EP2524970A1 - Hochfestes Stahlflachprodukt und Verfahren zu dessen Herstellung - Google Patents

Hochfestes Stahlflachprodukt und Verfahren zu dessen Herstellung Download PDF

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Publication number
EP2524970A1
EP2524970A1 EP11166622A EP11166622A EP2524970A1 EP 2524970 A1 EP2524970 A1 EP 2524970A1 EP 11166622 A EP11166622 A EP 11166622A EP 11166622 A EP11166622 A EP 11166622A EP 2524970 A1 EP2524970 A1 EP 2524970A1
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European Patent Office
Prior art keywords
steel
temperature
content
flat
heating
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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EP11166622A
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German (de)
English (en)
French (fr)
Inventor
Jens-Ulrik Dr.-Ing. Becker
Jian Dr.-Ing. Bian
Thomas Dr. Heller
Rudolf Dipl.-Ing. Schönenberg
Richard G. Dr. Thiessen
Sabine Dipl.-Ing. Zeizinger
Thomas Dipl.-Ing. Rieger
Oliver Dipl.-Ing. Bülters
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=46124355&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP2524970(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to EP11166622A priority Critical patent/EP2524970A1/de
Priority to JP2014510785A priority patent/JP6193219B2/ja
Priority to KR1020137030555A priority patent/KR102001648B1/ko
Priority to ES12721842.8T priority patent/ES2628409T3/es
Priority to PCT/EP2012/059076 priority patent/WO2012156428A1/de
Priority to EP12721842.8A priority patent/EP2710158B1/de
Priority to US14/117,711 priority patent/US9650708B2/en
Priority to CN201280024105.XA priority patent/CN103597100B/zh
Priority to PL12721842T priority patent/PL2710158T3/pl
Publication of EP2524970A1 publication Critical patent/EP2524970A1/de
Withdrawn legal-status Critical Current

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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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • 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
    • C22C38/02—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
    • C22C38/04—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
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the invention relates to a high-strength flat steel product and to a method for producing such a flat steel product.
  • the invention relates to a high-strength flat steel product provided with a metallic protective layer and to a method for producing such a product.
  • cooling rates are given a negative value because they lead to a decrease in temperature. Accordingly, cooling rates have a lower value for a rapid cooling than for a slower cooling. The leading to an increase in temperature heating rates, however, are given a positive.
  • High strength steels regularly tend to corrode because of their alloying constituents and are therefore typically coated with a metallic protective layer which protects the respective steel substrate from contact with the ambient oxygen.
  • a metallic protective layer which protects the respective steel substrate from contact with the ambient oxygen.
  • Various methods for applying such a metallic protective layer are known. These include hot-dip coating, also known in technical language as "fire-coating", and electrolytic coating.
  • the coating metal is deposited electrochemically on the flat steel product to be coated, which is at most slightly heated in the process, during hot dip coating the products to be coated are subjected to a heat treatment before immersion in the respective melt bath.
  • the respective flat steel product is heated to high temperatures under a certain atmosphere in order to set the desired structure and to produce an optimum for the adhesion of the metallic coating surface state of the respective flat steel product.
  • the flat steel product passes through the melt bath, which also has an elevated temperature, to keep the coating material molten.
  • the steel strip is dip-coated.
  • the metallic coating applied in this case should preferably be a zinc coating.
  • a cold strip is to be obtained in this way, the optimized mechanical properties, such as a tensile strength of at least 1200 MPa, an elongation of at least 13% and a hole widening of at least 50%, has.
  • the cold rolled strip processed in the manner described above is said to be made of a steel containing, in addition to iron and unavoidable impurities (in% by weight) 0.05-0.5% C, 0.01-2.5% Si, 0.5 - 3.5% Mn, 0.003 - 0.100% P, up to 0.02% S and 0.010 - 0.5 Al.
  • the steel should have a microstructure comprising (in area%) up to 10% ferrite, up to 10% martensite and 60-95 tempered martensite, and further 5 - 20% retained austenite, as determined by X-ray diffraction.
  • the steel (in weight%) can be 0.005 - 2.00% Cr, 0.005 - 2.00 Mo, 0.005 - 2.00% V, 0.005 - 2.00% Ni and 0.005 - 2.00% Cu and 0.01-0.20% Ti, 0.01-0.20 Nb, 0.0002-0.005% B, 0.001-0.005% Ca and 0.001-0.005% of rare earths.
  • the object of the invention was to provide a low-cost producible high-strength flat steel product which has further optimized mechanical properties, which are expressed in particular in a very good bending behavior.
  • a method for producing such a flat steel product should be specified.
  • this method should be incorporated into a process for hot dip coating of flat steel products.
  • the solution according to the invention of the abovementioned object consists in that during the production of a flat steel product according to the invention at least the steps mentioned in claim 6 are completed.
  • the operations specified in claim 7 can optionally also be carried out.
