen on steel properties becomes more pronounced, the addition of nitrogen to plastic die steel has begun to be of interest and development. The addition of nitrogen element can not only not affect other properties of the stainless steel, but also partially replace expensive Ni and other alloy elements to improve the corrosion resistance of the die steel. The common corrosion-resistant plastic die steel is 4Cr13, 9Cr18, etc., and belongs to martensitic stainless steel. However, the existing steel types have the problems of serious carbide segregation, poor structure uniformity, insufficient corrosion resistance and the like, so that the quality stabilization and market elevation of the steel types are restricted, and the performance of the steel types is still required to be further improved.
Disclosure of Invention
In view of the above, the invention aims to provide nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel and a preparation method thereof, which are used for solving the problems of serious carbide segregation and poor tissue uniformity of the existing high-nitrogen corrosion-resistant plastic die steel; the hardness, the corrosion resistance and the wear resistance cannot be simultaneously considered.
The aim of the invention is mainly realized by the following technical scheme:
the invention provides nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistance steel, which comprises the following components in percentage by mass: c:0.25 to 0.50 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:15.0 to 20.0 percent of Ni:0.005% -2.0%, mo:0.9 to 3.0 percent, V: less than or equal to 0.20 percent, N:0.35 to 0.60 percent, and the balance of Fe and unavoidable impurities.
Further, the nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel further comprises one or more of the following elements in percentage by mass: w is less than or equal to 0.5%, cu is less than or equal to 0.5%, nb is less than or equal to 0.05%, co is less than or equal to 0.5%, and rare earth element is less than or equal to 0.05%.
Further, the nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel comprises the following components in percentage by mass: c:0.26 to 0.49 percent, si:0.3 to 0.9 percent, mn:0.25 to 0.9 percent, cr:15.2 to 20.0 percent of Ni:0.006% -2.0%, mo:0.95 to 3.0 percent, V: less than or equal to 0.20 percent, N:0.35 to 0.60 percent, and the balance of Fe and unavoidable impurities.
The invention also provides a preparation method of the nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel, which is used for preparing the nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel and comprises the following steps:
step 1, smelting and pouring to obtain an electrode blank, and carrying out slow cooling or heat preservation annealing treatment on the electrode blank;
step 2, remelting the electrode blank by a pressurizing electroslag furnace, casting into a steel ingot, and carrying out slow cooling or heat preservation annealing treatment on the steel ingot;
step 3, forging the steel ingot to obtain a forging stock;
step 4, performing dispersion treatment on the forging stock;
step 5, annealing the steel subjected to the dispersion treatment;
and step 6, quenching the annealed steel, then performing cryogenic treatment, and then performing tempering treatment.
Further, in step 3, forging includes: fully heating and preserving heat of the steel ingot, and forging; the heating temperature is controlled to 1160-1200 ℃, and the heat preservation time is 10-15 h.
In the step 3, the initial forging temperature is 1150-1200 ℃ and the final forging temperature is 830-860 ℃.
Further, in step 4, the dispersion treatment includes: heating the forging stock to the first heat preservation temperature of 960-1020 ℃ for heat preservation for 1-2 h, and then cooling to room temperature; then preserving heat for 2-4 hours at the temperature of 620-680 ℃ for the second time, and air cooling to room temperature.
Further, in step 5, the annealing treatment includes: heating the steel subjected to the dispersion treatment to 850+/-10 ℃, and preserving heat for 1-2 hours; furnace cooling to 650+/-10 ℃, preserving heat for 1-2 h, and then discharging after furnace cooling to below 400 ℃.
Further, in step 6, the quenching treatment includes: preserving heat for 0.5-2 h at 950-1050 ℃, discharging, water-cooling or oil-cooling to room temperature.
Further, in step 6, the cryogenic treatment includes: preserving heat for 0.5-2 h at-73 to-84 ℃, and air-cooling to room temperature.
