WO2009145563A2 - Tôle d'acier à très haute résistance présentant d'excellentes propriétés de traitement à chaud pour le pressage à chaud, élément trempé, et procédé de production correspondant - Google Patents

Tôle d'acier à très haute résistance présentant d'excellentes propriétés de traitement à chaud pour le pressage à chaud, élément trempé, et procédé de production correspondant Download PDF

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Publication number
WO2009145563A2
WO2009145563A2 PCT/KR2009/002811 KR2009002811W WO2009145563A2 WO 2009145563 A2 WO2009145563 A2 WO 2009145563A2 KR 2009002811 W KR2009002811 W KR 2009002811W WO 2009145563 A2 WO2009145563 A2 WO 2009145563A2
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WIPO (PCT)
Prior art keywords
steel sheet
less
heat treatment
hot forming
high strength
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Ceased
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PCT/KR2009/002811
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English (en)
Korean (ko)
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WO2009145563A3 (fr
Inventor
오진근
강대영
진광근
신동석
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Posco Holdings Inc
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Posco Co Ltd
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Publication date
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Publication of WO2009145563A2 publication Critical patent/WO2009145563A2/fr
Publication of WO2009145563A3 publication Critical patent/WO2009145563A3/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • C22C38/02—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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium

Definitions

  • the present invention relates to a steel sheet mainly used for structural members, reinforcement, and the like of an automobile body, and provides an ultra high strength hot forming steel sheet having excellent heat treatment property having a tensile strength of 800 MPa or less before hot forming, and a method of manufacturing the steel sheet.
  • the present invention relates to a heat-treated hardened member and a method of manufacturing the same, having a high strength of 1800 MPa or more in tensile strength and a yield strength of 100 MPa or more after coating by heat-hardening after hot forming.
  • TRIP Transformation Induced Plasticity
  • An object of the present invention is to provide an ultra-high strength hot forming processing steel sheet and a method for manufacturing the same, which have excellent heat treatment properties that can be used for automobile structural members and reinforcement materials because of excellent moldability of 800 MPa or less before hot forming. It is another object of the present invention to form a heat-curing hot forming member and a method for producing a product having a complex shape at a high temperature and then quenching, and having excellent impact characteristics having a high tensile strength of 1800 MPa or more and a yield strength increase of 100 MPa or more after coating heat treatment. The purpose is to provide.
  • the present invention is in weight percent, C: 0.2-0.5%, Si: 0.01-1.5%, Mn: 0.5-2.0%, P: 0.1% or less (excluding 0%), S: 0.03% or less (excluding 0%) ), Soluble Al: 0.1% or less (excluding 0%), N: 0.01% to 0.1%, Cr: 0.1% to 2.0%, and the rest is characterized in that the tensile strength of 800MPa or less in the steel sheet composed of Fe and other impurities It is to provide an ultra-high strength hot forming steel sheet excellent in heat treatment.
  • the present invention comprises the steps of reheating the steel slab of the composition at 1100 ⁇ 1300 °C, hot finishing rolling at Ar3 transformation point or more and less than 1000 °C and winding step at 500 ⁇ 750 °C excellent heat treatment It is to provide a method for producing a steel sheet for ultra high strength hot forming processing.
  • W 0.001-0.3%
  • B 0.01% or less (except 0%)
  • Ti 0.01-0.1%
  • Nb 0.01-0.1%
  • Zr 0.01-0.1%
  • Mo 0.01- as needed for the said composition as needed. It is to provide an ultra-high strength hot forming steel sheet having excellent heat treatment property containing one or two or more selected from the group consisting of 0.5%, Cu: 0.005 to 1.0%, and Ni: 0.005 to 2.0%, and a method of manufacturing the same.
  • the present invention is a weight%, C: 0.2-0.5%, Si: 0.01-1.5%, Mn: 0.5-2.0%, P: 0.1% or less (excluding 0%), S: 0.03% (0% is Soluble Al: less than 0.1% (except 0%), N: 0.01 ⁇ 0.1%, Cr: 0.1 ⁇ 2.0%, the remainder is composed of Fe and other impurities, tensile strength after hot forming and quenching more than 1800MPa It is to provide a heat treatment curable member, characterized in that the yield strength after coating is increased by 100MPa or more.
