CN114480808A - 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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- CN114480808A CN114480808A CN202210135102.9A CN202210135102A CN114480808A CN 114480808 A CN114480808 A CN 114480808A CN 202210135102 A CN202210135102 A CN 202210135102A CN 114480808 A CN114480808 A CN 114480808A
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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
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 alloy components of the manganese steel, smelting, forging and hot rolling the raw materials, annealing the manganese steel in a hot rolling state in a two-phase region, processing an annealed steel plate into a bar-shaped sample and carrying out torsion treatment on the bar-shaped sample; the torsion processing method comprises the following steps: the annealed steel sheet is processed into a bar-like sample, and the bar-like sample is twisted at a twist rate of 60 to 120 DEG/min by 30 to 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 rolling state is subjected to two-phase region annealing, a specific torsion process is matched to prepare the novel medium manganese steel with a composite gradient structure in which phase-change martensite, austenite and ferrite, and crystal grain size and dislocation density are in gradient distribution from the outside 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 the TRIP effect, the strain gradient effect, the dislocation strengthening and the 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 been developed for three generations, the first generation of advanced high-strength steel has lower cost, but the product of strength and elongation is also lower, and the requirement of the automotive steel field is difficult to meet. The strength-elongation product of the second-generation advanced high-strength steel can reach 50 GPa%, but the added alloy elements are higher than 25%, the manufacturing difficulty is high, and the application of the second-generation advanced high-strength steel is limited. The medium manganese steel (with the manganese content of 4-12%) is one of typical representatives of the third-generation advanced high-strength steel, the strength-product of the medium manganese steel can reach 30 GPa%, and the cost of the medium manganese steel 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 of energy conservation and emission reduction and the sound of light weight of automobiles, the research and development of advanced high-strength steel with higher strength (yield strength and tensile strength) and more excellent plasticity is urgent. The medium manganese steel matrix generally consists of austenite and ferrite, and the austenite (about 30 percent) undergoes martensite phase transformation in the deformation process, so that the medium manganese steel matrix has excellent properties of high strength, high plasticity and the like. However, the yield strength of medium manganese steel is generally low (<680MPa), and the higher and higher collision safety requirements in the automobile industry are difficult to meet.
In recent years, as a new field, a gradient structure material gradually draws attention, the gradient structure means that microstructure characteristics (phase, grain size, dislocation density, texture, element distribution and the like) are in continuous gradient distribution in space, the gradient material has a natural transition internal structure, and the coordination effect among different regions enables the gradient material to have a plurality of remarkable mechanical properties including ultrahigh strength, excellent strain strengthening capability, good plasticity, excellent corrosion resistance and the like. Chinese patent CN201711173222.3 discloses a method for preparing high-strength high-toughness martensite austenite dual-phase steel, which is characterized in that the method carries out single-phase torsion or repeated torsion on the austenite steel to prepare the austenite steel with martensite presenting gradient distribution, so that the yield strength and the tensile strength are effectively improved. However, the plasticity of this material is accompanied by a large drop.
Disclosure of Invention
Technical problem to be solved
In view of the defects and shortcomings of the prior art, the invention provides a preparation method of manganese steel in a composite gradient structure, which enables a medium manganese steel matrix to present composite gradient structure characteristics from the outside to the inside, and the composite gradient structures comprise austenite, phase-change martensite, ferrite, grain size and dislocation density which are in gradient distribution, so that the yield strength of the medium manganese steel is greatly improved, and simultaneously, high-strength plasticity is obtained, thereby improving the performance of the medium manganese steel and meeting the requirements of steel for the automobile industry.
(II) technical scheme
In order to achieve the purpose, the invention adopts the main technical scheme that:
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 and hot rolling, carrying out two-phase region annealing on the medium manganese steel in a hot rolling state, processing the annealed steel plate into a bar-shaped sample and carrying out torsion treatment; the torsion processing method comprises the following steps: the annealed steel sheet is processed into a bar-like sample, and the bar-like sample is twisted at a twist rate of 60 to 120 DEG/min to 30 to 270 deg.