Compared with the prior art, the invention has the following beneficial effects:
a) According to the high-hardness high-wear-resistance corrosion-resistant steel, a proper amount of Cr, ni, mo and N elements are added, and martensite and fine dispersed precipitated phases are obtained under the proper dispersion treatment and quenching, deep cooling and tempering processes, so that higher strength and hardness are obtained.
b) The high-hardness high-wear-resistance corrosion-resistant steel obtains good impact toughness and reduces element and tissue segregation through the alloying design of Cr-Ni-Mo-N composite alloying; the nitrogen element distribution type strengthening technology means is adopted to obtain higher strength and hardness, so that good wear resistance can be obtained; the Mo-Ni composite corrosion resistance treatment of the invention obtains more excellent corrosion resistance through reasonable element matching, a diffusion treatment preparation process and a proper heat treatment process.
c) The high-hardness high-wear-resistance corrosion-resistant steel prepared by the components and the method has good comprehensive mechanical properties, the steel subjected to low-temperature tempering treatment can reach the room-temperature hardness of more than or equal to 56HRC, and hard carbide and carbonitride precipitated phases capable of resisting abrasion exist, so that the dual strengthening effect of solid solution strengthening and precipitation strengthening is achieved, and the effect of strengthening the wear-resistance performance can be achieved while the hardness is higher. The steel after high-temperature tempering treatment can have higher impact toughness and tensile strength, for example, the impact toughness Ak is more than or equal to 460J, and the tensile strength is more than or equal to 1040MPa. Meanwhile, the corrosion resistance is excellent, and the corrosion rate is 0.012g/m 2 H or less.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and claims thereof as well as the appended drawings.
Drawings
The drawings are only for purposes of illustrating particular embodiments and are not to be construed as limiting the invention, like reference numerals being used to refer to like parts throughout the several views.
FIG. 1 is a grain size diagram of the steel of example 2 of the present invention after quenching;
FIG. 2 is a grain size diagram of the steel of example 2 of the present invention after quenching;
FIG. 3 is a grain size diagram of the steel of comparative example 1 after quenching;
FIG. 4 is a grain size diagram of the steel of comparative example 1 after quenching;
FIG. 5 is a drawing showing the low temperature tempered structure of example 4 of the present invention;
FIG. 6 is a drawing showing a high temperature tempered structure of example 4 of the present invention;
FIG. 7 is a low temperature tempered SEM image of example 4 of the present invention;
FIG. 8 is a high temperature tempered SEM image of example 4 of the present invention.
FIG. 9 is a drawing showing the low temperature tempered structure of comparative example 1;
FIG. 10 is a drawing showing the high temperature tempered structure of comparative example 1;
FIG. 11 is a low temperature tempered SEM image of comparative example 1;
FIG. 12 is a high temperature tempered SEM image of comparative example 1.
Detailed Description
Preferred embodiments of the present invention are described in detail below with reference to the attached drawing figures, which form a part of the present invention and are used in conjunction with embodiments of the present invention to illustrate the principles of the present invention.
The invention provides nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistance steel, which comprises the following components in percentage by mass: c:0.25 to 0.50 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:15.0 to 20.0 percent of Ni:0.005% -2.0%, mo:0.9 to 3.0 percent, V: less than or equal to 0.20 percent, N:0.35 to 0.60 percent, and the balance of Fe and unavoidable impurities.
The following is a specific description of the action and the selection of the amounts of the components contained in the invention:
c: the carbon content in the steel determines the hardness of the matrix of the steel, and for tool and die steels, one part of carbon is dissolved into the matrix to play a solid solution strengthening role, and the other part of carbon is combined with a strong carbide forming element to form alloy carbide. The C and some alloy elements form alloy carbide to improve the hardness and wear resistance of the steel, and the evenly dispersed alloy carbide and tempered martensite structure affect the corrosion resistance of the steel. In order to obtain higher hardness, wear resistance and corrosion resistance, the carbon content is controlled to be 0.25-0.50 percent in the invention.
