CN114480808B - Manganese steel in composite gradient structure and preparation method thereof - Google Patents
Manganese steel in composite gradient structure and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B39/00—Arrangements for moving, supporting, or positioning work, or controlling its movement, combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B39/20—Revolving, turning-over, or like manipulation of work, e.g. revolving in trio stands
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- 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
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Abstract
The invention relates to a preparation method of manganese steel in a composite gradient structure, which comprises the steps of preparing raw materials according to preset manganese steel alloy components, smelting, forging, hot rolling, carrying out two-phase zone annealing on the hot-rolled manganese steel, processing the annealed steel plate into a rod-shaped sample, and carrying out torsion treatment; the torsion treatment method comprises the following steps: the annealed steel sheet is processed into a rod-shaped sample, and the rod-shaped sample is twisted at a twist rate of 60-120 DEG/min for 30-270 deg. According to the invention, through the design of the alloy components of the medium manganese steel, the medium manganese steel in a hot rolled state is annealed in a two-phase region, and a specific torsion process is matched to prepare the novel medium manganese steel with a composite gradient structure in which the transformation martensite, austenite and ferrite, the grain size and dislocation density are distributed in a gradient manner from the surface to the inner side, and in the subsequent deformation process, the yield strength of the medium manganese steel is greatly improved and the plasticity of the medium manganese steel is also greatly improved through the synergistic effect of TRIP effect, strain gradient effect, dislocation strengthening and precipitation strengthening effect.
Description
Technical Field
The invention relates to the technical field of steel preparation, in particular to manganese steel in a composite gradient structure and a preparation method thereof.
Background
The advanced high-strength steel has undergone three generations, the first generation of advanced high-strength steel has lower cost, but the product of strength and plasticity is also lower, and the requirements of the steel field for automobiles are difficult to meet. The product of strength and plasticity of the second generation advanced high-strength steel can reach 50GPa, but the added alloy element is higher than 25 percent, the manufacturing difficulty is high, and the application of the second generation advanced high-strength steel is limited. The medium manganese steel (the manganese content is 4-12%) is one of typical representatives of the third generation advanced high-strength steel, the strength-plastic product can reach 30GPa percent, and the cost is far lower than that of the second generation advanced high-strength steel, so that the medium manganese steel has a huge application prospect in the field of automobile steel. With the rising energy saving and emission reduction and light weight of automobiles, it is urgent to develop advanced high-strength steel with higher strength (yield strength and tensile strength) and more excellent plasticity. The medium manganese steel matrix is generally composed of austenite and ferrite, and austenite (about 30%) undergoes martensitic transformation in the deformation process, so that the medium manganese steel matrix has excellent properties such as high strength and high plasticity. However, the yield strength of medium manganese steel is generally low (< 680 MPa), and it is difficult to meet the requirements of the automobile industry for higher and higher collision safety.
In recent years, gradient structure materials are increasingly attracting attention as an emerging field, wherein the gradient structure refers to microstructure characteristics (such as phase, grain size, dislocation density, texture, element distribution and the like) which are continuously distributed in a gradient manner in space, and the gradient materials have natural transition internal structures, so that the gradient materials have a plurality of remarkable mechanical properties including ultrahigh strength, excellent strain strengthening capability, good plasticity, excellent corrosion resistance and the like due to the coordination effect among different regions. Chinese patent CN201711173222.3 discloses a method for preparing high-strength high-toughness martensite austenitic dual-phase steel, which performs single-phase torsion or repeated torsion on austenitic steel to prepare austenitic steel with martensite in gradient distribution, so that yield strength and tensile strength of the austenitic steel are effectively improved. However, the plasticity of the material is accompanied by a substantial decrease.
Disclosure of Invention
First, the technical problem to be solved
In view of the above-mentioned shortcomings and disadvantages of the prior art, the present invention provides a method for preparing a manganese steel in a composite gradient structure, which makes a manganese steel matrix show a composite gradient structure characteristic from the surface to the inside, and the composite gradient structures include austenite, phase-change martensite, ferrite, grain size and dislocation density all show gradient distribution, so as to greatly improve the yield strength of the manganese steel and obtain high strength and plasticity, thereby improving the performance of the manganese steel and meeting the steel requirements for the automobile industry.
