US20130118647A1 - Method of producing an austenitic steel - Google Patents

Method of producing an austenitic steel Download PDF

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Publication number
US20130118647A1
US20130118647A1 US13/699,516 US201113699516A US2013118647A1 US 20130118647 A1 US20130118647 A1 US 20130118647A1 US 201113699516 A US201113699516 A US 201113699516A US 2013118647 A1 US2013118647 A1 US 2013118647A1
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Prior art keywords
strip
sheet
process according
hot
metallic coating
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US13/699,516
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Inventor
Basjan Berkhout
Marcus Cornelis Maria Cornelissen
Jayesh Ramjibhai Patel
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Tata Steel Ijmuiden BV
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Tata Steel Ijmuiden BV
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Assigned to TATA STEEL IJMUIDEN BV reassignment TATA STEEL IJMUIDEN BV ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: BERKHOUT, BASJAN, CORNELISSEN, MARCUS CORNELIS MARIA, PATEL, JAYESH RAMJIBHAI
Publication of US20130118647A1 publication Critical patent/US20130118647A1/en
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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
    • C21D1/68—Temporary coatings or embedding materials applied before or during heat treatment
    • C21D1/70—Temporary coatings or embedding materials applied before or during heat treatment while heating or 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • C21D8/0421—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 working steps
    • C21D8/0436—Cold rolling
    • 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
    • C21D8/0421—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 working steps
    • C21D8/0442—Flattening; Dressing; Flexing
    • 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
    • C21D8/0473—Final recrystallisation 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/34—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tyres; for rims
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • 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
    • 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
    • C23C2/0222—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating in a reactive atmosphere, e.g. oxidising or reducing atmosphere
    • 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
    • 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
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching

Definitions

  • the invention relates to a method of producing an austenitic steel sheet excellent in resistance to delayed cracking.
  • small amounts of hydrogen may be introduced at some stages of steel fabrication such as chemical or electrochemical pickling, annealing under special atmospheres, electroplating or hot dip galvanizing. Subsequent machining operations using lubricating oils and greases may also cause hydrogen production after decomposition of these substances at high temperatures.
  • the SFE of the steel increases. Any adverse effects of the elements that lower the SFE, such as silicon, are counteracted by the addition of aluminium. Additionally, aluminium lowers the activity and the diffusivity of carbon in austenite, which reduces the driving force for forming carbides.
  • the vanadium which is added as an essential alloying addition, forms carbides. These vanadium-carbides act as hydrogen sinks if and when the size and distribution of the vanadium-carbides is correct.
  • the increased aluminium content is therefore essential to control the vanadium-carbide precipitation because it prevents the vanadium-carbides from coarsening due to the reduced carbon activity and diffusivity as a result of the presence of aluminium.
  • the annealing treatment is crucial in that it controls the precipitation of the vanadium-carbides and causes the recrystallisation of the cold-deformed microstructure caused by the cold-rolling to result in a fine grain structure.
  • the silicon content is very low, i.e. at impurity level.
  • the aluminium content is limited only by the fact that the steel according to the invention is an austenitic steel.
  • the maximum aluminium content is 5%.
  • the aluminium content is at least 1.25 and/or at most 3.5%, more preferably at least 1.5 and/or at most 2.5%.
  • the maximum annealing temperature T a is 825° C. or even 800° C.
  • the cooling rate V c is between 10 and 100° C./s.
  • a preferable cooling rate is between 20 and 80° C./s.
  • the heating rate is preferably between 3 and 60° C./s.
  • the annealing time t a is preferably between 15 and 300 seconds.
  • the maximum annealing temperature T a is from 775 to 795° C. (i.e. 785 ⁇ 10° C.).
  • the steel strip material has been pickled before cold rolling.
  • Pickling is (often) necessary before cold rolling to remove oxides, to prevent rolling in of oxides.
  • the cold rolled strip material is produced from a hot rolled strip material or a belt cast strip material.
  • the strip is led through a hot dip bath for providing a metallic coating by hot dipping the strip into a molten bath of the metal making up the metallic coating.
  • the metallic coating can be any known common coating such as zinc or zinc alloy, wherein the zinc may be alloyed with elements such as aluminium and/or magnesium.
  • the strip is pickled after continuous annealing and wherein the strip is provided with a metallic coating by pickling after annealing followed by heating to a temperature below the continuous annealing temperature before the strip is led through a hot dip bath for providing a metallic coating by hot dipping the strip into a molten bath of the metal making up the metallic coating.
  • This alternative process is available if the economical process as described hereinabove is not preferred. There may be issues with adhesion with certain specific metallic coatings for which a pickling treatment may be necessary. After pickling, it is not necessary nor desirable to heat the strip above the T a . It is preferable that the heating temperature remain below T a.
  • the strip material is heated only to a temperature high enough to form a closed inhibition layer.
  • This temperature is lower than the normal continuous annealing temperature necessary for metallurgical reasons (such as recrystallisation to influence mechanical properties). The forming of oxides on the surface of the steel strip material is thereby reduced.
  • the temperature below the continuous annealing temperature is between 400 and 600° C. In this temperature range the forming of oxides is considerably reduced and the strip material is heated sufficiently for the subsequent hot dip galvanizing.
  • the Fe in the strip material is reduced during or after the heating to a temperature below the continuous annealing temperature and before the hot dip galvanising.
  • the Fe-oxides that are formed are reduced, and in this way the amount of oxides present on the surface of the strip material before hot dip galvanizing is decreased considerably.
  • the reduction is performed using H 2 N 2 , more preferably using 5-30% H 2 N 2 in the reducing atmosphere. It has been found that with the use of this atmosphere most oxides can be removed.
  • an excess amount of O 2 is provided in the atmosphere during or after the heating of the strip material and before the reduction of the strip material.
  • the providing of an excess amount of oxygen improves the quality of the surface of the steel strip material before the hot dip galvanizing, and thus the quality of the zinc layer coated on the AHSS strip material. It is supposed that the oxygen binds the alloying elements in the AHSS strip material both at the surface of the strip material and internally, and that in this way the oxides formed cannot migrate to the surface of the strip material.
  • the reducing atmosphere that follows after the oxidation will then reduce the oxides at the surface of the strip material, and in this way the amount of oxides at the surface of the strip material is considerably reduced or even almost absent, as experiments have shown.
  • the excess amount of O 2 is provided in an amount of 0,05-5% O 2 . This amount of oxygen has been found to suffice.
  • V-alloyed TWIP steel strip material according to the invention was hot rolled, pickled and cold rolled, and continuously annealed to a temperature according to the invention and pickled again. Then the strip material is heated to a temperature of 527° C. in an annealing line, and thereafter hot dip galvanised in a galvanising bath at approximately 450° C.
  • the strip material is reduced using approximately 5% H 2 N 2 . The reduction of the strip material removes the oxides from the surface, but the oxides formed under the surface remain where they are and cannot migrate to the surface.
  • the oxides are effectively removed and no new oxides can be formed at the surface.
  • These oxides when not removed, cause a bad adhesion of the zinc layer to the substrate, resulting in bare spots, flaking and the forming of cracks in the zinc layer when the material is bent.
  • the alloying elements migrate to the surface very fast at the alloying temperature and thus form oxides at the surface again before the hot dip galvanising takes place. Whatever the exact mechanism may be, it has been found that the use of this method diminishes or almost eliminates the amount of oxides found in a hot dip galvanised zinc layer on a V-alloyed TWIP steel.
  • the cold-rolling reduction is between 10 to 90%, more preferably between 30 and 85, even more preferably between 45 and 80%.
  • the annealed strip is temper rolled with a reduction of from 0.5 to 10% prior to or after the metallic coating has been provided to the strip.
  • the Vanadium content is between 0.06 and 0.22%.
  • a strip or sheet is provided produced by a method according to any one of claims 1 to 6 , wherein the steel preferably is provided with a metallic coating.
  • the strip or sheet is used for the production of automotive inner or outer parts or wheels or for hydroforming applications.
  • the finish rolling temperature was chosen to ensure recrystallisation of the deformed microstructure and the coiling temperature was kept below 500° C. to avoid carbide precipitation. Recrystallisation does not solely depend on the FRT but also depends on the time, on the rolling strain accumulated since the last recrystallisation event during hot rolling and on the strain rate.
  • the material softens due to an increased fraction of recrystallised material and probably some grain growth. At these temperatures, the effect of precipitation is limited.
  • the difference between the (fully recrystallised) materials annealed at 775° C. and 800° C. is small because the precipitation is considered optimal in this temperature region for minimising grain growth. Based on these observations, the recommended annealing temperature is 785° C. ⁇ 10° C.
  • V-alloyed grades show a lower susceptibility to crack formation as the material is annealed at a higher temperature.
  • V addition is clearly beneficial at an annealing temperature of 750° C., but also at higher annealing temperatures.
  • V-alloys were subjected to a resistance spot welding tests. Hot cracking in the weld was largely reduced compared to the Si-free non V-alloyed material.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Steel (AREA)
US13/699,516 2010-06-10 2011-06-10 Method of producing an austenitic steel Abandoned US20130118647A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP10165596 2010-06-10
EP10165596.7 2010-06-10
PCT/EP2011/002868 WO2011154153A1 (en) 2010-06-10 2011-06-10 Method of producing an austenitic steel