  • a steel flat product according to the invention consists of a steel which, in addition to iron and unavoidable impurities (in% by weight) C: 0.10-0.50%, Si: 0.1-2.5%, Mn: 1.0. 3.5%, Al: up to 2.5%, P: up to 0.020%, S: up to 0.003%, N: up to 0.02%, and optionally one or more of the elements "Cr, Mo, V, Ti, Nb, B and Ca" in the following contents: Cr: 0.1-0.5%, Mo: 0.1-0.3%, V : 0.01 - 0.1%, Ti: 0.001 - 0.15%, Nb: 0.02 - 0.05%, wherein for the sum ⁇ (V, Ti, Nb) of the contents of V, Ti and Nb ⁇ (V, Ti, Nb) is at most equal to 0.2%, B: 0.0005 - 0.005%, Ca: up to 0.01%.
  • Essential for the superior mechanical properties of the flat steel product according to the invention is that it has a structure with (in area%) less than 5% ferrite, less than 10% bainite, 5-70% unanbergem martensite, 5-30% retained austenite and 25 80% tempered martensite. At least 99% of the number of iron carbides contained in tempered martensite has a size of less than 500 nm.
  • Over-tempered martensite is characterized in that more than 1% number of carbide grains (iron carbides) are more than 500 nm in size.
  • over-cut martensite can be detected by scanning electron microscopy at 20,000 magnifications on steel samples etched with 3% nitric acid.
  • the C content of the steel of a flat steel product according to the invention is limited to values between 0.10 and 0.50 wt.%. Carbon influences a flat steel product according to the invention in many respects.
  • C plays a major role in the formation of austenite and lowering the Ac3 temperature.
  • a sufficient concentration of C allows complete austenitization at temperatures ⁇ 960 ° C, even if at the same time elements, such as Al, are present, which increase the Ac3 temperature.
  • the retained austenite is also stabilized by the presence of C. This effect continues during the partitioning step.
  • a stable residual austenite leads to a maximum strain range, in which the effect of the TRIP effect (TRANSformation Induced Plasticity) becomes noticeable.
  • the strength of the martensite is most strongly influenced by the respective C content. Too high a content of C leads to such a strong shift of the martensite start temperature to ever lower temperatures that the production of the flat steel product according to the invention becomes excessively difficult. In addition, too high C contents can adversely affect weldability.
  • the Si content in the steel of the flat steel product according to the invention should be less than 2.5% by weight. Silicon is important for suppressing cementite formation. The formation of cementite would break the C as a carbide and would then no longer stand for the stabilization of the retained austenite to disposal. In addition, the stretch would be worsened.
  • the effect achieved by the addition of Si can in part also be achieved by alloying aluminum. However, a minimum of 0.1% by weight of Si should always be present in the flat steel product according to the invention in order to utilize its positive effect.
  • Manganese contents of 1.0-3.5% by weight, in particular up to 3.0% by weight, are important for the hardenability of the flat steel product according to the invention and the prevention of perlite formation during cooling. These properties make it possible to form a starting structure consisting of martensite and retained austenite, and as such is suitable for the partitioning step carried out according to the invention.
  • manganese proves advantageous with regard to the setting of comparatively low cooling rates of, for example, faster than -100 K / s.
  • an excessively high Mn concentration has a negative influence on the elongation properties and the weldability of a flat steel product according to the invention.
  • Aluminum is present in the steel of a flat steel product of the present invention at levels of up to 2.5% for deoxidation and for the setting of any nitrogen present.
  • Al can also be used for the suppression of cementite and does not have such a negative effect on the surface properties as high contents of Si.
  • Al is not as effective as Si and also increases the austenitizing temperature. Therefore, the Al content is of a flat steel product according to the invention is limited to a maximum of 2.5% by weight and preferably to values of between 0.01 and 1.5% by weight.
  • Phosphorus is unfavorable to weldability and should therefore be present in the steel of a flat steel product of the present invention at levels less than 0.02% by weight.
  • the S content in the steel of a flat steel product according to the invention should be below 0.003 wt .-%.
  • nitrogen in the steel of a flat steel product according to the invention has a detrimental effect on the formability.
  • the N content of a flat steel product according to the invention should therefore be less than 0.02% by weight.
  • V, Ti and Nb are added to the steel of a flat steel product according to the invention.
  • These elements contribute to higher strength through the formation of very finely divided carbides or carbonitrides.
  • a minimum Ti content of 0.001% by weight leads to a freezing of the grain and phase boundaries during the Partitioning step.
  • too high a concentration of V, Ti and Nb can be detrimental to the stabilization of retained austenite. Therefore, the sum of the contents of V, Ti and Nb in a flat steel product according to the invention is limited to 0.2% by weight.
  • Chromium is an effective inhibitor of perlite, contributes to the strength and therefore may be added up to 0.5% by weight to the steel of a flat steel product according to the invention. Above 0.5% by weight, there is a risk of pronounced grain boundary oxidation. In order to be able to safely use the positive influence of Cr, the Cr content can be set to 0.1-0.5% by weight.
  • molybdenum is also a very effective element for suppressing perlite formation.
  • the steel of a flat steel product according to the invention can be alloyed with 0.1-0.3% by weight.
  • Calcium in contents of up to 0.01% by weight is used in the steel of a steel flat product according to the invention for setting sulfur and for inclusion modification.
