CN110484834B - Cr and Mn alloyed TRIP steel and preparation method thereof - Google Patents

Cr and Mn alloyed TRIP steel and preparation method thereof Download PDF

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CN110484834B
CN110484834B CN201910772997.5A CN201910772997A CN110484834B CN 110484834 B CN110484834 B CN 110484834B CN 201910772997 A CN201910772997 A CN 201910772997A CN 110484834 B CN110484834 B CN 110484834B
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rolling
hot
steel
steel plate
heating
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CN110484834A (en
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阳锋
韩赟
姜英花
刘华赛
谢春乾
邱木生
潘丽梅
白雪
滕华湘
陈斌
曹杰
章军
朱国森
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Shougang Corp
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Abstract

The invention provides Cr and Mn alloyed TRIP steel, which comprises the following chemical components: c, by mass percent: 0.03-0.5%, Cr: 0.8 to 11.0%, Mn: 0.1-7.0%, Al: 0.001-3.0%, Si: 0.001-2.0%, P is less than or equal to 0.02%, S is less than or equal to 0.02%, and the balance is Fe and inevitable impurities. Smelting molten steel to obtain a casting blank, heating the casting blank, and hot rolling to obtain a hot rolled coil. Austenite with moderate stability is obtained after hot rolling and coil annealing, and the preparation of a high-performance steel plate is completed; the hot rolled plate can also be subjected to online or offline heat treatment, the hot rolled plate is austenitized or partially austenitized by a heating furnace, then cooled to room temperature, then heated for annealing or directly annealed to obtain austenite with moderate stability, and the preparation of the high-performance hot rolled plate is completed. The invention can also carry out cold rolling on the hot rolled coil, and the process comprises the following steps: and softening and annealing the hot-rolled coil, carrying out acid pickling treatment, then rolling in a cold rolling unit, and annealing the cold-rolled steel plate to obtain the cold-rolled steel plate with required performance.

Description

Cr and Mn alloyed TRIP steel and preparation method thereof
Technical Field
The invention belongs to the technical field of steel for automobiles and steel for engineering structures, and particularly relates to Cr and Mn alloyed TRIP steel and a preparation method thereof.
Background
At present, medium manganese TRIP steel with excellent comprehensive mechanical properties is more and more the focus of attention of people. In order to obtain a certain volume fraction of metastable austenite, the Mn content in the medium manganese steel is generally between 5 and 12 percent. However, when the Mn content in the steel is greatly increased, the production processes such as casting and rolling are difficult. Cr is one of common alloy elements in steel, the influence of Cr on smelting and rolling processes is relatively small, and the price of ferrochrome is not much different from that of ferromanganese. For example, the Cr content in stainless steel is generally more than 12 percent, but the continuous casting and hot rolling processes of stainless steel are relatively mature at present. The reasons for this may come from two aspects. Firstly, the production of stainless steel is explored for a long time, the process is relatively mature, the development time of TWIP steel or medium manganese steel with high Mn content is short, and the production process is difficult to mature in a short time. Secondly, Ni in the stainless steel is toughened grain boundaries, and Cr has limited effect of toughening the grain boundaries but can not obviously embrittle the grain boundaries; while Mn is a typical grain boundary embrittlement element. In the process of drawing and rolling, because the temperature of the corner part of the slab is lower, the tendency of Mn element to be segregated towards the grain boundary is higher (segregation energy is higher) at lower temperature, so that the grain boundary is further embrittled, and the casting and rolling processes of medium and high Mn steel are easy to have problems. And Mn atoms and C atoms in austenite of the medium manganese steel are easily combined into Mn-C atom pairs to cause the generation of dynamic strain aging, which is unfavorable for the surface quality of the medium manganese steel after formability. How to reduce the production difficulty of medium manganese steel and improve the comprehensive performance becomes the problem to be solved urgently.
Disclosure of Invention
In view of the above, the invention provides Cr and Mn alloyed TRIP steel and a preparation method thereof, aiming at reducing the difficulty of producing medium manganese steel.