(II) technical scheme
In order to achieve the above purpose, the main technical scheme adopted by the invention comprises the following steps:
the invention provides a preparation method of manganese steel in a composite gradient structure, which comprises the following steps:
preparing raw materials according to preset medium manganese steel alloy components, smelting, forging, hot rolling, performing two-phase zone annealing on the medium manganese steel in a hot rolled state, processing the annealed steel plate into a rod-shaped sample, and performing torsion treatment; the torsion treatment method comprises the following steps: the annealed steel sheet is processed into a rod-shaped sample, and the rod-shaped sample is twisted at a twist rate of 60-120 DEG/min for 30-270 deg.
Wherein, the working procedures of smelting, forging, hot rolling, two-phase zone annealing and the like can be carried out by referring to the traditional/conventional medium manganese steel preparation process.
As a preferred embodiment of the present invention, the total angle of twist is 30-270 degrees in the present invention. For medium manganese steel, the torsion angle is too small, the shearing stress or strain of the steel bar matrix is insufficient, the austenite transformation amount is small (the martensite content is insufficient), and an effective gradient structure cannot be generated; in contrast, when the torsion angle is too large, the shear strain is too large, and a large number of defects (particularly surface areas) exist in the matrix, such as crack initiation and the like, and the performance is greatly reduced.
As a preferred embodiment of the invention, the preparation method comprises the following steps:
s1, smelting, forging and hot rolling: vacuum smelting the medium manganese steel alloy components to prepare a steel ingot, heating the steel ingot to 1200 ℃, preserving heat for 1.5-3h, and forging the steel ingot into a steel billet with the thickness of 30-50 mm; heating the billet to 1200 ℃ and preserving heat for 1-2 hours, performing hot rolling for multiple times, performing air cooling to room temperature, and obtaining a hot rolled plate blank, wherein the final rolling temperature is not lower than 900 ℃;
s2, annealing of a two-phase region: annealing the hot-rolled plate blank prepared in the step S1 at 660-720 ℃ for 1-3 hours, and then air-cooling to room temperature to obtain an annealed steel plate;
s3, room temperature torsion: the annealed steel sheet of S2 is processed into a bar-shaped specimen, and is twisted at a twist rate of 60-120 DEG/min for 30-270 deg.
The homogenization treatment is needed before forging or hot rolling of the medium manganese steel, and the conventional temperature of the homogenization treatment is 1200 ℃ so as to ensure that the steel billet is not cracked in the forging and hot rolling processes of the medium manganese steel. The homogenization treatment is performed at too high a temperature, and the prior austenite grain size is too large, the strength is insufficient, and the homogenization degree is insufficient at too low a temperature. The annealing temperature is between the two-phase region temperature, the annealing heat-preserving time is related to the actual annealing temperature, and the heat-preserving time required by the higher annealing temperature is shorter, and conversely, the longer the heat-preserving time is. However, the long heat preservation time may generate coarse grain size, complete recrystallization, insufficient strength and other phenomena, while the short heat preservation time may cause insufficient austenite content and certain influence on performance. Regarding the twist rate, the twist rate of 10 to 1800 DEG/min is disclosed in the prior art (CN 201711173222.3), and the rates used are 10 DEG/min, 720 DEG/min, 1800 DEG/min, etc., but the resulting steel has low plasticity.
As a preferred embodiment of the invention, the medium manganese steel alloy comprises the following components in percentage by mass: c:0.06-0.2%, mn 5-12%, al 1-3%, ni 1-3%, ce:0.04-0.1%, and the balance being Fe.
