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CN114561584A - Preparation method of steel with high yield strength and high elongation and steel - Google Patents

Preparation method of steel with high yield strength and high elongation and steel Download PDF

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CN114561584A
CN114561584A CN202210192104.1A CN202210192104A CN114561584A CN 114561584 A CN114561584 A CN 114561584A CN 202210192104 A CN202210192104 A CN 202210192104A CN 114561584 A CN114561584 A CN 114561584A
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CN114561584B (en
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王坤
章如海
施利进
于海成
方前锋
林继兴
魏爱平
陶子雄
童先
徐临超
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Zhejiang Industry and Trade Vocational College
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
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    • C—CHEMISTRY; METALLURGY
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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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
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Abstract

The invention provides a preparation method of a steel material with high yield strength and high elongation and the steel material, wherein the preparation method comprises the following steps: s1: adding alloy raw materials into an electric arc melting furnace to smelt the alloy; s2: heating the obtained alloy ingot, carrying out solution treatment, preserving heat, quenching, and carrying out surface machining on the ingot; s3: coating the surface of the cast ingot with the anti-decarbonization coating, preserving heat, quickly taking out the cast ingot, placing the cast ingot on a hot forging machine, roughly hot-forging the cast ingot into a round rod, and performing water quenching; s4: cutting the rough forging round bar into the length of 300-500 mm, heating, preserving heat, taking out the round bar, and placing the round bar on a warm rolling mill to finish rolling to a round bar A at medium temperature; s5: placing the round bar A in liquid nitrogen for cryogenic treatment, taking out the round bar A, and placing the round bar A on a rolling mill for ultra-low temperature finish rolling to obtain a round bar B; s6: and carrying out metallographic examination on the sample. The preparation method can prepare the steel with high yield strength, high elongation and excellent comprehensive mechanical properties.

Description

Preparation method of steel with high yield strength and high elongation and steel
Technical Field
The invention relates to a preparation method of a steel with high yield strength and high elongation and the steel, belonging to the technical field of metal material processing and forming.
Background
The statements in this section merely provide background information related to the present disclosure and may not constitute prior art.
Twip (twinning induced plasticity) steel, also called twin induced plasticity steel, generally contains more than 15% of manganese element, and thus is also a high manganese steel. The TWIP has high strain hardening rate, is derived from high-density deformation twin crystals generated in the plastic deformation process, and the interaction of the deformation twin crystal boundaries of micro-nano scale with dislocation and crystal boundaries causes remarkable work hardening, so that the TWIP steel has excellent elongation which is generally more than 60 percent, and has great application potential in multiple fields of energy, traffic and the like.
The ratio of yield point (yield strength) to tensile strength of a steel material is called the yield ratio. The greater the yield ratio, the greater the reliability of the structural part. However, in order to fully guarantee the twinning induced plasticity effect of the TWIP, different series of TWIP steels designed based on the stacking fault energy theory, such as Fe-Mn-Al-Si, Fe-Mn-Al-C, Fe-Mn-Cu-C, Fe-Mn-C, are all austenite structures, and the problem of low yield strength is generally existed.
The grain size is refined by large-deformation cold rolling and annealing heat treatment means, such as Atef Hamada (DOI:10.1016/j.msea.2018.01.132), G.Dini (DOI:10.1016/j.matdes.2010.01.049) and Wangshu break Liu Zhen Wang Chinese (influence of grain size in TWIP steel on TWIP effect [ J ]. metal science report, 2009,45(9): 1083-. However, compared with coarse grains, the fine grain structure greatly improves the critical stress of deformation twinning initiation and inhibits the effect of twinning induced plasticity. This in turn leads to an increase in the TWIP yield strength while at the same time causing a rapid decrease in the elongation.
Dini (DOI:10.1016/j. mats.2010.01.049) produced a Fe-31% Mn-3% Al-3% Si TWIP steel with a grain size of 72.6 μm with an elongation of only 76.3% at a yield strength of 123 MP. When the grain size was reduced to 2.1. mu.m, the elongation was only 39.8% at a yield strength of 572 MP.
