CN110872641A - Method for producing automobile safety part through austenite counter-rotating transformation and sub-temperature forming - Google Patents

Method for producing automobile safety part through austenite counter-rotating transformation and sub-temperature forming Download PDF

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CN110872641A
CN110872641A CN201811019483.4A CN201811019483A CN110872641A CN 110872641 A CN110872641 A CN 110872641A CN 201811019483 A CN201811019483 A CN 201811019483A CN 110872641 A CN110872641 A CN 110872641A
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temperature
austenite
quenching
stamping
sub
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景财年
邢兆贺
丁啸云
候玉栋
吕明桦
涂英明
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Shandong Jianzhu University
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Shandong Jianzhu University
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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • 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
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/008—Martensite

Abstract

The invention discloses a method for producing an automobile safety part by austenite counter-rotating transformation and sub-temperature forming. Selecting chemical components in percentage by mass as C: 0.15-0.20%, Mn: 2.0-2.5%, Si: 1.0-1.2%, Al: 0.6-1.0%, V: 0.05-0.08%, B: 0.001%, Cr: 0.4-0.6% of cold-rolled low-carbon silicomanganese steel sheet. Combining the reverse and forward austenite transformation process with the hot forming technology, quenching after austenitizing the plate, and measuring the transformation point of the plate; heating to perform austenite reversion annealing; transferring the plate material into a hot stamping die, and carrying out sub-temperature stamping forming; quenching to M in the diesAnd MfTemperature, or MsAnd BsAnd maintaining the pressure, and then performing water quenching to room temperature. According to the invention, by utilizing the distribution of C, Mn elements in the reverse and forward transformation processes of austenite and combining the two-phase zone sub-temperature stamping, the microstructure is martensite/bainite, ferrite and residual austenite, the problem of poor plasticity of a hot-formed part is solved, and the hot-formed part has good strength and plasticity matching. The invention has simple process, short heat preservation time, higher production efficiency and lower cost.