Wherein, the working procedures of smelting, forging, hot rolling, two-phase region annealing and the like can be carried out according to the traditional/conventional preparation process of the medium manganese steel.
In the present invention, as a preferred embodiment of the present invention, the total angle of twist is 30 to 270 °. For medium manganese steel, the torsion angle is too small, the shear stress or strain of a steel bar matrix is insufficient, the austenite phase variable is small (the martensite content is insufficient), and an effective gradient structure cannot be generated; on the contrary, the torsion angle is too large, the shear strain is too large, a large number of defects (particularly surface regions) are formed 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 according to the alloy components of the medium manganese steel to prepare a steel ingot, heating the steel ingot to 1200 ℃, preserving heat for 1.5-3h, and forging the steel ingot into a billet with the thickness of 30-50 mm; heating the steel billet to 1200 ℃, preserving heat for 1-2h, carrying out multi-pass hot rolling, and then air-cooling to room temperature, wherein the final rolling temperature is not lower than 900 ℃, thus obtaining a hot-rolled plate blank;
s2, two-phase region annealing: annealing the hot rolled plate blank prepared by S1 at 660-720 ℃ for 1-3h, and then air-cooling to room temperature to obtain an annealed steel plate;
s3, room-temperature torsion: the annealed steel sheet of S2 was processed into a bar-like specimen, and twisted at a twist rate of 60 to 120 °/min by 30 to 270 °.
The medium manganese steel needs homogenization treatment before forging or hot rolling, and the conventional temperature of the homogenization treatment is 1200 ℃, so as to ensure that the steel billet does not crack in the forging and hot rolling processes of the medium manganese steel. The prior austenite crystal grain size is too large when the homogenization treatment temperature is too high, the strength is insufficient, and the homogenization degree is insufficient when the temperature is too low. The annealing temperature is between the two-phase region temperature, the annealing heat preservation time is related to the actual annealing temperature, the higher the annealing temperature is, the shorter the required heat preservation time is, and the longer the annealing temperature is. However, too long a holding time may result in coarse grain size, complete recrystallization, insufficient strength, etc., while too short a holding time may result in insufficient austenite content and may adversely affect the performance. As for the twisting rate, the prior art (CN201711173222.3) discloses that the twisting rate is 10 to 1800 DEG/min, and the twisting rates used are 10 DEG/min, 720 DEG/min, 1800 DEG/min and the like, but the resulting steel-plastic properties are low.
As a preferred embodiment of the invention, the medium manganese steel comprises the following alloy 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 Fe.
In the medium manganese steel alloy components, Al and Ni with the mass fraction of 1-3% are added, and NiAl precipitation can be generated so as to increase the precipitation strengthening effect; meanwhile, the content ratio of austenite can be increased by a proper amount of Ni. In addition, the addition of Al and Ni can regulate the stacking fault energy of the medium manganese steel and improve the stability of austenite. Rare earth Ce is added for purifying a matrix, the grain size of the medium manganese steel is refined, the austenite stability is improved, the high austenite stability is beneficial to improving the gradient rate of martensite from the surface to the inside of the round rod in the twisting process, namely the high austenite stability can ensure that the austenite from the center of the round rod to the middle position does not undergo martensite phase transformation (or a small amount of phase transformation), and the austenite on the surface with the maximum shearing force or shearing strain and the positions nearby mostly undergo martensite phase transformation, so that the round rod generates a maximum gradient structure from the surface to the inside. And if the austenite stability is lower, the positions except the core part of the steel rod after torsion all have martensite phase transformation, and the difficulty of forming a composite gradient structure is increased.
In the present invention, the components of the medium manganese steel are not particularly specified, and as long as the austenite content in the annealed steel billet matrix is greater than 40% and the austenite has high stability, the high yield strength and plasticity of the steel can be achieved through the processes of hot rolling, two-phase region annealing and twisting. The above-mentioned medium manganese steel alloy composition can satisfy the requirements of "the austenite content in the annealed steel billet matrix is greater than 40% and the austenite has high stability".