The invention reduces the Mn content in the matrix and simultaneously improves the Cr content. Although Cr does not expand the austenite phase region like Mn, it can lower the Ms point of austenite and also serves to stabilize metastable austenite. And the addition of Cr can theoretically reduce the generation of dynamic strain aging. Finally, the corrosion resistance of the substrate after addition of Cr is also improved.
Under the guidance of the principle, the TRIP steel provided by the invention obtains metastable austenite with equivalent volume fraction by simultaneously adding Mn and Cr or adding Cr on the basis that the Mn content of a matrix is not greatly improved (less than or equal to 3%), thereby obtaining the TRIP steel with higher comprehensive mechanical property on the premise of low production difficulty.
The invention provides Cr and Mn alloyed TRIP steel in a first aspect, which comprises the following chemical components: c, by mass percent: 0.03-0.5%, Cr: 0.8 to 11.0%, Mn: 0.1-7.0%, Al: 0.001-3.0%, Si: 0.001-2.0%, P is less than or equal to 0.02%, S is less than or equal to 0.02%, and the balance is Fe and inevitable impurities.
Preferably, the Cr-Mn alloyed TRIP steel further includes, in chemical composition: by mass percent, Ni: 0-3.0%, Mo: 0-0.8%, Cu: 0-2.0%, B: 0-0.005%, Nb: 0-0.2%, Ti: 0-0.3%, V: 0-0.8%, Zr: 0-0.2%, N: 0.001-0.3%, rare earth elements: 0-0.005%, Ca: 0-0.03% of one or more of the above-mentioned materials.
From the economical point of view, the invention takes C, Cr and Mn as the basis, adjusts and improves the performance by adding other alloy elements, and the alloy composition of the invention has the following characteristics:
c, carbon C: the contents of main austenitizing elements and interstitial solid solution strengthening elements are important. A lower content may result in an insufficient content of metastable austenite; an excessively high content results in, on the one hand, a reduction in the weldability and, on the other hand, a difficulty in cold rolling the coil. The carbon content should be controlled at 0.03-0.5%.
Chromium Cr: the main solid solution strengthening element can improve the hardenability of the matrix and reduce the Ms point of austenite. The chromium content should be controlled at 0.8-11.0%.
Manganese Mn: the main austenitizing element has the function of improving hardenability, and the content is very important. Too high a content can embrittle the matrix. The Mn content is controlled to be 0.1-7.0%.
Aluminum Al: in addition to deoxidation and grain refinement, the aluminum element may also inhibit precipitation of carbides during coiling and annealing. More importantly, the two-phase region of the aluminum is expanded on one hand, so that the selectable reverse phase transition annealing temperature range is expanded; on the other hand, the aluminum can also increase the stacking fault energy of the metastable austenite, and the reasonable aluminum content can ensure that the stacking fault energy of the metastable austenite is in a range capable of simultaneously generating a TWIP effect and a TRIP effect, thereby achieving the purpose of improving the matrix product of strength and elongation; in addition, aluminum is a ferrite-forming element, and can inhibit the generation of austenite, and the austenite with reduced volume fraction can absorb more alloying elements such as carbon, manganese and the like from the matrix, thereby improving the stability of metastable austenite. However, the aluminum content should not be too high, which would make continuous casting difficult and would tend to produce coarse delta ferrite, which is disadvantageous in tensile strength. The invention controls the content of aluminum at 0.001-3.0%.
Silicon Si: the silicon element can inhibit the precipitation of carbide in the coiling and annealing processes, can also enlarge a two-phase region, and can improve the ferrite strength by dissolving silicon in a solid solution in ferrite. However, too high silicon content can increase the red rust defect on the hot rolling surface and reduce the surface quality of the finished product. Therefore, the amount of silicon added depends on the application, and the silicon content used in the present invention is 0.001-2.0%.
Phosphorus P: micro segregation is formed when molten steel is solidified, and then the micro segregation is easy to be deviated to a grain boundary when the molten steel is heated, so that the brittleness of the steel is increased. Therefore, the P content should be controlled below 0.02%.
S, sulfur: unavoidable impurities, formation of MnS inclusions and segregation at grain boundaries deteriorate the toughness of the steel and increase the hydrogen-induced delayed fracture sensitivity. Therefore, the S content should be controlled below 0.02%.