Description

Method for producing automobile safety part through austenite counter-rotating transformation and sub-temperature forming
Technical Field
The invention relates to a method for forming automobile parts, in particular to a method for producing an automobile safety part by utilizing austenite reverse and forward transformation and sub-temperature forming.
Background
In recent years, the automobile industry in China has been developed at a high speed. At present, the quantity of automobiles in China exceeds 2 hundred million. The rapid development of the automobile industry brings great convenience to people, and simultaneously faces a series of difficulties of energy, environmental protection, safety and the like. In order to save energy and reduce the emission, and meet the increasingly strict environmental protection regulations of various countries and the increasingly high requirements of people on the performance of automobiles, the light weight of automobiles becomes one of the main trends of the development of the automobile industry in the world. The light weight of the automobile has important significance for the traditional fuel oil automobile, the electric automobile and the like.
The adoption of the hot forming technology to manufacture the body structure and the safety part is an important way for realizing the light weight of the body and improving the safety of the automobile. The hot forming technology is a forming process for rapidly transferring a steel plate into a hot stamping die with a cooling system after the steel plate is completely austenitized, rapidly stamping and forming the steel plate, and maintaining the pressure for a certain time to obtain a workpiece with a certain shape and size. The hot forming technology has the advantages of small forming pressure, low resilience after forming, high dimensional accuracy and high strength. However, since the steel after hot forming has a fully martensitic structure, the elongation is about 5%, and the plasticity is poor. The increasing demands on the performance of the motor vehicle cannot be met, which limits the application of thermoforming techniques.
The positive austenite transformation generally means that after austenitizing the C-Si-Mn steel, the steel is rapidly quenched to the bainite transformation region or rapidly quenched to the martensite transformation temperature (M) starting temperatures) And martensite finish temperature (M)f) And C element distribution is carried out, and finally quenching is carried out to room temperature, so that a certain amount of residual austenite is obtained. Among them, the so-called TRIP (transformation induced plasticity) process in which after austenitization, rapid quenching to the bainite transformation region is performed; austenitizing and quenching the steel plate to Ms and MfIs called Q&P (queuing and copying) process. Q&The P process, TRIP process, is a typical austenite forward transformation process. For both processes, increasing the content of C element in the steel is beneficial to increase the stability of the retained austenite, but too high content of C may reduce the weldability of the steel sheet. In order to ensure the weldability of steel, low-carbon steel is selected, and the Mn element is distributed in a two-phase region in a heat-insulating way, so that the stability of austenite can be improved. C. The distribution of Mn element is beneficial to improving the comprehensive mechanical property of the steel.
The austenite reverse transformation refers to that a precursor of martensite or incomplete martensite structure is formed by quenching, then the two-phase region is heated again for annealing, in the process, the austenite is newly formed, alloy elements such as C, Mn are re-enriched in the austenite, and finally the residual austenite and other structures which are stable at room temperature are obtained by quenching to room temperature. At present, the research of the reverse transformation process is mainly carried out on medium manganese steel, but the austenite reverse transformation annealing time of the medium manganese steel is too long, so that the practical application of the process is limited.
Combines advanced manufacturing technology with the heat treatment process of high-strength steel. The plasticity of the automobile safety part is improved on the premise of ensuring the high strength of the automobile safety part, an ideal product of strength and elongation is obtained, the automobile safety part is properly thinned, and the lightweight level of the automobile can be effectively improved, so that the energy-saving emission-reducing level and the collision safety of the automobile are improved.
Disclosure of Invention
The invention combines the advanced manufacturing technology (hot forming) and the high-strength steel heat treatment process (austenite reversion)Transformation process and austenite forward transformation process), namely combining a hot forming technology with an austenite forward and backward transformation method, and provides a method for producing automobile safety parts by austenite forward and backward transformation and sub-temperature forming. Selecting a cold-rolled low-carbon silicon-manganese thin steel plate, and cutting the plate by laser; transferring the plate material into a heating furnace, heating to a temperature higher than austenitizing temperature, preserving heat for a certain time to enable the plate material to be completely austenitized, and then quenching to room temperature; determination of A of Steel by thermal dilatometer after quenchingC1、Ms、Mf、BSAt the equal phase transition point, reheating to AC1Preserving heat for a certain time at the certain temperature, and carrying out reverse transformation annealing and heat preservation; transferring the steel plate into a hot stamping die, carrying out stamping forming, and carrying out in-die quenching until MsAnd MfBetween temperatures, or MsKeeping the pressure for a certain time when the temperature is higher than the temperature and the temperature is lower than the temperature Bs, and finally carrying out water quenching to room temperature.
The invention selects low-carbon silicon-manganese steel, preferably, the steel comprises the following chemical components: 0.15-0.20%, Mn: 2.0-2.5%, Si: 1.0-1.2%, Al: 0.6-1.0%, V: 0.05-0.08%, B: 0.001%, Cr: 0.4 to 0.6 percent.
The invention comprises the following steps:
step 1, blanking, namely cutting a steel plate by laser to obtain a required plate;
step 2, austenitizing, namely rapidly heating the plate material in a heat treatment furnace to austenite AC3Keeping the temperature at 30-50 ℃ for 3-7min to completely austenitize the steel;
step 3, quenching, namely quenching the plate material completely austenitized in the step 2 to room temperature, and adopting a thermal expansion instrument to quench the quenched steel plate AC1、Ms、Mf、BSThe measurement is carried out, because martensite is obtained after the steel plate is quenched, C, Mn elements are enriched, and the transformation point is reduced;