  • the present invention is the step of raising the temperature of the steel sheet of the composition at a rate of 1 ⁇ 100 °C / second in the temperature range of 800 ⁇ 1000 °C and maintaining this temperature range of 10 ⁇ 1000 seconds and the hot-formed steel sheet of 10 ⁇ 500 °C / second It is to provide a method for producing a heat treatment curable member comprising the step of quenching at a rate.
  • the present invention has a tensile strength of less than 800MPa before hot forming, and can not only secure a high tensile strength of 1800MPa or more after hot forming and quenching, but also expect an increase in yield strength of 100MPa or more after coating, and excellent tensile to density.
  • a structural member or reinforcement of a vehicle requiring strength there is an advantage that can greatly improve the weight reduction and collision characteristics of the vehicle body.
  • the content of C is 0.2 to 0.5%.
  • C is an essential element for increasing the strength of the steel sheet and generates hard phases such as austenite and martensite.
  • Tensile strength In order to obtain a strength of 1800 MPa or more, the C content should contain 0.2% or more. If it is less than 0.2%, sufficient strength cannot be obtained even if heat treatment is performed in the austenitic single phase region.
  • the toughness and weldability are easily decreased, and it is not only difficult to weld the steel sheet during the production of the steel sheet, that is, in the pickling and rolling process, but also in the annealing and plating process.
  • C is limited to 0.2 to 0.5% because the plate of the steel sheet is too high to be difficult.
  • the content of Si is made 0.01 to 1.5%. Si increases the strength of the steel sheet as a substituted solid solution strengthening element. When the Si content is more than 1.5%, it is difficult to remove the surface scale of the hot rolled steel sheet, and the production cost problem occurs at less than 0.01%, so Si is limited to 0.01 to 1.5%.
  • Mn The content of Mn is 0.5 to 2.0%.
  • Mn is an element having a very high solid solution effect and at the same time delaying the transformation of austenite to ferrite. If the Mn content is less than 0.5%, a high heat treatment temperature is required to heat-treat the steel sheet in the austenitic single phase region, which accelerates the oxidation of the steel sheet and degrades the corrosion resistance of the plated steel sheet even when plated steel sheet is used. In addition, desired high strength cannot be secured by ferrite and austenite abnormal reverse heat treatment. When Mn content exceeds 2.0%, since it may become a problem in weldability, hot rolling property, etc., Mn is limited to 0.5 to 2.0%.
  • the content of P is to be 0.1% or less (excluding 0%). P exhibits an effect of reinforcing steel, but if contained in an excessive amount, workability deteriorates, so the upper limit is limited to 0.1%.
  • the content of S is made 0.03% or less (excluding 0%). S exists as an impurity in steel and is an element which inhibits the ductility and weldability of a steel plate. If the content of S is less than 0.03%, such an adverse effect is not so large that the upper limit is made 0.03%.
  • the content of soluble Al should be 0.1% or less (excluding 0%).
  • Al is a deoxidation element exceeding 0.1%, the effect is not only saturated. Since the inclusions of alumina and the like are increased, and AlN is combined with N to form AlN, the solid solution N is reduced to suppress the increase in yield strength, so the upper limit is made 0.1%.
  • N is made 0.01 to 0.1%.
  • N is a very important element in the present invention.
  • N is a solid solution strengthening element and at the same time is an element that combines with Ti, Nb, Al, and the like to form a nitride, and in the present invention, N must be sufficient to increase the yield strength after heat treatment and coating. If the N content is less than 0.01%, such an effect cannot be expected. If the N content is more than 0.1%, it is difficult to manufacture and play molten steel, and may cause workability deterioration or blow hole during welding. Therefore, N is limited to 0.01 to 0.1%.
