WO2010109702A1 - Tôle d'acier laminée à froid - Google Patents

Tôle d'acier laminée à froid Download PDF

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Publication number
WO2010109702A1
WO2010109702A1 PCT/JP2009/067172 JP2009067172W WO2010109702A1 WO 2010109702 A1 WO2010109702 A1 WO 2010109702A1 JP 2009067172 W JP2009067172 W JP 2009067172W WO 2010109702 A1 WO2010109702 A1 WO 2010109702A1
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WO
WIPO (PCT)
Prior art keywords
mass
less
steel sheet
cold
rolled steel
Prior art date
Application number
PCT/JP2009/067172
Other languages
English (en)
Japanese (ja)
Inventor
英雄 畠
俊夫 村上
朗 伊庭野
文雄 湯瀬
潤一郎 衣笠
Original Assignee
株式会社神戸製鋼所
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 claimed from JP2009079775A external-priority patent/JP4712882B2/ja
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 US13/257,639 priority Critical patent/US8876986B2/en
Priority to CN200980157926.9A priority patent/CN102348823B/zh
Publication of WO2010109702A1 publication Critical patent/WO2010109702A1/fr

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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • 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
    • C22C38/04—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
    • C21D2211/004—Dispersions; Precipitations
    • 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 above thin steel sheet exhibits excellent strength and elongation and resistance to hydrogen embrittlement.
  • retained austenite becomes a starting point of fracture and becomes a factor of lowering the stretch flangeability. Therefore, the stretch flangeability, which is becoming increasingly important in recent years, has a desired level (at least 70%, preferably 90%) was difficult to achieve reliably.
  • the cold-rolled steel sheet according to the present invention at least 1 type of Nb, Ti, and Zr is combined so as to satisfy the above-mentioned formula 1, and 0.01% by mass or more, and the crystal grain difference is 15 ° or more at a large angle grain boundary.
  • the average particle size of the surrounded ferrite is preferably 5 ⁇ m or less.
  • the number of precipitates containing V: 0.001 to 0.20 mass% and having an equivalent circle diameter of 20 nm or more containing V is 10 or less per 1 ⁇ m 2 of the tempered martensite.
  • the cold-rolled steel sheet according to the present invention preferably contains B: 0.0001 to 0.0050 mass%.
  • the present inventors paid attention to a high-strength steel sheet having a tempered martensite (hereinafter sometimes simply referred to as “martensite”) single phase or a two-phase structure composed of ferrite and tempered martensite.
  • the inventors then added V as an alloy element, or added one or more of Nb, Ti, and Zr to the carbides and carbonitrides of V that strongly act as hydrogen trap sites. It was thought that stretch flangeability could be improved while securing hydrogen embrittlement resistance by introducing carbides and carbonitrides of Nb, Ti, and Zr into martensite with appropriate sizes.
  • the inventors have conducted intensive studies such as investigating the influence of various factors on hydrogen embrittlement resistance and stretch flangeability.
  • V carbides and carbonitrides, Nb, Ti, and Zr carbides and carbonitrides may be collectively referred to as “V-containing precipitates”.
  • V-containing precipitates As a result, the inventors have found that, in addition to reducing the proportion of ferrite, by refining precipitates containing V or the like, it is possible to improve stretch flangeability while ensuring hydrogen embrittlement resistance, The present invention has been completed based on this finding.
  • the steel sheet of the present invention is based on a tempered martensite single phase or a two-phase structure (ferrite + tempered martensite), and in particular, the distribution state of precipitates containing V and the like in the tempered martensite. Is characterized in that is controlled.
  • the tempered martensite is 50% or more in area ratio, preferably 60% or more, more preferably 70% or more (including 100%).
  • the balance is ferrite.
  • the number of fine precipitates having an equivalent circle diameter of 1 to 10 nm is 20 or more, preferably 50 or more, more preferably 100 or more per 1 ⁇ m 2 of tempered martensite.
