EP2439290B1 - Mehrphasenstahl, aus einem solchen Mehrphasenstahl hergestelltes kaltgewalztes Flachprodukt und Verfahren zu dessen Herstellung - Google Patents

Mehrphasenstahl, aus einem solchen Mehrphasenstahl hergestelltes kaltgewalztes Flachprodukt und Verfahren zu dessen Herstellung Download PDF

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Publication number
EP2439290B1
EP2439290B1 EP10186553.3A EP10186553A EP2439290B1 EP 2439290 B1 EP2439290 B1 EP 2439290B1 EP 10186553 A EP10186553 A EP 10186553A EP 2439290 B1 EP2439290 B1 EP 2439290B1
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EP
European Patent Office
Prior art keywords
phase steel
cold
annealing
content
steel
Prior art date
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Active
Application number
EP10186553.3A
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German (de)
English (en)
French (fr)
Other versions
EP2439290A1 (de
Inventor
Dr. Ekaterina Bocharova
Dr. Dorothea Mattissen
Dr. Roland Sebald
Dr. Daniel Krizan
Dr. Andreas Pichler
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Voestalpine Stahl GmbH
ThyssenKrupp Steel Europe AG
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Voestalpine Stahl GmbH
ThyssenKrupp Steel Europe AG
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Filing date
Publication date
Application filed by Voestalpine Stahl GmbH, ThyssenKrupp Steel Europe AG filed Critical Voestalpine Stahl GmbH
Priority to EP10186553.3A priority Critical patent/EP2439290B1/de
Priority to CN201180048744.5A priority patent/CN103210097B/zh
Priority to KR1020137011457A priority patent/KR101848876B1/ko
Priority to US13/877,782 priority patent/US9970088B2/en
Priority to JP2013532112A priority patent/JP6001541B2/ja
Priority to PCT/EP2011/066522 priority patent/WO2012045595A1/de
Publication of EP2439290A1 publication Critical patent/EP2439290A1/de
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Publication of EP2439290B1 publication Critical patent/EP2439290B1/de
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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
    • C22C38/14—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
    • C21D6/00—Heat treatment 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
    • 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
    • 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
    • C21D8/0247—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
    • C22C38/001—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
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/005—Ferrite
    • 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 multiphase steel, a Kaltwalzflach etc. produced by such a multi-phase steel by cold rolling and a process for its preparation.
  • the "flat products” according to the invention may be sheets, strips, blanks obtained therefrom or comparable products. If this is referred to as "cold flat products", it means flat products produced by cold rolling.
  • a multiphase steel which should have a balanced property profile in this respect, is from the EP 1 367 143 A1 known. In addition to a comparable high strength and good ductility of the known steel should also have a particularly good weldability.
  • the known steel contains to 0.03 - 0.25 wt .-% C, by its presence in combination with the other alloying elements tensile strengths of at least 700 MPa to be achieved.
  • the strength of the known steel is to be supported by Mn in contents of 1.4-3.5% by weight.
  • Al is used in the melting of the known steel as the oxidizing agent and may be present in the steel in amounts of up to 0.1% by weight.
  • the known steel may also have up to 0.7% by weight of Si, the presence of which stabilizes the ferritic-martensitic structure of the steel.
  • Cr is added to the known steel in amounts of 0.05-1% by weight in order to reduce the influence of the heat introduced by the welding process in the region of the weld.
  • Nb should additionally have a positive influence on the deformability of the steel, since its presence brings about a thinning of the ferrite grain.
  • 0.05 to 1% by weight of Mo, 0.02 to 0.5% by weight of V, 0.005 to 0.05% by weight of Ti and 0.0002 to 0.002% by weight of the known steel can be used.
  • % B are added. Mo and V contribute to the hardenability of the known steel, while Ti and B should additionally have a positive effect on the strength of the steel.
  • Another, also made of a high strength multiphase steel, well malleable steel sheet is from the EP 1 589 126 B1 known.
  • This known steel sheet contains 0.10-0.28 wt% C, 1.0-2.0 wt% Si, 1.0-3.0 wt% Mn, 0.03-0.10 Wt% Nb, up to 0.5 wt% Al, up to 0.15 wt% P, up to 0.02 wt% S.
  • the steel sheet up to 1.0 wt% Mo, up to 0.5 wt% Ni, up to 0.5 wt% Cu, to 0.003 wt% Ca, up to 0.003 Wt .-% rare earth metals, up to 0.1 wt .-% Ti or up to 0.1 wt .-% V be present.
  • the structure of the known steel sheet based on its overall structure, has a retained austenite content of 5 to 20% and at least 50% bainitic ferrite.
  • the proportion of polygonal ferrite in the structure of the known steel sheet should be at most 30%.
  • the proportion of polygonal ferrite in the known steel sheet bainite to form the matrix phase and Restautenit shares be present, which contribute to the balance of tensile strength and ductility.
  • the presence of Nb should ensure that the retained austenite content of the microstructure is fine-grained.
  • this is also a final annealing at temperatures above the Ac 3 temperature, followed by controlled cooling with a Cooling rate of at least 10 ° C / s up to a lying in the range of 300 - 450 ° C temperature at which the bainite transformation is completed, and finally a holding at this temperature for a sufficiently long time may be required.
