EP3243923B1 - Plattiertes stahlblech mit extrem hoher festigkeit mit zugfestigkeit von 1300 mpa oder mehr - Google Patents

Plattiertes stahlblech mit extrem hoher festigkeit mit zugfestigkeit von 1300 mpa oder mehr Download PDF

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Publication number
EP3243923B1
EP3243923B1 EP15877109.7A EP15877109A EP3243923B1 EP 3243923 B1 EP3243923 B1 EP 3243923B1 EP 15877109 A EP15877109 A EP 15877109A EP 3243923 B1 EP3243923 B1 EP 3243923B1
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EP
European Patent Office
Prior art keywords
steel sheet
less
plated steel
excluding
high strength
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EP15877109.7A
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English (en)
French (fr)
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EP3243923A4 (de
EP3243923A1 (de
Inventor
Kyoo-Young Lee
Joo-Hyun Ryu
Sim-Kun MIN
Se-Don CHOO
Dong-Seoug Sin
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Posco Holdings Inc
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Posco Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • 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
    • 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
    • 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
    • C22C38/18—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
    • C22C38/38—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
    • 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
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon

Definitions

  • the present disclosure relates to a plated steel sheet having ultra-high strength and used in vehicles and the like, and more particularly, to a plated steel sheet having ultra-high strength and a tensile strength of 1300 MPa or more, and a method of manufacturing the same.
  • KR 2013 0056052 A describes a galvannealed steel sheet with high strength and a corresponding production method.
  • US 2014/234657 A12 discloses a high strength hot dip galvanized steel sheet and its production process. Further examples for high strength galvanized steel sheets can be found, for example, in US 2014/377584 A1 , JP 2012 229466 A and US 2011/198002 A1 .
  • martensite steel having a tensile strength of 1300 MPa or more has been developed and used as an ultra-high strength plated steel sheet, and plating products having enhanced corrosion resistance have also been being developed.
  • steel sheet coils commonly produced in steel mills are slit and coiled to be formed as coils having a relatively narrow width, and then, are formed as components by applying a roll forming method or a simple forming method thereto.
  • An aspect of the present disclosure is to provide a plated steel sheet having ultra-high strength, in which the occurrence and propagation of cracking in edges thereof in a width direction may be prevented, even when a slitting and coiling process is performed on a plated steel sheet having ultra-high strength, and a method of manufacturing the same.
  • a plated steel sheet having ultra-high strength in which the occurrence of cracking in an edge portion in a width direction, after a slitting and coiling process, may be prevented, may be provided.
  • FIG. 1 illustrates a result of observing whether or not cracking occurs after slitting heat-treated and untreated plated sheets having ultra-high strength.
  • the present inventors have found that cracking in a width direction edge portion after slitting and coiling a plated steel sheet having ultra-high strength is related to an amount of hydrogen, and thus, a plated steel sheet having ultra-high strength and a reduced amount of hydrogen, and a method for effectively reducing an amount of hydrogen, may be provided.
  • a plated steel sheet having ultra-high strength, and having an amount of hydrogen of 0.000015 wt% or less and a tensile strength of 1300 MPa or more, may be provided.
  • the plated steel sheet having ultra-high strength may include 0.12 wt% to 0.2 wt% of carbon (C), 0.5 wt% or less of silicon (Si) (excluding 0wt%), 2.6 wt% to 4.0 wt% of manganese (Mn), 0.03 wt% or less of phosphorus (P) (excluding 0 wt%), 0.015 wt% or less of sulfur (S) (excluding 0 wt%), 0.1 wt% or less of aluminum (Al) (excluding 0 w%), 1 wt% or less of chromium (Cr) (excluding 0 wt%), 48/14*[N] to 0.1 wt% of titanium (Ti), 0.1 wt% or less of niobium (Nb) (excluding 0 wt%), 0.005 wt% or less of boron (B) (excluding 0 wt%), 0.01 wt% or less of nitrogen
  • Carbon (C) is an element essentially added to secure strength of a steel. In order to obtain the above-mentioned effect, carbon (C) may be added in an amount of 0.12% or more. However, if the content thereof is relatively high, exceeding 0.20%, a problem in which weldability is deteriorated may occur, which may be problematic.
  • the content of C may be limited to 0.12% to 0.20%.