  • a preferable range of the size (equivalent circle diameter) of the fine precipitate is 1 to 8 nm, and a more preferable range is 1 to 6 nm.
  • the reason why the lower limit of the equivalent circle diameter of the fine precipitate is set to 1 nm is that the fine precipitate having a smaller diameter is less effective as a hydrogen trap site.
  • coarse V-containing precipitates having an equivalent circle diameter of 20 nm or more are limited to 10 or less, preferably 5 or less, more preferably 3 or less per 1 ⁇ m 2 of tempered martensite.
  • the structure of the steel sheet of the present invention satisfies the above requirements. Further, when one or more of Nb, Ti and Zr are contained, it is recommended to satisfy the following organization regulations in addition to the essential organization regulations. ⁇ Average grain size of ferrite surrounded by large grain boundaries with a crystal orientation difference of 15 ° or more: 5 ⁇ m or less> By making effective ferrite finer, even if fatigue cracks occur at the interface with martensite, the cracks are difficult to propagate into the ferrite grains. Thereby, stretch flangeability can be improved.
  • the average grain size of ferrite surrounded by large-angle grain boundaries with a crystal orientation difference of 15 ° or more is limited to 5 ⁇ m or less, preferably 10 ⁇ m or less.
  • Nb, Ti and Zr and also contains V it is recommended that the content of V is 0.001 to 0.20 mass%.
  • V like Nb, Ti and Zr, is an element that contributes to the improvement of hydrogen embrittlement resistance because it functions as a hydrogen trap site by being present in steel as fine carbides and carbonitrides.
  • the amount of V is less than 0.001% by mass, the effect of improving the hydrogen embrittlement resistance cannot be sufficiently obtained.
  • V is present in the steel in an insoluble state during heating during annealing.
  • the range of V content in the case of containing one or more of Nb, Ti and Zr is more preferably 0.01% by mass or more and less than 0.15% by mass, particularly preferably 0.02% by mass or more and 0.12% by mass. %.
  • the structure of the steel sheet of the present invention preferably satisfies the following recommended structure provision (a) or (b) in addition to the above essential structure provision.
  • the dislocation density in the entire structure is 1 ⁇ 10 15 to 1 ⁇ 10 16 m ⁇ 2 .
  • the lower limit of the C content is preferably 0.05% by mass, more preferably 0.07% by mass, and still more preferably 0.08% by mass.
  • the upper limit of the C content is preferably 0.25% by mass, more preferably 0.20% by mass.
  • Si 3.0% by mass or less (including 0% by mass)
  • Si is a useful element that can increase strength without deteriorating elongation as a solid solution strengthening element. If the Si content exceeds 3.0% by mass, the formation of austenite during heating is inhibited, so the area ratio of martensite cannot be ensured and stretch flangeability cannot be ensured.
  • the range of the Si content is preferably 2.5% by mass or less, more preferably 2.0% by mass or less, further preferably 1.8% by mass or less, and particularly preferably 1.5% by mass or less (0% by mass). Included).
  • the left side Pf of the above equation 4 is obtained from an equation that thermodynamically expresses the precipitation and dissolution behavior of Nb, Ti and Zr as a parameter representing the solid solution amount of Nb, Ti and Zr during annealing heating. (See Japan Iron and Steel Institute, 3rd edition Handbook of Steel, Volume I Basics, p. 412). If the annealing heating temperature is set so as to satisfy Pf> 0.0010, a sufficient amount of solute Nb and Ti can be secured.
  • Example 1 when V is contained
  • Steels having the components shown in Table 1 below were melted to produce 120 mm thick ingots. After this was hot rolled to a thickness of 25 mm, it was again hot rolled to a thickness of 3 mm. After pickling, this was cold-rolled to a thickness of 1.2 mm to obtain a test material, which was heat-treated under the conditions shown in Tables 2-4.
  • SSRT low strain rate technique
  • Steel No. No. 68 has a martensite area ratio that is insufficient due to the C content being too low, so that the stretch flangeability and hydrogenation embrittlement resistance are excellent, but the tensile strength is inferior.