Si: silicon is added as a reducing agent and a deoxidizing agent in the steelmaking process, which has an obvious effect on improving corrosion resistance, however, too high a content of Si not only causes the toughness of steel to be reduced, but also promotes the generation of segregation, so that the silicon content is controlled to be less than 1 percent.
Mn: manganese is an element for improving the hardenability of steel, so that the core can achieve the desired mechanical properties. The proper amount of manganese can also effectively improve the strength, hardness and toughness of the steel, eliminate the harmful effects of sulfur and oxygen on the steel, improve the hot processing performance of the steel and improve the cold embrittlement tendency of the steel. However, since segregation is likely to occur when the Mn content is too high, the Mn content in the present invention is controlled to be 1.0% or less.
Ni: nickel is an important hardenability enhancing element that can improve the strength and toughness of steel in some steels. The addition of Ni can improve the passivation tendency of Fe-Cr alloy, not only can improve the corrosion resistance of steel in acid and alkali mediums, but also has the corrosion resistance to atmosphere and salt. The Ni content in the steel of the invention is 0.005% -2.0%.
Cr: chromium is used as a main constituent element of the corrosion resistant steel, so that not only can the hardenability of Fe-Cr alloy be improved, but also the corrosion resistance and the stainless property of the steel can be ensured. However, the excessive Cr content promotes the formation of high-temperature ferrite and network carbide and affects the service performance of the steel, so the Cr content is controlled to be 15.0-20.0%.
Mo: molybdenum can improve the hardenability of steel in the steel, and meanwhile, mo and C, N elements are combined to form carbide and carbonitride, so that the secondary hardening capacity and tempering stability of the steel are improved. Mo is also a main element for improving corrosion resistance, but the excessive content of Mo promotes ferrite formation, reduces the strength and toughness of steel, and controls the content of Mo to be 0.9-3.0%.
V: vanadium can reduce the overheat sensitivity of steel, a small amount of V element can refine grains, and proper heat treatment promotes carbide to disperse and separate out, thereby playing a role in strengthening secondary hardening. However, the too high V content can increase the formation probability of primary carbide in the steel, and influence the toughness of the steel, and the V content is controlled to be less than or equal to 0.20 percent.
N: nitrogen is used as austenitizing element, can replace Ni to reduce cost, can improve corrosion resistance of steel, and combines with partial elements to generate nitride dispersed phase to refine crystal grains and play a role of pinning, thereby improving strength and hardness of steel and achieving the purpose of improving wear resistance. The invention controls N to be 0.35-0.60%.
P: phosphorus forms microscopic segregation when molten steel is solidified, and then is biased to grain boundaries when heated at an austenitizing temperature, so that the brittleness of the steel is remarkably increased. The invention controls the content of P below 0.030%, and the lower the content is, the better.
S: sulfur is an unavoidable impurity, forming FeS, imparting hot shortness to the steel strip. The invention controls the S content below 0.030%, and the lower the S content is, the better.
In order to further improve the comprehensive performance of the high-hardness high-wear-resistance corrosion-resistant steel, the components of the high-hardness high-wear-resistance corrosion-resistant steel can be added with one or more of the following elements in percentage by mass: w is less than or equal to 0.5%, cu is less than or equal to 0.5%, nb is less than or equal to 0.05%, co is less than or equal to 0.5%, and rare earth element is less than or equal to 0.05%.
The functions and the proportions of the elements are as follows:
w: tungsten is one of the strong carbide forming elements, which can increase the tempering stability, red hardness and hot strength of the steel, and it combines with carbon to form special carbide, which can increase the wear resistance of the steel. Tungsten of less than or equal to 0.5% is added in the invention.
Cu: copper is an austenite forming element, can improve corrosion resistance and can cause secondary hardening effect, but the overheat sensitivity tendency can occur when the copper content is too high, and the copper content is controlled to be less than or equal to 0.5 percent.