The invention patent with the publication number of CN101956134B and the publication date of 2012.08.08 discloses a high-strength and high-plasticity copper-containing high-carbon TWIP steel and a preparation process thereof, wherein the TWIP steel comprises the following chemical components in percentage by mass: c: 1.1 to 1.5%, Mn: 19.5-20.7%, Cu: 2.5-4.5%, rare earth Ce: 0.21-0.24%, and the balance of Fe and inevitable impurities. The TWIP steel is strengthened by a large amount of carbon elements and copper elements, and the example shows that the yield strength of the TWIP steel is about 504-540 MPa. In the method, the alloy in a cold rolling state is subjected to water quenching after heat preservation for 10-20 min at the temperature of 1000-1055 ℃, and in the step, high-temperature recovery and recrystallization of the material can cause the density of high-density dislocation and deformation twin crystals formed in the cold rolling process to be sharply reduced, so that the yield strength of the alloy material is not improved.
The invention patent application with the application publication number of CN113278908A and the application publication number of 2021.08.20 discloses high-strength-toughness corrosion-resistant TWIP steel and a preparation method thereof, wherein the yield strength of a steel wire of the TWIP steel is 400-800 MPa, the tensile strength is 700-1000 MPa, and the elongation is 20-60%. However, when the yield strength is 523.6MPa, the elongation A of the TWIP steel is 48.6%; the elongation A of the TWIP steel was 39.7% when the yield strength was 662.5 MPa.
The invention patent with the publication number of CN103667913B and the publication date of 2015.09.16 discloses a production method of TWIP steel with high yield strength and high plasticity, which achieves the purposes of grain refinement and precipitation strengthening by using nano-sized carbon nitride precipitates such as V (C, N) and Al (C, N) and the like, and greatly increases the yield strength of the TWIP steel to over 1000MPa, but the elongation can only be ensured to over 10 percent. In other words, the fine grains and the precipitated phases are not beneficial to twinning induced plasticity effect, so that the improvement of the yield strength greatly sacrifices the plasticity, and is not beneficial to practical application.
From the above, the TWIP steel has a significant reduction in elongation with an increase in yield strength. It is impossible to obtain a high elongation while having a high yield strength.
It should be noted that the above background description is only for the convenience of clear and complete description of the technical solutions in the present specification and for the understanding of those skilled in the art. Such solutions are not considered to be known to the person skilled in the art merely because they have been set forth in the background section of the present specification.
Disclosure of Invention
The invention provides a preparation method of a steel with high yield strength and high elongation and the steel aiming at the defects in the prior art.
The scheme is realized by the following technical measures: a preparation method of a steel material with high yield strength and high elongation comprises the following steps:
s1: adding alloy raw materials into an electric arc melting furnace protected by vacuum argon to smelt the alloy, wherein the alloy raw materials comprise the following components in percentage by mass: 0.8 to 1%, Cu: 1-3%, Mn: 22-25%, P is less than or equal to 0.005%, s is less than or equal to 0.005%, and the balance is Fe, the smelting temperature is 1550-1650 ℃, and a refining agent and a deslagging agent are required to be added in the smelting process;
s2: heating the obtained alloy ingot to 1100 ℃ for solution treatment, preserving heat for 12-24 h, then quenching, and carrying out surface machining on the ingot after solution treatment to remove a surface layer with the thickness of more than or equal to 1.5 mm;
s3: coating an anti-decarbonization coating with the thickness of 0.1-0.3 mm on the surface of the machined cast ingot, placing the cast ingot in a heat preservation furnace, preserving heat for 1-4 hours at the temperature of 1100 ℃, quickly taking out the heat-preserved cast ingot, placing the heat-preserved cast ingot on a hot forging machine within 15-30 s, roughly hot-forging the cast ingot into a round rod, and performing water quenching after forging;
s4: cutting a rough forging round bar into the length of 300-500 mm, then placing the round bar in a controlled atmosphere furnace for heating at the heating temperature of 400 ℃, preserving heat for 1-4 h, preheating a warm rolling mill roller in advance, then quickly taking out the round bar, placing the round bar in a warm rolling mill for 15-30 s, and performing medium-temperature finish rolling on the round bar A to obtain the round bar A, wherein the diameter of the round bar A is
Figure BDA0003525266030000031
S5: placing the round bar A in liquid nitrogen for cryogenic treatment for 1h, taking out the round bar A subjected to cryogenic treatment, placing the round bar A on a rolling mill in 15-30 s, and performing ultra-low temperature finish rolling until the round bar B reaches the diameter of the round bar B
Figure BDA0003525266030000032
S6: and carrying out metallographic phase inspection on the sample to ensure that the sample material is an austenite structure, no obvious carbide and epsilon-Cu precipitated phase exist in the sample, and deformation twin crystals with proper density are contained in the crystal grains of the sample material.
Preferably, in step S3, the hot forging start temperature is 1050 to 1080 ℃ and the finish forging temperature is not less than 850 ℃.