  • the content of Cr is made 0.1 to 2.0%. Since Cr improves hardenability, strength reduction can be prevented at low cooling rates. If the Cr content is less than 0.1%, the above effects cannot be expected. If the Cr content is more than 2.0%, the effect is not only saturated but also increases the manufacturing cost, so the Cr content is set at 0.1 to 2.0%.
  • W, B, Mo, Ti, Nb, Zr, Cu, Ni is one or two or more types are contained as needed.
  • W is made 0.001 to 0.3%.
  • W is an effective element which can improve the heat treatment hardenability of the steel sheet. If the W content is less than 0.001%, such an effect cannot be expected. If the W content is more than 0.3%, the effect is not only saturated, but the manufacturing cost increases, so the content of W is made 0.001 to 0.3%.
  • the content of B is made 0.01% or less.
  • B is an element with very high hardenability, and even if a trace amount is added, high strength can be ensured in the heat-treated steel.
  • the content exceeds 0.01%, the effect is not only saturated but also deteriorates hot workability, so the content of B is set at 0.01% or less.
  • the content of Mo is 0.01 to 0.5%. Mo not only increases the hardenability but also increases the toughness of the heat-treated steel sheet. Therefore, the effect of Mo is great when added to steel sheets that require high collision energy characteristics. In addition, since the hardenability is improved, the strength reduction of the part which does not come into direct contact with the mold during high temperature forming processing can be prevented.
  • the content of Mo is less than 0.01%, the above effects cannot be expected, and when the content of Mo exceeds 0.5%, the effect is not only saturated, but the manufacturing cost increases, so the content of Mo is 0.01-0.5%.
  • the content of Ti, Nb and Zr is 0.001 to 0.1%.
  • Ti, Nb, and Zr are effective elements for increasing the strength of steel sheet, making grain size smaller, and improving heat treatment. If the content of Ti, Nb and Zr is less than 0.001%, such an effect cannot be obtained. If the content of Ti, Nb and Zr is less than 0.1%, the effect of the desired strength and yield strength cannot be expected due to an increase in manufacturing cost and excessive carbon and nitride production.
  • Cu content is made into 0.005 to 1.0%.
  • Cu is an effective element for increasing the strength due to fine Cu precipitates, and the Cu content is less than 0.005%, and the effect of strength is insignificant.
  • the content exceeds 1.0%, Cu is limited to 0.005 to 1.0%.
  • Ni content is made into 0.005 to 2.0%.
  • Ni is an effective element for increasing strength and improving heat treatment.
  • the effect is not acquired, and when it exceeds 2.0%, since manufacturing cost rises and workability deterioration occurs, Ni is limited to 0.005 to 2.0%.
  • the present invention is composed of Fe and other unavoidable impurities in addition to the above components.
  • the steel sheet of the present invention is preferably limited to the tensile strength of 800MPa or less before hot forming. If the tensile strength before the hot forming is 800MPa or more, it is difficult to produce the blank in a desired shape, and the mold wear is severe, which may cause an increase in manufacturing cost.
  • the microstructure before hot forming needs to contain 80% or more of ferrite and pearlite or ferrite and cementite as the main phase. If the microstructure before hot forming contains 20% or more of martensite or bainite, it is difficult to secure the tensile strength below 800 MPa.
  • the steel of the present invention which is formed as described above, may be used in the form of a hot rolled steel sheet or a cold rolled steel sheet, and plating or coating may be applied to the surface layer as necessary.
  • Plating that can be applied to the present invention include Al plating, zinc plating, alloyed zinc plating and the like.
  • the Al plating layer and the zinc plating layer may include an alloying component. That is, in the Al plating bath and the zinc plating bath, a plating bath containing an alloying component may be used as necessary.
  • the coating that can be applied in the present invention may use an organic or organic / inorganic composite binder, and may use a method of combining with a metal or nonmetal solid having excellent electrical conductivity.
  • the heat treatment curable member of the present invention is used as a member having ultra high strength characteristics by hot forming or post heat treatment after molding.