The invention mainly produces an austenite-ferrite two-phase structure by annealing after hot rolling a billet, and then utilizes torsion to make austenite in different positions of a round bar generate different martensite phase changes from the surface to the inside, thereby producing a gradient structure of martensite and austenite phases; in addition, due to torsion, the dislocation density and the grain size of the sample from the surface to the inside are correspondingly changed, so that a composite gradient structure is generated, and the strength and the plasticity of the medium manganese steel are greatly improved through various strengthening and toughening synergistic effects of a TRIP effect, a strain gradient effect (HDI strengthening + HDI processing hardening) + precipitation strengthening + dislocation strengthening and the like in the deformation process.
The invention provides manganese steel in a composite gradient structure, which is prepared by adopting the scheme.
Compared with the medium manganese steel (with a homogeneous structure) prepared by the traditional process and having the same alloy components, the yield strength of the medium manganese steel with the composite gradient structure prepared by the invention is improved by 25-45%, the elongation is improved by 0-49%, the tensile strength is slightly improved at the same time, and the product of strength and elongation is improved by 5-50%.
(III) advantageous effects
The manganese steel in the composite gradient structure has the following characteristics: (1) different from the gradient structure disclosed by the prior art, the manganese steel with the composite gradient structure mainly comprises phase gradients (austenite, phase-change martensite and ferrite), a grain size gradient and a dislocation density gradient. During the deformation process of the novel medium manganese steel, the TRIP effect, the strain gradient effect, the dislocation strengthening effect, the precipitation strengthening effect and other synergistic effects are generated, so that the strength (tensile strength and yield strength) and the 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 requirements that the tensile strength is more than 1250MPa, the yield strength is more than 680MPa, the elongation rate reaches 25-35 percent, and the maximum product of strength and elongation can reach about 45 GPa.
Drawings
FIG. 1 shows EBSD phase diagrams and KAM diagrams of different parts of the medium manganese steel (example 1) with a composite gradient structure according to the present invention.
FIG. 2 is a graph showing hardness distribution curves from the center to the surface position of the medium manganese steel having a composite gradient structure according to the present invention (example 1) and the manganese steel having a homogeneous structure (comparative example).
FIG. 3 is a graph showing the engineering stress-strain curves of the medium manganese steel having a composite gradient structure (example 1) and the medium manganese steel having a homogeneous structure of the same composition (comparative example).
FIG. 4 is a graph showing the engineering stress-strain curves of the medium manganese steel having a composite gradient structure (example 2) and the medium manganese steel having a homogeneous structure of the same composition (comparative example).
FIG. 5 is a graph showing the engineering stress-strain curves of the medium manganese steel having a composite gradient structure according to the present invention (example 3) and the medium manganese steel having 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 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 larger gradient from the surface to the inner shear strain, so that different parts of the steel bar are subjected to martensite phase transformation with different degrees, and the defects of different dislocation densities and the like are generated. In addition, the existence of the gradient shear strain enables ferrite to generate plastic deformation of different degrees, further grain refinement of different degrees is realized, and finally the structural characteristic of composite gradient from the outside to the inside is formed. The structural characteristics of the composite gradient can greatly improve the strength (yield strength) and plasticity of the material.
According to the invention, through the design of the alloy components of the medium manganese steel (the design mainly considers the stacking fault energy, austenite content and stability, phase transition temperature, phase transition dynamics and the like), and based on the martensite phase transition characteristics of the medium manganese steel and the principle that a large amount of dislocation and shear (BCC crystal grains can be refined by large plastic deformation) are generated in the phase transition process, the two-phase region annealing is carried out on the medium manganese steel in a hot rolling state, and the specific torsion process is matched to prepare the novel medium manganese steel with the composite structure of the phase transition martensite, austenite, crystal grain size and dislocation density which are in gradient distribution from the outside to the inside, and in the subsequent deformation process, through the synergistic effect of TRIP effect, gradient effect, dislocation strengthening and precipitation strengthening, the yield strength of the medium manganese steel is greatly improved, and meanwhile, the plasticity of the medium manganese steel is also greatly improved.