step 4, reverse transformation annealing, namely heating the plate material in a roller hearth type heating furnace to AC1Keeping the temperature at 10-30 deg.C for 3-10 min;
step 5, performing sub-temperature stamping forming, namely quickly transferring the plate material into a hot stamping die, and performing stamping forming at the stamping beat of 3-5 pieces per minute;
step 6, quenching in the mould, namely rapidly quenching the plate material formed by sub-temperature stamping in the mould to Ms and MfKeeping the temperature for 15-45 s;
step 7, quenching to room temperature;
the invention has the beneficial effects that:
(1) combining the reverse transformation and positive transformation process of austenite with the hot forming process, quenching after austenitizing, reheating to a two-phase region for annealing and heat preservation, performing sub-temperature hot stamping forming, and performing the austenite positive transformation process after forming. During the reverse transformation heat preservation process, the stability of austenite is increased through the distribution of C, Mn elements, and the stability of retained austenite is increased through the distribution of C elements at low temperature. Thereby improving the problem of poor plasticity of the hot formed piece.
(2) The invention selects low-carbon silicomanganese steel, and the chemical components are as follows: 0.15-0.20%, Mn: 2.0-2.5%, Si: 1.0-1.2%, Al: 0.6-1.0%, V: 0.05-0.08%, B: 0.001%, Cr: 0.4 to 0.6 percent. The steel plate has good weldability and good surface quality after hot forming. The invention has simple process and can obtain good comprehensive mechanical property under shorter reverse transformation annealing heat preservation time. The production efficiency is improved, and the energy is saved. Can be applied to the existing hot forming equipment.
(3) The invention measures A after quenching the plateC1At an equal phase transition point of AC1Stamping after the temperature is kept at 10-30 ℃, and introducing a fine-grain ferrite structure, which is beneficial to improving the plasticity of a hot forming piece.
(4) The microstructure obtained by the process of the invention is martensite, ferrite and retained austenite, the forming is accurate, the resilience is small, the tensile strength is more than 1200MPa, and the elongation is more than 10%. High strength and better plasticity. The problem of traditional thermoforming spare intensity height but the plasticity is relatively poor is solved.
Drawings
FIG. 1 is a process diagram of the present invention.
Fig. 2 is a schematic view of a standard sample cut on a wire on a safety element.
FIG. 3 shows the microstructure of example 1.
FIG. 4 shows the microstructure of example 2.
Detailed Description
The invention is further illustrated by the following examples in conjunction with the accompanying drawings.
Example 1
The low-carbon silicon-manganese cold-rolled steel sheet is selected, and comprises the following chemical components: 0.18%, Mn: 2.31%, Si: 1.1%, Al: 0.6%, V: 0.06%, B: 0.001%, Cr: 0.5 percent. The thickness is 1.2 mm. Blanking, namely cutting the steel plate by laser to obtain a plate material with a required shape; austenitizing, namely rapidly heating the plate to 930 ℃ in a heat treatment furnace, and preserving heat for 5min to completely austenitize the plate; quenching, namely quenching the plate in the step 2 to room temperature, and performing thermal expansion phase change instrument DIL805 on the quenched steel plate A according to standard YB T5127-1993 method for determining critical points of steel (expansion method), by adopting a TA instrument DIL805C1、BS、Ms、MfRespectively measuring 683 ℃, 462 ℃, 316 ℃ and 182 ℃; reverse transformation annealing, namely heating the plate to 720 ℃ in a roller hearth type heating furnace, and keeping the temperature for 8 min; performing sub-temperature stamping forming, namely quickly transferring the plate material into a hot stamping die, and stamping by adopting an 800MPa hydraulic press, wherein the stamping beat is 3-5 pieces per minute; quenching in the mould, namely rapidly quenching the plate material formed by sub-temperature stamping in the mould to MSAnd MfKeeping the temperature at 240 ℃ for 35 s; and quenching to room temperature to obtain the austenite counter-rotating and sub-temperature-changing formed automobile door protection plate.
Standard tensile specimens (as shown in FIG. 2) were cut on-line on the door fender produced by the process of example 1, and tensile tests were carried out according to GB/T228.1-2010 metallic Material tensile test method. The tensile strength of the sample is 1320MPa, and the elongation after fracture is 10.5%. The microstructure of the door fender is shown in fig. 3, and is lath martensite, fine-grained ferrite distributed in a dispersed manner, and retained austenite.
Example 2
The low-carbon silicon-manganese cold-rolled steel sheet is selected, and comprises the following chemical components: 0.18%, Mn: 2.31%, Si: 1.1%, Al: 0.6%, V: 0.06%, B: 0.001%, Cr: 0.5 percent. The thickness is 1.2 mm. Blanking, namely cutting the steel plate by laser to obtain a required plate; austenitizing, rapidly heating the plate material to 930 deg.C in a heat treatment furnace, and maintaining the temperature for 5min to make the plate material austenitizedIt is fully austenitized; quenching, namely quenching the plate in the step 2 to room temperature, and performing thermal expansion phase change instrument DIL805 on the quenched steel plate A according to standard YB T5127-1993 method for determining critical points of steel (expansion method), by adopting a TA instrument DIL805C1、BS、Ms、MfRespectively measuring 683 ℃, 462 ℃, 316 ℃ and 182 ℃; reverse transformation annealing, namely heating the plate to 700 ℃ in a roller hearth type heating furnace, and keeping the temperature for 5 min; performing sub-temperature stamping forming, namely quickly transferring the plate material into a hot stamping die, and stamping by adopting an 800MPa hydraulic press, wherein the stamping beat is 3-5 pieces per minute; quenching in the mould, namely rapidly quenching the plate material formed by sub-temperature stamping in the mould to 320 ℃ between Ms and Bs, and preserving heat for 30 s; and finally quenching to room temperature. And quenching to room temperature to obtain the austenite counter-rotating and sub-temperature-changing formed automobile door protection plate.
Standard tensile test samples are cut on the line of the car door protection plate produced by the process of the embodiment 2, and tensile test is carried out according to GB/T228.1-2010 metal material tensile test method. The tensile strength of the sample is 1240MPa, and the elongation after fracture is 12 percent. The microstructure of the door fender is shown in fig. 4 and is fine-grained ferrite, bainite/martensite and retained austenite.