  • Hot forming degree is not specifically limited about the post-heating method after shaping
  • the member of the present invention is characterized by securing a high tensile strength of 1800 MPa or more after hot forming and quenching in a hot forming steel sheet. Such a feature is because a sufficient impact resistance property cannot be secured at a tensile strength of less than 1800 MPa, which has a limitation in weight reduction of automobiles.
  • the member of the present invention preferably has a martensite single phase (100% martensite) or at least 95% of the martensite structure. It is because the martensite fraction below 95% cannot ensure the high tensile strength aimed at in this invention. As a more preferable range for showing the effect of the present invention, the fraction of martensite is made 99% or more. If the martensite fraction is 95% or more, the remainder is one or two of ferrite and bainite.
  • the member can be coated to secure a yield strength change rate ( ⁇ YS) of 100 MPa or more.
  • Yield strength is closely related to securing the impact resistance characteristics in heat-curable members. In other words, the higher the yield strength, the better the crash resistance characteristics, and from this it is advantageous in lightening the vehicle and passenger protection, the greater the yield strength after the coating process, the greater the crash resistance characteristics can be exhibited.
  • Nitrogen can be utilized as a means to secure this. Nitrogen, like carbon, exists in solid solution in steel and can increase its yield strength by interaction with dislocations when applied after deformation.
  • the steel slab that satisfies the steel component system of the present invention is reheated at 1100 to 1300 ° C. Tissue homogenization is not sufficient when the reheating temperature is below 1100 ° C. In addition, when Ti, Nb, Zr, W, and the like are added, re-use of these components may not be sufficient. If the reheating temperature exceeds 1300 ° C, the steel sheet structure tends to coarsen.
  • the reheated steel slab is hot-rolled under the condition that the finish rolling temperature is more than Ar3 transformation point and less than 1000 ° C. It is highly likely that the hot deformation resistance will increase rapidly when the hot-finish rolling temperature is less than Ar3 transformation point. When hot finishing rolling temperature exceeds 1000 degreeC, not only will an oxidation scale too thick generate
  • the coiling temperature is less than 500 °C excessive martensite or bainite is produced to cause an excessive increase in strength of the hot rolled steel sheet may cause a manufacturing problem such as a shape defect due to the load during cold rolling.
  • the coiling temperature exceeds 750 ° C, the scale layer may be excessively deteriorated in surface quality characteristics.
  • the hot rolled steel sheet may be used in a hot rolled steel sheet state or plated or coated to be used for a desired use.
  • the hot rolled steel sheet is cold rolled. That is, the wound hot rolled sheet is cold rolled with pickling and a reduction ratio of 30 to 80%. If the cold reduction rate is less than 30%, it is difficult to secure a target thickness. When the cold rolling reduction exceeds 80%, there is a high possibility that cracks in the steel sheet edge part occur, and there is a problem of bringing cold rolling load.
  • the cold rolled steel sheet is annealed, the annealing is heated at a rate of 1 ⁇ 100 °C / hour in the temperature range of 500 ⁇ 900 °C and maintained for 1 to 100 hours, it is preferable to perform slow cooling at a rate of 1 ⁇ 100 °C / hour Do. Continuous annealing can be performed. If the annealing temperature is less than 500 °C tends to not secure sufficient processability, while the temperature is higher than 900 °C is likely to increase the manufacturing cost and surface quality deterioration. If the temperature increase rate is less than 1 ° C / hour, productivity decreases, and if it exceeds 100 ° C / hour, excessive equipment is required.
  • the annealing temperature holding time is less than 1 hour, it is difficult to secure the desired strength after hot forming and quenching because sufficient carbide dissolution is not achieved. If the annealing temperature is maintained for more than 100 hours, problems of surface detachment and productivity are easily caused. In addition, when the cooling rate is less than 1 ° C / hour, productivity decreases, and when it exceeds 100 ° C / hour, a hard phase is likely to occur, thereby increasing the strength of the material before hot forming.
  • the annealed steel sheet may be used in a state in which the annealed steel sheet or plating or coating is applied to a desired use.
  • the plating can improve the heat resistance of the annealed steel sheet and the surface characteristics after the molding process.