Nickel Ni: the nickel element can increase the stability of austenite and effectively improve the toughness of the matrix. The nickel content depends on the application, and the nickel content adopted by the invention is 0-3.0%.
Molybdenum Mo: effectively improves the hardenability of the steel, strengthens the grain boundary and can also inhibit the growth of microalloy carbide. When the content exceeds 0.8%, the effect is nearly saturated, and the cost is high. The molybdenum content is 0-0.8%.
Copper Cu: the reinforcement is achieved by the precipitation of ε -Cu, and the corrosion resistance of the substrate can be improved by the combination with P. The range of copper addition in the present invention is 0-2.0%.
B, boron B: the hardenability and the purification grain boundary of the steel are obviously improved, and the effect is not obviously increased after the content is higher than 0.005 percent. Therefore, the addition range of the boron content is 0 to 0.005 percent.
Niobium Nb: the niobium is easy to form fine precipitates with carbon and nitrogen atoms in an austenite temperature range, can play a role in refining grains, and can improve the non-recrystallization temperature of austenite by solid solution of niobium. The addition amount of niobium is controlled to be 0-02%.
Titanium Ti: a strong carbonitride forming element. Titanium nitride can be formed in the heating temperature interval of the plate blank to refine austenite grains. The addition amount of titanium is controlled to be 0-0.3%.
V, V: in the form of fine carbonitride, has strong precipitation strengthening effect. It is also commonly used as a hydrogen trap in high strength steels to improve the hydrogen-induced delayed fracture resistance of the steel. The addition amount of vanadium in the invention is controlled to be 0-0.8%.
Zirconium Zr: one of the strong carbide forming elements can play a role in fine grain strengthening and precipitation strengthening. The adding amount of zirconium is controlled to be 0-0.2 percent.
N: forming compounds with Al, Ti, Nb, V, Zr, etc. to refine the crystal grains. Meanwhile, the material is also an austenite region enlarging element, so that the stability of metastable austenite can be improved. The addition amount of N in the invention is 0.001-0.03%.
Rare earth RE: has the functions of deoxidation and desulfurization, makes the inclusion denaturalized and improves the plasticity and toughness of the steel. When the content is higher than 0.05%, the effect is not obviously increased, so that the content of the rare earth is controlled to be 0-0.05%.
Calcium (Ca): deoxidizing and desulfurizing to modify the inclusion. The addition amount of the calcium is generally 3:1 relative to the sulfur, and the addition amount of the calcium is 0-0.03%.
More preferably, in the Cr-Mn alloyed TRIP steel, the chemical composition is preferably: c, by mass percent: 0.05-0.35%, Cr: 1.3-10.7%, Mn: 1.4-5.2%, Al: 0.001 to 3.0 percent of the total weight of the mixture,
si: 0.001-2.0%, P is less than or equal to 0.02%, S is less than or equal to 0.02%, and the balance is Fe and inevitable impurities.
More preferably, the Cr-Mn alloyed TRIP steel preferably contains 0.001 to 2.0% by mass of Al.
More preferably, the Cr-Mn alloyed TRIP steel has a Si content of 0.001 to 1.5% by mass.
More preferably, in the Cr-Mn alloyed TRIP steel, P is less than or equal to 0.015 percent and S is less than or equal to 0.01 percent in percentage by mass.
Preferably, the microstructure of the Cr-Mn alloyed TRIP steel contains 3-50% by volume of metastable austenite.
