WO2013084458A1 - 冷間圧延の素材用の熱延鋼板およびその製造方法 - Google Patents

冷間圧延の素材用の熱延鋼板およびその製造方法 Download PDF

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Publication number
WO2013084458A1
WO2013084458A1 PCT/JP2012/007721 JP2012007721W WO2013084458A1 WO 2013084458 A1 WO2013084458 A1 WO 2013084458A1 JP 2012007721 W JP2012007721 W JP 2012007721W WO 2013084458 A1 WO2013084458 A1 WO 2013084458A1
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WO
WIPO (PCT)
Prior art keywords
steel sheet
rolled steel
less
hot
cold
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2012/007721
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English (en)
French (fr)
Japanese (ja)
Inventor
藤田　耕一郎
重宏 ▲高▼城
太郎 木津
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.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Priority to KR1020147016617A priority Critical patent/KR101630548B1/ko
Priority to CN201280060631.1A priority patent/CN103998637B/zh
Priority to IN1067KON2014 priority patent/IN2014KN01067A/en
Priority to JP2013548082A priority patent/JP5534112B2/ja
Publication of WO2013084458A1 publication Critical patent/WO2013084458A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • 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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold 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
    • C22C38/002—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

Definitions

  • Patent Document 1 discloses a technique related to a hot-rolled steel sheet in which the amount of C in the steel is extremely low to 0.010 mass% or less.
  • Patent Document 2 proposes a technique related to a hot-rolled steel sheet in which the N content in steel is reduced to 0.0020% by mass or less.
  • Patent Document 3 describes hot rolling [so-called ⁇ (ferrite) rolling at a finishing temperature of 700 ° C. or more and an Ar 3 transformation point or less with a C content of 0.01 to 0.10 mass% and an N content of 0.010 mass% or less in steel. To obtain a hot-rolled steel sheet having coarse crystal grains has been proposed.
  • the present invention has been made on the basis of the above findings, and in mass%, C: 0.016-0.07%, Si: 0.1% or less, Mn: 0.05-0.5%, P: 0.03% or less, S: 0.03%
  • the chemical composition comprising Sol.Al: 0.02 to 0.1%, N: 0.005% or less, B: 0.0003 to 0.0030%, Ti: 0.004% or less, Nb: 0.003% or less, with the balance being Fe and inevitable impurities
  • the present invention provides a hot-rolled steel sheet for cold rolling material having an average grain size of 13 ⁇ m or less and an aging index AI of 10 MPa or less.
  • Si 0.1% or less When the Si content exceeds 0.1%, the strength increases and the cold rolling load increases. Therefore, the Si content is 0.1% or less.
  • the lower limit of the Si amount does not need to be specified in particular, but excessive reduction causes an increase in cost, so 0.001% is desirable.
  • Mn 0.05-0.5% Mn fixes S as MnS and has the function of improving hot ductility, so the amount needs to be 0.05% or more. However, if the Mn content exceeds 0.5%, the steel is hardened and the cold rolling load is increased. Therefore, the Mn content is 0.05 to 0.5%.
  • Sol.Al:0.02-0.1% Al has the effect of reducing the cold rolling load by reducing the solid solution N by fixing N not fixed by B as AlN. In order to obtain such an effect, the amount of Sol.Al needs to be 0.02% or more. However, if the amount exceeds 0.1%, the manufacturing cost increases. Therefore, the amount of Sol.Al is 0.02 to 0.1%.
  • N 0.005% or less N is likely to remain in the hot-rolled steel sheet in a solid solution state and increases the cold rolling load, so the amount needs to be 0.005% or less.
  • the lower limit need not be specified, but excessive reduction leads to an increase in cost, so 0.001% is desirable and 0.002% is more desirable.
  • the balance is Fe and inevitable impurities.
  • the finishing temperature exceeds (Ar 3 transformation point + 49 ° C) or the rolling reduction (also called rolling rate) of the final pass is less than 20%, it is coarsened by recrystallization in the ⁇ (austenite) region after the final pass.
  • the finishing temperature is in the temperature range of Ar 3 transformation point to (Ar 3 transformation point + 49 ° C.), and the rolling reduction in the final pass is 20% or more.