  • the method according to the invention for producing a high-strength steel flat product, optionally provided with a metallic protective coating provided by hot-dip coating comprises the following working steps:
  • the steel constituting the flat steel product contains C: 0.10-0.50%, Si: 0.1-2.5%, Mn: 1.0 - 3.5%, Al: up to 2.5%, P: up to 0.020%, S: up to 0.003%, N: up to 0.02%, and optionally one or more of the elements "Cr, Mo, V, Ti, Nb, B and Ca "in the following contents: Cr: 0.1 - 0.5%, Mo: 0.1 - 0.3%, V: 0.01 - 0.1%, Ti: 0.001 - 0.15%, Nb: 0.02 - 0.05%, where for the sum ⁇ (V, Ti, Nb) the contents of V, Ti and Nb holds ⁇ (V, Ti, Nb) ⁇ 0.2 %, B: 0.0005
  • the thus provided flat steel product is then heated to a above the Ac3 temperature of the steel of the steel flat product and at most 960 ° C amount austenitizing temperature T HZ at a heating rate ⁇ H1 , ⁇ H2 of at least 3 ° C / s. Fast heating reduces the process time and improves the overall cost-effectiveness of the process.
  • the heating to the Austenitmaschinestemperatur T HZ can in two uninterrupted successive stages be performed with different heating rates ⁇ H1 , ⁇ H2 .
  • the heating at lower temperatures can be done very quickly to increase the efficiency of the process.
  • the dissolution of carbides begins.
  • lower heating rates ⁇ H2 are advantageous in order to ensure a uniform distribution of the carbon and other possible alloying elements, such. Mo or Cr.
  • the carbides are deliberately annealed already below the A c1 temperature to exploit the faster diffusion in the ferrite over the slower diffusion in austenite.
  • the dissolved atoms can be distributed more uniformly in the material as a result of a lower heating rate ⁇ H2 .
  • a limited heating rate ⁇ H2 is also favorable during the austenite transformation, ie between A c1 and A c3 . This contributes to a homogeneous starting structure before quenching and thus a uniformly distributed martensite and a fine retained austenite after quenching and ultimately improved mechanical properties of the flat steel product.
  • the heating rate ⁇ H1 of the first stage may be 5-25 ° C / s and the heating rate ⁇ H2 of the second stage 3-10 ° C, especially 3-5 ° C / s amount.
  • the flat steel product with the first heating rate ⁇ H1 can be heated to an intermediate temperature T w of 200-500 ° C, in particular 250-500 ° C, and the heating can then be continued at the second heating rate ⁇ H2 up to the austenitizing temperature T HZ .
  • the flat steel product is kept at the austenitizing temperature T Hz for an austenitizing time t HZ of 20-180 s.
  • the annealing temperature in the holding zone should be above the A c3 temperature in order to achieve complete austenitization.
  • the steel sheet After annealing at temperatures above A c3 , the steel sheet is cooled to a cooling stop temperature T Q greater than the martensite stop temperature T Mf and less than the martensite start temperature T Ms (T Mf ⁇ T Q ⁇ T Ms ) at a cooling rate ⁇ Q ,
  • the cooling rate ⁇ Q is in the range of -20 ° C / s to -120 ° C / s.
  • the condition ⁇ Q ⁇ ⁇ Q (min) can be surely satisfied in practice even for steels having a low C or Mn content.
  • Parallel to the yield strength increase can be achieved by the inventively carried out cooling to the cooling stop temperature and the subsequent holding of the flat steel product at this temperature over the times prescribed by the invention, an improvement of the forming properties. If tensile strength and tensile elongation are to be maximized, the holding time t Q should rather be kept in the lower range, ie between 10 and 30 s. Longer holding times t Q of 30 - 60 s tend to have a positive effect on the forming properties. This concerns in particular the bending angle.
  • the cooling stop temperature T Q is at least 200 ° C.
  • the steel flat product After cooling and holding the steel flat product at the cooling stop temperature T Q , the steel flat product is heated to a 400-500 ° from the cooling stop temperature T Q with a heating rate ⁇ P1 of 2 - 80 ° C / s, especially 2 - 40 ° C / s C, in particular 450 - 490 ° C, amounting temperature T P heated.
  • the heating to the temperature T P is preferably carried out within a heating time t A of 1 - 150 s, in order to achieve optimum efficiency. At the same time, the heating can make a contribution x Dr to a diffusion length x D explained below.
  • the purpose of the heating and a subsequent optional additional holding of the flat steel product at the temperature T P over a holding period t Pi of up to 500 s is the enrichment of the retained austenite with carbon from the supersaturated martensite.
  • the holding period t Pi is in particular up to 200 s, wherein holding periods t Pi of less than 10 s are particularly practical.
  • the partitioning can already during the heating as a so-called “Ramped Partitioning” done by the held after the heating hold at the partitioning temperature T P (so-called “isothermal” partitioning) or by a combination of isothermal and ramped partitioning.
  • the high temperatures necessary for the subsequent hot-dip coating can be achieved without causing special tempering effects, ie over-tempering of the martensite.
