EP1918404B1 - Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Aluminium legierten Mehrphasenstahl - Google Patents

Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Aluminium legierten Mehrphasenstahl Download PDF

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Publication number
EP1918404B1
EP1918404B1 EP06123140A EP06123140A EP1918404B1 EP 1918404 B1 EP1918404 B1 EP 1918404B1 EP 06123140 A EP06123140 A EP 06123140A EP 06123140 A EP06123140 A EP 06123140A EP 1918404 B1 EP1918404 B1 EP 1918404B1
Authority
EP
European Patent Office
Prior art keywords
hot
strip
rolled strip
rolled
cold
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.)
Not-in-force
Application number
EP06123140A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP1918404A1 (de
Inventor
Brigitte Dr.-Ing. Hammer
Thomas Dr.-Ing. Heller
Johann Wilhelm Dr. Schmitz
Jochen Dr. Wans
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Steel AG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority to DE502006003832T priority Critical patent/DE502006003832D1/de
Application filed by ThyssenKrupp Steel AG filed Critical ThyssenKrupp Steel AG
Priority to PL06123140T priority patent/PL1918404T3/pl
Priority to EP06123140A priority patent/EP1918404B1/de
Priority to AT06123140T priority patent/ATE432374T1/de
Priority to ES06123140T priority patent/ES2325963T3/es
Priority to PCT/EP2007/061391 priority patent/WO2008052920A1/de
Priority to US12/447,627 priority patent/US20100065162A1/en
Priority to KR1020097007486A priority patent/KR101461584B1/ko
Priority to JP2009533823A priority patent/JP5350254B2/ja
Priority to CN2007800393899A priority patent/CN101528966B/zh
Publication of EP1918404A1 publication Critical patent/EP1918404A1/de
Application granted granted Critical
Publication of EP1918404B1 publication Critical patent/EP1918404B1/de
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • C21D8/041—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 involving a particular fabrication or treatment of ingot or slab
    • C21D8/0415—Rapid solidification; Thin strip casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • 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
    • C21D8/0426—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
    • C21D8/04—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
    • 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
    • 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
    • C21D2211/002—Bainite
    • 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