Nb: niobium can refine grains, increase the coarsening temperature of the grains, reduce the overheat sensitivity and the tempering brittleness of the steel, and improve the strength and the toughness of the steel under certain conditions. In the invention, less than or equal to 0.05 percent of niobium is added.
Co: cobalt is an austenite forming element, improving tempering stability. The cobalt can improve the strength performance of the steel in a solid solution strengthening mode, and can promote the dispersion precipitation strengthening effect of the second phase, so that the ultra-high strength and good comprehensive mechanical properties are obtained. The cobalt content is controlled to be less than or equal to 0.5 percent.
Rare earth element: the rare earth elements can refine the as-cast structure of the steel, and for large-specification steel, large ingot steel ingot smelting is required, and when necessary, the segregation of the as-cast structure is relieved by adding a small amount of rare earth elements, so that a uniform solidification structure is obtained. Meanwhile, the rare earth element can improve the plasticity and impact toughness of the steel, further strengthen the beneficial effects of silicon and manganese and enhance the oxidation resistance of the alloy. Rare earth elements less than or equal to 0.05% are added in the invention.
In order to further improve the comprehensive performance of the high-hardness high-wear-resistance corrosion-resistant steel, the high-hardness high-wear-resistance corrosion-resistant steel comprises the following components in percentage by mass: c:0.26 to 0.49 percent, si:0.3 to 0.9 percent, mn:0.25 to 0.9 percent, cr:15.2 to 20.0 percent of Ni:0.006% -2.0%, mo:0.95 to 3.0 percent, V: less than or equal to 0.20 percent, N:0.35 to 0.60 percent, and the balance of Fe and unavoidable impurities.
The invention also provides a preparation method of the nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel, which comprises the following steps:
step 1, smelting and pouring to obtain an electrode blank, and carrying out slow cooling or heat preservation annealing treatment at 800-900 ℃ on the electrode blank;
step 2, remelting the electrode blank by a pressurizing electroslag furnace, casting into a steel ingot, and performing slow cooling or heat preservation annealing treatment at 800-900 ℃ on the steel ingot;
step 3, forging the steel ingot to obtain a forging stock;
step 4, performing dispersion treatment on the forging stock;
step 5, annealing the steel subjected to the dispersion treatment;
and step 6, quenching the annealed steel, then performing cryogenic treatment, and then performing tempering treatment.
Specifically, in the step 1, the smelting may be performed by using a converter, an electric furnace, an induction furnace and external refining.
Specifically, in the step 3, forging includes: and (5) forging after fully heating and preserving the heat of the steel ingot. The problem that abnormal tissues caused by overburning of cast ingots can influence the subsequent processing and using performances of steel due to the fact that the heating temperature is too high or the heat preservation time is too long is considered, and energy is wasted due to the fact that the too high heating temperature and the too long heat preservation time; the heating temperature is low or the heat preservation time is short, and the homogenization effect of the tissue and carbide cannot be achieved, so that the heating temperature is controlled to be 1160-1200 ℃, and the heat preservation time is 10-15 h.
Specifically, in the step 3, considering that the excessive initial forging temperature may cause excessive burning and overheating, the too low initial forging temperature shortens the forging operation time, shortens the forging temperature range, and causes forging difficulty; the forging temperature is too high, the grains grow up rapidly at high temperature after forging, so that the grains of the forging are coarse, the mechanical property of the forging is reduced, the forging has poor plasticity, difficult deformation and increased internal stress due to the too low forging temperature, and the forging is cracked, so that the forging starting temperature is controlled to be 1150-1200 ℃, and the forging finishing temperature is controlled to be 830-860 ℃.
Specifically, in the step 4, the dispersion treatment includes: heating the forging stock to the first heat preservation temperature of 960-1020 ℃ for heat preservation for 1-2 h, and then cooling to room temperature; then preserving heat for 2-4 hours at the temperature of 620-680 ℃ for the second time, and air cooling to room temperature.
