EP3325678A1 - Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier - Google Patents

Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier

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Publication number
EP3325678A1
EP3325678A1 EP16750113.9A EP16750113A EP3325678A1 EP 3325678 A1 EP3325678 A1 EP 3325678A1 EP 16750113 A EP16750113 A EP 16750113A EP 3325678 A1 EP3325678 A1 EP 3325678A1
Authority
EP
European Patent Office
Prior art keywords
max
steel
elements
mpa
tensile strength
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.)
Granted
Application number
EP16750113.9A
Other languages
German (de)
English (en)
Other versions
EP3325678B1 (fr
Inventor
Peter PALZER
Zacharias Georgeou
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Salzgitter Flachstahl GmbH
Original Assignee
Salzgitter Flachstahl GmbH
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Publication of EP3325678A1 publication Critical patent/EP3325678A1/fr
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Classifications

    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0231—Warm rolling
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/0273—Final recrystallisation annealing

Definitions

  • the invention relates to a deformable lightweight structural steel with improved
  • the invention relates to a process for the production of semi-finished products from this steel.
  • semi-finished product is understood below to mean hot or cold strip produced from this steel or an intermediate or end product made therefrom, such as, for example, pipes.
  • lightweight steels which are characterized by a low specific weight while high strength and toughness and have a high ductility and thus are of great interest to the vehicle.
  • the high proportion of alloying constituents (Si, Al) having a specific gravity far below the specific gravity of iron achieves a weight reduction advantageous to the automobile industry while retaining the previous design construction.
  • the deformable lightweight structural steel known from the published patent application DE 10 2004 061 284 A1 has, for example, the following alloy composition (in% by weight): C 0.04 to ⁇ 1.0, Al 0.05 to ⁇ 4.0, Si 0, 05 to ⁇ 6.0, Mn 9.0 to ⁇ 18.0, the remainder being iron including conventional steel accompanying elements.
  • alloy composition in% by weight: C 0.04 to ⁇ 1.0, Al 0.05 to ⁇ 4.0, Si 0, 05 to ⁇ 6.0, Mn 9.0 to ⁇ 18.0, the remainder being iron including conventional steel accompanying elements.
  • Requirement Cr, Cu, Ti, Zr, V and Nb are added.
  • This lightweight steel has a partially stabilized ⁇ -mixed crystal structure with defined stacking fault energy with a z. T. multiple TRIP effect, which is the stress or strain-induced conversion of a face-centered ⁇ -mixed crystal (austenite) in an ⁇ -martensite (hexagonal closest packing) and then upon further deformation into a body-centered ⁇ -martensite and retained austenite.
  • TRIP Transformation Induced Plasticity
  • TWIP winning Induced Plasticity
  • WO 201 1/154153 A1 discloses an austenitic steel which is said to have outstanding resistance to delayed cracking.
  • the steel contains, in addition to iron and impurities in wt .-%: 0.5 to 0.8 C, 10 to 17 Mn, at least 1, 0 AI, at most 0.5 Si, at most 0.020 S, at most 0.050 P, 50 to 200 ppm N and 0.050 to 0.25 V.
  • WO 2009/142362 A1 discloses a steel alloy for a high-strength cold-rolled steel sheet, which should also have improved resistance to delayed cracking.
  • the steel contains, in addition to iron and impurities in wt .-%: 0.05 to 0.3 C, 0.3 to 1.6 Si, 4.0 to 7.0 Mn, 0.5 to 2.0 AI, 0 , 01 to 0.1 Cr, 0.02 to 0.1 Ni, 0.005 to 0.03 Ti, 5 to 30 ppm B, 0.01 to 0.03 Sb and 0.008 or less S.
  • EP 2 128 293 A1 discloses a lightweight structural steel with improved elongation, comprising iron and impurities in wt.%: 0.2 to 0.8 C, 2 to 10 Mn, 0.2 or less P , at most 0.015 S, 3.0 to 15 Al, at most 0.01 N and a ratio Mn / Al of 0.4 to 1.0.
  • a roll gap of a rolling mill during the production of the steel strip is selectively varied.
  • the object of the invention is to provide a lightweight steel of the generic type, while maintaining very good mechanical properties
  • This object is based on the preamble in connection with the
  • the deformable lightweight steel with TRIP is provided. According to the teachings of the invention, the deformable lightweight steel with TRIP and
  • TWIP properties the following elements in% by weight:
  • antimony causes the carbides to grow slower and thus finer and less precipitated. This will be
  • Alloying concepts result in improved mechanical properties and significant improvement with respect to avoiding delayed hydrogen-induced cracking (delayed fracture) and hydrogen embrittlement.
  • the evaluation of the mechanical properties is based on the product of tensile strength and elongation at break, which is a measure of the performance of the material.
  • the product or semifinished product produced from the alloy according to the invention by deformation which may be, for example, hot strip, cold strip, flexibly rolled hot or cold strip, a pipe or a body component, is therefore advantageously heat-treated at 480 to 770 ° C for 1 minute to 48 hours, for example, in a bell annealer with predominantly long annealing times or in a continuous annealing with predominantly short annealing times.