Preferably, in step S3, the single-pass deformation amount of hot forging is 10% to 20%, and the total forging deformation amount is equal to or greater than 70%.
Preferably, in the step S4, the warm rolling mill roller is preheated to 350 to 400 ℃ in advance.
Preferably, in the step S4, the single deformation of the medium-temperature finish rolling is 10% to 15%, and the total deformation is equal to or greater than 50%.
Preferably, in the step S5, the starting temperature of the finish rolling is less than or equal to-150 ℃, and the finishing temperature is less than or equal to-50 ℃.
Preferably, in the step S5, the single pass deformation amount of the ultra-low temperature finish rolling is 3% to 5%.
Preferably, in step S6, the number of the deformation twins contained in the sample material crystal grains includes intercrossing deformation twins is less than or equal to 10%, and the number of the single direction deformation twins is greater than or equal to 15%.
Preferably, the diameter of the round bar A
Figure BDA0003525266030000041
The value range of (A) is 20-40 mm.
The invention also provides a steel material with high yield strength and high elongation rate, which is prepared by the method, wherein the yield strength of the steel material is 550-700 MPa, and the elongation rate is more than 50%.
The invention has the beneficial effects that: according to the preparation method of the steel with high yield strength and high elongation, according to the alloy layer fault energy design theory, the rapid and accurate molding of the material is realized by optimizing the alloy components of the TWIP steel and adopting the means of combining large deformation amount hot forging, warm rolling with proper deformation amount and small deformation amount ultra-low temperature finish rolling, the material is of a uniform austenite structure, the material internally contains high-density dislocation and deformation twin crystal with proper density, and no second phase is separated out, so that the steel with high yield strength and high elongation and excellent comprehensive mechanical properties is obtained. Therefore, compared with the prior art, the invention has prominent substantive features and remarkable progress, and the beneficial effects of the implementation are also obvious.
Drawings
FIG. 1 is a microstructure analysis of the material of example 1 after ultra-low temperature finish rolling, which includes a set of crossed direction deformation twins T1 and T2.
FIG. 2 is a phase analysis diagram of the material of example 1 after finish rolling at ultralow temperature.
FIG. 3 is a view showing the microstructure of the material of example 1 after finish rolling at ultralow temperature.
FIG. 4 is a graph of the final mechanical properties of the materials of examples 1, 2 and 3.
Detailed Description
In order to clearly illustrate the technical features of the present solution, the following explains the present solution by way of specific embodiments and with reference to the accompanying drawings.
Example 1
A preparation method of a steel material with high yield strength and high elongation comprises the following steps:
s1: adding alloy raw materials into an electric arc melting furnace protected by vacuum argon to smelt the alloy, wherein the alloy raw materials comprise the following components in percentage by mass: 1%, Cu: 1%, Mn: 22%, P: 0.005%, s: 0.005 percent and the balance of Fe, the smelting temperature is 1550 ℃, and a refining agent and a deslagging agent are required to be added in the smelting process;
s2: heating the obtained alloy ingot to 1100 ℃ for solution treatment, keeping the temperature for 12h, then quenching, carrying out surface machining on the ingot subjected to solution treatment, and removing a surface layer with the thickness of 2mm to ensure that a surface decarburized layer is completely removed;
s3: coating an anti-decarbonization coating with the thickness of 0.1mm on the surface of the machined cast ingot, placing the cast ingot in a heat preservation furnace, preserving heat for 1h at the temperature of 1100 ℃, quickly taking out the heat-preserved cast ingot, placing the heat-preserved cast ingot in a hot forging machine within 30s, roughly hot-forging the cast ingot into a round bar, wherein the hot forging starting temperature is 1050 ℃, the finish forging temperature is 850 ℃, and performing water quenching after forging; the single deformation of hot forging is 10 percent, and the total deformation of hot forging is 70 percent;
s4: the roughly forged round bar was cut into a length of 500mm and then laidHeating in a controlled atmosphere furnace at 400 deg.C for 1 hr, preheating the roller of warm rolling mill to 400 deg.C, quickly taking out the round bar, placing in a warm rolling mill in 30s, and fine rolling to obtain round bar A with a single deformation of 15%, a total deformation of 60%, and a diameter of the round bar A
Figure BDA0003525266030000051
Is 20 mm;
s5: placing round bar A in liquid nitrogen for cryogenic treatment for 1h, taking out the round bar A after cryogenic treatment, placing the round bar A on a rolling mill in 30s, and performing ultra-low temperature finish rolling until the round bar B is obtained, wherein the deformation of the single time of ultra-low temperature finish rolling is 5%, the start temperature of finish rolling is-150 ℃, the finish rolling temperature is-60 ℃, and the diameter of the round bar B is
Figure BDA0003525266030000052
Figure BDA0003525266030000053
S6: and carrying out metallographic examination on the sample to ensure that the sample material is an austenite structure, no obvious carbide and epsilon-Cu precipitated phase exist in the sample, and deformation twin crystals with a proper density are contained in the crystal grains of the sample material, wherein specifically, the deformation twin crystals contained in the crystal grains of the sample material comprise 5% of crystal grains containing intercross deformation twin crystals and 20% of crystal grains containing unidirectional deformation twin crystals. As shown in fig. 3, the material is finish rolled at ultra-low temperature, and then high-density dislocations are stored therein.