For the purpose of better explaining the present invention and to facilitate understanding, the present invention will be described in detail by way of specific embodiments with reference to the accompanying 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 comprises the following components in design: 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 above% is mass percentage.
(2) Smelting, forging and hot rolling: and (3) carrying out vacuum melting according to the alloy components to prepare a steel ingot, carrying out heat preservation on the steel ingot at 1200 ℃ for 2h, forging the steel ingot into a plate blank with the thickness of 50mm, and carrying out air cooling to room temperature. And then heating the plate blank to 1200 ℃, preserving heat for 2h, rolling the plate blank into a plate blank with the thickness of 15mm for 3 times, wherein the final rolling temperature is not lower than 900 ℃, and obtaining the hot rolled plate blank.
(3) And (3) annealing the two-phase region: and annealing the hot-rolled plate blank at 680 ℃ for 1h, and then air-cooling to room temperature to obtain the annealed steel plate.
(4) Twisting at room temperature: 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 this example 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 austenite, ferrite and phase-change martensite contents at the center are 53.6%, 44.4% and 2%, respectively; the contents of austenite, ferrite and phase-change martensite at the intermediate position (around the central position) were 50.8%, 49.2% and 0%, respectively, and the contents of austenite, ferrite and phase-change martensite at the surface position were 29.5%, 55.5% and 15%, respectively. The dislocation density (KAM value) gradually decreases from the outside to the inside. The average grain sizes of austenite and ferrite at the central position are respectively as follows: 0.55 μm and 0.45 μm; the average grain sizes of austenite and ferrite at the middle position (around the center position) of the sample are respectively as follows: 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. mu.m.
As shown in fig. 2, the hardness of the 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 in the embodiment is shown in fig. 3, the tensile strength is 1253MPa, the yield strength is 682MPa, the elongation is 34.3%, and the product of strength and elongation is as high as 43 GPa. In the homogeneous structure of the same alloy components prepared by the traditional preparation process, the tensile strength of the manganese steel (comparative example) is 1249MPa, the yield strength is 545MPa, the elongation is 23 percent, and the product of strength and elongation is 28 GPa. As can be seen by comparison, the tensile strength of the manganese steel in the composite gradient structure prepared by the embodiment is slightly increased, the yield strength is improved by more than 25%, the elongation is increased by 49.1%, and the product of strength and elongation is increased by 53.6%.
The manganese steel in the homogeneous structure of the comparative example was prepared by following the steps (1) to (3) of example 1, but without performing the treatment of step (4). That is, the alloy composition of the middle manganese steel of the comparative example was the same as that of example 1, and the smelting, forging and hot rolling, two-phase zone annealing, etc. of steps (2) to (3) were all referred to example 1 except that the twisting treatment was not performed, and finally, the middle manganese steel of the homogeneous structure was prepared.
Example 2
This example provides a method for preparing manganese steel in a composite gradient structure, the steps (1) to (3) are the same as those in example 1, and the step (4) is changed to: the annealed steel sheet was processed into a bar-like specimen and twisted at a rate of 90 DEG/min by 90 deg.
The engineering stress-strain curve of the manganese steel in the composite gradient structure prepared in the embodiment is shown in fig. 4, the tensile strength is 1298MPa, the yield strength is 704MPa, the elongation is 29.3%, and the product of strength and elongation is as high as 38 GPa. Compared with the homogeneous structure medium manganese steel with the same alloy components prepared by the traditional preparation process, the composite gradient structure medium manganese steel prepared by the embodiment has the advantages that the tensile strength is obviously increased, the yield strength is improved by over 29.1 percent, the elongation is increased by 27.4 percent, and the product of strength and elongation is increased by 35.7 percent.
Example 3
This example provides a method for preparing manganese steel in a composite gradient structure, the steps (1) to (3) are the same as those in example 1, and the step (4) is changed to: the annealed steel sheet was processed into a bar-shaped specimen and twisted at a rate of 60 DEG/min by 180 deg.