  • the slower heating rate ⁇ P1 envisaged for ramped partitioning in comparison to isothermal partitioning permits a particularly precise control of the respectively prescribed partitioning temperature T P with reduced energy input, since higher temperature gradients require a higher energy expenditure in the system.
  • the inventively predetermined partitioning temperature T P ensures sufficient homogenization of the carbon in the austenite, this homogenization being able to be influenced by the heating speed ⁇ P1 , the partitioning temperature T P and the optional holding at the partitioning temperature T P over a suitable holding time t Pi .
  • the proportions x Dr or x Di can also be "0" depending on the respective process control, the total diffusion length x D being always> 0 as a result of the method according to the invention.
  • the method according to the invention provides optimum work results if the sum of the respective diffusion lengths x Di , x Dr to be considered is at least 1.0 ⁇ m, in particular at least 1.5 ⁇ m.
  • the operating parameters in the heat treatment so that the diffusion length increases, the bending angle of the respective flat steel product can be improved, while the hole expansion is only slightly affected.
  • the hole widening can be improved, but this can be accompanied by a deterioration of the bending properties.
  • Even larger diffusion lengths eventually cause the deterioration of both bending properties and hole widening.
  • Optimal work results arise when the operating parameters are set in the method according to the invention so that diffusion lengths of 1.5 to 5.7 microns, in particular from 2.0 to 4.5 microns are achieved.
  • the interaction with the cooling and holding step preceding the partitioning can also be achieved by the Yield ratio can be influenced. If, for example, a high martensite content of 40% or more is generated by selecting a low cooling stop temperature T Q and / or a longer hold time t Q in the cooling step, by selecting a high partitioning temperature T P and time t Pt a larger diffusion length x D and thus ultimately a high yield ratio can be achieved. If less than about 40% martensite is produced, then the influence of the diffusion length x D on the yield ratio is rather small.
  • the yield ratio is a measure of the solidification potential of the steel.
  • a relatively low yield ratio of about 0.50 has a positive effect on the tensile elongation, but is unfavorable for the hole widening and the bending angle.
  • a higher yield ratio of about 0.90 can improve hole widening and bending properties, but leads to losses in tensile elongation.
  • the steel flat product is cooled starting from the partitioning temperature T P with a cooling rate ⁇ P2 which amounts to -3 ° C / s to -25 ° C / s, in particular -5 ° C / s to -15 ° C / s.
  • the flat steel product according to the invention is to be additionally provided with a hot-dip coating in the course of the method according to the invention, it is initially cooled to a melt-bath inlet temperature T B of 400-500 ° C., starting from the partitioning temperature T P at the cooling rate ⁇ P2 .
  • the steel flat product for hot dip coating passes through a melt bath, at the leaving of which the thickness of the protective coating produced on the flat steel product is adjusted in a conventional manner, for example by wiping nozzles.
  • the protective coated steel flat product exiting the melt bath is finally cooled to room temperature at the cooling rate ⁇ P2 to again produce martensite.
  • the process according to the invention is particularly suitable for the production of flat steel products which are provided with a zinc coating.
  • other metallic coatings which can be applied by hot-dip coating to the respective flat steel product, such as ZnAl, ZnMg or comparable protective coatings, are also possible.
  • the product produced according to the invention has a microstructure containing 25 to 80% tempered martensite (martensite from the first cooling step), 5 to 70% unannealed, new martensite (martensite from the second cooling step), 5 to 30% retained austenite, less than 10% Bainite (0% included) and less than 5% ferrite (0% included).
  • the inventive method thus enables the production of a refined flat steel product having a tensile strength of 1200 to 1900 MPa, a yield strength of 600 to 1400 MPa, a yield ratio of 0.40 to 0.95, an elongation (A 50 ) of 10 to 30% and a very good formability.
  • the product R m * A 50 is 15,000-35,000 MPa%.
  • high strength and good forming properties are paired with each other.
  • FIG. 1 a variant of the method according to the invention is shown in which the heating time t A required for heating the steel flat product from the cooling stop temperature T Q to the partitioning temperature T P is equal to the duration t Pr of the ramped partitioning and the flat steel product in the course of this process a hot dip coating in a Zinc bath ("zinc pot”) is subjected.
  • the heating time t A required for heating the steel flat product from the cooling stop temperature T Q to the partitioning temperature T P is equal to the duration t Pr of the ramped partitioning and the flat steel product in the course of this process a hot dip coating in a Zinc bath ("zinc pot”) is subjected.
  • the variant comprising a hot-dip coating of the method according to the invention can be carried out in a conventional fire-coating system if certain modifications are made to it.
  • ceramic radiant tubes may be needed.
  • the high cooling rates ⁇ Q of up to -120 K / s can be achieved with modern gas jet cooling.
  • the heating to the partitioning temperature T P after holding at the cooling stop temperature T Q can be achieved through use a booster can be achieved. After the partitioning step, the belt passes through the melt bath and is cooled in a controlled manner to regenerate martensite.
  • the samples have the inventively given, in FIG. 1 through process steps shown with the process parameters given in Table 2.