  • the characteristics of the hot-rolled steel sheet of the present invention will not change even if it is pickled or remains black (non-pickled). Even if temper rolling and leveling are performed for the purpose of improving pickling performance and shape correction, or even if temper rolling and leveling are not performed, the characteristics are not changed.
  • the hot-rolled steel sheet of the present invention is cold-rolled in order to use a cold-rolled steel sheet or a surface-treated steel sheet. Since the hot-rolled steel sheet of the present invention has good cold rolling properties, the cold rolling reduction ratio of the cold rolling is as large as about 95% to produce a thin cold-rolled steel sheet with a thickness of 0.5 mm or less. Can be rolled without any problems. In general, the reduction ratio of cold rolling of a thin cold-rolled steel sheet is 60% or more.
  • the hot-rolled steel sheet of the present invention has good cold-rollability and exhibits recrystallization behavior similar to the case where B is not added as described above even when recrystallization annealing is performed. Accordingly, not only cold-rolled steel sheets that have been cold-rolled or surface-treated steel sheets that have been surface-treated to cold-rolled steel sheets that have been cold-rolled, but also cold-rolled steel sheets that are manufactured by annealing after cold rolling or such cold-rolled steel sheets. It can preferably be used as a hot-rolled steel sheet for a cold-rolled material for a surface-treated steel sheet obtained by subjecting a rolled steel sheet to a surface treatment.
  • Ar 3 transformation point (°C) 901-325 ⁇ [C] + 33 ⁇ [Si] -92 ⁇ [Mn] + 287 ⁇ [P]
  • [M] represents the content (mass%) of the element M.
  • the obtained hot-rolled steel sheet was pickled, subjected to temper rolling with an elongation of 1%, and the average crystal grain size and AI were measured by the above methods.
  • the hot-rolled steel sheet after pickling is cold-rolled at a reduction rate of 80% to produce a cold-rolled steel sheet (sheet thickness: 0.36 mm), and the TS of the cold-rolled steel sheet as described above is used. Measurements were made.
  • the plate thickness at the center in the width direction of the cold-rolled steel plate was measured at 30 points at regular intervals from the full length of the steel plate to obtain the standard deviation.
  • the hot-rolled steel sheets D, I, N, and O which are examples of the present invention, are soft as cold-rolled TS is 725 MPa or less, can reduce the cold-rolling load, and the recrystallization temperature is 550 ° C. It can be seen that there is no need for annealing, and cold-rolled steel sheets and surface-treated cold-rolled steel sheets can be manufactured at low cost.
  • the hot-rolled steel sheets A, E, F, G, and H which are comparative examples, have a large average crystal grain size, and do not sufficiently precipitate cementite, resulting in high AI, and the hot-rolled steel sheets B, C, and K are Because of the presence of solute N, the AI becomes high and the cold-rolled TS exceeds 725 MPa and is hard, and the cold rolling load cannot be reduced.
  • Hot-rolled steel sheets J, L, and M with Ti and Nb contents exceeding 0.004% have a recrystallization temperature of 650 ° C or higher and require high-temperature annealing, increasing the manufacturing cost of cold-rolled steel sheets and surface-treated cold-rolled steel sheets. Invite.
  • the gauge fluctuation of the steel sheet after cold rolling due to the material variation of the hot-rolled sheet is large, and the desired steel sheet quality cannot be obtained.

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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)
PCT/JP2012/007721 2011-12-08 2012-12-03 冷間圧延の素材用の熱延鋼板およびその製造方法 Ceased WO2013084458A1 (ja)

Priority Applications (4)

Application Number Priority Date Filing Date Title
KR1020147016617A KR101630548B1 (ko) 2011-12-08 2012-12-03 냉간 압연의 소재용 열연 강판 및 그 제조 방법
CN201280060631.1A CN103998637B (zh) 2011-12-08 2012-12-03 用作冷轧原材料的热轧钢板及其制造方法
IN1067KON2014 IN2014KN01067A (enExample) 2011-12-08 2012-12-03
JP2013548082A JP5534112B2 (ja) 2011-12-08 2012-12-03 冷間圧延の素材用の熱延鋼板およびその製造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2011268492 2011-12-08
JP2011-268492 2011-12-08

Publications (1)

Publication Number Publication Date
WO2013084458A1 true WO2013084458A1 (ja) 2013-06-13

