WO2016129548A1 - Tôle d'acier à ultra-haute résistance présentant un module d'élasticité et une aptitude au façonnage excellents - Google Patents

Tôle d'acier à ultra-haute résistance présentant un module d'élasticité et une aptitude au façonnage excellents Download PDF

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Publication number
WO2016129548A1
WO2016129548A1 PCT/JP2016/053640 JP2016053640W WO2016129548A1 WO 2016129548 A1 WO2016129548 A1 WO 2016129548A1 JP 2016053640 W JP2016053640 W JP 2016053640W WO 2016129548 A1 WO2016129548 A1 WO 2016129548A1
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Prior art keywords
less
steel sheet
ultra
yield ratio
workability
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PCT/JP2016/053640
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English (en)
Japanese (ja)
Inventor
航佑 柴田
隼矢 中田
俊夫 村上
敬祐 小澤
文雄 湯瀬
厚寛 白木
賢司 斉藤
幸博 内海
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株式会社神戸製鋼所
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Application filed by 株式会社神戸製鋼所 filed Critical 株式会社神戸製鋼所
Priority to CN201680009463.1A priority Critical patent/CN107208227A/zh
Priority to US15/550,180 priority patent/US20190032166A1/en
Priority to MX2017010270A priority patent/MX2017010270A/es
Priority to KR1020177022118A priority patent/KR20170103905A/ko
Publication of WO2016129548A1 publication Critical patent/WO2016129548A1/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
    • 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
    • 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
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/008—Martensite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • Patent Document 1 by increasing the Mn content in a steel sheet, a large amount of austenite is retained, thereby improving hydrogen embrittlement resistance in an ultra-high strength region having a tensile strength of 1180 MPa or more and punching.
  • a steel plate that is also excellent in delayed fracture resistance in a hole-drilled part.
  • the steel sheets of the present invention all have a room for improvement in terms of weldability because the Mn content in the steel sheet exceeds 1.5 mass%. .
  • Patent Document 2 discloses a component composition satisfying C of 0.35% by mass or less and Mn of 1.5% by mass or less by increasing the fraction of the soft ferrite phase, and a tensile strength of 1470 MPa or more. And the steel plate which can implement
  • an object of the present invention is to provide an ultra-high strength steel sheet excellent in yield ratio and workability that can satisfy a tensile strength of 1470 MPa or more, a yield ratio of 0.75 or more, and a total elongation of 10% or more. There is.
  • the steel sheet of the present invention contains a predetermined amount of retained austenite (hereinafter, austenite may be expressed as ⁇ ) in which Mn is further concentrated after the matrix phase is martensite. It is a feature.
  • the average Mn concentration in the steel sheet needs to satisfy 1.5% by mass or less, so that the Mn concentration region is formed in the steel sheet of the present invention. That is, the retained austenite formed in the Mn concentration region is stabilized while keeping the Mn concentration of the matrix phase low.
  • N 0.01% or less N is also unavoidably present as an impurity element and lowers the workability of the steel sheet by strain aging, so the N content is 0.01% or less, preferably 0.005% or less, more preferably 0.003% or less. Restrict.
  • an annealing treatment is performed under the condition of holding at 680 ° C. to Ac1 point (more preferably 690 ° C. to [Ac1-10 ° C.]) for 0.8 h or more (more preferably 1 h or more).
  • the carbide is spheroidized and coarsened, and Mn in the carbide is concentrated to 1.2 times or more of the amount of Mn added to the steel sheet.
  • this annealing treatment after cooling to Ac1 point or less, it may be kept in the above temperature range, or may be gradually cooled in this temperature range, or after hot rolling, it is once cooled to less than 680 ° C. You may go after.
  • the tempered martensite is formed by tempering the heat-treated plate at a temperature of 150 to 300 ° C. for 30 to 1200 s, and the strength-elongation balance can be improved.
  • An ultra-high strength steel sheet having excellent properties can be obtained.
  • ⁇ Test method A steel having the composition of each of A to K shown in Table 1 is melted to prepare an ingot having a thickness of 120 mm, and hot rolling is performed using the ingot to obtain a thickness of 2.8 mm. Annealing was performed under the annealing conditions shown in Table 2. After this annealed plate was pickled, it was cold-rolled to a thickness of 1.0 mm to obtain a cold-rolled plate, and the cold-rolled plate was subjected to gamma heat treatment and tempering under the conditions shown in Table 2 below.
  • the local Mn concentration is roughly 3 ⁇ m in the area of 20 ⁇ m ⁇ 20 mm, and quantitative analysis is performed using a field emission electron beam microanalyzer (FE-EPMA). In each field of view, the measurement area is a small area of 1 ⁇ m ⁇ 1 mm. And the Mn concentration in each small region was averaged. The ratio of the small region where the average Mn concentration is 1.2 times or more of the Mn content of the steel sheet is calculated by defining the area ratio of the Mn concentrated region in each field of view, and the area of the Mn concentrated region in three fields of view. Evaluation was performed by arithmetically averaging the rates.
  • FE-EPMA field emission electron beam microanalyzer
  • steel No. Nos. 5 and 10 show the production numbers in Table 2. As shown in FIGS. 5 and 10, since the annealing temperature after hot rolling is too high outside the recommended range, Mn is homogenized by diffusion, and as shown in Table 3, Mn is concentrated in the retained austenite. The total elongation EL is inferior.
  • the ultra-high-strength steel sheet of the present invention is excellent in yield ratio and workability, and is useful for car bodies as cold-rolled steel sheets and various plated steel sheets.