  • the process parameters between parameters according to the invention and parameters not according to the invention have been varied in order to demonstrate the effects of a procedure which is outside the scope of the invention.
  • the calculation of the diffusion length was based on time steps of 1 s each.
  • microstructural constituents of the cold strip samples obtained are given in Table 4.

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EP11166622A 2011-05-18 2011-05-18 Hochfestes Stahlflachprodukt und Verfahren zu dessen Herstellung Withdrawn EP2524970A1 (de)

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EP11166622A EP2524970A1 (de) 2011-05-18 2011-05-18 Hochfestes Stahlflachprodukt und Verfahren zu dessen Herstellung
PL12721842T PL2710158T3 (pl) 2011-05-18 2012-05-16 Wysoko wytrzymały płaski produkt stalowy i sposób jego wytwarzania
PCT/EP2012/059076 WO2012156428A1 (de) 2011-05-18 2012-05-16 Hochfestes stahlflachprodukt und verfahren zu dessen herstellung
KR1020137030555A KR102001648B1 (ko) 2011-05-18 2012-05-16 고강도 판상 강 제품 및 그 제조 방법
ES12721842.8T ES2628409T3 (es) 2011-05-18 2012-05-16 Producto plano de acero, de alta resistencia, y procedimiento para su fabricación
JP2014510785A JP6193219B2 (ja) 2011-05-18 2012-05-16 高強度鋼板製品及びその製造方法
EP12721842.8A EP2710158B1 (de) 2011-05-18 2012-05-16 Hochfestes stahlflachprodukt und verfahren zu dessen herstellung
US14/117,711 US9650708B2 (en) 2011-05-18 2012-05-16 High-strength flat steel product and method for producing same
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Cited By (41)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103160680A (zh) * 2013-04-03 2013-06-19 北京科技大学 一种制备30GPa%级复相钢的Q&PB热处理工艺
WO2014114159A1 (zh) * 2013-01-22 2014-07-31 宝山钢铁股份有限公司 一种具有低屈服比的超高强韧钢板及其制造方法
WO2014186722A3 (en) * 2013-05-17 2015-01-08 Ak Steel Properties, Inc. High strength steel exhibiting good ductility and method of production via quenching and partitioning treatment by zinc bath
EP2905348A1 (de) * 2014-02-07 2015-08-12 ThyssenKrupp Steel Europe AG Hochfestes Stahlflachprodukt mit bainitisch-martensitischem Gefüge und Verfahren zur Herstellung eines solchen Stahlflachprodukts
CN104928590A (zh) * 2015-06-11 2015-09-23 北京交通大学 一种Mn-Si-Cr低碳贝氏体钢、钎杆及其制备方法
WO2015177615A1 (fr) * 2014-05-20 2015-11-26 Arcelormittal Tôle d'acier doublement recuite a hautes caracteristiques mecaniques de resistance et de ductilite, procede de fabrication et utilisation de telles tôles
WO2016001702A1 (en) * 2014-07-03 2016-01-07 Arcelormittal Method for producing a high strength coated steel sheet having improved strength, ductility and formability
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WO2016005615A1 (es) * 2014-07-08 2016-01-14 Gerdau Investigacion Y Desarrollo Europa, S.A. Acero microaleado para conformado en caliente de piezas de alta resistencia y alto limite elastico y procedimiento para obtener componentes de dicho acero
WO2016016683A1 (en) * 2014-07-30 2016-02-04 Arcelormittal A method for producing a high strength steel piece
EP1997923B1 (en) * 2006-03-20 2016-03-09 National Institute for Materials Science Method for producing an ni-base superalloy
DE102014017273A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Hochfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
DE102014017275A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Hochfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
DE102014017274A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Höchstfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
WO2016177420A1 (de) 2015-05-06 2016-11-10 Thyssenkrupp Steel Europe Ag Stahlflachprodukt und verfahren zu seiner herstellung
EP2710158B1 (de) 2011-05-18 2017-03-15 ThyssenKrupp Steel Europe AG Hochfestes stahlflachprodukt und verfahren zu dessen herstellung
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CN107429363A (zh) * 2015-04-08 2017-12-01 新日铁住金株式会社 热处理钢板构件以及其的制造方法
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US10822680B2 (en) 2015-04-08 2020-11-03 Nippon Steel Corporation Steel sheet for heat treatment
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EP3988679A4 (en) * 2019-08-20 2022-11-02 JFE Steel Corporation HIGH STRENGTH COLD ROLLED STEEL PLATE AND METHOD OF PRODUCTION THEREOF
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US11613789B2 (en) 2018-05-24 2023-03-28 GM Global Technology Operations LLC Method for improving both strength and ductility of a press-hardening steel