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JP (1) JP5534112B2 (enExample)
KR (1) KR101630548B1 (enExample)
CN (1) CN103998637B (enExample)
IN (1) IN2014KN01067A (enExample)
WO (1) WO2013084458A1 (enExample)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2015111378A1 (ja) * 2014-01-24 2015-07-30 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
WO2015146186A1 (ja) * 2014-03-28 2015-10-01 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20260021327A (ko) 2024-08-06 2026-02-13 한국재료연구원 고체냉각 소재 및 이의 제조방법

Citations (6)

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Publication number Priority date Publication date Assignee Title
JPS5848635A (ja) * 1981-09-18 1983-03-22 Nippon Steel Corp 加工性のすぐれた冷延鋼板の製造方法
JP2001335841A (ja) * 2000-05-31 2001-12-04 Sumitomo Metal Ind Ltd 溶融亜鉛めっき鋼板の製造方法
JP2002003951A (ja) * 2000-06-26 2002-01-09 Nkk Corp 異方性の小さい冷延鋼板の製造方法
JP2003293083A (ja) * 2002-04-01 2003-10-15 Sumitomo Metal Ind Ltd 熱延鋼板並びに熱延鋼板及び冷延鋼板の製造方法
JP2010270384A (ja) * 2009-05-25 2010-12-02 Jfe Steel Corp 熱延鋼板の製造方法
JP2010270383A (ja) * 2009-05-25 2010-12-02 Jfe Steel Corp 成形性に優れた熱延鋼板およびその製造方法

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JPS6330969A (ja) 1986-07-25 1988-02-09 Dainippon Printing Co Ltd カタログ編集システム
JP2879575B2 (ja) 1989-08-22 1999-04-05 日新製鋼株式会社 高い延性と深絞り性とを兼備した極薄冷延鋼板の製造法
JP4276482B2 (ja) * 2003-06-26 2009-06-10 新日本製鐵株式会社 極限変形能と形状凍結性に優れた高強度熱延鋼板とその製造方法
JP2005200739A (ja) * 2004-01-19 2005-07-28 Nippon Steel Corp 化成処理性に優れた熱延鋼板およびその製造方法
JP5396793B2 (ja) * 2008-09-25 2014-01-22 Ｊｆｅスチール株式会社 建材用極薄冷延鋼板およびその製造方法
CN101775540A (zh) * 2009-01-13 2010-07-14 宝山钢铁股份有限公司 加工性优良的耐时效钢板及其制造方法
JP5862254B2 (ja) * 2011-12-08 2016-02-16 Ｊｆｅスチール株式会社 冷間圧延の素材用の熱延鋼板およびその製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5848635A (ja) * 1981-09-18 1983-03-22 Nippon Steel Corp 加工性のすぐれた冷延鋼板の製造方法
JP2001335841A (ja) * 2000-05-31 2001-12-04 Sumitomo Metal Ind Ltd 溶融亜鉛めっき鋼板の製造方法
JP2002003951A (ja) * 2000-06-26 2002-01-09 Nkk Corp 異方性の小さい冷延鋼板の製造方法
JP2003293083A (ja) * 2002-04-01 2003-10-15 Sumitomo Metal Ind Ltd 熱延鋼板並びに熱延鋼板及び冷延鋼板の製造方法
JP2010270384A (ja) * 2009-05-25 2010-12-02 Jfe Steel Corp 熱延鋼板の製造方法
JP2010270383A (ja) * 2009-05-25 2010-12-02 Jfe Steel Corp 成形性に優れた熱延鋼板およびその製造方法

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2015111378A1 (ja) * 2014-01-24 2015-07-30 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
WO2015146186A1 (ja) * 2014-03-28 2015-10-01 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
JP2015190027A (ja) * 2014-03-28 2015-11-02 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
CN106103780A (zh) * 2014-03-28 2016-11-09 杰富意钢铁株式会社 热轧钢板及其制造方法
CN106103780B (zh) * 2014-03-28 2018-01-26 杰富意钢铁株式会社 热轧钢板及其制造方法
KR101920981B1 (ko) * 2014-03-28 2018-11-21 제이에프이 스틸 가부시키가이샤 열연 강판 및 그 제조 방법

Also Published As

Publication number Publication date
CN103998637A (zh) 2014-08-20
CN103998637B (zh) 2016-08-10
JPWO2013084458A1 (ja) 2015-04-27
KR101630548B1 (ko) 2016-06-14
JP5534112B2 (ja) 2014-06-25
IN2014KN01067A (enExample) 2015-10-09
KR20140095097A (ko) 2014-07-31

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