  • the timing of the annealing can therefore be flexibly adapted to the production process.
  • An annealing of the end product in addition to an already performed annealing of the semifinished product can lead to a further improvement of the material properties.
  • Annealing temperature 480 to 770 ° C
  • annealing time 1 minute to 48 hours.
  • Annealing temperature 480 to 770 ° C
  • annealing time 1 minute to 48 hours.
  • the annealing is preferably carried out at temperatures of 670 to 770 ° C at annealing times of 1 minute to 12 hours, as lower temperatures and longer annealing times lead to lower tensile strength and elongation at break.
  • a continuous annealing is preferably used for hot-rolled strip, cold strip and flexibly rolled strips for short annealing times, and preferably for long annealing times a crown annealing.
  • other annealing devices can be used with the given parameters, such as a muffle furnace.
  • Manganese-containing steels are possible, which have a better tensile strength and elongation at break than non-Sb-alloyed higher manganese-containing steels with the same chemical composition.
  • antimony also significantly improves the behavior towards hydrogen (delayed cracking and hydrogen embrittlement).
  • the reason for the improvement in the material properties is that antimony inhibits the diffusion of carbon and aluminum.
  • antimony lowers the interfacial energy, resulting in a finer distribution of the carbides.
  • the reduced carbon diffusion thus delays the local accumulation of carbon at the grain boundaries and in the microstructure and, in conjunction with aluminum, the formation of kappa carbides or in particular with V, Nb, Mo, Cr, W, Zr and Ti, the formation of local larger carbides.
  • the homogeneity of the material is thereby improved with the described positive effects on the mechanical properties and the resistance to delayed cracking and hydrogen embrittlement.
  • the precipitation of finely divided carbides leads to grain refining in the microstructure, which leads to an improvement in the behavior with respect to hydrogen-related negative effects (delayed cracking,
  • antimony For antimony to be effective, at least levels of 30 ppm are necessary. However, antimony contents of more than 0.8 wt.% Embrittle the material and should therefore be avoided. Optimal, the maximum content of antimony is 0.5 wt .-%.
  • Precipitated carbides improve the utilization of the corresponding alloying elements, potentially allowing a reduction in the amount of addition. Furthermore, due to the reduced carbon diffusion and the reduced grain growth due to the addition of antimony, the process window for the heat treatments necessary according to the invention is increased, that is, the steel is less sensitive to the resulting mechanical properties
  • AI Improves the strength and elongation properties, lowers the specific gravity, and influences the conversion behavior of the invention Alloys. Al contents of more than 15% by weight deteriorate the
  • Ca Used to modify non-metallic oxide inclusions, which can lead to inhomogeneities and unwanted material failure.
  • Mn Stabilizes austenite, increases strength and toughness, and allows for deformation-induced martensite and / or twinning in the
  • Mo acts as a strong carbide former and increases strength. Contents of Mo exceeding 2% by weight deteriorate the elongation properties, and therefore a maximum content of 2% by weight is determined.
  • Nb + V Grain-refining, in particular through the formation of carbides, which simultaneously improves the strength, toughness and elongation properties. Contents of over 1 wt .-% bring no further advantages.
  • Ni Stabilizes austenite and improves elongation properties, especially at low application temperatures. More than the addition of 5 wt .-% Ni brings no further advantage.
  • Si hinders carbon diffusion, reduces specific gravity and increases strength and elongation and toughness properties. Furthermore, an improvement in cold rollability by alloying Si could be observed.
  • Elongation properties which is why a maximum content of 2 wt .-% is set.
  • W acts as a carbide former and increases strength and heat resistance. Content W of more than 1 wt% deteriorate the elongation properties, therefore, a maximum content of 1 wt .-% is determined.
  • Zr acts as a carbide former and improves strength. Contents of Zr of more than 0.3% by weight deteriorate the elongation properties, therefore, a maximum content of 0.3% by weight is set.
  • Heat treatment parameters (see Table 1 to 4) a product of tensile strength and elongation at break of at least 20,000 MPa% and a tensile strength of at least 800 MPa.
  • the product of tensile strength and elongation at break is a measure of the material's performance during forming.
  • An alloy according to claim 4 comprises a product of tensile strength
  • An alloy according to claim 5 comprises finely divided kappa-carbide precipitates and a product of tensile strength and elongation at break of at least 30,000 MPa% and a yield strength of at least 700 MPa and a tensile strength of at least 800 MPa.
  • Table 1 lists the alloy compositions tested. With otherwise approximately the same chemical composition, the content of Sb and additions of Nb were varied.