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RU2812417C1 (ru) * 2023-07-18 2024-01-30 Федеральное государственное бюджетное образовательное учреждение высшего образования "Российский государственный аграрный университет - МСХА имени К.А. Тимирязева" (ФГБОУ ВО РГАУ - МСХА имени К.А. Тимирязева) Способ получения высокопрочного стального листа
DE102022125128A1 (de) * 2022-09-29 2024-04-04 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes aus einem hochfesten Mehrphasenstahl und entsprechendes Stahlband

Families Citing this family (57)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FI20115702L (fi) 2011-07-01 2013-01-02 Rautaruukki Oyj Menetelmä suurlujuuksisen rakenneteräksen valmistamiseksi ja suurlujuuksinen rakenneteräs
JP6017341B2 (ja) * 2013-02-19 2016-10-26 株式会社神戸製鋼所 曲げ性に優れた高強度冷延鋼板
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WO2016001704A1 (en) 2014-07-03 2016-01-07 Arcelormittal Method for manufacturing a high strength steel sheet and sheet obtained
CN106661652B (zh) 2014-07-03 2018-10-12 安赛乐米塔尔公司 用于制造超高强度涂覆或未涂覆钢板的方法和获得的板
DE102014114365A1 (de) * 2014-10-02 2016-04-07 Thyssenkrupp Steel Europe Ag Mehrschichtiges Stahlflachprodukt und daraus hergestelltes Bauteil
WO2016079565A1 (en) * 2014-11-18 2016-05-26 Arcelormittal Method for manufacturing a high strength steel product and steel product thereby obtained
WO2016092733A1 (ja) 2014-12-12 2016-06-16 Ｊｆｅスチール株式会社 高強度冷延鋼板及びその製造方法
JP2016153524A (ja) * 2015-02-13 2016-08-25 株式会社神戸製鋼所 切断端部での耐遅れ破壊特性に優れた超高強度鋼板
CN104831180B (zh) * 2015-05-15 2016-09-28 东北大学 一种深海用海洋软管铠装层用钢及其制备方法
DE102015111177A1 (de) * 2015-07-10 2017-01-12 Salzgitter Flachstahl Gmbh Höchstfester Mehrphasenstahl und Verfahren zur Herstellung eines kaltgewalzten Stahlbandes hieraus
DE102015119839A1 (de) * 2015-11-17 2017-05-18 Benteler Steel/Tube Gmbh Stahllegierung mit hohem Energieaufnahmevermögen und Stahlrohrprodukt
JP2018538440A (ja) 2015-11-16 2018-12-27 ベントラー スティール ／ チューブ ゲーエムベーハー 高エネルギー吸収能力を備えた合金鋼及び鋼管製品
SE539519C2 (en) * 2015-12-21 2017-10-03 High strength galvannealed steel sheet and method of producing such steel sheet
WO2017109542A1 (en) * 2015-12-21 2017-06-29 Arcelormittal Method for producing a high strength steel sheet having improved ductility and formability, and obtained steel sheet
KR101714930B1 (ko) * 2015-12-23 2017-03-10 주식회사 포스코 구멍확장성이 우수한 초고강도 강판 및 그 제조방법
US11035020B2 (en) 2015-12-29 2021-06-15 Arcelormittal Galvannealed steel sheet
MX2018009099A (es) * 2016-01-27 2018-09-03 Jfe Steel Corp Lamina de acero galvanizada de alta resistencia de alta relacion de cedencia y metodo para fabricar la misma.
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CA3067159A1 (en) 2016-11-29 2018-06-07 Tata Steel Ijmuiden B.V. Method for manufacturing a hot-formed article, and obtained article
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US12286682B2 (en) 2019-04-30 2025-04-29 Tata Steel Nederland Technology B.V. High strength steel product and a process to produce a high strength steel product
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ES2911662T5 (en) 2019-06-17 2025-06-05 Tata Steel Ijmuiden Bv Method of heat treating a high strength cold rolled steel strip
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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0693340A (ja) * 1992-09-14 1994-04-05 Kobe Steel Ltd 伸びフランジ性の優れた高強度合金化溶融亜鉛めっき鋼板の製造方法及び製造設備
WO2004022794A1 (en) * 2002-09-04 2004-03-18 Colorado School Of Mines Method for producing steel with retained austenite
CA2734976A1 (en) * 2008-09-10 2010-03-18 Jfe Steel Corporation High strength steel sheet and method for manufacturing the same
EP2267176A1 (en) 2008-02-08 2010-12-29 JFE Steel Corporation High-strength hot-dip galvanized steel sheet with excellent processability and process for producing the same

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6395108B2 (en) * 1998-07-08 2002-05-28 Recherche Et Developpement Du Groupe Cockerill Sambre Flat product, such as sheet, made of steel having a high yield strength and exhibiting good ductility and process for manufacturing this product
JP5365216B2 (ja) * 2008-01-31 2013-12-11 Ｊｆｅスチール株式会社 高強度鋼板とその製造方法
JP4324225B1 (ja) 2008-03-07 2009-09-02 株式会社神戸製鋼所 伸びフランジ性に優れた高強度冷延鋼板
JP5400484B2 (ja) 2009-06-09 2014-01-29 株式会社神戸製鋼所 伸び、伸びフランジ性および溶接性を兼備した高強度冷延鋼板