The invention provides a preparation method of the Cr and Mn alloyed TRIP steel, which comprises the following steps:
s1, producing a casting blank by continuous casting or producing a cast ingot by die casting;
s2, hot rolling or hot continuous rolling of the casting blank or the ingot:
the hot continuous rolling comprises the following steps: heating a casting blank or a cast ingot at 1100-1250 ℃, and then carrying out rough rolling and hot continuous rolling;
the hot rolling comprises: heating the casting blank or the ingot at 1100-1250 ℃, and carrying out multi-pass rolling;
s3, performing one of controlled cooling, heat treatment and cold rolling on the hot-rolled steel plate;
the heat treatment comprises: online heat treatment or offline heat treatment;
the on-line heat treatment comprises the following steps: heating the hot rolled steel plate to above Ac1 or Ac3, cooling after heat preservation to obtain a steel plate with a structure mainly comprising martensite, annealing after reheating, preserving heat for 5min-5h to complete the distribution of alloy elements, and cooling to room temperature; the off-line heat treatment comprises: directly placing the hot rolled steel plate in a heating furnace or a bell-type annealing furnace for annealing so as to carry out the distribution process of alloy elements;
the cold rolling comprises the following steps: softening annealing, pickling and cold rolling annealing;
the softening annealing comprises: putting the hot rolled steel plate into an annealing furnace, heating and preserving heat to fully soften the matrix structure; the cold rolling annealing comprises the following steps: and (3) cold rolling the acid-washed steel plate, wherein the cold rolling reduction is 10-85%, and then carrying out continuous annealing or galvanizing treatment.
Preferably, in step S1, the steel is smelted by using a converter, an electric furnace or an induction furnace, and then a casting blank is produced by continuous casting or an ingot is produced by die casting.
Preferably, in step S2, the hot continuous rolling includes: heating the casting blank or the cast ingot at 1100-1250 ℃, carrying out multi-pass rough rolling to the thickness of 30-50 mm, and carrying out 5-7-pass continuous rolling by a finishing mill group;
the hot rolling comprises: heating the casting blank or the ingot at 1100-1250 ℃, preserving heat for 1.5-2.5 h, and then hot rolling.
More preferably, the final rolling temperature of the hot rolling and the hot continuous rolling can be determined according to subsequent process requirements, and specifically, in one embodiment of the invention, a better hot rolling process condition is provided, the final rolling temperature of the hot rolling is not less than 860 ℃, the final rolling thickness is 2-4 mm, the steel plate after rolling is cooled to 500-600 ℃, the temperature is kept for 0.8-1.5 h, and the steel plate is cooled to room temperature.
Preferably, in the online heat treatment in step S3, the normal phase change process or the reverse phase change process is used for annealing and heat preservation after reheating; and obtaining a considerable volume fraction of metastable austenite through the forward phase transformation or the reverse phase transformation so as to improve the comprehensive performance of the steel plate.
Under the condition of low Cr and Mn content, the matrix structure of ferrite + bainite/martensite + metastable austenite or bainite/martensite + metastable austenite can be obtained by adopting a positive phase transformation process. Specifically, the normal phase transformation process comprises the following steps: heating the steel plate to 940-960 ℃, preserving heat for 3-7 min, and then preserving heat for 5-10 min at 250-350 ℃;
in the case of higher alloy content or higher elongation requirement, a reverse transformation process can be used to obtain a higher volume fraction (> 10%) of metastable austenite. Specifically, the reverse phase transition process comprises the following steps: heating the steel plate to 940-960 ℃, preserving heat for 3-7 min, then carrying out oil quenching to room temperature, and preserving heat for 0.8-2 h at 600-700 ℃ for the oil-quenched steel plate.
Preferably, in the cold rolling process in step S3, the softening annealing includes: putting the hot rolled steel plate into an annealing furnace, heating to a ferrite-austenite two-phase region or an austenite-cementite two-phase region, preserving heat for 1-5 hours to fully soften a matrix structure, and cooling to room temperature; the cold rolling annealing comprises the following steps: and (3) cold rolling the acid-washed and dephosphorized steel plate at room temperature, wherein the cold rolling reduction amount is 30-70%, and then continuously annealing, wherein the temperature of a soaking section of the continuous annealing is 680-850 ℃, the temperature of a slow cooling section is 580-810 ℃, and the temperature of a fast cooling section is 250-270 ℃.
Compared with the prior art, the invention has the following advantages:
(1) the Cr and Mn alloyed TRIP steel provided by the invention is based on C, Cr and Mn, the content of Mn in a matrix is reduced, the content of Cr is increased, metastable austenite with a considerable volume fraction is obtained by adding Cr, and the performance is further adjusted and improved by matching with other alloy elements, so that the TRIP steel with higher comprehensive mechanical property is obtained on the premise of low production difficulty.
