CN114703417A - Method for preparing superfine-grain high-toughness medium manganese steel based on TWIP effect and microalloy precipitation - Google Patents
Method for preparing superfine-grain high-toughness medium manganese steel based on TWIP effect and microalloy precipitation Download PDFInfo
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- 229910000617 Mangalloy Inorganic materials 0.000 title claims abstract description 51
- 230000000694 effects Effects 0.000 title claims abstract description 30
- 238000000034 method Methods 0.000 title claims abstract description 23
- 238000001556 precipitation Methods 0.000 title claims abstract description 19
- 238000005096 rolling process Methods 0.000 claims abstract description 40
- 238000010438 heat treatment Methods 0.000 claims abstract description 30
- 238000005098 hot rolling Methods 0.000 claims abstract description 18
- 239000013078 crystal Substances 0.000 claims abstract description 14
- 238000005242 forging Methods 0.000 claims abstract description 13
- 239000011572 manganese Substances 0.000 claims abstract description 11
- 238000003723 Smelting Methods 0.000 claims abstract description 10
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 claims abstract description 10
- 239000010955 niobium Substances 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 28
- 239000010959 steel Substances 0.000 claims description 28
- 239000002244 precipitate Substances 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 6
- 230000009467 reduction Effects 0.000 claims description 6
- 238000005457 optimization Methods 0.000 abstract 2
- 229910001566 austenite Inorganic materials 0.000 description 16
- 239000000463 material Substances 0.000 description 11
- 238000005520 cutting process Methods 0.000 description 7
- 229910052748 manganese Inorganic materials 0.000 description 7
- 230000008569 process Effects 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
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- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 230000007246 mechanism Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- VLTRZXGMWDSKGL-UHFFFAOYSA-N perchloric acid Chemical compound OCl(=O)(=O)=O VLTRZXGMWDSKGL-UHFFFAOYSA-N 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000794 TRIP steel Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 229960000583 acetic acid Drugs 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0231—Warm rolling
-
- 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
-
- 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
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Abstract
The invention discloses a method for preparing ultrafine-grained high-strength and high-toughness medium manganese steel based on TWIP effect and microalloy precipitation, which comprises the steps of smelting, forging, multi-pass hot rolling, multi-pass medium-temperature rolling and critical heat treatment, wherein in the smelting step, the proportioning is carried out according to the weight percentages of 0.05-0.2% of C, 4-7% of Mn, 0-3% of Al, 0.01-0.1% of Nb and the balance of Fe and inevitable impurities; the multi-pass medium-temperature rolling is to roll the hot rolled plate obtained by multi-pass hot rolling for 6-7 passes at the temperature range of 350-500 ℃. According to the invention, the medium manganese steel is subjected to component optimization and rolling process optimization, so that twin crystal deformation and niobium carbide precipitation are generated in the rolling process of the medium manganese steel, the purpose of grain refinement is further realized, and the mechanical property of the medium manganese steel is improved.
Description
Technical Field
The invention relates to the technical field of metal heat treatment, in particular to a method for preparing ultrafine-grained high-strength and high-toughness medium manganese steel based on TWIP effect and microalloy precipitation.
Background
At present, the promotion effect of the automobile industry on national economic development and social progress is more and more important, and the automobile industry becomes one of the main pillars of national economy. The development of the automobile industry brings a series of problems of environmental pollution, energy shortage and the like. Environmental protection, energy conservation and safety become the development theme of the automobile manufacturing industry. Among various measures for saving oil consumption and reducing exhaust emission, the effect of light weight of the automobile is most obvious. The advanced high-strength steel can obviously reduce the weight of the automobile body on the premise of not increasing the production cost of the automobile, and becomes the main material for lightening the automobile at present.
The medium manganese steel is taken as a typical representative of third-generation advanced high-strength steel, has a ferrite and austenite multiphase structure, wherein the volume fraction of austenite is up to more than 20%, under a certain heat treatment condition, the austenite in the steel structure can generate a TRIP (transformation Induced plasticity) effect in a plastic deformation process, the strength and the plasticity of the steel are improved, and compared with the traditional TRIP steel and Q & P steel, the medium manganese steel has the advantages of relatively excellent mechanical property, lower production cost, simple production process and the like, and is favored by researchers and experts in the automobile industry.