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US (1) US20130118647A1 (enExample)
EP (1) EP2580359B1 (enExample)
JP (1) JP6009438B2 (enExample)
KR (1) KR101900963B1 (enExample)
CN (1) CN102939394A (enExample)
BR (1) BR112012031466B1 (enExample)
WO (1) WO2011154153A1 (enExample)
ZA (1) ZA201300240B (enExample)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2017203348A1 (en) * 2016-05-24 2017-11-30 Arcelormittal Twip steel sheet having an austenitic matrix
WO2017203312A1 (en) * 2016-05-24 2017-11-30 Arcelormittal Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts
CN108929991A (zh) * 2017-05-26 2018-12-04 宝山钢铁股份有限公司 一种热浸镀高锰钢及其制造方法
US10995381B2 (en) 2016-05-24 2021-05-04 Arcelormittal Method for producing a TWIP steel sheet having an austenitic microstructure
US11414721B2 (en) 2016-05-24 2022-08-16 Arcelormittal Method for the manufacture of TWIP steel sheet having an austenitic matrix
US11486017B2 (en) 2016-05-24 2022-11-01 Arcelormittal Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts
US20220410303A1 (en) * 2019-12-06 2022-12-29 Posco Method for manufacturing welded structure, and welded structure manufactured thereby
US11591664B2 (en) 2016-12-21 2023-02-28 Posco Co., Ltd Hot rolled steel sheet having excellent formability and fatigue properties and manufacturing method therefor

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Publication number Priority date Publication date Assignee Title
DE102013003516A1 (de) 2013-03-04 2014-09-04 Outokumpu Nirosta Gmbh Verfahren zur Herstellung eines ultrahochfesten Werkstoffs mit hoher Dehnung
DE102015111866A1 (de) 2015-07-22 2017-01-26 Salzgitter Flachstahl Gmbh Umformbarer Leichtbaustahl mit verbesserten mechanischen Eigenschaften und Verfahren zur Herstellung von Halbzeug aus diesem Stahl
EP4119683A1 (en) 2015-12-28 2023-01-18 United States Steel Corporation Delayed cracking prevention during drawing of high strength steel
KR101747034B1 (ko) * 2016-04-28 2017-06-14 주식회사 포스코 항복비가 우수한 초고강도 고연성 강판 및 이의 제조방법
WO2017203309A1 (en) * 2016-05-24 2017-11-30 Arcelormittal Twip steel sheet having an austenitic matrix
WO2017203311A1 (en) * 2016-05-24 2017-11-30 Arcelormittal Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts
DE102016117508B4 (de) 2016-09-16 2019-10-10 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlflachprodukts aus einem mittelmanganhaltigen Stahl und ein derartiges Stahlflachprodukt

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WO2008078940A1 (en) * 2006-12-27 2008-07-03 Posco High manganese high strength steel sheets with excellent crashworthiness, and method for manufacturing of it
WO2008135445A1 (en) * 2007-05-02 2008-11-13 Corus Staal B.V. Method for hot dip galvanising of ahss or uhss strip material, and such material

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EP2580359B1 (en) 2017-08-09
EP2580359A1 (en) 2013-04-17
KR20130111214A (ko) 2013-10-10
ZA201300240B (en) 2014-03-26
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CN102939394A (zh) 2013-02-20
JP6009438B2 (ja) 2016-10-19

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