Definitions

  • the invention relates to a method for producing steel flat products, such as strips or sheet metal blanks, from high-strength, alloyed with aluminum steels.
  • steels belong to the group of multiphase steels. These are usually steels whose properties are determined by the type, amount and arrangement of the phases of the structure.
  • the structure therefore has at least two phases (eg ferrite, martensite, bainite). This gives them a strength / formability combination that is superior to conventional steels.
  • This preparation route presents problems in particular when casting peritectically solidifying compositions.
  • These steel grades there is the danger of the formation of longitudinal cracks during continuous casting.
  • the formation of such longitudinal cracks can reduce the quality of the hot strips produced from the cast slabs or thin slabs so much that they become unusable.
  • extensive measures such as increased insulation costs, are required, which can go so far that the processing of such steel grades becomes uneconomical.
  • multiphase steels are of particular interest for the automotive industry because of their high strength, they permit the use of lower material thicknesses and concomitantly a reduction in vehicle weight and, secondly, the safety of the vehicle body in the event of a collision (crash behavior) .
  • multiphase steels with at least constant strength of the overall body allow a reduction in the sheet thickness of a component produced from such multiphase steels compared to a body produced from conventional steels.
  • multiphase steels are melted in the converter steelworks and cast on a continuous casting plant into slabs or thin slabs, which are then hot rolled into hot strip and coiled.
  • the mechanical properties of the hot strip can be varied.
  • the hot strips can be cold rolled to cold strip to provide thinner sheet thicknesses ( EP 0 910 675 B1 . EP 0 966 547 B1 . EP 1 169 486 B1 . EP 1 319 725 B1 . EP 1 398 390 A1 ).
  • a problem in the production of flat products made of high-strength multiphase steels with tensile strengths of more than 800 MPa is that high rolling forces must be applied when rolling such steels. This requirement has the consequence that high-strength hot strips made of steels of the type in question can usually only be made available in width and thickness with the currently customarily available production facilities, which do not meet the demands made today in the field of automobile construction more fully. Above all, tapes of small thicknesses with sufficient widths can be poorly represented on conventional systems. It also turns out in conventional practice in practice difficult to produce multiphase steels cold strips with strengths of more than 800 MPa.
  • the cast strip is then hot rolled in-line in one or more passes of between 25% and 70% strain to a hot strip.
  • the final temperature of hot rolling is above the Ar 3 temperature.
  • the hot strip obtained is then cooled in two stages. In the first stage of this cooling, a cooling rate of 5 - 100 ° C / s is maintained until a temperature between 400 - 550 ° C is reached. At this temperature, the hot-rolled strip is left to rest for a period of time required to allow bainitic transformation of the steel with a residual austenite content greater than 5%. The formation of perlite should be avoided.
  • the conversion process is started by the beginning of the second stage of the Cooling stopped, in which the hot strip is brought to a temperature below 400 ° C, to then wrap it at a reel temperature lying below 350 ° C to form a coil.
  • the object of the invention was therefore to provide a method by means of which high-strength steel flat products can be produced over a wide range of geometric dimensions with reduced manufacturing outlay.
  • this object has been achieved by a method according to claim 1 for the production of steel flat products, in which a multiphase structure forming steel, the (in wt .-%) 0.10 - 0.14% C, 1.30-1.70% Mn, up to 0.030% P, up to 0.004% S, 0.10-0.30% Si, 0.90-1.2% Al, up to 0.0070% N, 0.070-0.130% Ti, 0.040-0.060% Nb, 0.140-0.260% Mo and the remainder contains iron and unavoidable impurities, is cast to a cast strip with a thickness of 1-4 mm, in which the cast strip in a continuous working process with a degree of deformation of more than 20% in-line at a hot rolling end temperature in the range of 850-1000 ° C to a hot strip with a thickness of 0, 5 - 3.2 mm is hot rolled and the the hot strip is coiled at a coiler temperature of 350-480 ° C, so that a hot strip is
  • the invention makes use of the possibility of strip casting to process a particularly high-strength, peritectically solidifying multiphase steel into a hot strip. Since the cast strip itself already has a small thickness, in the course of hot rolling of this strip only relatively small degrees of deformation must be maintained in order to produce flat products with small thicknesses, as are required in particular in the automotive industry. Thus, by specifying a corresponding initial thickness of the cast strip, it is easily possible to produce hot strips with the method according to the invention, which have a maximum property distribution of at most 1.5 mm and from which, for example, elements for the support structure of an automobile can be produced.
  • the invention makes it possible to manufacture high-strength hot strips consisting of a multiphase steel of the specified composition processed according to the invention, whose width is more than 1,200 mm, in particular more than 1,600 mm.
  • the use according to the invention of the strip casting method in the processing of high-strength steels of the type assembled according to the invention offers the possibility, in addition to the above-mentioned advantages due to its process-specific properties and manipulated variables (eg hot rolling end temperature, cooling, coiling temperature), of also critical steel compositions according to the invention with regard to their solidification behavior to safely shed processed species.
  • process-specific properties and manipulated variables eg hot rolling end temperature, cooling, coiling temperature
  • critical steel compositions according to the invention with regard to their solidification behavior to safely shed processed species.
  • the very rapid solidification of the cast strip which is characteristic of strip casting, leads to a significantly reduced risk of the formation of center segregations compared with conventional production, with the result that the hot strip produced according to the invention has a particularly uniform distribution of properties and microstructure over its cross section and its length.
  • the hot strip produced according to the invention has high strengths of at least 800 MPa, without having to observe a special cooling cycle of the hot strip between the end of the hot rolling and the reeling, as described in US Pat EP 1 072 689 B1 is prescribed by the need for a cooling break.
  • it merely has to be ensured that the hot rolling ends in a relatively narrow temperature window and that the reeling is also carried out in a precisely defined temperature range. In between there is a one-stage cooling down.
  • Another advantage of the procedure according to the invention is that an extension of the range of mechanical properties of the strip produced according to the invention based on only one steel analysis by a Variation of the cooling and rolling conditions can be achieved.
  • Hot strips produced according to the invention are particularly suitable for further processing into cold rolled strip. Accordingly, a practice-oriented embodiment of the invention provides that the hot strip is cold rolled to a cold strip having a thickness of 0.5-1.4 mm, in particular 0.7 mm to 1.3 mm, as is required for the construction of automobile bodies.
  • the cold strip can be annealed at an annealing temperature of 750-850 ° C.
  • tensile strengths of at least 800 MPa can be reliably ensured.
  • the breaking elongation A 50 of the cold strip is just as safe at least 10%.
  • the flat product produced according to the invention is characterized by a particularly good coatability.
  • the cold strip is provided in a conventional manner with a metallic coating, which may be, for example, a galvanizing.
  • the strength and elongation values according to the invention produced hot strips can be adjusted over a wide range by an appropriate vote of the Hotwalzend- and reel temperatures. If, for example, hot strips are to be produced which have a tensile strength R m of at least 800 MPa at an elongation at break A 80 of the resulting hot strip of at least 10%, this can be achieved by setting the hot rolling end temperature to 900-1000 ° C. and Coiler temperature 400 - 480 ° C amount.
  • the hot rolling end temperature in the range of 850-1100 ° C and the coiler temperature in the range of 350-400 ° C selected.
  • the tapes cast from steels A and B were hot rolled into a hot strip whose thickness was 1.25 mm in four different trials immediately after in-line strip casting at a hot rolling end temperature WET. Subsequently, each hot strip obtained has been cooled directly in a cooling step to a coiler temperature HT and coiled. After coiling, the hot strips produced from steels A and B each had a tensile strength R m and an elongation at break A 80 , which, like the hot rolling end temperature WET and reel temperature HT, respectively, maintained in their preparation, are given in Table 2.
  • Table 2 attempt stolen WET [° C] HT [° C] R m [MPa] A 80 [%] 1 A 950 450 901 12.4 2 B 900 400 811 13.1 3 A 920 400 1184 5.6 4 B 900 390 1159 5.2
  • the hot strip produced from the steel A was cold rolled after the coiling to a 0.74 mm thick cold strip and annealed at an annealing temperature of 800 ° C in the flow to recrystallize the strip.
  • the tensile strength R m of the cold strip thus obtained was 985 MPa.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Rolling (AREA)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
EP06123140A 2006-10-30 2006-10-30 Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Aluminium legierten Mehrphasenstahl Not-in-force EP1918404B1 (de)