(2) The production process of the TRIP steel provided by the invention can be selected and adjusted according to requirements, and after a casting blank meeting the requirements of chemical components is subjected to hot rolling, the casting blank can be directly controlled to be cooled, or subjected to online or offline heat treatment, or a hot rolled coil is subjected to cold rolling, so that a high-performance hot rolled steel plate and a high-performance cold rolled steel plate meeting the requirements of strength, elongation and the like are finally obtained.
Drawings
FIG. 1 is a microstructure diagram of an annealed structure of a hot-rolled sheet according to the present invention.
FIG. 2 is a microstructure diagram of an annealed structure of a cold-rolled sheet according to the present invention.
Detailed Description
In order to facilitate understanding of the present invention, the present invention will be described in more detail with reference to the following examples, but the scope of the present invention is not limited to the following specific examples.
Unless otherwise defined, all terms of art used hereinafter have the same meaning as commonly understood by one of ordinary skill in the art. The terminology used herein is for the purpose of describing particular embodiments only and is not intended to limit the scope of the present invention. For example, the room temperature in the present invention means an indoor temperature of 10 to 35 ℃.
Unless otherwise specifically stated, various raw materials, reagents, instruments, equipment and the like used in the present invention are commercially available or can be prepared by existing methods.
The Cr, Mn alloyed TRIP steel of the present invention and the method of manufacturing the same will be described in detail with reference to a number of specific examples. The specific chemical components and process conditions are determined mainly aiming at the development of hot rolled steel plates and cold rolled steel plates for automobiles in the embodiment of the invention, but the idea of the invention is also suitable for medium plates, profiles and bar wires.
Example 1
The embodiment provides Cr and Mn alloyed TRIP steel and a preparation method thereof, and the preparation method comprises the following steps:
(1) smelting of steel: this example was smelted in a laboratory vacuum induction furnace and cast into 50kg square ingots. In the embodiment, 10-furnace steel is smelted, the number of the 10-furnace steel is 1-10, the chemical components corresponding to each steel are shown in table 1, the content of the element corresponding to the element in table 1 is the mass percentage content, and the steel in each steel comprises the element corresponding to table 1 and the balance of Fe and inevitable impurities.
TABLE 11-10 chemical composition table (unit: wt%)
Figure BDA0002174173080000071
(2) Hot rolling
Heating the steel ingot at 1100-1250 ℃, and carrying out hot rolling after heat preservation for about 2 h. The final rolling thickness is 3mm, and the final rolling temperature is not lower than 860 ℃. After rolling, the steel plate is immediately placed into a box type heating furnace at 500-600 ℃ after being cooled to 500-600 ℃, and the furnace is cooled to room temperature after heat preservation for 1h so as to simulate the coiling process.
(3) Heat treatment of hot rolled steel sheet
Heating the hot-rolled steel sheet to Ac1 (680-780 ℃) or higher to partially austenitize or fully austenitize the hot-rolled steel sheet, and cooling the hot-rolled steel sheet after heat preservation.
Aiming at No. 1-8 steel, an inverse phase change process is adopted, and the steps comprise: the steel plate was heated to 950 ℃ and held for 5min, followed by oil quenching to room temperature. And then placing the oil-quenched steel plate into a box furnace at 600-700 ℃ for heat preservation for 1h, and finally air-cooling to room temperature.
Aiming at No. 9-10 steel, a positive phase transformation process is adopted, and the steps comprise: heating the steel plate to 950 ℃ and preserving heat for 5min, then putting the steel plate into a salt bath furnace with the temperature of about 300 ℃ and preserving heat for 5min, and then air-cooling the steel plate to room temperature.
The specific heat treatment process conditions for each steel, and the mechanical properties of the hot rolled steel sheets obtained by the different heat treatment process conditions are shown in Table 2. The microstructure of the annealed structure of the hot-rolled steel plate No. 2 is shown in the attached FIG. 1.