The engineering stress-strain curve of the manganese steel in the composite gradient structure prepared in the embodiment is shown in fig. 5, the tensile strength is 1305MPa, the yield strength is 792MPa, the elongation is 24%, and the product of strength and elongation is as high as 31 GPa. Compared with the homogeneous structure medium manganese steel with the same alloy components prepared by the traditional preparation process, the composite gradient structure medium manganese steel prepared by the embodiment has the advantages that the tensile strength is obviously increased, the yield strength is improved by over 45.3 percent, the elongation is slightly increased, and the product of strength and elongation is increased by 10.7 percent.
Finally, it should be noted that: the above embodiments are only used to illustrate the technical solution of the present invention, and not to limit the same; while the invention has been described in detail and with reference to the foregoing embodiments, it will be understood by those skilled in the art that: the technical solutions described in the foregoing embodiments may still be modified, or some or all of the technical features may be equivalently replaced; and the modifications or the substitutions do not make the essence of the corresponding technical solutions depart from the scope of the technical solutions of the embodiments of the present invention.
Claims (6)
1. The preparation method of the manganese steel in the composite gradient structure is characterized by comprising the following steps:
preparing raw materials according to preset medium manganese steel alloy components, smelting, forging and hot rolling, carrying out two-phase region annealing on the medium manganese steel in a hot rolling state, processing the annealed steel plate into a bar-shaped sample and carrying out torsion treatment; the torsion processing method comprises the following steps: the annealed steel sheet is processed into a bar-like sample, and the bar-like sample is twisted at a twist rate of 60 to 120 DEG/min to 30 to 270 deg.
2. The method of claim 1, wherein the method comprises:
s1, smelting, forging and hot rolling: vacuum smelting according to the alloy components of the medium manganese steel to prepare a steel ingot, heating the steel ingot to 1200 ℃, preserving heat for 1.5-3h, and forging the steel ingot into a billet with the thickness of 30-50 mm; heating the steel billet to 1200 ℃, preserving heat for 1-2h, carrying out multi-pass hot rolling, and then air-cooling to room temperature, wherein the final rolling temperature is not lower than 900 ℃, thus obtaining a hot-rolled plate blank;
s2, two-phase region annealing: annealing the hot rolled plate blank prepared by S1 at 660-720 ℃ for 1-3h, and then air-cooling to room temperature to obtain an annealed steel plate;
s3, room-temperature torsion: the annealed steel sheet of S2 was processed into a bar-like specimen and twisted at a twist rate of 60 to 120 DEG/min to 30 to 270 deg.
3. The production method according to claim 1 or 2, characterized in that the austenite content in the medium manganese steel matrix is > 40% by two-phase zone annealing.
4. The preparation method according to claim 1 or 2, wherein 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 Fe.
5. Manganese steel in a composite gradient structure, produced by the method of any one of claims 1 to 4.
6. The manganese steel in the composite gradient structure as set forth in claim 5, wherein the manganese steel in the gradient structure has tensile strength of 1250MPa, yield strength of 680MPa or more, elongation of 25-35%, and product of strength and elongation of 45 GPa%.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN117358756A (en) * | 2023-09-26 | 2024-01-09 | 安徽富凯特材有限公司 | Rolling method for improving internal structure of ferronickel-chromium high-temperature corrosion-resistant alloy |
| CN117385149A (en) * | 2023-10-16 | 2024-01-12 | 河北工程大学 | Austenitic stainless steel wire rod with gradient nano dislocation structure and preparation method thereof |
| CN117358756B (en) * | 2023-09-26 | 2024-05-14 | 安徽富凯特材有限公司 | Rolling method for improving internal structure of ferronickel-chromium high-temperature corrosion-resistant alloy |
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| CN117358756B (en) * | 2023-09-26 | 2024-05-14 | 安徽富凯特材有限公司 | Rolling method for improving internal structure of ferronickel-chromium high-temperature corrosion-resistant alloy |
| CN117385149A (en) * | 2023-10-16 | 2024-01-12 | 河北工程大学 | Austenitic stainless steel wire rod with gradient nano dislocation structure and preparation method thereof |
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