Specifically, in the step 4, the effect of the first heat preservation is to make the steel reach the austenitizing temperature, the carbide is dissolved and refined, and the structure and the crystal grains are coarsened in consideration of the fact that the first heat preservation temperature is too high and the heat preservation time is too long; the heat preservation temperature is too low and the heat preservation time is too short, so that the effect of carbide dissolution and refinement is difficult to achieve, and therefore, the first heat preservation temperature is controlled to 960-1020 ℃ and the heat preservation time is controlled to be 1-2 h.
Specifically, in the step 4, the second heat preservation is performed to obtain a granular pearlite structure in which granular carbide is uniformly dispersed and distributed with ferrite as a matrix. Considering that the second heat preservation temperature is too high or too low to exceed the pearlite formation temperature range, the heat preservation time is too long to cause coarse structure and too short to achieve the effect of pearlite dispersion distribution, the second heat preservation temperature is controlled to be 620-680 ℃, and the heat preservation is carried out for 2-4 hours.
Specifically, in the above step 5, the annealing treatment has the effects of reducing the hardness of the steel, improving the machinability and the processing performance, eliminating or reducing the internal stress, preventing deformation and cracking during the processing, and refining the grains, and uniform chemical composition and structure. The annealing treatment comprises the following steps: heating the steel subjected to the dispersion treatment to 850+/-10 ℃, and preserving heat for 1-2 hours; furnace cooling to 650+/-10 ℃, preserving heat for 1-2 h, and then discharging after furnace cooling to below 400 ℃. The granular pearlite is the most ideal annealed structure state, not only can ensure the uniformity of the structure, but also has lower hardness, and is convenient for subsequent cutting processing. According to the structural transformation and phase transformation characteristics of the steel, the steel is required to be subjected to specific austenitizing at 850+/-10 ℃, and in the temperature range, a little undissolved carbide is reserved as non-spontaneous nucleation points for supercooled austenite decomposition to form pearlite crystal nuclei; then supercooled austenite decomposition is carried out in the temperature range of 650+/-10 ℃ to obtain a granular pearlite structure with ferrite as a matrix and granular carbide uniformly dispersed and distributed; the pearlite transformation is completed and stabilized after cooling to 400 ℃, and the furnace is discharged.
Specifically, in the step 6, the quenching treatment includes: preserving heat for 0.5-2 h at 950-1050 ℃, discharging, water-cooling or oil-cooling to room temperature.
Specifically, in the step 6, the cryogenic treatment is to reduce the content of retained austenite in the quenched steel, improve the strength and hardness of the steel, and the cryogenic treatment includes: preserving heat for 0.5-2 h at-73 to-84 ℃, and air-cooling to room temperature.
Specifically, in the step 6, the steel may be tempered at a high temperature or tempered at a low temperature according to the hardness requirement of the user.
Specifically, in the step 6, the high-temperature tempering treatment can be performed at 450-700 ℃ for 1-5 hours.
Specifically, in the step 6, the low-temperature tempering treatment can be performed at 150-280 ℃ for 0.5-5 hours.
Specifically, in the above step 6, the structure of the quenched steel material is martensite and a small amount of undissolved carbide having a size of about 1 μm, and the crystal grains are uniform and fine, for example, the grain size is about 9.
Specifically, in the step 6, the structure of the steel after the low-temperature tempering treatment is martensite+fine dispersed carbide and carbonitride, martensite laths are uniform, no obvious network segregation and strap segregation are seen, the structure is more uniform, the carbides and the carbonitride are fewer and the size is less than 1 μm, the fine dispersion is distributed on a matrix structure, and the uniformity of the structure is beneficial to the improvement of various service performances of the steel.
Specifically, in the step 6, the structure of the steel after the high-temperature tempering treatment is martensite+tiny dispersed carbide and carbonitride, the more size of the high-temperature tempering precipitated phase is about 1 μm, the precipitated phase is tiny dispersed and distributed on the matrix structure, and the uniformity of the structure is beneficial to the improvement of various service performances of the steel.