TABLE 2 mechanical Properties of the hot-rolled Steel sheets after Heat treatment by different Processes
Steel grade Heat treatment process Rp0.2/MPa Rm/MPa A/％
1 5min at 950 ℃; oil quenching; at 640 ℃ for 1 h; air cooling 633 912 35
2 5min at 950 ℃; oil quenching; at 640 ℃ for 1 h; air cooling 662 981 42
3 950℃,5min; oil quenching; 650 ℃ for 1 h; air cooling 648 967 46
4 5min at 950 ℃; oil quenching; 690 ℃ and 1 h; air cooling 476 872 54
5 5min at 950 ℃; oil quenching; 660 ℃,1 h; air cooling 735 1035 43
6 5min at 950 ℃; oil quenching; 660 ℃,1 h; air cooling 657 978 42
7 5min at 950 ℃; oil quenching; 650 ℃ for 1 h; air cooling 792 1056 41
8 5min at 950 ℃; oil quenching; 650 ℃ for 1 h; air cooling 826 1127 38
9 5min at 950 ℃; at 270 ℃ for 5 min; air cooling 1026 1360 14
10 5min at 950 ℃; at 260 ℃ for 5 min; air cooling 956 1290 15
Example 2
In this embodiment, a group of cold-rolled sheets is prepared from the steels No. 1 to 10 obtained in example 1 under different process conditions, and the preparation steps include:
(1) smelting of steel: in this example, steels Nos. 1 to 10 of example 1 were used, and the steels were cast into 50kg ingots by smelting in a laboratory vacuum induction furnace.
(2) Hot rolling: the hot rolling process was identical to example 1.
(3) Cold rolling: softening and annealing the hot rolled plate corresponding to the No. 1-10 steel, wherein the softening and annealing process is different according to different chemical components, the general principle is that the hot rolled plate is heated to a two-phase region (680-phase 980 ℃) and is kept for 1-5 hours, the hot rolled plate is pickled after being cooled to room temperature, and finally the cold rolled plate is cold rolled at room temperature. The cold rolling reductions of the steels No. 1 to 10 in this example were all 50%. The steel plate after cold rolling is cut to a proper size, a continuous annealing process is simulated on a continuous annealing simulator, and the specific parameters of the cold rolling continuous annealing process and the mechanical properties of the cold-rolled steel plate obtained under different process conditions are shown in Table 3. The microstructure of the annealed structure of the cold-rolled steel sheet No. 2 is shown in FIG. 2.
TABLE 3 mechanical Properties of Cold-rolled sheets treated by different Processes
Steel grade Heat treatment process Rp0.2,Rel/MPa Rm/MPa A/％
1 Soaking at 680 deg.C; slow cooling 580; quick cooling 260 816 967 17
2 Soaking at 680 deg.C; slow cooling 580; quick cooling 260 823 985 21
3 Soaking at 700 deg.c; slow cooling is carried out, wherein the cooling speed is 600; quick cooling 260 623 1075 19
4 Soaking 720 parts of heat; slow cooling 620; quick cooling 260 475 895 48
5 Soaking at 700 deg.c; slow cooling is carried out, wherein the cooling speed is 600; quick cooling 260 712 1145 18
6 Soaking at 680 deg.C; slow cooling 580; quick cooling 260 845 1056 29
7 Soaking at 680 deg.C; slow cooling 580; quick cooling 260 917 1150 28
8 Soaking at 700 deg.c; slow cooling is carried out, wherein the cooling speed is 600; quick cooling 260 883 1132 35
9 Soaking at 850 deg.C; slow cooling 810; quick cooling 260 855 1186 16
10 Soaking at 850 deg.C; slow cooling 810; quick cooling 260 826 1167 17
While preferred embodiments of the present invention have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all such alterations and modifications as fall within the scope of the invention.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.