  • the flat steel product has in addition to iron and unavoidable impurities (in% by mass) 0.06 - 0.6% C, 1 - 6% Mn, 0.1 - 2% Si and 0.01 - 3% Al, wherein for the contents of Si and Mn should satisfy the condition Si / Mn ⁇ 0.40.
  • the flat steel product may be 0.005 - 0.1% Nb, up to 0.02% S, 0.0005 - 0.1% P, up to 0.01% N, 0.005 - 0.1% Ti, 0.0003 - 0.01% B and 0.005 - 0.1% V contained.
  • the structure of the flat steel product should have at least 75% bainitic ferrite and polygonal ferrite and at least 3% retained austenite, the proportion of the polygonal ferrite being 1-50% and the proportion of bainitic ferrite being at least 40%.
  • the microstructure may also contain at least 75% tempered martensite and ferrite and at least 3% retained austenite, in which case the proportion of ferrite should be 4-40% and the proportion of martensite at least 50%.
  • the flat steel product undergoes hot rolling followed by surface and heat treatment, with specially adapted temperature specifications Need to become. In this way, not only the desired surface texture, but also the formation of cracks during forming should be avoided.
  • the object of the invention was to further increase a multiphase steel To provide strength, which also has a high elongation at break.
  • a flat product with a further optimized combination of high strength and good ductility and a method for producing such a flat product should be specified.
  • the solution of the above-mentioned object consists of a cold flat product designed according to claim 11.
  • a multiphase steel according to the invention contains (in% by weight) C: 0.14-0.25%, Mn: 1, 7-2.5%, Si: 0.2-0.7%, Al: 0.5- 1, 5%, Cr: ⁇ 0.1%, Mo: ⁇ 0.05%, Nb: 0.02-0.06%, S: up to 0.01%, in particular up to 0.005%, P: to to 0.02%, N: up to 0.01%, and optionally at least one element from the group "Ti, B, V", and the balance iron and unavoidable impurities, wherein for the contents of the optionally provided elements are provided such that Ti: ⁇ 0.1%, B: ⁇ 0.002%, V: ⁇ 0.15% and wherein in the structure of the steel at least 10% by volume of ferrite and at least 6% by volume. % Retained austenite are present.
  • a steel assembled and obtained according to the invention achieves a tensile strength R m of at least 950 MPa, a yield strength R eL of at least 500 MPa and an elongation at break A 80 in the transverse direction of at least 15%.
  • Carbon increases the amount and stability of retained austenite. Therefore, in the steel of the present invention, at least 0.14 wt% of carbon is present to stabilize the austenite to room temperature and to prevent complete conversion of the austenite formed in an annealing treatment into martensite, ferrite or bainite, and bainitic ferrite, respectively. However, over 0.25 wt .-% lying carbon contents have a negative effect on the weldability.
  • Mn Like C, Mn contributes to the strength and increase the amount and stability of the retained austenite. However, excessive Mn levels increase the risk of segregation. They also have a negative effect on the elongation at break, since the ferrite and bainite conversions are greatly delayed and, as a result, comparatively high amounts of martensite remain in the microstructure.
  • the Mn content of a steel according to the invention is set at 1.7-2.5% by weight.
  • Al are present in amounts of 0.5-1.5% by weight and Si in contents of 0.2-0.7% by weight. present in order to avoid carbide formation in the bainite step in the over-aging treatment carried out in the course of the inventive processing of the steel.
  • the bainite transformation does not proceed completely due to the presence of Al and Si, so that only bainitic ferrite is formed and carbide formation does not occur. In this way, the present invention desired stability of carbon-enriched retained austenite is achieved.
  • This effect can be ensured particularly reliably by limiting the Si content to 0.6% by weight or the Al content to 0.7-1.4% by weight, with Si contents of more than are set as 0.2 wt .-% and less than 0.6 wt .-% and the Al contents between 0.7 wt .-% and 1.4 wt .-% are.
  • Si contents of more than are set as 0.2 wt .-% and less than 0.6 wt .-% and the Al contents between 0.7 wt .-% and 1.4 wt .-% are.
  • optimum properties of the multiphase steel according to the invention result when the sum of its Al and Si contents is 1.2-2.0% by weight.
  • the Cr content is limited to less than 0.1% by weight and the Mo content of a steel according to the invention to less than 0.05% by weight, in particular less than 0.01% by weight.
  • a steel according to the invention contains Nb in amounts of 0.02-0.06% by weight and optionally one or more of the elements "Ti, V, B" in order to increase the strength of the steel steel according to the invention.
  • Nb, Ti, V and B form very fine precipitates with the C and N present in the steel according to the invention. These precipitates increase strength and yield strength by particle hardening and grain refining. The grain refining is also of great advantage for the forming properties of the steel.
  • Ti still binds N during solidification or at very high temperatures, so that possible negative effects of this element on the properties of the steel according to the invention are reduced to a minimum.
  • up to 0.1% by weight of Ti and up to 0.15% by weight of V can be added to a steel according to the invention in addition to the ever present Nb.