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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)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un acier léger déformable de construction, présentant des propriétés mécaniques améliorées et une résistance élevée à la formation retardée de fissures induite par l'hydrogène et à la fragilisation due à l'hydrogène, comprenant les éléments suivants (en pourcentage en poids) : C 0,02 à ≤1,0 ; Mn 3 à 30 ; Si ≤4 ; P au maximum 0,1 ; S au maximum 0,1 ; N au maximum 0,03 ; Sb 0,003 à 0,8, en particulier de manière avantageuse jusqu'à 0,5, ainsi qu'au moins un ou plusieurs des éléments formant des carbures suivants dans les teneurs indiquées (en pourcentage en poids) : Al ≤15 ; Cr > 0,1 à 8 ; Mo 0,05 à 2 ; Ti 0,01 à 2 ; V 0,005 à 1 ; Nb 0,00 à 1 ; W 0,005 à 1 ; Zr 0,001 à 0,3 ; le reste étant du fer, y compris des éléments habituels d'accompagnement de l'acier, avec addition éventuelle des éléments suivants en pourcentage en poids : au maximum 5 de Ni, au maximum 10 de Co, au maximum 0,005 de Ca, au maximum 0,01 de B et 0,05 à 2 de Cu. L'invention concerne également un procédé de fabrication dudit acier léger de construction.
EP16750113.9A 2015-07-22 2016-07-20 Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier Active EP3325678B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102015111866.1A DE102015111866A1 (de) 2015-07-22 2015-07-22 Umformbarer Leichtbaustahl mit verbesserten mechanischen Eigenschaften und Verfahren zur Herstellung von Halbzeug aus diesem Stahl
PCT/EP2016/067347 WO2017013193A1 (fr) 2015-07-22 2016-07-20 Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier

Publications (2)

Publication Number Publication Date
EP3325678A1 true EP3325678A1 (fr) 2018-05-30
EP3325678B1 EP3325678B1 (fr) 2021-04-21

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Country Status (6)

Country Link
US (1) US20180216207A1 (fr)
EP (1) EP3325678B1 (fr)
KR (1) KR102096190B1 (fr)
DE (1) DE102015111866A1 (fr)
RU (1) RU2691436C1 (fr)
WO (1) WO2017013193A1 (fr)

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CN107841691B (zh) * 2017-10-25 2019-05-21 河北工业大学 一种750MPa级超高强度Fe-Mn-Al-C系轻质铸钢及其制备方法
DE102017223633A1 (de) 2017-12-21 2019-06-27 Voestalpine Stahl Gmbh Kaltgewalztes Stahlflachprodukt mit metallischer Korrosionsschutzschicht und Verfahren zur Herstellung eines solchen
RU2721681C1 (ru) * 2019-12-23 2020-05-22 Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") Способ производства холоднокатаного непрерывно отожженого листового проката из if-стали
CN111593263A (zh) * 2020-06-24 2020-08-28 安徽工业大学 一种高强度低密度钢的制备方法及高强度低密度钢
CN111607740A (zh) * 2020-06-24 2020-09-01 安徽工业大学 高强度低密度钢的制备方法及高强度低密度钢
CN114752867B (zh) * 2022-04-25 2022-10-11 燕山大学 一种高强韧轻质钢及其制备方法和应用

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KR100985286B1 (ko) * 2007-12-28 2010-10-04 주식회사 포스코 내지연파괴 특성이 우수한 고강도 고망간강 및 제조방법
KR101027250B1 (ko) 2008-05-20 2011-04-06 주식회사 포스코 고연성 및 내지연파괴 특성이 우수한 고강도 냉연강판,용융아연 도금강판 및 그 제조방법
KR100985298B1 (ko) * 2008-05-27 2010-10-04 주식회사 포스코 리징 저항성이 우수한 저비중 고강도 열연 강판, 냉연강판, 아연도금 강판 및 이들의 제조방법
KR101115739B1 (ko) * 2009-09-09 2012-03-06 주식회사 포스코 점용접성, 강도 및 연신율이 우수한 자동차용 강판 및 그 제조방법
EP2383353B1 (fr) * 2010-04-30 2019-11-06 ThyssenKrupp Steel Europe AG Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication
JP6009438B2 (ja) 2010-06-10 2016-10-19 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ オーステナイト鋼の製造方法
ES2455222T5 (es) * 2010-07-02 2018-03-05 Thyssenkrupp Steel Europe Ag Acero de resistencia superior, conformable en frío y producto plano de acero compuesto de un acero de este tipo
KR101382981B1 (ko) * 2011-11-07 2014-04-09 주식회사 포스코 온간프레스 성형용 강판, 온간프레스 성형 부재 및 이들의 제조방법

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WO2017013193A1 (fr) 2017-01-26
DE102015111866A1 (de) 2017-01-26
KR102096190B1 (ko) 2020-04-02
RU2691436C1 (ru) 2019-06-13
EP3325678B1 (fr) 2021-04-21
KR20180033202A (ko) 2018-04-02
US20180216207A1 (en) 2018-08-02

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