EP2489748A9 - Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication - Google Patents

Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication Download PDF

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Publication number
EP2489748A9
EP2489748A9 EP11154973A EP11154973A EP2489748A9 EP 2489748 A9 EP2489748 A9 EP 2489748A9 EP 11154973 A EP11154973 A EP 11154973A EP 11154973 A EP11154973 A EP 11154973A EP 2489748 A9 EP2489748 A9 EP 2489748A9
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EP
European Patent Office
Prior art keywords
steel
complex phase
content
hot
product according
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
EP11154973A
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German (de)
English (en)
Other versions
EP2489748A1 (fr
EP2489748B1 (fr
Inventor
Brigitte Dr. Hammer
Jörg Dipl.-Ing. Mertens
Günther Dipl.-Ing Stich
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 Europe 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 EP11154973.9A priority Critical patent/EP2489748B1/fr
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to CA2825240A priority patent/CA2825240A1/fr
Priority to US13/985,420 priority patent/US20140041767A1/en
Priority to CN201180067938.XA priority patent/CN103380217B/zh
Priority to KR1020137024831A priority patent/KR20140005293A/ko
Priority to PCT/EP2011/074251 priority patent/WO2012110165A1/fr
Priority to JP2013553818A priority patent/JP5864619B2/ja
Publication of EP2489748A1 publication Critical patent/EP2489748A1/fr
Publication of EP2489748A9 publication Critical patent/EP2489748A9/fr
Application granted granted Critical
Publication of EP2489748B1 publication Critical patent/EP2489748B1/fr
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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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
    • 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
    • C21D8/0221—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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • 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 hot rolled flat steel product made from a complex phase steel and to a process for producing such a product.
  • a flat steel cold-rolled from a dual-phase steel which, in addition to a tensile strength of at least 950 MPa and good ductility, also has a surface finish which allows, using a simple manufacturing process, the flat product produced from this steel in uncoated or anti-corrosion coating provided state to deform a complex-shaped component, such as a part of an automobile body.
  • the steel according to the invention consists of 20-70% of martensite, up to 8% of retained austenite and the remainder of ferrite and / or bainite and (in% by weight): C: 0.10-0, 20%, Si: 0.10-0.60%, Mn: 1.50-2.50%, Cr: 0.20-0.80%, Ti: 0.02-0.08%, B: ⁇ 0.0020%, Mo: ⁇ 0.25%, Al: ⁇ 0.10%, P: ⁇ 0.2%, S: ⁇ 0.01%, N: ⁇ 0.012%, and the remainder contains iron and unavoidable impurities ,
  • the in practice of such steel produced flat steel products achieve tensile strengths of up to 1050 MPa.
  • a cooling of the hot strip with a cooling speed on the outlet roller table of at least 30 ° C / s so that the conversion of the steel is largely carried out in the Bainitement and a conversion of the steel is avoided to perlite.
  • Parts of martensite in the structure of the hot strip can further increase the tensile strengths.
  • the comparatively rapid cooling contributes to the precipitation of very fine particles, which further increases the strength.
  • the cooling process is to be stopped at a temperature below 600 ° C by winding the tape on a reel and then cooling in the coil on.
  • the hot strip thus obtained regularly reaches tensile strengths of up to 1150 MPa.
  • the object of the invention was to provide a flat steel product in which further increased tensile strengths with good elongation properties and thus accompanied by good deformation properties are combined. Likewise, a method for producing such a flat steel product should be specified.
  • the complex phase steel used for the production of a hot rolled flat steel product according to the invention contains, in addition to iron and unavoidable impurities (in% by weight) C: 0.13-0.2%, Mn: 1.8-2.5%, Si: 0.70 - 1.3%, Al: up to 0.1%, P: up to 0.1%, S: up to 0.01%, Cr: 0.25 - 0.70%, optionally Mo, where the sum the Cr and Mo contents are 0.25-0.7%, Ti: 0.08-0.2%, and B: 0.0005-0.005%.
  • a steel flat product hot-rolled from the steel according to the invention has high strength combined with good elongation.
  • the microstructure of a flat steel product according to the invention is due to its narrow limits selected alloy characterized in that its structure consists of at most 10% by volume of retained austenite, 10 to 60% by volume of martensite, at most 30% by volume of ferrite and the remainder of bainite, the proportion being at least 10% Vol .-% should be.
  • Perlite is present in a steel flat product according to the invention at most in ineffective traces, the perlite content is reduced as possible to a minimum.
  • flat steel products according to the invention thus achieve a tensile strength Rm which is more than 1100 MPa, in particular regularly reaches at least 1150 MPa and more, and a yield strength Re of likewise regularly at least 720 MPa.