A steel material with high yield strength and high elongation prepared by the method has the yield strength of 594.5MPa and the elongation of 61.5 percent as shown in figure 4.
Example 2
A preparation method of a steel material with high yield strength and high elongation comprises the following steps:
s1: adding alloy raw materials into an electric arc melting furnace protected by vacuum argon to smelt the alloy, wherein the alloy raw materials comprise the following components in percentage by mass: 0.8%, Cu: 2.5%, Mn: 25%, P: 0.003%, s: 0.004 percent of the balance of Fe, the smelting temperature is 1650 ℃, and a refining agent and a deslagging agent are required to be added in the smelting process;
s2: heating the obtained alloy ingot to 1100 ℃ for solution treatment, preserving heat for 18h, then quenching, and carrying out surface machining on the ingot subjected to solution treatment to remove a surface layer with the thickness of 1.5mm so as to ensure that a surface decarburized layer is completely removed;
s3: coating an anti-decarbonization coating with the thickness of 0.3mm on the surface of the machined ingot, placing the ingot in a heat preservation furnace, preserving heat for 2 hours at the temperature of 1100 ℃, quickly taking out the heat-preserved ingot, placing the ingot in a hot forging machine within 30 seconds, roughly hot-forging the ingot into a round bar, and performing water quenching after the hot forging, wherein the hot forging starting temperature is 1070 ℃, the finish forging temperature is 860 ℃; the single deformation of hot forging is 20 percent, and the total deformation of hot forging is 80 percent;
s4: cutting a rough forging round bar into the length of 300mm, then placing the round bar in a controlled atmosphere furnace for heating at the heating temperature of 400 ℃, preserving heat for 3 hours, preheating a warm rolling mill roller to 350 ℃ in advance, then quickly taking out the round bar, placing the round bar in a warm rolling mill in 20s, and performing medium-temperature finish rolling to the round bar A, wherein the single deformation of the medium-temperature finish rolling is 10%, the total deformation is 50%, and the diameter of the round bar A is
Figure BDA0003525266030000061
Is 22 mm;
s5: placing round bar A in liquid nitrogen for cryogenic treatment for 1h, taking out the round bar A after cryogenic treatment, placing the round bar A on a rolling mill in 20s, and performing ultra-low temperature finish rolling until the round bar B is obtained, wherein the deformation of the single time of ultra-low temperature finish rolling is 4%, the start temperature of finish rolling is-170 ℃, the finish rolling temperature is-50 ℃, and the diameter of the round bar B is
Figure BDA0003525266030000062
Figure BDA0003525266030000063
S6: and carrying out metallographic examination on the sample to ensure that the sample material is an austenite structure, no obvious carbide and epsilon-Cu precipitated phase exist in the sample, and deformation twin crystals with a proper density are contained in the crystal grains of the sample material, wherein specifically, the deformation twin crystals contained in the crystal grains of the sample material comprise 3% of crystal grains containing intercrossing deformation twin crystals and 15% of crystal grains containing unidirectional deformation twin crystals.
A steel material having high yield strength and high elongation, which is prepared by the above method, has a yield strength of 557.3MPa and an elongation of 57.4%, as shown in FIG. 4.