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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

La présente invention concerne une tôle d'acier à haute résistance laminée à froid qui présente une aptitude améliorée au formage de bord tombé tout en conservant une excellente résistance à la fragilisation due à l'hydrogène. La tôle d'acier laminée à froid comprend 0,03 à 0,30 % en masse de C, 3,0 % en masse ou moins (y compris 0 % en masse) de Si, plus de 0,1 % en masse et pas plus de 2,8 % en masse de Mn, 0,1 % en masse ou moins de P, 0,005 % en masse ou moins de S, 0,01 % en masse ou moins de N, et 0,01 à 0,50 % en masse de Al. La tôle d'acier laminée à froid comprend en outre V en quantité allant de 0,001 à 1,00 % en masse ou un ou plusieurs éléments choisis parmi Nb, Ti et Zr en quantité totale de 0,01 % en masse ou plus, le reste étant composé de fer et d'impuretés inévitables, les teneurs en un ou plusieurs éléments choisis parmi Nb, Ti et Zr remplissant les conditions représentées par la formule suivante : [% C]-[% Nb]/92,9×12-[% Ti]/47,9×12-[% Zr]/91,2×12 > 0,03. Dans la tôle d'acier laminée à froid, le rapport de section de martensite revenue est de 50 % ou plus (y compris 100 %), et la ferrite compose le reste. Dans la tôle d'acier laminée à froid, la distribution des précipités dans la martensite revenue est la suivante : le nombre de précipités ayant chacun un diamètre de cercle équivalent allant de 1 à 10 nm est de 20 particules ou plus pou 1 μm2 de la martensite revenue et le nombre de précipité contenant chacun V ou au moins un élément choisi parmi Nb, Ti et Zr et ayant chacun un diamètre de cercle équivalent de 20 nm ou plus est de 10 particules ou moins pour 1 μm2 de la martensite revenue.
PCT/JP2009/067172 2008-07-11 2009-10-01 Tôle d'acier laminée à froid WO2010109702A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
US13/257,639 US8876986B2 (en) 2008-07-11 2009-10-01 Cold-rolled steel sheet
CN200980157926.9A CN102348823B (zh) 2008-07-11 2009-10-01 冷轧钢板

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2009079775A JP4712882B2 (ja) 2008-07-11 2009-03-27 耐水素脆化特性および加工性に優れた高強度冷延鋼板
JP2009-079775 2009-03-27

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2017009936A1 (fr) * 2015-07-13 2017-01-19 新日鐵住金株式会社 Tôle d'acier, tôle d'acier galvanisée par immersion à chaud, tôle d'acier galvanisée par immersion à chaud alliée et procédés de production associés
WO2017009938A1 (fr) * 2015-07-13 2017-01-19 新日鐵住金株式会社 Tôle d'acier, tôle d'acier galvanisée par immersion à chaud, tôle d'acier galvanisée par immersion à chaud alliée et procédés de production associés
CN109563592A (zh) * 2016-08-30 2019-04-02 杰富意钢铁株式会社 薄钢板及其制造方法
WO2022070636A1 (fr) * 2020-09-30 2022-04-07 日本製鉄株式会社 Tôle d'acier et procédé pour fabriquer une tôle d'acier

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08311600A (ja) * 1995-05-19 1996-11-26 Kobe Steel Ltd 耐水素脆化特性にすぐれる超高強度鋼板及びその製造方法
JP2005213603A (ja) * 2004-01-30 2005-08-11 Jfe Steel Kk 高加工性超高強度冷延鋼板およびその製造方法
JP2007138262A (ja) * 2005-11-21 2007-06-07 Jfe Steel Kk 機械特性ばらつきの小さい高強度冷延鋼板およびその製造方法
WO2008007785A1 (fr) * 2006-07-14 2008-01-17 Kabushiki Kaisha Kobe Seiko Sho Feuilles d'acier très résistantes et procédés de production de celles-ci
JP2009215572A (ja) * 2008-03-07 2009-09-24 Kobe Steel Ltd 降伏応力と伸びと伸びフランジ性に優れた高強度冷延鋼板
JP2009215571A (ja) * 2008-03-07 2009-09-24 Kobe Steel Ltd 伸びフランジ性に優れた高強度冷延鋼板