In the medium manganese steel alloy composition, the mass fraction of Al and Ni is increased by 1-3%, and NiAl precipitation can be generated so as to increase the precipitation strengthening effect; while a proper amount of Ni can increase the content ratio of austenite. In addition, the addition of Al and Ni can regulate and control the stacking fault energy of the medium manganese steel and improve the stability of austenite. The rare earth Ce is added for purifying the matrix, the grain size of the medium manganese steel is refined, the austenite stability is improved, the gradient rate of the round bar from the surface to the inside in the torsion process is improved by the high austenite stability, namely, the high austenite stability can ensure that the austenite from the center of the round bar to the middle position does not generate martensite phase transformation (or small amount of phase transformation), and most of the austenite at the surface and the position near the surface with the largest shearing force or shearing strain generates martensite phase transformation, so that the round bar generates the gradient structure from the surface to the inside to the greatest extent. If the austenite stability is lower, martensitic transformation is generated at the positions except the core of the steel bar after torsion, and the difficulty of forming a composite gradient structure is increased.
In the invention, the components of the medium manganese steel are not particularly limited, as long as the austenite content in the annealed billet matrix is more than 40% and the austenite has higher stability, and the high yield strength and the plasticity of the steel can be both achieved through the treatment of hot rolling, two-phase zone annealing and torsion processes. The medium manganese steel alloy composition can meet the requirement that the austenite content in the annealed steel billet matrix is more than 40 percent and the austenite has higher stability.
Annealing after hot rolling of a billet to generate an austenite-ferrite two-phase structure, and then utilizing torsion to enable austenite at different positions of a round bar from the outside to the inside to generate different martensite phase changes, so as to generate a gradient structure of martensite and austenite phases; in addition, due to torsion, dislocation density, grain size and the like of the sample from the surface to the inside are correspondingly changed, so that a composite gradient structure is generated, and in the deformation process, the strength and plasticity of the medium manganese steel are greatly improved through the toughening synergistic effects of TRIP effect, strain gradient effect (HDI strengthening+HDI work hardening) +precipitation strengthening+dislocation strengthening and the like.
The invention provides manganese steel in a composite gradient structure, which is prepared by adopting the scheme.
Compared with the manganese steel in the same alloy composition (homogeneous structure) prepared by the traditional process, the manganese steel in the composite gradient structure prepared by the invention has the advantages that the yield strength is improved by 25% -45%, the elongation is improved by 0% -49%, the tensile strength is slightly improved, and the strength-plastic product is improved by 5% -50%.
(III) beneficial effects
The manganese steel in the composite gradient structure has the following characteristics: (1) Unlike the gradient structure disclosed in the prior art, the manganese steel with composite gradient structure prepared by the invention mainly comprises a phase gradient (austenite, transformation martensite and ferrite), a grain size gradient and a dislocation density gradient. In the deformation process of the novel medium manganese steel, the generated TRIP effect, the strain gradient effect, the dislocation strengthening effect, the precipitation strengthening effect and the like have synergistic effects, so that the strength (tensile strength and yield strength) and plasticity of the medium manganese steel can be greatly improved; (2) The preparation method is simple and feasible, the required equipment is conventional equipment, the process is relatively simple, the period is short, and the operability is strong; (3) The mechanical property of the manganese TRIP steel in the gradient structure meets the conditions that the tensile strength is more than 1250MPa, the yield strength is more than 680MPa, the elongation is 25-35%, and the maximum strength-plastic product can reach about 45GPa percent.
Drawings
FIG. 1 is an EBSD phase diagram and KAM diagram of different parts of a medium manganese steel (example 1) with a composite gradient structure according to the present invention.
FIG. 2 shows the hardness distribution curves from the center to the surface of the medium manganese steel with a composite gradient structure (example 1) and the medium manganese steel with a homogeneous structure (comparative example) according to the present invention.
Fig. 3 is an engineering stress strain curve of a medium manganese steel with a composite gradient structure according to the present invention (example 1) and a medium manganese steel with a homogeneous structure of the same composition (comparative example).
Fig. 4 is an engineering stress strain curve of a medium manganese steel (example 2) having a composite gradient structure according to the present invention and a medium manganese steel (comparative example) having a homogeneous structure of the same composition.
Fig. 5 is an engineering stress strain curve of a medium manganese steel with a composite gradient structure according to the present invention (example 3) and a medium manganese steel with a homogeneous structure of the same composition (comparative example).