Specifically, in the step 6, the steel after the low-temperature tempering treatment can reach a room-temperature hardness of more than or equal to 56HRC (for example, 56.5-62 HRC), has hard carbide and carbonitride precipitated phases capable of resisting abrasion, has dual strengthening effects of solid solution strengthening and precipitation strengthening, and has the effect of strengthening the wear resistance while having higher hardness.
Specifically, in the step 6, the steel after the high-temperature tempering treatment can have higher impact toughness and tensile strength, for example, the impact toughness Ak is more than or equal to 460J (for example, 462-600J), and the tensile strength is more than or equal to 1040MPa (for example, 1048-1350 MPa).
Specifically, in the step 6, the steel after the high-temperature tempering treatment has uniform structure, dispersed and distributed carbonitride, fine size, good interface coordination degree between the carbonitride and a martensitic matrix, less pitting origin, and 0.012g/m corrosion rate after 120h salt spray corrosion experiment by adopting 5% NaCl solution 2 H or less, and excellent corrosion resistance.
Compared with the prior art, the high-hardness high-wear-resistance corrosion-resistant steel provided by the invention has the advantages that by adding a proper amount of CrNi, mo and N elements, martensite and fine dispersed precipitated phases are obtained under the proper dispersion treatment and quenching, deep cooling and tempering processes, so that higher strength and hardness are obtained.
The high-hardness high-wear-resistance corrosion-resistant steel obtains good impact toughness and reduces element and tissue segregation through the alloying design of Cr-Ni-Mo-N composite alloying; the nitrogen element distribution type strengthening technology means is adopted to obtain higher strength and hardness, so that good wear resistance can be obtained; the Mo-Ni composite corrosion resistance treatment of the invention obtains more excellent corrosion resistance through reasonable element matching, a diffusion treatment preparation process and a proper heat treatment process.
The components of the invention are adoptedThe high-hardness high-wear-resistance corrosion-resistant steel prepared by the method has good comprehensive mechanical properties, the steel subjected to low-temperature tempering treatment can reach the room-temperature hardness of more than or equal to 56HRC, hard carbides and carbonitride precipitated phases capable of resisting abrasion exist, the dual strengthening effect of solid solution strengthening and precipitation strengthening is achieved, and the effect of strengthening the wear-resistance performance can be achieved while the hardness is high. The steel after high-temperature tempering treatment can have higher impact toughness and tensile strength, for example, the impact toughness Ak is more than or equal to 460J, and the tensile strength is more than or equal to 1040MPa. Meanwhile, the corrosion resistance is excellent, and the corrosion rate is 0.012g/m 2 H or less.
Examples 1 to 6
The invention provides high-hardness high-wear-resistance corrosion-resistant steel and a preparation method thereof, wherein the components of the steel in the embodiment 1-4 comprise the following components in percentage by mass: c:0.25 to 0.50 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:15.0 to 20.0 percent of Ni:0.005% -2.0%, mo:0.9 to 3.0 percent, V: less than or equal to 0.20 percent, N:0.35 to 0.60 percent, and the balance of Fe and unavoidable impurities.
Specifically, the steel of examples 5 to 6 may further include one or more elements selected from the following elements, in mass percent: w is less than or equal to 0.5%, cu is less than or equal to 0.5%, nb is less than or equal to 0.05%, co is less than or equal to 0.5%, and rare earth element is less than or equal to 0.05%.
The compositions of the steels of examples 1-6 are shown in Table 1 below.