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08311600A (ja) * 1995-05-19 1996-11-26 Kobe Steel Ltd 耐水素脆化特性にすぐれる超高強度鋼板及びその製造方法
JP2005213603A (ja) * 2004-01-30 2005-08-11 Jfe Steel Kk 高加工性超高強度冷延鋼板およびその製造方法
JP2007138262A (ja) * 2005-11-21 2007-06-07 Jfe Steel Kk 機械特性ばらつきの小さい高強度冷延鋼板およびその製造方法
WO2008007785A1 (fr) * 2006-07-14 2008-01-17 Kabushiki Kaisha Kobe Seiko Sho Feuilles d'acier très résistantes et procédés de production de celles-ci
JP2009215572A (ja) * 2008-03-07 2009-09-24 Kobe Steel Ltd 降伏応力と伸びと伸びフランジ性に優れた高強度冷延鋼板
JP2009215571A (ja) * 2008-03-07 2009-09-24 Kobe Steel Ltd 伸びフランジ性に優れた高強度冷延鋼板

Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10822672B2 (en) 2015-07-13 2020-11-03 Nippon Steel Corporation Steel sheet, hot-dip galvanized steel sheet, galvanized steel sheet, and manufacturing methods therefor
WO2017009938A1 (fr) * 2015-07-13 2017-01-19 新日鐵住金株式会社 Tôle d'acier, tôle d'acier galvanisée par immersion à chaud, tôle d'acier galvanisée par immersion à chaud alliée et procédés de production associés
JPWO2017009938A1 (ja) * 2015-07-13 2018-03-29 新日鐵住金株式会社 鋼板、溶融亜鉛めっき鋼板、及び合金化溶融亜鉛めっき鋼板、並びにそれらの製造方法
JPWO2017009936A1 (ja) * 2015-07-13 2018-04-19 新日鐵住金株式会社 鋼板、溶融亜鉛めっき鋼板、及び合金化溶融亜鉛めっき鋼板、並びにそれらの製造方法
US10808291B2 (en) 2015-07-13 2020-10-20 Nippon Steel Corporation Steel sheet, hot-dip galvanized steel sheet, galvannealed steel sheet, and manufacturing methods therefor
WO2017009936A1 (fr) * 2015-07-13 2017-01-19 新日鐵住金株式会社 Tôle d'acier, tôle d'acier galvanisée par immersion à chaud, tôle d'acier galvanisée par immersion à chaud alliée et procédés de production associés
CN109563592A (zh) * 2016-08-30 2019-04-02 杰富意钢铁株式会社 薄钢板及其制造方法
CN109563592B (zh) * 2016-08-30 2021-02-19 杰富意钢铁株式会社 薄钢板及其制造方法
US11220722B2 (en) 2016-08-30 2022-01-11 Jfe Steel Corporation Steel sheet and method for manufacturing the same
WO2022070636A1 (fr) * 2020-09-30 2022-04-07 日本製鉄株式会社 Tôle d'acier et procédé pour fabriquer une tôle d'acier
CN115735012A (zh) * 2020-09-30 2023-03-03 日本制铁株式会社 钢板以及钢板的制造方法
JP7401826B2 (ja) 2020-09-30 2023-12-20 日本製鉄株式会社 鋼板、及び鋼板の製造方法
EP4223899A4 (fr) * 2020-09-30 2024-03-13 Nippon Steel Corp Tôle d'acier et procédé pour fabriquer une tôle d'acier

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