Example 3
A preparation method of a steel material with high yield strength and high elongation comprises the following steps:
s1: adding alloy raw materials into an electric arc melting furnace protected by vacuum argon to smelt the alloy, wherein the alloy raw materials comprise the following components in percentage by mass: 1%, Cu: 3%, Mn: 25%, P: 0.004%, s: 0.004 percent of the balance of Fe, the smelting temperature is 1600 ℃, and a refining agent and a deslagging agent are required to be added in the smelting process;
s2: heating the obtained alloy ingot to 1100 ℃ for solution treatment, keeping the temperature for 24h, then quenching, carrying out surface machining on the ingot subjected to solution treatment, and removing a surface layer with the thickness of 2mm to ensure that a surface decarburized layer is completely removed;
s3: coating an anti-decarbonization coating with the thickness of 0.2mm on the surface of the machined cast ingot, placing the cast ingot in a heat preservation furnace, preserving heat for 3 hours at the temperature of 1100 ℃, quickly taking out the heat-preserved cast ingot, placing the heat-preserved cast ingot in 15 seconds, placing the heat-preserved cast ingot on a hot forging machine, roughly hot-forging the heat-preserved cast ingot into a round rod, wherein the hot forging starting temperature is 1080 ℃, the finish forging temperature is 865 ℃, and performing water quenching after forging; the single deformation of hot forging is 15 percent, and the total deformation of hot forging is 70 percent;
s4: cutting a rough forging round bar into a length of 400mm, then placing the round bar in a controlled atmosphere furnace for heating at a heating temperature of 400 ℃, preserving heat for 4 hours, preheating a warm rolling mill roller to 365 ℃ in advance, then quickly taking out the round bar, placing the round bar in a warm rolling mill in 15s, and performing medium-temperature finish rolling to obtain a round bar A, wherein the single deformation of the medium-temperature finish rolling is 10%, the total deformation is 60%, and the diameter of the round bar A is
Figure BDA0003525266030000071
Is 20 mm;
s5: round barPlacing A in liquid nitrogen for cryogenic treatment for 1h, taking out the round bar A after cryogenic treatment, placing the round bar A on a rolling mill in 15s, and performing ultra-low temperature finish rolling to obtain a round bar B, wherein the single deformation of the ultra-low temperature finish rolling is 3%, the start temperature of the finish rolling is-180 ℃, the finish rolling temperature is-80 ℃, and the diameter of the round bar B is
Figure BDA0003525266030000072
Figure BDA0003525266030000073
S6: and carrying out metallographic examination on the sample to ensure that the sample material is an austenite structure, no obvious carbide and epsilon-Cu precipitated phase exist in the sample, and deformation twin crystals with a proper density are contained in the crystal grains of the sample material, wherein specifically, the deformation twin crystals contained in the crystal grains of the sample material comprise the crystal grains with the intercrossing deformation twin crystals in the proportion of 7% and the crystal grains with the unidirectional deformation twin crystals in the proportion of 20%.
A steel material with high yield strength and high elongation prepared by the method has the yield strength of 683.1MPa and the elongation of 53.0 percent as shown in figure 4.
In summary, the preparation method of the steel with high yield strength and high elongation and the steel have the following advantages:
(1) the mass percentage of each component is C: 0.8-1%, Cu: 1-3%, Mn: 22-25%, P is less than or equal to 0.005%, s is less than or equal to 0.005%, and the balance is Fe, wherein C and Cu can form solid solution strengthening, and Mn can reduce alloy fault energy, so that twinning induced plasticity effect is more sufficient, and high elongation is obtained;
(2) the method combining large deformation hot forging, warm rolling with proper deformation and small deformation ultralow temperature finish rolling can realize the rapid and accurate forming of the material, and a relatively accurate forming process window is established: for hot forging, the initial temperature is 1050-1080 ℃, the finish forging temperature is more than or equal to 850 ℃, and then a quenching process is added, so that C and Cu are fully dissolved to a matrix, carbide and epsilon-Cu are prevented from being separated out, and the hot forging stress is reduced to facilitate forming; for warm rolling, the rolling temperature is controlled to be 350-400 ℃, mainly aiming at promoting dynamic recrystallization in the warm rolling process to refine grains, eliminating anisotropy caused by rolling flow lines, preventing carbide from being precipitated at the temperature of more than 400 ℃, and reducing rolling deformation resistance to ensure that the rolling deformation of the rolled surface of the sample and the core part of the sample is relatively uniform; for ultra-low temperature finish rolling, the initial temperature of finish rolling is less than or equal to-150 ℃, the final rolling temperature is less than or equal to-50 ℃, high-density dislocation in the finish rolling process can be retained to the maximum extent, the yield strength of the material is obviously improved, and meanwhile, the finish rolling amount is controlled, so that the excessive consumption of the plasticity of the material is prevented;
(3) the material is a uniform austenite structure, contains high-density dislocation and deformation twin crystals with proper density in the material and has no second phase precipitation, and has excellent comprehensive mechanical properties of high yield strength and high elongation through composite synergistic strengthening means such as C and Cu element solid solution strengthening, dislocation deformation strengthening, deformation twin crystal fine crystal strengthening and the like.