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

Abstract

Cette invention concerne une tôle d'acier à ultra-haute résistance présentant une composition de composants qui comprend des teneurs spécifiques en chacun des éléments parmi : C, Si, Mn, et Al, le reste étant du fer et les inévitables impuretés, les teneurs de chacun des éléments parmi : P, S, et N parmi les impuretés inévitables étant limitées à une teneur spécifique. Ladite tôle d'acier à ultra-haute résistance comprend une région de proportion supérieure ou égale à 1 % en surface, dans laquelle la martensite constitue 90 % ou plus en surface, l'austentite résiduelle constitue 0,5 % ou plus en surface, et la concentration locale en Mn est au moins 1,2 fois celle de la teneur en Mn de la tôle d'acier dans son ensemble. Ladite tôle d'acier à ultra-haute résistance présente une résistance à la traction supérieure ou égale à 1470 MPa, un module d'élasticité supérieur ou égal à 0.75 et un allongement total supérieur ou égal à 10 %.
PCT/JP2016/053640 2015-02-13 2016-02-08 Tôle d'acier à ultra-haute résistance présentant un module d'élasticité et une aptitude au façonnage excellents WO2016129548A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
CN201680009463.1A CN107208227A (zh) 2015-02-13 2016-02-08 屈强比和加工性优异的超高强度钢板
US15/550,180 US20190032166A1 (en) 2015-02-13 2016-02-08 Ultra-high-strength steel sheet having excellent yield ratio and workability
MX2017010270A MX2017010270A (es) 2015-02-13 2016-02-08 Lamina de acero de alta resistencia que tiene una excelente proporcion de rendimiento y capacidad de trabajo.
KR1020177022118A KR20170103905A (ko) 2015-02-13 2016-02-08 항복비와 가공성이 우수한 초고강도 강판

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2015-026736 2015-02-13
JP2015026736A JP2016148098A (ja) 2015-02-13 2015-02-13 降伏比と加工性に優れた超高強度鋼板

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WO2016129548A1 true WO2016129548A1 (fr) 2016-08-18

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Country Status (6)