  • Silicon (Si) is a ferrite stabilizing element and may have a disadvantage in that strength may be reduced by accelerating generation of ferrite at the time of slow cooling after annealing in a continuous annealing type hop-dip heat treatment furnace of the related art in which a slow cooling section is present.
  • an upper limit of Si may be determined. In detail, the content of Si may be limited to 0.5% or less.
  • Manganese (Mn) is well known as an element inhibiting the formation of ferrite and facilitating the formation of austenite.
  • Mn Manganese
  • a content of Mn is less than 2.6%, ferrite may be easily formed during slow cooling, while if the content of Mn exceeds 4.0%, band formation due to slabs, and segregation caused in a hot rolling process, may be excessive, and a problem in which a cost of alloy iron is increased due to an excessive amount of alloying input when a convertor is operated.
  • the content of Mn may be limited to 2.6% to 4.0%.
  • Phosphorus (P) may be an impurity element in steel. If the content thereof exceeds 0.03%, weldability may be decreased, a risk of brittleness of steel may be increased, and a possibility of the occurrence of dent defects may increase. Thus, the content of P may be limited to 0.03% or less.
  • S may be an impurity element in steel as well as P, and if the content thereof exceeds 0.015%, a possibility of deterioration of ductility and weldability of steel may increase. Thus, the content of S may be limited to 0.015% or less.
  • Aluminum (Al) is an element for expanding a ferrite region.
  • a general continuous annealing type hop-dip heat treatment furnace having a slow cooling section there may be a disadvantage in that ferrite formation is promoted, and the possibility of causing deteriorations in high temperature heat hot-rolling characteristics due to the formation of AlN may increase.
  • the content of Al may be limited to 0.1% or less.
  • Chromium (Cr) is an element suppressing ferrite transformation and facilitating low-temperature transformation.
  • a general continuous annealing type hop-dip heat treatment furnace having a slow cooling section there may be an advantage in that ferrite formation is suppressed.
  • the content thereof exceeds 1%, a problem in which a cost of alloying iron is increased due to an excessive amount of alloying may occur.
  • the content thereof may be limited to 1% or less.
  • Titanium (Ti) is an element for forming a nitride, and may serve to precipitate N in steel as TiN to scavenge N therein. To this end, Ti may be required to be added at a chemical equivalent of 48/14 *[N] or more. On the other hand, if Ti is not added, a problem in which cracks may occur during continuous casting by AlN formation may be caused. However, if the content thereof exceeds 0.1%, a problem in which the strength of martensite is reduced due to precipitation of additional carbides in addition to the removal of solid solution N, may be caused.
  • Niobium is an element segregated at an austenite grain boundary to suppress coarsening of austenite grains during an annealing heat treatment, and thus, may be added. However, if the content thereof exceeds 0.1%, a problem in which a cost of alloy iron is increased due to an excessive amount of added alloy may occur. Thus, the content of Nb may be limited 0.1% or less.
  • B Boron (B) is an element inhibiting ferrite formation.
  • B has an advantage of inhibiting the formation of ferrite at the time of cooling after annealing, and thus, may be added.
  • the content thereof exceeds 0.005%, since a problem in which ferrite formation is promoted by precipitation of Fe 23 (C,B) 6 may occur, the content thereof may be limited to 0.005% or less.
  • Nitrogen (N) is an element reacting with Al to be precipitated into AlN nitride, and the formed AlN may have a problem in that it is a cause of occurrence of cracking during continuous casting.
  • the content of Al may be limited to 0.01% or less, and thus, the formation of AlN may be suppressed.
  • Fe and unavoidable impurities may be included as a remainder.
  • the impurities may include molybdenum (Mo), vanadium (V), nickel (Ni), rare earth metals (REM), and the like.
  • a steel sheet used to obtain a plated steel sheet having ultra-high strength may have a microstructure comprised of 90% or more of martensite and 10% or less of ferrite and bainite in a volume fraction, while satisfying the above-mentioned compositional composition.
  • a microstructure comprised of 90% or more of martensite and 10% or less of ferrite and bainite in a volume fraction, while satisfying the above-mentioned compositional composition.
  • As effective characteristics according to the configuration of the microstructure as martensite of a hard phase has a microstructure, a main phase, securing ultra-high strength may be facilitated.
  • the plated steel sheet having ultra-high strength, ultimately obtained by heat-treating the steel sheet as described above, according to an exemplary embodiment may also have the same microstructure as above, and when an additional tempering heat treatment thereto is performed, martensite may be converted into tempered martensite.