  • the plating method any method can be used as long as the protective film can be coated on the steel sheet.
  • the steel sheet is a hot rolled steel sheet, a cold rolled steel sheet, or plating or coating is applied to these steel sheets as needed, and the type of the steel sheet is not particularly limited.
  • the molding of the member may be performed by a hot press forming method or a method by heat treatment after molding.
  • the temperature is increased at a speed of 1 to 100 ° C./second in the temperature range of 800 to 1000 ° C. and maintained at 10 to 1000 seconds, and then hot forming is performed in the mold, and then at a speed of 10 to 500 ° C./second. It is preferable to perform quenching.
  • the hot formed member according to the present invention has a martensite single phase or a fraction of martensite of 95% or more, and becomes one or two of the remaining ferrites and bainite and has an ultra high strength characteristic of 1800 MPa.
  • the yield strength change mule rises by more than 100MPa in the baking process after the coating (baking) process.
  • Table 1 shows the chemical composition of the present invention steel and fertilizer steel, to produce a steel slab by vacuum melting the steel having a composition of Table 1, and then reheating the steel slab in a heating furnace 1 in the temperature range of 1150 ⁇ 1250 °C 1 It heated for time and performed hot rolling. At this time, hot rolling was finished hot rolling in the temperature range of 850 ⁇ 950 °C, winding temperature was set to 650 °C (hot rolled steel sheet).
  • the cold rolled steel sheet was annealed in two ways.
  • the first cold rolling 1 was heated at a heating rate of 10 ⁇ 50 °C / hour, and then maintained at 600 ⁇ 700 °C 1 ⁇ 10 hours and then subjected to annealing at a cooling rate of 10 ⁇ 50 °C / hour (cold rolled sheet 1).
  • the second cold rolling 2 was heated at a heating rate of 2 ⁇ 10 °C / hour, and then maintained and annealed for 1 to 5 minutes at 750 ⁇ 850 °C and then subjected to continuous annealing with an overaging temperature of 350 ⁇ 400 °C (cold rolled steel sheet 2).
  • a tensile test piece of JIS Z 22015 was prepared from the hot rolled steel sheets and the cold rolled steel sheets 1 and 2, and a tensile test was performed using a tensile tester.
  • the steel sheet was heated to 800 ⁇ 900 °C for 5 minutes and then press-worked using a mold to prepare a tensile test piece. In the press working, the steel sheet is quenched at the same time as processing.
  • the tensile test piece produced as described above was boiled in oil at 170 ° C. for 20 minutes and then subjected to a tensile test. Tensile tests were carried out using a universal tensile tester.
  • hot-rolled steel sheet and cold-rolled steel sheet 1 in the A ⁇ H steel grades the microstructure before hot pressing, the martensite or bainite fraction is less than 10% to secure a tensile strength of less than 800MPa, room temperature blanking and hot forming This is easy.
  • the final product shows ultra high strength of 1800MPa or more.
  • the yield strength change after coating simulation at 170 ° C. for 20 minutes is all excellent in the steel of the present invention at 100 MPa or more.
  • the cold rolled steel sheet 2 of comparative steel grades A to G has a tensile strength of 1800 MPa or more after hot press molding and a yield strength of 100 MPa or more after coating.
  • the tensile strength of the martensite or bainite fraction is 10% or more in the microstructure before hot pressing. Molding is difficult beyond 800 MPa.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Abstract

La présente invention concerne une tôle d'acier à très haute résistance présentant d'excellentes propriétés de traitement à chaud, ladite tôle contenant, en % en poids, C: 0,2 à 0,5%, Si: 0,01 à 1,5%, Mn: 0,5 à 2,0%, P: 0,1% ou moins (mais pas 0%), S: 0,03% ou moins (mais pas 0%), Al soluble: 0,1% ou moins (mais pas 0%), N: 0,01 à 0,1%, et Cr: 0,1 à 2,0%,, le reste étant constitué de Fe et d'impuretés inévitables. Cette tôle d'acier présente une résistance à la traction, mesurée avant le pressage à chaud, inférieure ou égale à 800 MPa. L'invention concerne également un procédé de production de ladite tôle d'acier. Elle concerne en outre un élément trempé, formé par pressage à chaud et refroidissement rapide de la tôle de façon à présenter une résistance à la traction supérieure ou égale à 1800 MPa, ainsi que son procédé de production. Elle concerne également une tôle d'acier dont la résistance à la traction, mesurée avant le pressage à chaud, est inférieure ou égale à 800 MPa, et dont la résistance à la traction, mesurée après le pressage à chaud et le refroidissement rapide, est supérieure ou égale à 1800 MPa, La tôle en acier selon l'invention présente une limite d'élasticité supérieure ou égale à 100 MPa après enduction.