The preparation method of the steel of examples 1 to 6 includes:
(1) Casting molten steel into an ingot;
(2) Heating the cast ingot to 1160-1200 ℃, preserving heat for 10-15 hours, and forging to obtain the product
Figure BDA0004019651270000122
And
Figure BDA0004019651270000123
is a bar of (2); the initial forging temperature is 1150-1200 ℃, and the final forging temperature is 830-860 ℃;
(3) Carrying out dispersion treatment on the bar: heating to 960-1020 ℃ for heat preservation for 1-2 h, and then water-cooling to room temperature; then preserving heat for 2-4 hours at the second heat preservation temperature of 620-680 ℃, and air cooling to room temperature;
(4) Then annealing treatment is carried out: heating the steel subjected to the dispersion treatment to 850+/-10 ℃ for heat preservation for 1-2 hours, slowly cooling to 650+/-10 ℃ for heat preservation for 1-2 hours, cooling to below 400 ℃ in a furnace, discharging the steel, processing the steel into a sample, and carrying out quenching, deep cooling and tempering treatment. Wherein, the processes of quenching, deep cooling and tempering are shown in table 2.
TABLE 1 chemical composition (%)
Figure BDA0004019651270000121
Figure BDA0004019651270000131
Table 2 heat treatment process
Figure BDA0004019651270000132
The example 2, example 3, example 5, example 6 had finer grain size grades than the comparative example steels by quenching at different temperatures, and the example steels had smaller grain coarsening degree with increasing quenching temperature, the grain size grades were around 9 grades, and the comparative example steels had grain size grades of only around 8 grades. The grain size diagrams after quenching in example 2 are shown in fig. 1 and 2, the grain size diagrams after quenching in comparative example 1 steel are shown in fig. 3 and 4, and the grain size grades are shown in table 3.
TABLE 3 grain size grades at different quenching temperatures
Figure BDA0004019651270000133
The tempering structure of the example 4 is martensite+carbide and carbonitride, the tempering structure of the example 4 is martensite+carbide, the low-temperature tempering and high-temperature tempering structures of the steel of the example 4 are dispersed carbonitride, the structure is compact, carbide particles are fine and dispersed, carbide particles are larger in the tempering structure of the example 1, and a large-particle carbide aggregation phenomenon exists, the structure of the example 4 is more uniform than that of the example 1, the carbides and the carbonitride are more finely dispersed and distributed on a matrix structure, and the structure is uniform and beneficial to various service performances of the steel. FIG. 5 is a drawing of a low temperature tempered structure of example 4, FIG. 6 is a drawing of a high temperature tempered structure of example 4, FIG. 7 is a drawing of a low temperature tempered SEM of example 4, and FIG. 8 is a drawing of a high temperature tempered SEM of example 4; fig. 9 is a low temperature tempered structure chart of comparative example 1, fig. 10 is a low temperature tempered SEM chart of comparative example 1, fig. 11 is a high temperature tempered structure chart of comparative example 1, and fig. 12 is a high temperature tempered SEM chart of comparative example 1.
Experiments were performed according to different heat treatment processes, and the results are shown in table 4. The heat treatment was performed at different quenching temperatures, cryogenic treatments and tempering temperatures, examples 1-6 of the present invention having higher hardness values than comparative example 1. Wherein the room temperature hardness under the partial heat treatment process can reach 60HRC.
Table 4 hardness of examples and comparative steels at different heat treatment processes
Figure BDA0004019651270000141
Experiments were performed through the heat treatment process of process 4 and process 5, and the results are shown in table 5. Examples 1 to 6 of the present invention have higher impact toughness and tensile strength than comparative example 1, and are more excellent in both strength and toughness.
Table 5 impact toughness and tensile strength of examples and comparative steels under different heat treatment processes
Figure BDA0004019651270000151
Corrosion resistance tests were performed by heat treatment of process 6, and corrosion rates of examples and comparative examples are shown in table 6. Real worldExamples have a much lower corrosion rate than the comparative examples, e.g., a corrosion rate of 0.012g/m 2 H or less, and excellent corrosion resistance.
Table 6 comparison of corrosion resistance of examples and comparative steels
Figure BDA0004019651270000152
The present invention is not limited to the above-mentioned embodiments, and any changes or substitutions that can be easily understood by those skilled in the art within the technical scope of the present invention are intended to be included in the scope of the present invention.