  • Rm tensile strength
  • Re yield strength
  • Carbon is added in the complex phase steel used according to the invention for the surface hardening and for the formation of ultrafine precipitates.
  • C in the inventively predetermined contents of 0.13-0.2% by weight, a sufficiently high martensite and bainite content for the desired hardness is formed in the microstructure.
  • carbon hinders the formation of the desired high bainitic structure content.
  • higher C contents have a negative effect on the weldability, which is for the application of the material according to the invention, for example in the field of automotive engineering is of particular importance.
  • the advantageous effect of carbon in a steel used to produce a flat steel product according to the invention can be used particularly reliably if the C content is 0.15-0.18% by weight, in particular not more than 0.17% by weight.
  • Manganese at a level of at least 1.8% by weight, retards the conversion and causes the formation of hard, strength increasing conversion products. Thus, the presence of Mn supports the formation of martensite. To avoid unduly high microsegregations, the content is according to the invention to max. 2.5 wt .-% limited, with the beneficial effects of Mn then occur particularly safe when the Mn content of the steel according to the invention is limited to 2.05-2.2 wt .-%.
  • Si also serves to increase the strength by, on the one hand, promoting the solid-solution hardening of the ferrite or bainite and, on the other hand, stabilizing the retained austenite.
  • the retained austenite content contributes to increasing elongation and strength (TRIP effect).
  • steel according to the invention has 0.70-1.3% by weight of Si, in particular at least 0.75% by weight of Si.
  • the strength and elongation-increasing effect occurs in particular when the Si content of a steel according to the invention is at least 0.75% by weight, in particular at least 0.85% by weight.
  • the steel constituting the flat steel product of the invention is Al-killed.
  • Aluminum is used in the melting of a steel according to the invention for deoxidizing and for setting nitrogen which may be present in the steel.
  • Al may be added in amounts of less than 0.1% by weight to the steel according to the invention, the desired effect of Al occurring particularly safely if its contents in the range of 0.01-0.06 wt. -%, in particular 0.020 - 0.050 wt .-%, are.
  • Phosphorus can be used to further increase the solid solution hardening, but for reasons of weldability should not exceed a content of 0.1 wt .-% because of the otherwise increasing risk of the formation of segregations.
  • Chromium inhibits ferrite and pearlite formation at levels of at least 0.25% by weight. Accordingly, it promotes the formation of a hardened structure and thus the strength of the steel used for the flat steel product according to the invention. In order not to delay the conversion too much, its content should be reduced to max. 0.7 wt .-% are limited.
  • the Cr content of a steel according to the invention By limiting the Cr content of a steel according to the invention to 0.7% by weight, the risk of grain boundary oxidation is reduced and the good elongation properties of the steel according to the invention are ensured. Also, adhering to this upper limit, a surface of the steel flat product produced from the steel is achieved, which can be well provided with a metallic coating.
  • the optionally present levels of molybdenum, like Cr, contribute to increasing the strength of a steel according to the invention by promoting the formation of ultrafine precipitates and martensite in the structure of the steel.
  • the presence of Mo does not adversely affect the coatability of the flat product with a metallic coating and its ductility. Practical experiments have shown that the positive effects of Mo up to contents of 0.25% by weight, in particular 0.22% by weight, can be used particularly effectively, even from a cost point of view. For example, contents of 0.05% by weight Mo have a positive effect on the properties of the steel according to the invention.
  • the sum of the Cr and Mo contents in a steel used according to the invention is limited to 0.25-0.7% by weight.
  • titanium in contents of at least 0.08 to at most 0.2 wt .-%, in particular 0.09 to 0.15 wt .-%, can be in inventive steel, the formation of ultrafine precipitates in the form of TiC or Ti ( C, N) with hardening effect and cause grain refining.
  • Another positive effect of Ti is the setting of possibly present nitrogen, so that the formation of boron nitrides in the steel according to the invention is prevented.
  • the presence of Ti thus also ensures, in the case of an addition of boron to increase the strength, that the boron can fully develop its effect in the dissolved state.
  • the positive effect of Ti in a steel according to the invention can be used with particular reliability if its Ti content is 0.11-0.13% by weight.
  • Boron improves hardenability in steel used in the present invention when B is present at levels of 0.0005-0.005 weight percent.