Detailed Description
The idea or design idea of the invention is as follows: firstly, through component design and optimization, the content of austenite and ferrite after annealing in a two-phase region is ensured to reach 50% volume ratio respectively, the stability of the austenite is proper, and the stacking fault energy is in a proper range; after the two-phase region is annealed, torsional deformation is realized by utilizing a torsion mode, and due to the existence of gradient shear strain, the steel bar has a larger gradient from the outside to the inside, so that different parts of the steel bar generate different degrees of martensitic transformation, and the defects such as different dislocation densities and the like are generated. In addition, the existence of gradient shear strain enables ferrite to generate different degrees of plastic deformation, so that different degrees of grain refinement are realized, and finally, the structural characteristics of composite gradients from the surface to the inside are formed. The structural characteristics of the composite gradient can greatly improve the strength (yield strength) and plasticity of the material.
According to the invention, by designing the alloy components of the medium manganese steel (mainly considering the fault energy, the austenite content and stability, the transformation temperature, the transformation dynamics and the like during design), and based on the martensite transformation characteristics of the medium manganese steel and the principle that a large amount of dislocation and shear (large plastic deformation can refine BCC crystal grains) are generated during the transformation process, the medium manganese steel in a hot rolled state is annealed in a two-phase region, and a specific torsion process is matched to prepare the novel medium manganese steel with a composite structure in which the transformation martensite, austenite, crystal grain size and dislocation density are distributed in a gradient manner from the surface to the inside, and in the subsequent deformation process, the yield strength of the medium manganese steel is greatly improved and the plasticity of the medium manganese steel is also greatly improved through the synergistic effect of TRIP effect, gradient effect, dislocation strengthening and precipitation strengthening.
The invention will be better explained by the following detailed description of the embodiments with reference to the drawings.
Example 1
The embodiment provides a preparation method of manganese steel in a composite gradient structure, which comprises the following steps:
(1) The manganese steel alloy in the design comprises the following components: c:0.18%, mn 7.8%, al 1.8%, ni 2.1%, ce:0.06%, P <0.008%, S <0.008%, and the balance Fe. The percentages are mass percentages.
(2) Smelting, forging and hot rolling: vacuum smelting the alloy components to prepare a steel ingot, preserving the temperature of the steel ingot at 1200 ℃ for 2 hours, forging the steel ingot into a plate blank with the thickness of 50mm, and air-cooling the steel ingot to room temperature. And then heating the slab to 1200 ℃, preserving heat for 2 hours, and rolling for 3 times to obtain a slab with the thickness of 15mm, wherein the final rolling temperature is not lower than 900 ℃, thus obtaining the hot-rolled slab.
(3) Annealing of the two-phase region: and (3) annealing the hot-rolled plate blank at 680 ℃ for 1h, and then air-cooling to room temperature to obtain the annealed steel plate.
(4) Room temperature torsion: the annealed steel sheet was processed into a bar-shaped specimen and twisted at a rate of 60 DEG/min by 60 deg.
The microstructure (left EBSD phase diagram, right KAM diagram) of the middle manganese steel prepared in the embodiment from the center to different parts of the surface is shown in fig. 1, white is austenite, gray is ferrite, black is phase-change martensite, and the contents of austenite, ferrite and phase-change martensite at the center are 53.6%, 44.4% and 2% respectively; the austenite, ferrite and transformed martensite contents in the intermediate positions (around the center position) were 50.8%, 49.2% and 0%, respectively, and the austenite, ferrite and transformed martensite contents in the surface positions were 29.5%, 55.5% and 15%, respectively. Dislocation density (KAM value) gradually decreases from the outside to the inside. The average grain sizes of austenite and ferrite at the center are respectively: 0.55 μm and 0.45 μm; the average grain sizes of austenite and ferrite at the intermediate positions (around the center position) of the sample are respectively: 0.29 μm and 0.30 μm; the average grain sizes of austenite and ferrite at the surface positions of the sample are respectively as follows: 0.22 μm and 0.21 μm.