Although the existing medium manganese steel can meet the requirement of light weight of the automobile at present, the rolling process mainly comprises hot rolling and cold rolling, the grain size of the obtained medium manganese steel is mainly distributed in the range of 0.3-5 mu m, the comprehensive mechanical property is not high, and the further light weight of the automobile is limited.
Disclosure of Invention
In order to solve the technical problems, the invention provides a method for preparing ultrafine-grained high-toughness medium manganese steel based on a TWIP effect and microalloy precipitation.
The technical scheme adopted by the invention is as follows:
a method for preparing superfine crystal high-strength and high-toughness medium manganese steel based on TWIP effect and microalloy precipitation comprises the following steps;
step 1, smelting: proportioning, smelting and casting 0.05-0.2% of C, 4-7% of Mn, 0-3% of Al, 0.01-0.1% of Nb and the balance of Fe and inevitable impurities to obtain a steel ingot;
step 2, forging: heating the steel ingot to 1200-1250 ℃, preserving heat for 2-3 h, and forging into a steel billet;
step 3, multi-pass hot rolling: heating the steel billet to 1050-1200 ℃, and preserving heat for 2-3 h; carrying out hot rolling for 6-7 times at the rolling temperature range of 900-1000 ℃, and then cooling to 350-500 ℃ to obtain a hot rolled plate;
during the hot rolling, the material structure is mainly austenite, and at the moment, as the rolling reduction rate is increased continuously, austenite grains are flattened and gradually reduced in size.
Step 4, multi-pass medium-temperature rolling: rolling the hot rolled plate for 6-7 times at the temperature of 350-500 ℃ to obtain a warm rolled plate;
the rolling temperature is the control core of the invention, and the rolling temperature is in AC within the temperature range of 350-500 DEG C1And a martensite start temperature MSAt the moment, the material structure is mainly austenite, the stacking fault of the austenite can meet the condition of generating the TWIP effect, the austenite in the material structure generates twin crystal deformation along with the rolling, the grain size of the austenite is obviously reduced, and a certain volume fraction of niobium carbide is precipitated in the grain boundary and the crystal.
Step 5, critical heat treatment: and carrying out critical heat treatment on the warm-rolled plate at the temperature of 600-700 ℃ in a two-phase region to obtain the ultrafine-grained high-strength and high-toughness medium manganese steel.
In the critical heat treatment process, the material structure generates austenite and ferrite phase transformation, the early austenite generates TWIP effect to enable the material to have smaller grain size, in the process, recrystallization can be generated in grain boundary and crystal interior to form finer structure, the grain size is further refined, and the mechanical property is improved.
Preferably, in the step 2, the thickness of the obtained billet is 30-40 mm.
Preferably, in the step 3, the total rolling reduction rate of the multi-pass hot rolling is 40 to 50%. The effect of multi-pass medium temperature rolling is improved.
Preferably, in the step 4, the total rolling reduction rate of the multi-pass medium-temperature rolling is 50-90%. Within the range of the reduction ratio, the TWIP effect of the manganese steel can be fully performed in the warm rolling process, and niobium carbide can be fully separated out, so that the crystal grains are further refined.
Preferably, in the step 4, the volume fraction of the niobium carbide precipitates in the obtained warm-rolled plate is more than or equal to 10-3The average size of the niobium carbide precipitates is within the range of 1 to 20 nm.
Preferably, the heat treatment time is 30min to 1 h.
The invention has the beneficial effects that:
twinning deformation is a plastic deformation mechanism of material, also called twip (twinning induced plasticity) effect, which usually occurs in high manganese or high carbon medium manganese steel materials, and during cold deformation of low manganese or low carbon medium manganese steel, such as medium manganese steel with Mn content below 7 wt.%, the deformation mechanism is mainly TRIP effect because the stacking fault energy does not satisfy the condition for twinning deformation. However, compared with the TRIP effect, the twin deformation can obviously refine the grain size of the material and realize the synchronous improvement of the strong plasticity. The invention is designed by optimizing the components of the medium manganese steel and is adopted in the intermediate AC1And the martensite transformation starting temperature, so that the austenite fault energy in the medium manganese steel can meet the condition of generating the TWIP effect, thereby introducing twin crystal deformation into the rolling process of the medium manganese steel, and further realizing the microcosmic rolling process of the high-strength and high-toughness superfine medium manganese steelAnd (4) preparing tissues. In addition, in the process of medium and low temperature rolling, the invention fully utilizes the precipitation strengthening and fine grain strengthening of microalloy Nb element to improve the strengthening potential of the medium manganese steel, thereby further improving the mechanical property of the medium manganese steel.