Claims (5)

1. A preparation method of Cr and Mn alloyed TRIP steel is characterized by comprising the following steps: the method comprises the following steps:
s1, producing a casting blank by continuous casting or producing a cast ingot by die casting;
s2, hot rolling or hot continuous rolling of the casting blank or the ingot:
the hot continuous rolling comprises the following steps: heating a casting blank or a cast ingot at 1100-1250 ℃, and then carrying out rough rolling and hot continuous rolling;
the hot rolling comprises: heating the casting blank or the ingot at 1100-1250 ℃, and carrying out multi-pass rolling;
s3, performing heat treatment on the hot-rolled steel plate;
the heat treatment comprises: carrying out online heat treatment;
the on-line heat treatment comprises the following steps: heating the hot rolled steel plate to above Ac1, cooling after heat preservation to obtain a steel plate with a structure mainly comprising martensite, heating, annealing, preserving heat for 5min-5h, and cooling to room temperature;
in the online heat treatment, a normal phase change process or a reverse phase change process is adopted for annealing and heat preservation after reheating;
the normal phase transformation process comprises the following steps: heating the steel plate to 940-960 ℃, preserving heat for 3-7 min, and then preserving heat for 5-10 min at 280-320 ℃;
the reverse phase change process comprises the following steps: heating the steel plate to 940-960 ℃, preserving heat for 3-7 min, then carrying out oil quenching to room temperature, and preserving heat for 0.8-2 h at 600-700 ℃ for the oil-quenched steel plate;
the Cr and Mn alloyed TRIP steel comprises the following chemical components: c, by mass percent: 0.03-0.5%, Cr: 0.8 to 11.0%, Mn: 0.1-7.0%, Al: 0.001-3.0%, Si: 0.001-2.0%, P is less than or equal to 0.02%, S is less than or equal to 0.02%, and the balance is Fe and inevitable impurities.
2. Method of producing a Cr, Mn alloyed TRIP steel according to claim 1, characterized in that: the chemical components of the Cr and Mn alloyed TRIP steel further comprise: by mass percent, Ni: 0-3.0%, Mo: 0-0.8%, Cu: 0-2.0%, B: 0-0.005%, Nb: 0-0.2%, Ti: 0-0.3%, V: 0-0.8%, Zr: 0-0.2%, N: 0.001-0.3%, rare earth elements: 0-0.005%, Ca: 0-0.03% of one or more of the above-mentioned materials.
3. Method for producing a Cr, Mn alloyed TRIP steel according to claim 1 or 2, characterized in that: the Cr and Mn alloyed TRIP steel comprises the following chemical components: c, by mass percent: 0.05-0.35%, Cr: 1.3-10.7%, Mn: 1.4-5.2%, Al: 0.001-3.0%, Si: 0.001-2.0%, P is less than or equal to 0.02%, S is less than or equal to 0.02%, and the balance is Fe and inevitable impurities.
4. Method of producing a Cr, Mn alloyed TRIP steel according to claim 1, characterized in that: the microstructure of the Cr and Mn alloyed TRIP steel contains 3-50% of metastable austenite in volume percentage.
5. Method of producing a Cr, Mn alloyed TRIP steel according to claim 1, characterized in that: in step S2, the hot continuous rolling includes: heating the casting blank or the cast ingot at 1100-1250 ℃, carrying out multi-pass rough rolling to the thickness of 30-50 mm, and carrying out 5-7-pass continuous rolling by a finishing mill group;
the hot rolling comprises: heating the casting blank or the cast ingot at 1100-1250 ℃, carrying out heat preservation for 1.5-2.5 h, carrying out hot rolling, wherein the final rolling temperature of the hot rolling is more than or equal to 860 ℃, the final rolling thickness is 2-4 mm, cooling the rolled steel plate to 500-600 ℃, carrying out heat preservation for 0.8-1.5 h, and cooling to room temperature.
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Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101638749A (en) * 2009-08-12 2010-02-03 钢铁研究总院 Automobile steel with low cost and high strength ductility balance and preparation method thereof
CN108546812A (en) * 2018-05-14 2018-09-18 东北大学 A kind of preparation method of high-strength medium managese steel plate

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101638749A (en) * 2009-08-12 2010-02-03 钢铁研究总院 Automobile steel with low cost and high strength ductility balance and preparation method thereof
CN108546812A (en) * 2018-05-14 2018-09-18 东北大学 A kind of preparation method of high-strength medium managese steel plate

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