As shown in fig. 2, the hardness of manganese steel in the gradient structure gradually increases from the center to the surface. The engineering stress strain curve of the manganese steel in the composite gradient structure prepared by the embodiment is shown in figure 3, the tensile strength is 1253MPa, the yield strength is 682MPa, the elongation is 34.3%, and the strength-plastic product is up to 43 GPa%. In the homogeneous structure of the same alloy component prepared by the traditional preparation process, the tensile strength of manganese steel (comparative example) is 1249MPa, the yield strength is 545MPa, the elongation is 23%, and the strength-plastic product is 28GPa percent. As is evident from comparison, the tensile strength of the manganese steel in the composite gradient structure prepared by the embodiment is slightly increased, the yield strength is increased by more than 25%, the elongation is increased by 49.1%, and the strength-plastic product is increased by 53.6%.
The manganese steel in the homogeneous structure of the comparative example was prepared in accordance with steps (1) to (3) of example 1, but without performing the treatment of step (4). That is, the medium manganese steel alloy of the comparative example was the same as in example 1, and the smelting, forging and hot rolling, two-phase zone annealing and the like of steps (2) to (3) were all conducted with reference to example 1, except that no twisting treatment was conducted, and finally a medium manganese steel of a homogeneous structure was produced.
Example 2
The present example provides a method for preparing manganese steel in a composite gradient structure, wherein steps (1) - (3) are the same as those of example 1, and step (4) is changed to: the annealed steel sheet was processed into a bar-shaped specimen and twisted at 90 DEG/min.
The engineering stress strain curve of the manganese steel in the composite gradient structure prepared by the embodiment is shown in fig. 4, the tensile strength is 1298MPa, the yield strength is 704MPa, the elongation is 29.3%, and the strength-plastic product is as high as 38GPa percent. Compared with the manganese steel in the homogeneous structure with the same alloy composition prepared by the traditional preparation process, the manganese steel in the composite gradient structure prepared by the embodiment has obviously increased tensile strength, the yield strength is increased by more than 29.1%, the elongation is increased by 27.4%, and the strength-plastic product is increased by 35.7%.
Example 3
The present example provides a method for preparing manganese steel in a composite gradient structure, wherein steps (1) - (3) are the same as those of example 1, and step (4) is changed to: the annealed steel sheet was processed into a bar-shaped specimen and twisted 180 ° at a rate of 60 °/min.
The engineering stress strain curve of the manganese steel in the composite gradient structure prepared by the embodiment is shown in fig. 5, the tensile strength is 1305MPa, the yield strength is 792MPa, the elongation is 24%, and the strength-plastic product is up to 31GPa percent. Compared with the manganese steel in the homogeneous structure with the same alloy composition prepared by the traditional preparation process, the manganese steel in the composite gradient structure prepared by the embodiment has the advantages that the tensile strength is obviously increased, the yield strength is increased by more than 45.3%, the elongation is slightly increased, and the strength-plastic product is increased by 10.7%.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solution of the present invention, and not for limiting the same; although the invention has been described in detail with reference to the foregoing embodiments, it will be understood by those of ordinary skill in the art that: the technical scheme described in the foregoing embodiments can be modified or some or all of the technical features thereof can be replaced by equivalents; such modifications and substitutions do not depart from the spirit of the invention.
Claims (4)
1. The preparation method of the manganese steel in the composite gradient structure is characterized by comprising the following steps of:
preparing raw materials according to preset medium manganese steel alloy components, smelting, forging, hot rolling, and carrying out two-phase zone annealing on the medium manganese steel in a hot rolled state, wherein the austenite content in a medium manganese steel matrix is more than 40% after the two-phase zone annealing; processing the annealed steel plate into a rod-shaped sample and performing torsion treatment; the torsion treatment method comprises the following steps: processing the annealed steel plate into a rod-shaped sample, and twisting the rod-shaped sample for 30-270 degrees at a twisting rate of 60-120 degrees/min;
the preset medium manganese steel alloy comprises the following components in percentage by mass: c:0.06-0.2%, mn 5-12%, al 1-3%, ni 1-3%, ce:0.04-0.1%, and the balance being Fe.