JP5333298B2 (ja) 2010-03-09 2013-11-06 Ｊｆｅスチール株式会社 高強度鋼板の製造方法
EP2524970A1 (de) 2011-05-18 2012-11-21 ThyssenKrupp Steel Europe AG Hochfestes Stahlflachprodukt und Verfahren zu dessen Herstellung

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0693340A (ja) * 1992-09-14 1994-04-05 Kobe Steel Ltd 伸びフランジ性の優れた高強度合金化溶融亜鉛めっき鋼板の製造方法及び製造設備
WO2004022794A1 (en) * 2002-09-04 2004-03-18 Colorado School Of Mines Method for producing steel with retained austenite
EP2267176A1 (en) 2008-02-08 2010-12-29 JFE Steel Corporation High-strength hot-dip galvanized steel sheet with excellent processability and process for producing the same
CA2734976A1 (en) * 2008-09-10 2010-03-18 Jfe Steel Corporation High strength steel sheet and method for manufacturing the same

Cited By (100)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1997923B1 (en) * 2006-03-20 2016-03-09 National Institute for Materials Science Method for producing an ni-base superalloy
EP2710158B1 (de) 2011-05-18 2017-03-15 ThyssenKrupp Steel Europe AG Hochfestes stahlflachprodukt und verfahren zu dessen herstellung
US10801090B2 (en) 2013-01-22 2020-10-13 Baoshan Iron & Steel Co., Ltd. Ultra high obdurability steel plate having low yield ratio and process of manufacturing same
WO2014114159A1 (zh) * 2013-01-22 2014-07-31 宝山钢铁股份有限公司 一种具有低屈服比的超高强韧钢板及其制造方法
CN103160680A (zh) * 2013-04-03 2013-06-19 北京科技大学 一种制备30GPa%级复相钢的Q&PB热处理工艺
CN105392906A (zh) * 2013-05-17 2016-03-09 Ak钢铁资产公司 表现出良好延展性的高强度钢及通过在熔融镀锌槽下游在线热处理的生产方法
JP2016524038A (ja) * 2013-05-17 2016-08-12 エイケイ・スティール・プロパティーズ・インコーポレイテッドＡｋ Ｓｔｅｅｌ Ｐｒｏｐｅｒｔｉｅｓ， Ｉｎｃ． 良好な耐久性を示す高強度鋼、および焼入れと亜鉛浴による分配処理とによる製造方法
CN113151735A (zh) * 2013-05-17 2021-07-23 克利夫兰-克利夫斯钢铁资产公司 表现出良好延展性的高强度钢以及通过镀锌槽进行淬火和分配处理的制备方法
EP2997172B1 (en) * 2013-05-17 2020-08-26 Ak Steel Properties, Inc. Method of producton of a high strength steel exhibiting good ductility via quenching and partitioning treatment by zinc bath
JP2018178262A (ja) * 2013-05-17 2018-11-15 エイケイ・スティール・プロパティーズ・インコーポレイテッドＡｋ Ｓｔｅｅｌ Ｐｒｏｐｅｒｔｉｅｓ， Ｉｎｃ． 鋼板の処理方法
WO2014186722A3 (en) * 2013-05-17 2015-01-08 Ak Steel Properties, Inc. High strength steel exhibiting good ductility and method of production via quenching and partitioning treatment by zinc bath
WO2014186689A3 (en) * 2013-05-17 2015-01-22 Ak Steel Properties, Inc. High strength steel exhibiting good ductility and method of production via in-line heat treatment downstream of molten zinc bath
CN105247090A (zh) * 2013-05-17 2016-01-13 Ak钢铁资产公司 表现出良好延展性的高强度钢以及通过镀锌槽进行淬火和分配处理的制备方法
RU2632042C2 (ru) * 2013-05-17 2017-10-02 Ак Стил Пропертиз, Инк. Высокопрочная сталь, обладающая хорошей пластичностью, и способ получения посредством обработки методом закалки с распределением с помощью ванны для цинкования
EP2905348A1 (de) * 2014-02-07 2015-08-12 ThyssenKrupp Steel Europe AG Hochfestes Stahlflachprodukt mit bainitisch-martensitischem Gefüge und Verfahren zur Herstellung eines solchen Stahlflachprodukts
US10724113B2 (en) 2014-02-07 2020-07-28 Thyssenkrupp Steel Europe Ag High-strength flat steel product having a bainitic-martensitic microstructure and method for producing such a flat steel product
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US10435762B2 (en) 2014-03-31 2019-10-08 Jfe Steel Corporation High-yield-ratio high-strength cold-rolled steel sheet and method of producing the same
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WO2016005615A1 (es) * 2014-07-08 2016-01-14 Gerdau Investigacion Y Desarrollo Europa, S.A. Acero microaleado para conformado en caliente de piezas de alta resistencia y alto limite elastico y procedimiento para obtener componentes de dicho acero
US10415112B2 (en) 2014-07-30 2019-09-17 Arcelormittal Method for producing a high strength steel piece
RU2690851C2 (ru) * 2014-07-30 2019-06-06 Арселормиттал Способ изготовления высокопрочной стальной детали
CN108283003B (zh) * 2014-07-30 2019-11-01 安赛乐米塔尔公司 用于制造高强度钢件的方法
WO2016016779A3 (en) * 2014-07-30 2016-03-31 Arcelormittal A method for producing a high strength steel piece
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WO2016016683A1 (en) * 2014-07-30 2016-02-04 Arcelormittal A method for producing a high strength steel piece
KR20170041704A (ko) * 2014-07-30 2017-04-17 아르셀러미탈 고강도 강 피스를 제조하기 위한 방법
DE102014017273A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Hochfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