PCT/KR2009/002811 2008-05-29 2009-05-27 Tôle d'acier à très haute résistance présentant d'excellentes propriétés de traitement à chaud pour le pressage à chaud, élément trempé, et procédé de production correspondant Ceased WO2009145563A2 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR10-2008-0050365 2008-05-29
KR1020080050365A KR101027285B1 (ko) 2008-05-29 2008-05-29 열처리성이 우수한 초고강도 열간성형 가공용 강판, 열처리경화형 부재 및 이들의 제조방법

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WO2009145563A2 true WO2009145563A2 (fr) 2009-12-03
WO2009145563A3 WO2009145563A3 (fr) 2010-03-04

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WO2013034815A1 (fr) 2011-09-06 2013-03-14 Arcelormittal Investigación Y Desarrollo Sl Acier lamine durcissant par precipitation apres formage a chaud et/ou trempe sous outil a tres haute resistance et ductilite et son procede de fabrication
JP2015504486A (ja) * 2011-11-28 2015-02-12 アルセロルミタル・インベステイガシオン・イ・デサロジヨ・エセ・エレ １７００から２２００ｍｐａの引張強度を有するマルテンサイト鋼
EP2719787B1 (fr) 2011-06-10 2016-04-13 Kabushiki Kaisha Kobe Seiko Sho Article moulé par pressage à chaud, procédé pour produire celui-ci, et tôle d'acier mince pour moulage à la presse à chaud
CN105849298A (zh) * 2013-12-25 2016-08-10 Posco公司 具有优异的弯曲性能及超高强度的热压成型品用钢板、利用该钢板的热压成型品以及它们的制备方法
CN107109509A (zh) * 2014-12-24 2017-08-29 Posco公司 热处理钢材、耐久特性优异的超高强度成型品及其制造方法
CN109844142A (zh) * 2016-09-26 2019-06-04 Posco公司 耐蚀性和点焊性优异的热成型用冷轧钢板、热成型部件及其制造方法
EP3483299A4 (fr) * 2016-07-08 2020-03-11 Northeastern University Acier pour formage par estampage à chaud, procédé de formage par estampage à chaud et élément formé par estampage à chaud
CN111511953A (zh) * 2017-12-26 2020-08-07 Posco公司 超高强度热轧钢板、钢管、部件及其制造方法
CN114262847A (zh) * 2021-12-20 2022-04-01 马鞍山钢铁股份有限公司 一种抗拉强度大于1300MPa高表面质量的热轧汽车用钢及其制造方法
CN114540712A (zh) * 2022-02-28 2022-05-27 北京理工大学重庆创新中心 一种添加Ce元素的无涂层增强抗高温氧化热冲压成形钢
CN114561591A (zh) * 2022-02-28 2022-05-31 北京理工大学重庆创新中心 一种添加y元素的无涂层增强抗高温氧化热冲压成形钢
CN116121623A (zh) * 2022-12-19 2023-05-16 攀钢集团攀枝花钢铁研究院有限公司 一种抗高温氧化热成形钢及其冶炼方法
EP3929321B1 (fr) 2019-02-21 2023-09-27 JFE Steel Corporation Élément pressé à chaud, tôle d'acier laminée à froid pour le pressage à chaud et procédés de fabrication correspondants

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