2. The preparation method according to claim 1, characterized in that the preparation method is:
s1, smelting, forging and hot rolling: vacuum smelting the medium manganese steel alloy components to prepare a steel ingot, heating the steel ingot to 1200 ℃, preserving heat for 1.5-3h, and forging the steel ingot into a steel billet with the thickness of 30-50 mm; heating the billet to 1200 ℃ and preserving heat for 1-2 hours, performing hot rolling for multiple times, performing air cooling to room temperature, and obtaining a hot rolled plate blank, wherein the final rolling temperature is not lower than 900 ℃;
s2, annealing of a two-phase region: annealing the hot-rolled plate blank prepared in the step S1 at 660-720 ℃ for 1-3 hours, and then air-cooling to room temperature to obtain an annealed steel plate;
s3, room temperature torsion: the annealed steel sheet of S2 is processed into a bar-shaped specimen, and is twisted at a twist rate of 60-120 DEG/min for 30-270 deg.
3. A manganese steel in a composite gradient structure, which is produced by the production method according to claim 1 or 2.
4. The manganese steel in the composite gradient structure according to claim 3, wherein the tensile strength of the manganese steel in the gradient structure is more than 1250MPa, the yield strength is more than 680MPa, the elongation is 25-35%, and the product of strength and elongation is up to 45 GPa%.
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1335414A (en) * | 2000-07-21 | 2002-02-13 | 大连金华特钢集团有限公司 | Forming process of heat-resisting Cr-Mn-Ni-N austenic steel rod |
| CN107893154A (en) * | 2017-11-22 | 2018-04-10 | 西南大学 | A kind of preparation method of high-strength and high ductility gradient martensitic-austenitic dual phase steel |
| CN109680130A (en) * | 2019-02-27 | 2019-04-26 | 河北工程大学 | A kind of high strength and ductility cold rolling medium managese steel and preparation method thereof |
| CN110243675A (en) * | 2019-05-10 | 2019-09-17 | 燕山大学 | A method of assessment various deformation condition influences TRIP/TWIP plate property |
| CN110551948A (en) * | 2019-10-22 | 2019-12-10 | 河北工程大学 | Low-carbon steel and preparation method thereof |
| CN110592490A (en) * | 2019-09-17 | 2019-12-20 | 北京科技大学 | High-strength-ductility plasticity-free unstable hot-rolled medium manganese steel and preparation method thereof |
| WO2021098208A1 (en) * | 2019-11-20 | 2021-05-27 | 南京钢铁股份有限公司 | 690 mpa-grade medium manganese steel medium thick steel with high strength and low yield ratio and manufacturing method therefor |
| CN113088821A (en) * | 2021-04-02 | 2021-07-09 | 河北工程大学 | Gradient grain structure high-strength and high-plasticity matching low alloy steel and preparation method thereof |
-
2022
- 2022-02-14 CN CN202210135102.9A patent/CN114480808B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1335414A (en) * | 2000-07-21 | 2002-02-13 | 大连金华特钢集团有限公司 | Forming process of heat-resisting Cr-Mn-Ni-N austenic steel rod |
| CN107893154A (en) * | 2017-11-22 | 2018-04-10 | 西南大学 | A kind of preparation method of high-strength and high ductility gradient martensitic-austenitic dual phase steel |
| CN109680130A (en) * | 2019-02-27 | 2019-04-26 | 河北工程大学 | A kind of high strength and ductility cold rolling medium managese steel and preparation method thereof |
| CN110243675A (en) * | 2019-05-10 | 2019-09-17 | 燕山大学 | A method of assessment various deformation condition influences TRIP/TWIP plate property |
| CN110592490A (en) * | 2019-09-17 | 2019-12-20 | 北京科技大学 | High-strength-ductility plasticity-free unstable hot-rolled medium manganese steel and preparation method thereof |
| CN110551948A (en) * | 2019-10-22 | 2019-12-10 | 河北工程大学 | Low-carbon steel and preparation method thereof |
| WO2021098208A1 (en) * | 2019-11-20 | 2021-05-27 | 南京钢铁股份有限公司 | 690 mpa-grade medium manganese steel medium thick steel with high strength and low yield ratio and manufacturing method therefor |
| CN113088821A (en) * | 2021-04-02 | 2021-07-09 | 河北工程大学 | Gradient grain structure high-strength and high-plasticity matching low alloy steel and preparation method thereof |
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