Claims (10)

1. The nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel is characterized by comprising the following components in percentage by mass: c:0.25 to 0.50 percent, si: less than or equal to 1 percent, mn: less than or equal to 1 percent, cr:15.0 to 20.0 percent of Ni:0.005% -2.0%, mo:0.9 to 3.0 percent, V: less than or equal to 0.20 percent, N:0.35 to 0.60 percent, and the balance of Fe and unavoidable impurities.
2. The nitrogen-distributed reinforced high-hardness high-wear-resistant corrosion-resistant steel according to claim 1, wherein the components of the nitrogen-distributed reinforced high-hardness high-wear-resistant corrosion-resistant steel further comprise one or more elements selected from the group consisting of, in mass percent: w is less than or equal to 0.5%, cu is less than or equal to 0.5%, nb is less than or equal to 0.05%, co is less than or equal to 0.5%, and rare earth element is less than or equal to 0.05%.
3. The nitrogen-distributed reinforced high-hardness high-wear-resistant corrosion-resistant steel according to claim 1, wherein the nitrogen-distributed reinforced high-hardness high-wear-resistant corrosion-resistant steel comprises the following components in mass percent: c:0.26 to 0.49 percent, si:0.3 to 0.9 percent, mn:0.25 to 0.9 percent, cr:15.2 to 20.0 percent of Ni:0.006% -2.0%, mo:0.95 to 3.0 percent, V: less than or equal to 0.20 percent, N:0.35 to 0.60 percent, and the balance of Fe and unavoidable impurities.
4. A method for preparing nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel, characterized in that the method is used for preparing the nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel as claimed in any one of claims 1 to 3, comprising:
step 1, smelting and pouring to obtain an electrode blank, and carrying out slow cooling or heat preservation annealing treatment on the electrode blank;
step 2, remelting the electrode blank by a pressurizing electroslag furnace, casting into a steel ingot, and carrying out slow cooling or heat preservation annealing treatment on the steel ingot;
step 3, forging the steel ingot to obtain a forging stock;
step 4, performing dispersion treatment on the forging stock;
step 5, annealing the steel subjected to the dispersion treatment;
and step 6, quenching the annealed steel, then performing cryogenic treatment, and then performing tempering treatment.
5. The method according to claim 4, wherein in the step 3, forging includes: fully heating and preserving heat of the steel ingot, and forging; the heating temperature is controlled to 1160-1200 ℃, and the heat preservation time is 10-15 h.
6. The method according to claim 5, wherein in the step 3, the initial forging temperature is 1150 to 1200 ℃ and the final forging temperature is 830 to 860 ℃.
7. The method according to claim 4, wherein in the step 4, the dispersing treatment comprises: heating the forging stock to the first heat preservation temperature of 960-1020 ℃ for heat preservation for 1-2 h, and then cooling to room temperature; then preserving heat for 2-4 hours at the temperature of 620-680 ℃ for the second time, and air cooling to room temperature.
8. The method according to claim 4, wherein in the step 5, the annealing treatment comprises: heating the steel subjected to the dispersion treatment to 850+/-10 ℃, and preserving heat for 1-2 hours; furnace cooling to 650+/-10 ℃, preserving heat for 1-2 h, and then discharging after furnace cooling to below 400 ℃.
9. The method according to claim 4, wherein in the step 6, the quenching treatment includes: preserving heat for 0.5-2 h at 950-1050 ℃, discharging, water-cooling or oil-cooling to room temperature.
10. The method according to any one of claims 4 to 9, wherein in step 6, the cryogenic treatment comprises: preserving heat for 0.5-2 h at-73 to-84 ℃, and air-cooling to room temperature.
CN202211682701.9A 2022-12-27 2022-12-27 Nitrogen-distributed reinforced high-hardness high-wear-resistance corrosion-resistant steel and preparation method thereof Pending CN116179943A (en)

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