DE102014017275A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Hochfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
DE102014017274A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Höchstfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
DE102015119417B4 (de) * 2014-11-26 2017-10-19 GM Global Technology Operations LLC (n. d. Ges. d. Staates Delaware) Verfahren zum presshärten einer galvanisierten stahllegierung
US11041225B2 (en) 2015-04-08 2021-06-22 Nippon Steel Corporation Heat-treated steel sheet member and method for producing the same
US10822680B2 (en) 2015-04-08 2020-11-03 Nippon Steel Corporation Steel sheet for heat treatment
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CN107429363A (zh) * 2015-04-08 2017-12-01 新日铁住金株式会社 热处理钢板构件以及其的制造方法
WO2016177763A1 (de) 2015-05-06 2016-11-10 Thyssenkrupp Steel Europe Ag Stahlflachprodukt und verfahren zu seiner herstellung
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US10597746B2 (en) 2015-07-24 2020-03-24 Thyssenkrupp Steel Europe Ag High-strength steel having a high minimum yield limit and method for producing a steel of this type
CN107922986A (zh) * 2015-07-24 2018-04-17 蒂森克虏伯钢铁欧洲股份公司 具有高最小屈服极限的高强度钢和这种钢的生产方法
EP3390040B1 (en) 2015-12-15 2020-08-26 Tata Steel IJmuiden B.V. High strength hot dip galvanised steel strip
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US10954580B2 (en) 2015-12-21 2021-03-23 Arcelormittal Method for producing a high strength steel sheet having improved strength and formability, and obtained high strength steel sheet
US10385415B2 (en) 2016-04-28 2019-08-20 GM Global Technology Operations LLC Zinc-coated hot formed high strength steel part with through-thickness gradient microstructure
US10619223B2 (en) 2016-04-28 2020-04-14 GM Global Technology Operations LLC Zinc-coated hot formed steel component with tailored property
DE102017130237A1 (de) * 2017-12-15 2019-06-19 Salzgitter Flachstahl Gmbh Hochfestes, warmgewalztes Stahlflachprodukt mit hohem Kantenrisswiderstand und gleichzeitig hohem Bake-Hardening Potential, ein Verfahren zur Herstellung eines solchen Stahlflachprodukts
US11584971B2 (en) 2017-12-15 2023-02-21 Salzgitter Flachstahl Gmbh High-strength, hot-rolled flat steel product with high edge cracking resistance and, at the same time, high bake-hardening potential, and method for producing such a flat steel product
EP3511430A1 (de) * 2018-01-12 2019-07-17 SMS Group GmbH Verfahren für eine kontinuierliche wärmebehandlung eines stahlbands, und anlage zum schmelztauchbeschichten eines stahlbands
US11613789B2 (en) 2018-05-24 2023-03-28 GM Global Technology Operations LLC Method for improving both strength and ductility of a press-hardening steel
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JP2021530624A (ja) * 2018-09-26 2021-11-11 ティッセンクルップ スチール ヨーロッパ アクチェンゲゼルシャフトThyssenKrupp Steel Europe AG コーティングされた平鋼生産物を製造する方法及びコーティングされた平鋼生産物
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JP7029574B2 (ja) 2018-09-26 2022-03-03 ティッセンクルップ スチール ヨーロッパ アクチェンゲゼルシャフト コーティングされた平鋼生産物を製造する方法及びコーティングされた平鋼生産物
WO2020169342A1 (de) 2019-02-21 2020-08-27 Thyssenkrupp Steel Europe Ag Verfahren zum herstellen eines bauteils mittels innenhochdruckumformen
US11530469B2 (en) 2019-07-02 2022-12-20 GM Global Technology Operations LLC Press hardened steel with surface layered homogenous oxide after hot forming
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US11926881B2 (en) 2019-08-20 2024-03-12 Jfe Steel Corporation High-strength cold-rolled steel sheet and method for manufacturing the same
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WO2023233036A1 (en) * 2022-06-03 2023-12-07 Thyssenkrupp Steel Europe Ag High strength, cold rolled steel with reduced sensitivity to hydrogen embrittlement and method for the manufacture thereof
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DE102022125128A1 (de) * 2022-09-29 2024-04-04 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes aus einem hochfesten Mehrphasenstahl und entsprechendes Stahlband
RU2812417C1 (ru) * 2023-07-18 2024-01-30 Федеральное государственное бюджетное образовательное учреждение высшего образования "Российский государственный аграрный университет - МСХА имени К.А. Тимирязева" (ФГБОУ ВО РГАУ - МСХА имени К.А. Тимирязева) Способ получения высокопрочного стального листа

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