Drawings
FIG. 1 is a microstructure and morphology diagram of the ultra-fine grained high-toughness medium manganese steel obtained in example 1 of the invention.
FIG. 2 is a diagram showing the morphology of the precipitates of niobium carbide in the ultra-fine grained high-toughness medium manganese steel obtained in example 2 of the present invention.
FIG. 3 is an XRD spectrum of the ultra-fine grain high-toughness medium manganese steel obtained in example 3 of the invention.
Detailed Description
The invention is further described below with reference to specific examples to facilitate understanding of the invention, but the invention is not limited thereto.
Example 1
A method for preparing superfine crystal high-strength and high-toughness medium manganese steel based on TWIP effect and microalloy precipitation comprises the following steps:
step 1, smelting: according to the following steps: c0.05 wt.%, Mn 4.0 wt.%, Al 3.0 wt.%, Nb 0.01 wt.%, and the balance Fe and inevitable impurities, and performing proportioning, vacuum melting and casting to obtain a steel ingot;
step 2, forging: heating the steel ingot to 1200 ℃, preserving heat for 2h, and forging into a steel billet with the thickness of 100mm x 40 mm;
step 3, multi-pass hot rolling: heating the steel billet to 1050 ℃, preserving heat for 2 hours, carrying out 7-pass hot rolling at the rolling temperature range of 900-1000 ℃, rolling into a hot rolled plate with the thickness of 20mm, and then cooling to 350-500 ℃;
step 4, multi-pass medium-temperature rolling: rolling the hot rolled plate at the temperature of 350-500 ℃ for 7 times to form a hot rolled plate with the thickness of 10 mm;
and 5, critical heat treatment: and carrying out critical heat treatment on the warm-rolled plate at the temperature of 600 ℃ in a two-phase region for 30min to obtain the ultrafine-grained high-strength and high-toughness medium manganese steel A.
The obtained ultra-fine grain high strength and toughness medium manganese steel A is processed into a hot tensile sample according to the ASTM-E8-E8M standard by means of wire cutting, and then tensile property test is carried out according to the tensile rate of 1.5mm/min, and the test results are shown in Table 1.
Heat-treated test pieces of 10mm × 10mm were prepared by means of wire cutting, ground stepwise to 2000# with different types of sandpaper, and then polished and etched, and microstructure observation was performed on the heat-treated test pieces, see fig. 1. As can be seen from FIG. 1, the average grain size of the ultra-fine grained high toughness medium manganese steel obtained in example 1 according to the present invention can be refined to 0.15. mu.m.
Example 2
A method for preparing superfine crystal high-strength and high-toughness medium manganese steel based on TWIP effect and microalloy precipitation comprises the following steps:
step 1, smelting: according to the following steps: c is 0.2 wt.%, Mn is 6.2 wt.%, Al is 1.5 wt.%, Nb is 0.05 wt.%, and the balance is Fe and inevitable impurities, and steel ingots are obtained by proportioning, vacuum melting and casting;
step 2, forging: heating the steel ingot to 1250 ℃, preserving heat for 3 hours, and forging into a billet with the thickness of 100mm x 30 mm;
step 3, multi-pass hot rolling: heating the steel billet to 1200 ℃, preserving heat for 2.5h, carrying out 6-pass hot rolling at the rolling temperature range of 900-1000 ℃, rolling into a hot rolled plate with the thickness of 15mm, and then cooling to 350-500 ℃;
step 4, multi-pass medium-temperature rolling: rolling the hot rolled plate at the temperature of 350-500 ℃ for 6 times to obtain a warm rolled plate with the thickness of 2 mm;
step 5, critical heat treatment: and (3) carrying out critical heat treatment on the warm-rolled plate at the temperature of 650 ℃ in a two-phase region for 1h to obtain the superfine-grain high-strength and high-toughness medium manganese steel B.