Priority Applications (10)

Application Number Priority Date Filing Date Title
PL06123140T PL1918404T3 (pl) 2006-10-30 2006-10-30 Sposób wytwarzania płaskich produktów stalowych z wielofazowej stali stopowej z aluminium
EP06123140A EP1918404B1 (de) 2006-10-30 2006-10-30 Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Aluminium legierten Mehrphasenstahl
AT06123140T ATE432374T1 (de) 2006-10-30 2006-10-30 Verfahren zum herstellen von stahl-flachprodukten aus einem mit aluminium legierten mehrphasenstahl
ES06123140T ES2325963T3 (es) 2006-10-30 2006-10-30 Procedimiento para fabricar productos planos de acero a partir de un acero multifasico aleado con aluminio.
DE502006003832T DE502006003832D1 (de) 2006-10-30 2006-10-30 Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Aluminium legierten Mehrphasenstahl
US12/447,627 US20100065162A1 (en) 2006-10-30 2007-10-24 Method for Manufacturing Flat Steel Products From Aluminum Alloyed Multi-Phase Steel
PCT/EP2007/061391 WO2008052920A1 (de) 2006-10-30 2007-10-24 Verfahren zum herstellen von stahl-flachprodukten aus einem mit aluminium legierten mehrphasenstahl
KR1020097007486A KR101461584B1 (ko) 2006-10-30 2007-10-24 알루미늄으로 합금화된 다상 강으로부터 평판형 강 제품을 제조하는 방법
JP2009533823A JP5350254B2 (ja) 2006-10-30 2007-10-24 アルミニウム合金化多相鋼からフラット鋼生成物を製造する方法
CN2007800393899A CN101528966B (zh) 2006-10-30 2007-10-24 由铝合金化多相钢制备扁钢产品的方法

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP06123140A EP1918404B1 (de) 2006-10-30 2006-10-30 Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Aluminium legierten Mehrphasenstahl

Publications (2)

Publication Number Publication Date
EP1918404A1 EP1918404A1 (de) 2008-05-07
EP1918404B1 true EP1918404B1 (de) 2009-05-27