  • volume fraction may not be easy to actually measure a volume fraction, a three-dimensional concept, and thus, measurement of the volume fraction may be replaced with area fraction measurement through a cross-sectional observation normally used in observation of a microstructure.
  • the steel sheet having the component system and the microstructure as described above may be plated and heat-treated, and an amount of hydrogen after heat treatment may be 0.000015 wt% or less, as compared with the case before the heat treatment.
  • the target ratio of a yield strength and a tensile strength of the plated steel sheet having ultra-high strength according to an exemplary embodiment may be 0.75 or more.
  • a steel sheet including 0.12 wt% to 0.2 wt% of carbon (C), 0.5 wt% or less of silicon (Si) (excluding 0wt%), 2.6 wt% to 4.0 wt% of manganese (Mn), 0.03 wt% or less of phosphorus (P) (excluding 0 wt%), 0.015 wt% or less of sulfur (S) (excluding 0 wt%), 0.1 wt% or less of aluminum (Al) (excluding 0 wt%), 1 wt% or less of chromium (Cr) (excluding 0 wt%), 48/14*[N] to 0.1 wt% of titanium (Ti), 0.1 wt% or less of niobium (Nb) (excluding 0 wt%), 0.005 wt% or less of boron (B) (excluding 0 wt%), 0.01 wt% or less of nitrogen (N) (excluding 0 wt%
  • the steel sheet may be plated to produce a plated steel sheet, and the plated steel sheet may be subjected to a heat treatment.
  • a plating process is not particularly limited, and for example, a process such as hot-dip galvanizing, hot-dip aluminum plating, electro-galvanizing, or the like may be performed.
  • a heat treatment after plating may be performed such that an amount of hydrogen in the plated steel sheet may be 0.000015 wt% or less.
  • an amount of hydrogen in the plated steel sheet may be 0.000015 wt% or less.
  • the heat treatment temperature and time may be set in consideration of a tensile strength level required by a customer.
  • a plated steel sheet having ultra-high strength is generally manufactured as a coil having a constant width through a slitting and coiling process, and the slitting process is a process of adding relatively high stress to an edge portion of a steel sheet.
  • the slitting process is a process of adding relatively high stress to an edge portion of a steel sheet.
  • a disadvantage in that the quality of a cut surface of an edge portion may be deteriorated due to a plating layer may be present. Hydrogen in steel tends to segregate under a relatively high stress state.
  • hydrogen in steel may segregate on a relatively highly stressed portion of an edge portion of the plated steel sheet after the slitting, whereby cracks may start to occur in the edge portion of the plated steel sheet having ultra-high strength and the propagation of cracks may occur in a width direction.
  • an amount of hydrogen of the plated steel sheet having ultra-high strength may be reduced to 0.000015 wt% or less, and thus, cracking of an edge portion over time during coiling, after slitting, may be effectively suppressed.
  • a plated steel sheet having ultra-high strength, an initial yield strength of 1149 MPa, and an initial tensile strength of 1556 MPa was evaluated for changes in an amount of hydrogen before a heat treatment and after a heat treatment under conditions provided in Table 1 below. Evaluation results are provided as illustrated in Table 1.
  • a steel material having a component system consisting of 0.18% of C, 0.1% of Si, 3.6% of Mn, 0.011% of P, 0.11% of Cr, 0.021% of Ti, 0.038% of Nb, 0.0017% of B, 0.003% of S, 0.025% of Al, and 0.004% of N was prepared as a specimen having a size of thickness*12mm*100mm, and was heated to a temperature from 25°C to 250°C at a heating rate of 100°C per hour. An amount of hydrogen was measured using gas chromatography, simultaneously with performing a heat treatment.
  • the cold rolled steel sheet had no hydrogen, 0 wt% of hydrogen, while the plated steel sheet had a relatively high content, 0.000022 wt% of hydrogen.
  • the amount of hydrogen may be further reduced.
  • a plated steel sheet (A) not subjected to heat treatment a plated steel sheet (B) having been subjected to heat treatment at 150°C for 24 hours in a 100% of hydrogen atmosphere, and a plated steel sheet (C) having been subjected to heat treatment at 200°C for 24 hours in a 7% of hydrogen atmosphere were slit, whether or not cracks occurred as time passed was observed, and the results thereof are provided in FIG. 1 .
  • a plated steel sheet having ultra-high strength and having a yield strength ratio of 0.75 or more with respect to a tensile strength by tempering heat treatment of an ultra-high strength plated steel sheet having martensite as a main phase, may be provided.
  • a decrease in tensile strength may increase.
  • setting heat treatment temperature and time according to a tensile strength level required by a customer may be required.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Coating With Molten Metal (AREA)