The obtained ultra-fine grain high strength and toughness medium manganese steel B is processed into a hot tensile sample according to the ASTM-E8-E8M standard by means of wire cutting, and then tensile property test is carried out according to the tensile rate of 1.5mm/min, and the test results are shown in Table 1.
Preparing heat-treated samples of 10mm x 10mm by means of wire-electrode cutting, grinding the heat-treated samples stepwise to 50-55 μm with different types of sandpaper, and punching out disks of 3mm diameter on a punch, followed by collectionContinuously grinding the mixture to 40-45 mu m by using 3000# abrasive paper; thinning and perforating by adopting an electrolysis double-spraying mode, wherein the electrolyte is a mixed solution of 5% perchloric acid and 95% glacial acetic acid; the morphology of the precipitates was analyzed by means of transmission electron microscopy, see FIG. 2. As can be seen from figure 2, the average size of the niobium carbide precipitate of the superfine crystal high-strength and high-toughness medium manganese steel obtained by the method is within the range of 1-20 nm, and the volume fraction of the niobium carbide precipitate is more than or equal to 10-3. As can be seen from FIG. 2, the invention not only utilizes the TWIP effect to refine the grain size of the medium manganese steel, but also can generate a large amount of microalloy precipitates, thereby further improving the mechanical property of the material.
Example 3
A method for preparing superfine crystal high-strength and high-toughness medium manganese steel based on TWIP effect and microalloy precipitation comprises the following steps:
step 1, smelting: according to the following steps: c is 0.2 wt.%, Mn is 7.0 wt.%, Nb is 0.1 wt.%, and the balance is Fe and inevitable impurities, and steel ingots are obtained by proportioning, vacuum melting and casting;
step 2, forging: heating the steel ingot to 1250 ℃, preserving heat for 2 hours, and forging into a billet with the thickness of 100mm x 35 mm;
step 3, multi-pass hot rolling: heating the steel billet to 1250 ℃, preserving heat for 3 hours, carrying out 7-pass hot rolling at the rolling temperature of 900-1000 ℃, rolling into a hot rolled plate with the thickness of 20mm, and then cooling to 350-500 ℃;
step 4, multi-pass medium-temperature rolling: rolling the hot rolled plate at the temperature of 350-500 ℃ for 7 times to form a warm rolled plate with the thickness of 2 mm;
step 5, critical heat treatment: and (3) carrying out critical heat treatment on the warm-rolled plate at the temperature of 680 ℃ in a two-phase region for 30min to obtain the superfine-crystal high-strength and high-toughness medium manganese steel C.
The ultra-fine grain high strength and toughness medium manganese steel C is processed into a hot tensile sample according to the ASTM-E8-E8M standard by means of wire cutting, and then tensile property test is carried out according to the tensile rate of 1.5mm/min, and the test results are shown in Table 1.
Heat-treated samples of 10mm × 10mm were prepared by means of wire cutting, and were ground stepwise to 2000# with different types of sandpaper, followed by polishing and etching, and XRD analysis was performed, and the analysis results are shown in fig. 3. According to the figure 3, the volume fraction of the retained austenite in the superfine grain high-toughness medium manganese steel C is counted to be 42%, and is improved by about 5% compared with the volume fraction of the retained austenite in the manganese steel with similar components widely reported at present. This is mainly because the present invention adopts a unique fine-grained process to refine the grain size of austenite, thereby improving its thermal stability. In addition, the higher austenite volume fraction can improve the mechanical property of the material by utilizing the TRIP effect in the normal-temperature deformation process.