Claims (2)

1. A method for producing an automobile safety part by austenite counter-rotation and forward transformation and sub-temperature forming is characterized in that a cold-rolled low-carbon silicon-manganese thin steel plate is selected, a hot forming technology is combined with an austenite counter-rotation transformation process and an austenite forward transformation process, two-phase region sub-temperature stamping forming is carried out after austenite counter-rotation transformation, C, Mn element distribution is carried out, then an austenite forward rotation heat treatment process is carried out, and the method comprises the following specific preparation steps:
(1) blanking, namely selecting a cold-rolled low-carbon silicon-manganese thin steel plate, and cutting by adopting laser to obtain a required plate;
(2) austenitizing, namely, rapidly heating the plate material in a heat treatment furnace to austenite AC3Keeping the temperature at 30-50 ℃ for 3-7min to completely austenitize the steel;
(3) quenching, quenching the plate material completely austenitized to room temperature, and adopting a thermal expansion instrument to quench the steel plate AC1、Ms、Mf、BSThe measurement is performed.
(4) Reverse transformation annealing, namely heating the plate material in a roller hearth type heating furnace to AC1Keeping the temperature at 10-30 deg.C for 3-10 min;
(5) performing sub-temperature stamping forming, namely quickly transferring the plate material into a hot stamping die, and stamping and forming by using an 800MPa hydraulic press to obtain the plate material with a certain shape, wherein the stamping beat is 3-5 pieces per minute;
(6) quenching in the mould, namely rapidly quenching the plate material formed by sub-temperature stamping in the mould to MSAnd MfOr M issKeeping the temperature above the temperature and below the Bs temperature for 15-45 s;
(7) quenching to room temperature.
2. The cold rolled low carbon steel sheet as set forth in, wherein the chemical composition C: 0.15-0.20%, Mn: 2.0-2.5%, Si: 1.0-1.2%, Al: 0.6-1.0%, V: 0.05-0.08%, B: 0.001%, Cr: 0.4-0.6%, and the thickness is 0.8-1.5 mm.
CN201811019483.4A 2018-09-03 2018-09-03 Method for producing automobile safety part through austenite counter-rotating transformation and sub-temperature forming Pending CN110872641A (en)

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111638238A (en) * 2020-05-15 2020-09-08 南京钢铁股份有限公司 Method for measuring reverse transformation austenite by adopting expansion method
WO2021236619A1 (en) * 2020-05-18 2021-11-25 Magna International Inc. Method for processing advanced high strength steel
CN114309069A (en) * 2022-01-07 2022-04-12 太原科技大学 Medium manganese steel sub-temperature forming method, medium manganese steel prepared by same and application of medium manganese steel
CN114635024A (en) * 2022-02-14 2022-06-17 苏州大学 Medium manganese steel part treatment method based on combination of plastic forming and heat treatment
CN115161549A (en) * 2022-05-27 2022-10-11 郑州轻研合金科技有限公司 High-tensile-strength alloy steel plate and preparation method thereof
CN115341130A (en) * 2022-09-06 2022-11-15 广西科技大学 Method for preparing high-strength-ductility hot-rolled cold-formed automobile structural steel

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CN102943169A (en) * 2012-12-10 2013-02-27 北京科技大学 Quenching and annealing preparation method of ultrahigh-strength thin steel plate for automobiles
CN104668326A (en) * 2015-03-05 2015-06-03 山东大王金泰集团有限公司 Hot stamping method for performance gradient distribution of high-strength steel parts

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Publication number Priority date Publication date Assignee Title
CN102943169A (en) * 2012-12-10 2013-02-27 北京科技大学 Quenching and annealing preparation method of ultrahigh-strength thin steel plate for automobiles
CN104668326A (en) * 2015-03-05 2015-06-03 山东大王金泰集团有限公司 Hot stamping method for performance gradient distribution of high-strength steel parts

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111638238A (en) * 2020-05-15 2020-09-08 南京钢铁股份有限公司 Method for measuring reverse transformation austenite by adopting expansion method
CN111638238B (en) * 2020-05-15 2022-11-18 南京钢铁股份有限公司 Method for measuring reverse transformation austenite by adopting expansion method
WO2021236619A1 (en) * 2020-05-18 2021-11-25 Magna International Inc. Method for processing advanced high strength steel
CN114309069A (en) * 2022-01-07 2022-04-12 太原科技大学 Medium manganese steel sub-temperature forming method, medium manganese steel prepared by same and application of medium manganese steel
CN114309069B (en) * 2022-01-07 2023-12-01 太原科技大学 Sub-temperature forming method of medium manganese steel, medium manganese steel prepared by sub-temperature forming method and application of medium manganese steel
CN114635024A (en) * 2022-02-14 2022-06-17 苏州大学 Medium manganese steel part treatment method based on combination of plastic forming and heat treatment
CN114635024B (en) * 2022-02-14 2023-08-15 苏州大学 Medium manganese steel part treatment method based on combination of plastic forming and heat treatment
CN115161549A (en) * 2022-05-27 2022-10-11 郑州轻研合金科技有限公司 High-tensile-strength alloy steel plate and preparation method thereof
CN115341130A (en) * 2022-09-06 2022-11-15 广西科技大学 Method for preparing high-strength-ductility hot-rolled cold-formed automobile structural steel
CN115341130B (en) * 2022-09-06 2023-08-11 广西科技大学 Method for preparing high-strength plastic product hot-rolled cold-formed automobile structural steel

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Application publication date: 20200310