  • the favorable effects of B on the alloy according to the invention are particularly reliable when the B content of the steel according to the invention is set at 0.001-0.002% by weight.
  • procured flat steel products are characterized by a particularly high granularity, a high yield strength and increased strength.
  • the proportions of martensite, bainite and ultrafine precipitates in its structure contribute to the high strength.
  • the residual austenite and ferrite portions of the microstructure ensure its good elongation properties.
  • the hot strips can be provided with a metallic protective coating before or after their transformation into a component. This can be done by hot-dip galvanizing or electrolytic coating.
  • a molten steel with a below the alloy of according to the invention used steel cast to a precursor, which is typically a strand which is cut into slabs or thin slabs.
  • the precursor is heated to a temperature of 1150-1350 ° C to ensure a fully austenitic structure of the steel for subsequent hot rolling and to bring the precipitates into solution.
  • the precursor is then hot rolled to a hot strip, the final temperature of hot rolling being 800-950 ° C.
  • the rolling end temperature should be in the range of the homogeneous austenite and thus not below 800 ° C in order to keep deformation-induced precipitations low and to enable the expression of the desired structure composition.
  • the hot strip obtained is cooled at a cooling rate which is at least 30 ° C / s, to the respectively selected coiler temperature.
  • the cooling conditions are to be chosen so that a conversion to perlite is avoided and the conversion is largely carried out so that the high bainite levels and the inventively given proportions of martensite and retained austenite are obtained.
  • the cooling process is terminated when the inventively predetermined range of reel temperature of 400 - 570 ° C. is reached, in which the Bainitcut of the steel according to the invention is reached.
  • the correspondingly cooled hot strip is then wound into a coil and cooled further in the coil. This leads to further transformations in bainite and martensite and to the formation of excretion.
  • steel according to the invention is particularly suitable for the production of highly loaded profiles in practical use as well as for crash and strength-relevant components for vehicle bodies.
  • the blocks were heated to 1270 ° C and hot rolled from this temperature to hot strip with a thickness of 2.5 mm.
  • the hot rolling end temperature was 900 ° C.
  • the hot strip obtained after hot rolling at a cooling rate of 80 ° C / s and at a temperature of 490 ° C in the oven was slowly cooled to simulate cooling in the coil.
  • the obtained hot strip had a tensile strength Rm of 1192 MPa and an elongation A80 of 10.5% transversely to the rolling direction.
  • the microstructure obtained consists of 35-40 vol.% Martensite, about 5 vol.% Ferrite, 6 vol.% Retained austenite and the remainder bainite.
  • the hot strips produced in the manner described above after hot rolling were first cooled to a temperature of 75 ° C and then slowly further in the oven to room temperature, to simulate cooling in the coil here.
  • the hot strips thus obtained had a tensile strength Rm of 1550 MPa and a comparatively low elongation A80 of 5.9%. They were predominantly martensitic.
  • the above-described hot strips after hot rolling were first cooled to a temperature corresponding to the "coiler temperature” of 600 ° C and then again slowly cooled to room temperature to simulate the cooling in the coil.
  • the hot strips thus obtained had a tensile strength Rm of 955 MPa and an elongation A80 of 15.5%.
  • the microstructure consisted of ferrite with a perlite content of 25-30% by volume.
  • the blocks were heated to 1270 ° C and hot rolled from this temperature to hot strip with a thickness of 2.5 mm.
  • the hot rolling end temperature was 900 ° C.
  • the hot strip obtained after hot rolling at a cooling rate of 80 ° C / s has been cooled to a "reel temperature" of 550 ° C, from which in turn the Coilabkühlung has been simulated in the manner already described above.
  • the resulting hot strip had a tensile strength Rm of 1180 MPa and an elongation A80 of 11%.
  • Their structure had a martensite content of 35-40% by volume, a residual austenite content of 7.5% by volume, a ferrite content of 10% by volume and the remainder bainite
  • a steel with the alloy according to the invention indicated in Table 3 has been melted and cast into a strand.
  • the slabs separated from the strand are then reheated to a temperature of about 1260 ° C, then hot rolled with a hot rolling temperature WET to hot strips with a thickness D and finally cooled at a cooling rate V T on a coiling temperature HT, in which they to a Coil have been reeled.
  • the respectively set parameters and the mechanical properties of the resulting hot strips are given in Table 4.
  • the hot strip obtained in the operating trial 3c had a significantly lower tensile strength than the hot strips obtained in the temperature range according to the invention, due to the high coiling temperature due to a high ferrite content (and perlite).