  • the positive influence of the presence of Ti with respect to the setting of the N content can be used particularly purposefully if the Ti content "% Ti" of a multiphase steel according to the invention fulfills the following condition [3]: % Ti ⁇ 3 . 4 x % N . where "% N" denotes the respective N content of the multiphase steel and this condition is to be observed, in particular, when the Ti content is 0.01-0.03 wt%.
  • the positive effect of Ti in a steel according to the invention occurs particularly reliably when its Ti content is at least 0.01% by weight.
  • the ferrite formation can be delayed upon cooling, so that a larger amount of austenite is present in the bainite. As a result, the amount and the stability of the retained austenite can be increased.
  • bainitic ferrite is formed instead of normal ferrite, which contributes to increasing the yield strength.
  • At least 10% by volume of ferrite, in particular at least 12% by volume of ferrite, and at least 6% by volume of retained austenite are present in the structure of a steel according to the invention, in order to ensure the desired high strength on the one hand and good ductility on the other hand.
  • up to 90% by volume of the microstructure can be used for this purpose Ferrite and up to 20 vol .-% consist of retained austenite.
  • Contents of at least 5 vol.% Martensite in the structure of the steel according to the invention contribute to its strength, wherein the martensite content to max. 40 vol .-% should be limited to ensure sufficient extensibility of the steel according to the invention.
  • optionally 5 to 40% by volume of bainite can be present in the microstructure of a steel according to the invention.
  • the retained austenite of a steel according to the invention is enriched with carbon in such a way that its content is as described in the article of A. Zarei Hanzaki et al. in ISIJ Int. Vol. 35, No 3, 1995, pp. 324 - 331 published formula [1] calculated C inRA content is more than 0.6 wt .-%.
  • C INRA a RA - a ⁇ / 0 . 0044 with a ⁇ : 0.3578 nm (lattice constant of austenite); a RA : respective lattice parameter of the retained austenite after final cooling in nm measured on the finished cold strip.
  • the amount of carbon present in the retained austenite substantially affects the TRIP properties and ductility of a steel according to the invention. Accordingly, it is advantageous if the C inRA content is as high as possible.
  • the invention further provides that the steel according to the invention has a compound of the formula [2] calculated quality G RA of the retained austenite ("retained austenite quality") of more than 6, in particular more than 8, having.
  • G RA % RA x C INRA with% RA: retained austenite content of the multiphase steel in% by volume;
  • C inRA C content of retained austenite calculated according to formula [1].
  • a cold-rolled flat product of the type according to the invention can be produced according to the invention by melting an inventive multi-phase steel in the first working step and casting it into a preliminary product.
  • This precursor may be a slab or thin slab.
  • the precursor is then, if necessary, reheated to a temperature of 1100-1300 ° C, from which the precursor is then hot rolled into a hot strip.
  • the final temperature of the hot rolling is according to the invention 820-950 ° C.
  • the resulting hot strip is wound into a coil at a reel temperature of 400-750 ° C., in particular 530-600 ° C.
  • the hot strip may be subjected to annealing after being reeled and before being cold rolled. This can be advantageously carried out as a bell annealing or completed in a continuous flow annealing.
  • the at the cold rolling preparatory annealing set annealing temperatures are typically 400 - 700 ° C.
  • the hot strip at cold rolling degrees of 30 - 80%, especially 50 - 70%, cold rolled to a cold rolled product, with cold rolling degrees of 30 - 75%, especially 50 - 65% lead particularly safe to the desired result.
  • the resulting cold-rolled product is then subjected to a heat treatment in which it undergoes a continuous annealing at a 750 - 900 ° C, in particular 800 - 830 ° C, amounting annealing temperature, then at 350 - 500 ° C, especially 370 - 460 ° C. to be subjected to an overaging treatment.
  • the annealing time over which the cold flat product is annealed in the course of continuous annealing at the annealing temperature is typically 10 - 300 s, while the duration of the over-aging treatment after annealing can be up to 800 s, with the minimum annealing time generally being 10 s becomes.
  • the annealed cold rolled product may be quenched between annealing and overaging to obtain a return to ferrite and to suppress the formation of perlite.
  • the respective set cooling rate can be at least 5 ° C / s.
  • a holding of the cold-flat product at the intermediate temperature takes place over a duration which is sufficient for the formation of the desired microstructure, on the down the cold flat product is then cooled further.
  • the annealing of the cold flat product can be carried out in the course of a fire coating, in which the cold flat product is provided with a metallic protective coating.
  • the cold strip produced according to the invention with a protective layer after the heat treatment by electrolytic coating or another deposition method.
  • the cold strip obtained can also be subjected to re-rolling at degrees of deformation of up to 10% in order to improve its dimensional stability, surface finish and mechanical properties.
  • melts S1 to S13 given in Table 1 were melted and processed into cold-rolled products K1-K41.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP10186553.3A 2010-10-05 2010-10-05 Mehrphasenstahl, aus einem solchen Mehrphasenstahl hergestelltes kaltgewalztes Flachprodukt und Verfahren zu dessen Herstellung Active EP2439290B1 (de)