Technical features not described in the present invention can be implemented by the prior art, and are not described in detail herein. The present invention is not limited to the above-described embodiments, and variations, modifications, additions and substitutions which are within the spirit of the invention and the scope of the invention may be made by those of ordinary skill in the art are also within the scope of the invention.

Claims (10)

1. A preparation method of steel with high yield strength and high elongation is characterized by comprising the following steps: it comprises the following steps:
s1: adding alloy raw materials into an electric arc melting furnace with vacuum argon protection to smelt the alloy, wherein the smelting temperature is 1550-1650 ℃, and a refining agent and a deslagging agent are required to be added in the smelting process;
s2: heating the obtained alloy ingot to 1100 ℃ for solution treatment, preserving heat for 12-24 h, then quenching, and carrying out surface machining on the ingot after solution treatment to remove a surface layer with the thickness of more than or equal to 1.5 mm;
s3: coating an anti-decarbonization coating with the thickness of 0.1-0.3 mm on the surface of the machined cast ingot, placing the cast ingot in a heat preservation furnace, preserving heat for 1-4 hours at the temperature of 1100 ℃, quickly taking out the heat-preserved cast ingot, placing the heat-preserved cast ingot on a hot forging machine within 15-30 s, roughly hot-forging the cast ingot into a round rod, and performing water quenching after forging;
s4: cutting a rough forging round bar into the length of 300-500 mm, then placing the round bar in a controlled atmosphere furnace for heating at the heating temperature of 400 ℃, preserving heat for 1-4 h, preheating a warm rolling mill roller in advance, then quickly taking out the round bar, placing the round bar in a warm rolling mill for 15-30 s, and performing medium-temperature finish rolling on the round bar A to obtain the round bar A, wherein the diameter of the round bar A is
Figure FDA0003525266020000011
S5: placing the round bar A in liquid nitrogen for cryogenic treatment for 1h, taking out the round bar A subjected to cryogenic treatment, placing the round bar A on a rolling mill in 15-30 s, and performing ultra-low temperature finish rolling until the round bar B reaches the diameter of the round bar B
Figure FDA0003525266020000012
S6: and carrying out metallographic phase inspection on the sample to ensure that the sample material is an austenite structure, no obvious carbide and epsilon-Cu precipitated phase exist in the sample, and deformation twin crystals with proper density are contained in the crystal grains of the sample material.
2. The method of producing a steel product with high yield strength and high elongation as claimed in claim 1, wherein: in the step S3, the hot forging starting temperature is 1050-1080 ℃, and the finish forging temperature is not less than 850 ℃.
3. The method of producing a steel product with high yield strength and high elongation as claimed in claim 2, wherein: in the step S3, the single deformation of hot forging is 10-20%, and the total deformation of hot forging is more than or equal to 70%.
4. The method of producing a steel product with high yield strength and high elongation as claimed in claim 3, wherein: in the step S4, the warm rolling mill roller is preheated to 350-400 ℃ in advance.
5. The method of producing a steel product with high yield strength and high elongation as claimed in claim 4, wherein: in the step S4, the single deformation of the medium-temperature finish rolling is 10-15%, and the total deformation is more than or equal to 50%.
6. The method of producing a steel product with high yield strength and high elongation as claimed in claim 5, wherein: in the step S5, the initial temperature of finish rolling is less than or equal to-150 ℃, and the final rolling temperature is less than or equal to-50 ℃.
7. The method for producing a steel material with high yield strength and high elongation as claimed in claim 6, wherein: in the step S5, the single pass deformation of the ultra-low temperature finish rolling is 3% to 5%.
8. The method of producing a steel product with high yield strength and high elongation as claimed in claim 7, wherein: in the step S6, the number of the deformation twin crystals contained in the sample material crystal grains includes the intercrossing deformation twin crystals is less than or equal to 10%, and the number of the unidirectional deformation twin crystals is greater than or equal to 15%.
9. The method of producing a steel product with high yield strength and high elongation as claimed in claim 8, wherein: diameter of the round bar A
Figure FDA0003525266020000021
The value range of (a) is 20-40 mm.
10. A high yield strength and high elongation steel product obtainable by the process of any one of claims 1 to 9, wherein: the yield strength of the steel is 550-700 MPa, and the elongation is more than 50%.
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