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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)
EP11154973.9A 2011-02-18 2011-02-18 Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication Active EP2489748B1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP11154973.9A EP2489748B1 (fr) 2011-02-18 2011-02-18 Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication
US13/985,420 US20140041767A1 (en) 2011-02-18 2011-12-29 Hot-Rolled Flat Steel Product Produced from a Complex Phase Steel and Method for the Production Thereof
CN201180067938.XA CN103380217B (zh) 2011-02-18 2011-12-29 由复相钢制成的热轧钢板产品及其制造方法
KR1020137024831A KR20140005293A (ko) 2011-02-18 2011-12-29 복상 강으로 제조된 열간 압연 판상 강 제품 및 그 제조 방법
CA2825240A CA2825240A1 (fr) 2011-02-18 2011-12-29 Produit plat en acier lamine a chaud fabrique a partir d'un acier a phase complexe et procede de fabrication correspondant
PCT/EP2011/074251 WO2012110165A1 (fr) 2011-02-18 2011-12-29 Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et procédé de fabrication correspondant
JP2013553818A JP5864619B2 (ja) 2011-02-18 2011-12-29 複合相鋼から製造される熱間圧延平鋼製品及びその製造方法

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP11154973.9A EP2489748B1 (fr) 2011-02-18 2011-02-18 Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication

Publications (3)

Publication Number Publication Date
EP2489748A1 EP2489748A1 (fr) 2012-08-22
EP2489748A9 true EP2489748A9 (fr) 2012-10-10
EP2489748B1 EP2489748B1 (fr) 2017-12-13

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EP11154973.9A Active EP2489748B1 (fr) 2011-02-18 2011-02-18 Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication

Country Status (7)

Country Link
US (1) US20140041767A1 (fr)
EP (1) EP2489748B1 (fr)
JP (1) JP5864619B2 (fr)
KR (1) KR20140005293A (fr)
CN (1) CN103380217B (fr)
CA (1) CA2825240A1 (fr)
WO (1) WO2012110165A1 (fr)