Priority Applications (6)

Application Number Priority Date Filing Date Title
EP10186553.3A EP2439290B1 (de) 2010-10-05 2010-10-05 Mehrphasenstahl, aus einem solchen Mehrphasenstahl hergestelltes kaltgewalztes Flachprodukt und Verfahren zu dessen Herstellung
CN201180048744.5A CN103210097B (zh) 2010-10-05 2011-09-22 多相钢、由这种多相钢制成的冷轧扁钢制品以及这种产品的制造方法
KR1020137011457A KR101848876B1 (ko) 2010-10-05 2011-09-22 복합조직강, 복합조직강으로 제조된 냉연 평판 제품 및 제조 방법
US13/877,782 US9970088B2 (en) 2010-10-05 2011-09-22 Multi-phase steel, cold-rolled flat product produced from such a multi-phase steel and method for producing it
JP2013532112A JP6001541B2 (ja) 2010-10-05 2011-09-22 多相鋼から作られた冷間圧延平鋼製品およびその製造方法
PCT/EP2011/066522 WO2012045595A1 (de) 2010-10-05 2011-09-22 Mehrphasenstahl, aus einem solchen mehrphasenstahl hergestelltes kaltgewalztes flachprodukt und verfahren zu dessen herstellung

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP10186553.3A EP2439290B1 (de) 2010-10-05 2010-10-05 Mehrphasenstahl, aus einem solchen Mehrphasenstahl hergestelltes kaltgewalztes Flachprodukt und Verfahren zu dessen Herstellung

Publications (2)

Publication Number Publication Date
EP2439290A1 EP2439290A1 (de) 2012-04-11
EP2439290B1 true EP2439290B1 (de) 2013-11-27

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EP10186553.3A Active EP2439290B1 (de) 2010-10-05 2010-10-05 Mehrphasenstahl, aus einem solchen Mehrphasenstahl hergestelltes kaltgewalztes Flachprodukt und Verfahren zu dessen Herstellung

Country Status (6)

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US (1) US9970088B2 (ko)
EP (1) EP2439290B1 (ko)
JP (1) JP6001541B2 (ko)
KR (1) KR101848876B1 (ko)
CN (1) CN103210097B (ko)
WO (1) WO2012045595A1 (ko)

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DE102022102418A1 (de) 2022-02-02 2023-08-03 Salzgitter Flachstahl Gmbh Hochfestes schmelztauchbeschichtetes Stahlband mit durch Gefügeumwandlung bewirkter Plastizität und Verfahren zu dessen Herstellung

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CN107002206B (zh) 2014-07-07 2019-03-15 塔塔钢铁艾默伊登有限责任公司 具有高强度和高度可成形性的钢带材、具有热浸锌基涂层的钢带材
CN104328336B (zh) * 2014-11-06 2016-04-20 东北大学 一种亚微米奥氏体强韧化的高强韧薄钢板及其制备方法
US11401571B2 (en) * 2015-02-20 2022-08-02 Nippon Steel Corporation Hot-rolled steel sheet
EP3390040B2 (en) 2015-12-15 2023-08-30 Tata Steel IJmuiden B.V. High strength hot dip galvanised steel strip
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CN103210097A (zh) 2013-07-17
WO2012045595A1 (de) 2012-04-12
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