Family

ID=37733702

Family Applications (1)

Application Number Title Priority Date Filing Date
EP06123140A Not-in-force EP1918404B1 (de) 2006-10-30 2006-10-30 Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Aluminium legierten Mehrphasenstahl

Country Status (10)

Country Link
US (1) US20100065162A1 (enExample)
EP (1) EP1918404B1 (enExample)
JP (1) JP5350254B2 (enExample)
KR (1) KR101461584B1 (enExample)
CN (1) CN101528966B (enExample)
AT (1) ATE432374T1 (enExample)
DE (1) DE502006003832D1 (enExample)
ES (1) ES2325963T3 (enExample)
PL (1) PL1918404T3 (enExample)
WO (1) WO2008052920A1 (enExample)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10071416B2 (en) * 2005-10-20 2018-09-11 Nucor Corporation High strength thin cast strip product and method for making the same
MX2010003835A (es) * 2007-10-10 2010-05-13 Nucor Corp Acero estructurado metalografico complejo y metodo para manufacturarlo.
WO2011100798A1 (en) 2010-02-20 2011-08-25 Bluescope Steel Limited Nitriding of niobium steel and product made thereby
KR102596515B1 (ko) 2014-12-19 2023-11-01 누코 코포레이션 열연 경량 마르텐사이트계 강판 및 이의 제조방법

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5470529A (en) * 1994-03-08 1995-11-28 Sumitomo Metal Industries, Ltd. High tensile strength steel sheet having improved formability
WO1998002589A1 (de) * 1996-07-12 1998-01-22 Thyssen Stahl Ag Warmband aus stahl und verfahren zu seiner herstellung
JP3498504B2 (ja) * 1996-10-23 2004-02-16 住友金属工業株式会社 高延性型高張力冷延鋼板と亜鉛メッキ鋼板
FR2796966B1 (fr) * 1999-07-30 2001-09-21 Ugine Sa Procede de fabrication de bandes minces en acier de type "trip" et bandes minces ainsi obtenues
FR2798871B1 (fr) * 1999-09-24 2001-11-02 Usinor Procede de fabrication de bandes d'acier au carbone, notamment d'acier pour emballages, et bandes ainsi produites
AUPQ779900A0 (en) * 2000-05-26 2000-06-22 Bhp Steel (Jla) Pty Limited Hot rolling thin strip
WO2002026424A1 (en) * 2000-09-29 2002-04-04 Ishikawajima-Harima Heavy Industries Company Limited Production of thin steel strip
WO2002033141A1 (en) * 2000-10-19 2002-04-25 Nkk Corporation Zinc-plated steel sheet and method for preparation thereof, and method for manufacturing formed article by press working
DE10128544C2 (de) * 2001-06-13 2003-06-05 Thyssenkrupp Stahl Ag Höherfestes, kaltumformbares Stahlblech, Verfahren zu seiner Herstellung und Verwendung eines solchen Blechs
US6878920B2 (en) * 2002-06-28 2005-04-12 Intel Corporation Optical receiver circuit, method, and system
EP1396550A1 (de) * 2002-08-28 2004-03-10 ThyssenKrupp Stahl AG Verfahren zum Herstellen eines Warmbandes
JP4510488B2 (ja) * 2004-03-11 2010-07-21 新日本製鐵株式会社 成形性および穴拡げ性に優れた溶融亜鉛めっき複合高強度鋼板およびその製造方法
AU2005227564B2 (en) 2004-03-31 2008-02-21 Jfe Steel Corporation High-rigidity high-strength thin steel sheet and method for producing same

Also Published As

Publication number Publication date
KR101461584B1 (ko) 2014-11-13
CN101528966B (zh) 2011-06-15
JP2010508436A (ja) 2010-03-18
ES2325963T3 (es) 2009-09-25
KR20090090302A (ko) 2009-08-25
PL1918404T3 (pl) 2009-10-30
CN101528966A (zh) 2009-09-09
EP1918404A1 (de) 2008-05-07
DE502006003832D1 (de) 2009-07-09
JP5350254B2 (ja) 2013-11-27
ATE432374T1 (de) 2009-06-15
US20100065162A1 (en) 2010-03-18
WO2008052920A1 (de) 2008-05-08

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