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WO2015158731A1 (fr) * 2014-04-15 2015-10-22 Thyssenkrupp Steel Europe Ag Procédé de production d'un produit plat en acier laminé à froid à limite d'élasticité élevée et produit plat en acier laminé à froid
JP2018003062A (ja) * 2016-06-29 2018-01-11 Ｊｆｅスチール株式会社 高強度高加工性熱延鋼板およびその製造方法
US11649531B2 (en) * 2016-08-05 2023-05-16 Nippon Steel Corporation Steel sheet and plated steel sheet
KR101917469B1 (ko) * 2016-12-23 2018-11-09 주식회사 포스코 재질편차가 적고 표면품질이 우수한 고강도 열연강판 및 그 제조방법
CN106756512B (zh) * 2017-01-12 2018-12-18 唐山钢铁集团有限责任公司 一钢多级的热轧复相高强钢板及其生产方法
DE102017218434A1 (de) 2017-10-16 2019-04-18 Thyssenkrupp Ag Emaillieren von höherfesten Stählen
KR102164108B1 (ko) * 2018-11-26 2020-10-12 주식회사 포스코 형상 품질 및 굽힘성이 우수한 초고강도 열연강판 및 그 제조방법
CN109680223B (zh) * 2019-03-08 2020-10-16 东北大学 一种易切削高强度复相非调质钢制备方法
CN112575267A (zh) * 2019-09-27 2021-03-30 宝山钢铁股份有限公司 一种高扩孔复相钢及其制造方法
CN110760756B (zh) * 2019-11-27 2021-06-22 河钢股份有限公司邯郸分公司 一种厚规格dp680级热轧双相钢及其制备方法
WO2023132351A1 (fr) * 2022-01-07 2023-07-13 日本製鉄株式会社 Tôle d'acier laminée à chaud et son procédé de production
JPWO2023132342A1 (fr) * 2022-01-07 2023-07-13
CN115710676A (zh) * 2023-01-10 2023-02-24 北京科技大学 一种低成本高强韧贝氏体/马氏体复相钢

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JP3440894B2 (ja) * 1998-08-05 2003-08-25 Ｊｆｅスチール株式会社 伸びフランジ性に優れる高強度熱延鋼板およびその製造方法
JP3644275B2 (ja) * 1998-10-28 2005-04-27 住友金属工業株式会社 被削性に優れたマルテンサイト・ベイナイト型非調質鋼材及びその製造方法
JP4430444B2 (ja) * 2004-03-26 2010-03-10 新日本製鐵株式会社 形状凍結性に優れた低降伏比型高強度熱延鋼板とその製造方法
JP3889766B2 (ja) * 2005-03-28 2007-03-07 株式会社神戸製鋼所 穴拡げ加工性に優れた高強度熱延鋼板およびその製造方法
JP4772497B2 (ja) * 2005-12-27 2011-09-14 新日本製鐵株式会社 穴拡げ性に優れた高強度冷延薄鋼板及びその製造方法
EP2053140B1 (fr) * 2006-07-14 2013-12-04 Kabushiki Kaisha Kobe Seiko Sho Feuilles d'acier très résistantes et procédés de production de celles-ci
ATE432376T1 (de) * 2006-10-30 2009-06-15 Thyssenkrupp Steel Ag Verfahren zum herstellen von stahl-flachprodukten aus einem mit bor mikrolegierten mehrphasenstahl
PL2028282T3 (pl) 2007-08-15 2012-11-30 Thyssenkrupp Steel Europe Ag Stal dwufazowa, płaski wyrób wytworzony ze stali dwufazowej i sposób wytwarzania płaskiego wyrobu
PL2103704T3 (pl) * 2008-03-10 2012-12-31 Swiss Steel Ag Walcowany na gorąco długi produkt i sposób jego wytwarzania
JP5206244B2 (ja) * 2008-09-02 2013-06-12 新日鐵住金株式会社 冷延鋼板

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EP2489748A1 (fr) 2012-08-22
KR20140005293A (ko) 2014-01-14
US20140041767A1 (en) 2014-02-13
CN103380217A (zh) 2013-10-30
JP2014510838A (ja) 2014-05-01
JP5864619B2 (ja) 2016-02-17
WO2012110165A1 (fr) 2012-08-23
EP2489748B1 (fr) 2017-12-13
CA2825240A1 (fr) 2012-08-23
CN103380217B (zh) 2015-09-23

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