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US (1) US20190032166A1 (fr)
JP (1) JP2016148098A (fr)
KR (1) KR20170103905A (fr)
CN (1) CN107208227A (fr)
MX (1) MX2017010270A (fr)
WO (1) WO2016129548A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102019217778A1 (de) 2018-11-26 2020-05-28 Mitsubishi Electric Corporation Halbleitervorrichtung
WO2022202023A1 (fr) * 2021-03-25 2022-09-29 日本製鉄株式会社 Tôle d'acier
WO2022259837A1 (fr) * 2021-06-11 2022-12-15 Ｊｆｅスチール株式会社 Tôle d'acier à haute résistance, et procédé de fabrication de celle-ci

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110284064B (zh) * 2019-07-18 2021-08-31 西华大学 一种高强度含硼钢及其制备方法
KR102250333B1 (ko) * 2019-12-09 2021-05-10 현대제철 주식회사 초고강도 냉연강판 및 이의 제조방법
CN111910129B (zh) * 2020-08-12 2022-01-11 宝武集团鄂城钢铁有限公司 一种极低屈强比1200MPa级超高强度厚钢板及其生产方法
CN113092255A (zh) * 2021-04-07 2021-07-09 大唐锅炉压力容器检验中心有限公司 一种评估耐热钢安全性的方法和系统
CN115725893B (zh) * 2021-08-25 2024-03-08 宝山钢铁股份有限公司 一种1300MPa级工程机械用超高强钢及其生产方法

Citations (3)

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JP2010215958A (ja) * 2009-03-16 2010-09-30 Jfe Steel Corp 曲げ加工性および耐遅れ破壊特性に優れる高強度冷延鋼板およびその製造方法
JP2012180570A (ja) * 2011-03-02 2012-09-20 Kobe Steel Ltd 室温および温間での深絞り性に優れた高強度鋼板およびその温間加工方法
WO2013018740A1 (fr) * 2011-07-29 2013-02-07 新日鐵住金株式会社 Feuille d'acier de haute résistance ayant une résistance supérieure au choc, son procédé de fabrication, feuille d'acier galvanisée de haute résistance et son procédé de fabrication

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JP4538094B2 (ja) * 2008-09-17 2010-09-08 新日本製鐵株式会社 高強度厚鋼板およびその製造方法
AU2009292610B8 (en) * 2008-11-11 2011-03-31 Nippon Steel Corporation High-strength steel plate and producing method therefor
CN103038387B (zh) * 2011-08-02 2015-05-27 新柯隆株式会社 碳化硅薄膜的成膜方法

Patent Citations (3)

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Publication number Priority date Publication date Assignee Title
JP2010215958A (ja) * 2009-03-16 2010-09-30 Jfe Steel Corp 曲げ加工性および耐遅れ破壊特性に優れる高強度冷延鋼板およびその製造方法
JP2012180570A (ja) * 2011-03-02 2012-09-20 Kobe Steel Ltd 室温および温間での深絞り性に優れた高強度鋼板およびその温間加工方法
WO2013018740A1 (fr) * 2011-07-29 2013-02-07 新日鐵住金株式会社 Feuille d'acier de haute résistance ayant une résistance supérieure au choc, son procédé de fabrication, feuille d'acier galvanisée de haute résistance et son procédé de fabrication

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102019217778A1 (de) 2018-11-26 2020-05-28 Mitsubishi Electric Corporation Halbleitervorrichtung
WO2022202023A1 (fr) * 2021-03-25 2022-09-29 日本製鉄株式会社 Tôle d'acier
WO2022259837A1 (fr) * 2021-06-11 2022-12-15 Ｊｆｅスチール株式会社 Tôle d'acier à haute résistance, et procédé de fabrication de celle-ci
JP7215647B1 (ja) * 2021-06-11 2023-01-31 Ｊｆｅスチール株式会社 高強度鋼板およびその製造方法

Also Published As

Publication number Publication date
MX2017010270A (es) 2017-11-28
JP2016148098A (ja) 2016-08-18
KR20170103905A (ko) 2017-09-13
CN107208227A (zh) 2017-09-26
US20190032166A1 (en) 2019-01-31

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