Claims (1)

  1. Plattiertes Stahlblech, das eine ultrahohe Festigkeit mit einer Zugfestigkeit von 1300 MPa oder mehr und ein Streckgrenzenverhältnis von 0,75 oder mehr hat,
    das dadurch gekennzeichnet ist, dass eine Menge an Wasserstoff in dem plattierten Stahlblech 0,000015 Gew.-% oder weniger beträgt, wobei das plattierte Stahlblech 0,12 Gew.-% bis 0,2 Gew.-% Kohlenstoff (C), 0,5 Gew.-% oder weniger Silicium (Si) (ausgenommen 0 Gew.-%), 2,6 Gew.-% bis 4,0 Gew.-% Mangan (Mn), 0,03 Gew.-% oder weniger Phosphor (P) (ausgenommen 0 Gew.-%), 0,015 Gew.-% oder weniger Schwefel (S) (ausgenommen 0 Gew.-%), 0,1 Gew.% oder weniger Aluminium (Al) (ausgenommen 0 Gew.-%), 1 Gew.-% oder weniger Chrom (Cr) (ausgenommen 0 Gew.-%), 48/14∗ [N] bis 0,1 Gew.-% Titan (Ti), 0,1 Gew.-% oder weniger Niob (Nb) (ausgenommen 0 Gew.-%), 0,005 Gew.-% oder weniger Bor (B) (ausgenommen 0 Gew.-%), 0,01 Gew.-% oder weniger Stickstoff (N) (ausgenommen 0 Gew.-%), Eisen (Fe) als Rest davon sowie weitere unvermeidbar enthaltene Verunreinigungen umfasst; und eine Mikrostruktur hat, die durch Plattieren und Wärmebehandeln eines Stahlblechs erhalten wird, das aus 90 % oder mehr getempertem Martensit und 10 % oder weniger Ferrit und Bainit in einem Volumenanteil besteht.
EP15877109.7A 2015-01-07 2015-01-07 Plattiertes stahlblech mit extrem hoher festigkeit mit zugfestigkeit von 1300 mpa oder mehr Active EP3243923B1 (de)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/KR2015/000136 WO2016111388A1 (ko) 2015-01-07 2015-01-07 인장강도 1300ＭＰａ 이상의 초고강도 도금강판 및 이의 제조방법

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EP3243923A4 EP3243923A4 (de) 2017-11-15
EP3243923A1 EP3243923A1 (de) 2017-11-15
EP3243923B1 true EP3243923B1 (de) 2019-10-23

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Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2016060248A1 (ja) * 2014-10-17 2016-04-21 新日鐵住金株式会社 絞り缶用鋼板及びその製造方法
EP3719157B1 (de) * 2017-11-29 2024-05-01 JFE Steel Corporation Hochfestes galvanisiertes stahlblech und verfahren zur herstellung davon
JP6544494B1 (ja) * 2017-11-29 2019-07-17 Ｊｆｅスチール株式会社 高強度亜鉛めっき鋼板およびその製造方法
US20200347479A1 (en) * 2018-01-17 2020-11-05 Jfe Steel Corporation High-strength electrogalvannealed steel sheet and method for manufacturing the same
CN111936650B (zh) 2018-03-30 2022-04-08 杰富意钢铁株式会社 高强度镀锌钢板、高强度部件和它们的制造方法
KR102400445B1 (ko) * 2018-03-30 2022-05-20 제이에프이 스틸 가부시키가이샤 고강도 아연 도금 강판, 고강도 부재 및 그들의 제조 방법

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
JP5402007B2 (ja) * 2008-02-08 2014-01-29 Ｊｆｅスチール株式会社 加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
JP5136609B2 (ja) * 2010-07-29 2013-02-06 Ｊｆｅスチール株式会社 成形性および耐衝撃性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
KR101220619B1 (ko) * 2010-11-09 2013-01-10 주식회사 포스코 초고강도 냉연강판, 용융아연도금강판 및 이들의 제조방법
JP5821260B2 (ja) * 2011-04-26 2015-11-24 Ｊｆｅスチール株式会社 成形性及び形状凍結性に優れた高強度溶融亜鉛めっき鋼板、並びにその製造方法
BR112014007530B1 (pt) * 2011-09-30 2018-12-11 Nippon Steel & Sumitomo Metal Corporation chapa de aço galvanizada por imersão a quente de alta resistência e processo para produção da mesma
WO2013047812A1 (ja) * 2011-09-30 2013-04-04 新日鐵住金株式会社 高強度溶融亜鉛めっき鋼板
KR20140068122A (ko) * 2011-09-30 2014-06-05 신닛테츠스미킨 카부시키카이샤 용융 아연 도금 강판 및 그 제조 방법
WO2013047836A1 (ja) * 2011-09-30 2013-04-04 新日鐵住金株式会社 亜鉛めっき鋼板及びその製造方法
KR20130056051A (ko) * 2011-11-21 2013-05-29 주식회사 포스코 슬라브 코너크랙이 없는 초고강도 강판 및 그 제조방법
KR20130056052A (ko) * 2011-11-21 2013-05-29 주식회사 포스코 합금화 특성이 우수한 초고강도 합금화 용융아연도금강판 및 그 제조방법
JP5811020B2 (ja) * 2012-04-25 2015-11-11 新日鐵住金株式会社 高い靱性と高い加工性および成形性とを有し水素脆化起因による遅れ破壊特性に優れた高強度鋼板

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
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EP3243923A4 (de) 2017-11-15
WO2016111388A8 (ko) 2016-12-15
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CN107148488A (zh) 2017-09-08
CN107148488B (zh) 2020-02-07
WO2016111388A1 (ko) 2016-07-14

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