Example 4
A method for preparing superfine crystal high-strength and high-toughness medium manganese steel based on TWIP effect and microalloy precipitation comprises the following steps:
step 1, smelting: according to the following steps: c is 0.05 wt.%, Mn is 4.0 wt.%, Al is 2 wt.%, Nb is 0.05 wt.%, and the balance is Fe and inevitable impurities, and the steel ingot is obtained by proportioning, vacuum melting and casting;
step 2, forging: heating the steel ingot to 1200 ℃, preserving heat for 2h, and forging into a steel billet with the thickness of 100mm x 30 mm;
step 3, multi-pass hot rolling: heating the steel billet to 1050 ℃, preserving heat for 2 hours, carrying out 6-pass hot rolling at the rolling temperature range of 900-1000 ℃, rolling into a hot rolled plate with the thickness of 18mm, and then cooling to 350-500 ℃;
step 4, multi-pass medium-temperature rolling: rolling the hot rolled plate at the temperature of 350-500 ℃ for 6 times to form a warm rolled plate with the thickness of 3 mm;
and 5, critical heat treatment: and (3) carrying out critical heat treatment on the warm-rolled plate at the temperature of 600 ℃ in a two-phase region for 30min to obtain the ultrafine-grained high-strength and high-toughness medium manganese steel D.
The obtained ultra-fine grain high strength and toughness medium manganese steel is processed into a hot tensile sample according to the ASTM-E8-E8M standard by means of wire cutting, and then tensile property test is carried out according to the tensile rate of 1.5mm/min, and the test results are shown in Table 1.
TABLE 1
| Yield strength/MPa | Tensile strength/MPa | Elongation/percent | |
| Example 1 | 1100 | 1405 | 46 |
| Example 2 | 1246 | 1678 | 51 |
| Example 3 | 1310 | 1704 | 40 |
| Example 4 | 1060 | 1505 | 43 |
As can be seen from the table 1, compared with the prior art, the yield strength, the tensile strength and the elongation of the ultrafine grained high-toughness medium manganese steel obtained by the invention have obvious advantages, which are mainly attributed to the TWIP effect and microalloy precipitation in the preparation process of the invention.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that those skilled in the art can make various improvements and modifications without departing from the principle of the present invention, and the improvements and modifications are also within the protection scope of the present invention.
Claims (6)
1. A method for preparing superfine crystal high-strength and high-toughness medium manganese steel based on TWIP effect and microalloy precipitation is characterized by comprising the following steps;
step 1, smelting: proportioning, smelting and casting according to 0.05-0.2% of C, 4-7% of Mn, 0-3% of Al, 0.01-0.1% of Nb and the balance of Fe and inevitable impurities to obtain a steel ingot;
step 2, forging: heating the steel ingot to 1200-1250 ℃, preserving heat for 2-3 h, and forging into a steel billet;
step 3, multi-pass hot rolling: heating the steel billet to 1050-1200 ℃, and preserving heat for 2-3 h; carrying out hot rolling for 6-7 times at the rolling temperature range of 900-1000 ℃, and then cooling to 350-500 ℃ to obtain a hot rolled plate;
step 4, multi-pass medium-temperature rolling: rolling the hot rolled plate for 6-7 times at the temperature of 350-500 ℃ to obtain a warm rolled plate;
and 5, critical heat treatment: and carrying out critical heat treatment on the warm-rolled plate at the temperature of 600-700 ℃ in a two-phase region to obtain the ultrafine-grained high-strength and high-toughness medium manganese steel.
2. The method for preparing the ultra-fine grained high-toughness medium manganese steel based on the TWIP effect and the microalloy precipitation according to claim 1, wherein the thickness of the steel billet obtained in the step 2 is 30-40 mm.
3. The method for preparing the ultra-fine grained high-toughness medium manganese steel based on the TWIP effect and the microalloy precipitation as claimed in claim 1, wherein in the step 3, the total reduction rate of the multi-pass hot rolling is 40-50%.
4. The method for preparing the ultrafine grained high-toughness medium manganese steel based on the TWIP effect and microalloy precipitation according to claim 1, wherein in the step 4, the total reduction ratio of multi-pass medium temperature rolling is 50-90%.
5. The method for preparing the ultra-fine grained high-toughness medium manganese steel based on the TWIP effect and the microalloy precipitation as recited in claim 1, wherein in the step 4, the volume fraction of the niobium carbide precipitates in the obtained warm-rolled plate is not less than 10-3The average size of the niobium carbide precipitates is within the range of 1 to 20 nm.
6. The method for preparing the ultra-fine grained high-toughness medium manganese steel based on the TWIP effect and the microalloy precipitation as recited in claim 1, wherein the heat treatment time is 30 min-1 h.
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| CN115927959B (en) * | 2022-11-15 | 2023-07-18 | 北京科技大学 | 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel and preparation method thereof |
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