JP7410936B2 - 穴拡げ性が高い高強度冷延鋼板、高強度溶融亜鉛めっき鋼板、及びこれらの製造方法 - Google Patents
穴拡げ性が高い高強度冷延鋼板、高強度溶融亜鉛めっき鋼板、及びこれらの製造方法 Download PDFInfo
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- JP7410936B2 JP7410936B2 JP2021516770A JP2021516770A JP7410936B2 JP 7410936 B2 JP7410936 B2 JP 7410936B2 JP 2021516770 A JP2021516770 A JP 2021516770A JP 2021516770 A JP2021516770 A JP 2021516770A JP 7410936 B2 JP7410936 B2 JP 7410936B2
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- 239000010960 cold rolled steel Substances 0.000 title claims description 42
- 238000004519 manufacturing process Methods 0.000 title claims description 18
- 229910001335 Galvanized steel Inorganic materials 0.000 title claims description 17
- 239000008397 galvanized steel Substances 0.000 title claims description 17
- 238000001816 cooling Methods 0.000 claims description 55
- 229910000831 Steel Inorganic materials 0.000 claims description 54
- 239000010959 steel Substances 0.000 claims description 54
- 229910000734 martensite Inorganic materials 0.000 claims description 34
- 229910052710 silicon Inorganic materials 0.000 claims description 29
- 229910052782 aluminium Inorganic materials 0.000 claims description 27
- 229910052799 carbon Inorganic materials 0.000 claims description 25
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 23
- 229910001566 austenite Inorganic materials 0.000 claims description 21
- 239000011572 manganese Substances 0.000 claims description 19
- 238000000034 method Methods 0.000 claims description 19
- 238000000137 annealing Methods 0.000 claims description 18
- 229910001563 bainite Inorganic materials 0.000 claims description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 17
- 239000011651 chromium Substances 0.000 claims description 17
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 16
- 239000010955 niobium Substances 0.000 claims description 16
- 239000010936 titanium Substances 0.000 claims description 16
- 239000010949 copper Substances 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 15
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 13
- 239000010703 silicon Substances 0.000 claims description 13
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 12
- 238000003303 reheating Methods 0.000 claims description 12
- 238000005096 rolling process Methods 0.000 claims description 12
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 11
- 229910052796 boron Inorganic materials 0.000 claims description 11
- 229910001567 cementite Inorganic materials 0.000 claims description 10
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 10
- 229910052748 manganese Inorganic materials 0.000 claims description 10
- 229910052758 niobium Inorganic materials 0.000 claims description 10
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 9
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 9
- 238000005097 cold rolling Methods 0.000 claims description 9
- 229910052802 copper Inorganic materials 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims description 9
- 229910052759 nickel Inorganic materials 0.000 claims description 9
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 9
- 229910052719 titanium Inorganic materials 0.000 claims description 9
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 9
- 229910000859 α-Fe Inorganic materials 0.000 claims description 9
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 8
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 8
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 8
- 229910052804 chromium Inorganic materials 0.000 claims description 8
- 238000005098 hot rolling Methods 0.000 claims description 8
- 239000011733 molybdenum Substances 0.000 claims description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims description 8
- 239000011574 phosphorus Substances 0.000 claims description 8
- 230000009467 reduction Effects 0.000 claims description 8
- 230000000717 retained effect Effects 0.000 claims description 8
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 7
- 229910052717 sulfur Inorganic materials 0.000 claims description 7
- 239000011593 sulfur Substances 0.000 claims description 7
- 238000005275 alloying Methods 0.000 claims description 6
- 238000005246 galvanizing Methods 0.000 claims description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 5
- 238000004804 winding Methods 0.000 claims description 4
- 239000000463 material Substances 0.000 description 28
- 230000009466 transformation Effects 0.000 description 11
- 239000000203 mixture Substances 0.000 description 10
- 230000008569 process Effects 0.000 description 10
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 239000002436 steel type Substances 0.000 description 9
- 230000007423 decrease Effects 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 230000000171 quenching effect Effects 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 4
- 229910052720 vanadium Inorganic materials 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000001771 impaired effect Effects 0.000 description 3
- 230000001965 increasing effect Effects 0.000 description 3
- 229910001338 liquidmetal Inorganic materials 0.000 description 3
- 238000007747 plating Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 239000011701 zinc Substances 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- 229910000794 TRIP steel Inorganic materials 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000001939 inductive effect Effects 0.000 description 2
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- 239000007788 liquid Substances 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 229910052580 B4C Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- INAHAJYZKVIDIZ-UHFFFAOYSA-N boron carbide Chemical compound B12B3B4C32B41 INAHAJYZKVIDIZ-UHFFFAOYSA-N 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000008878 coupling Effects 0.000 description 1
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- 238000005520 cutting process Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000001887 electron backscatter diffraction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000000149 penetrating effect Effects 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000002829 reductive effect Effects 0.000 description 1
- 238000004626 scanning electron microscopy Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
- 230000003313 weakening effect Effects 0.000 description 1
Classifications
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
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- 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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
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- 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")
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- C21D6/00—Heat treatment of ferrous alloys
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/0236—Cold rolling
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- 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
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- 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
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- 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
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- 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
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- 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
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- C21D8/0463—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 following hot rolling
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- 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
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Description
[数式(1)][C]+([Si]+[Al])/5≦0.35%
(ここで、[C]、[Si]、[Al]は、それぞれC、Si、Alの重量%を意味する。)
[数式(1)][C]+([Si]+[Al])/5≦0.35%
(ここで、[C]、[Si]、[Al]は、それぞれC、Si、Alの重量%を意味する。)
炭素は、固溶強化及び析出強化によって鋼材の強度を支える基本的な元素である。炭素の量が0.17%未満であると、他の材質を満たしながら引張強度(TS)1180MPa級に相当する強度を得ることが難しい。これに対し、炭素の量が0.21%を超えると、溶接性が悪くなり、所望する穴拡げ性の値を得ることができなくなる。したがって、本発明における炭素の含有量は0.17~0.21%に制限することが好ましい。上記Cの下限は0.18%であることがより好ましく、上記Cの上限は0.20%であることがより好ましい。
ケイ素は、ベイナイト領域でセメンタイトの析出を阻害することにより、残留オーステナイト分率及び延伸率を高める作用をするTRIP(Transformation Induced Plasticity)鋼の核心元素である。ケイ素が0.3%未満になると、残留オーステナイトがほとんど残らないようになって延伸率が非常に低くなり、これに対し、ケイ素が0.8%を超えると、LME亀裂の形成による溶接部の物性悪化を防ぐことができなくなり、鋼材の表面の特性及びめっき性が悪くなる。したがって、本発明におけるケイ素の含有量は0.3~0.8%に制限することが好ましい。上記Siの下限は0.4%であることがより好ましく、上記Siの上限は0.6%であることがより好ましい。
本発明におけるマンガンの量は2.7~3.3%であってもよい。マンガンの含有量が2.7%未満の場合、強度を確保し難くなり、3.3%を超える場合、ベイナイト変態速度が遅くなって、多すぎるフレッシュマルテンサイトが形成され、高い穴拡げ性を得ることが難しくなる。また、マンガンの含有量が高いと、マルテンサイト形成の開始温度が低くなり、焼鈍水冷段階で初期マルテンサイト相を得るために必要な冷却完了温度が低すぎるようになる。したがって、本発明におけるマンガンの含有量は、2.7~3.3%に制限することが好ましい。上記Mnの下限は2.8%であることがより好ましく、上記Mnの上限は3.1%であることがより好ましい。
本発明におけるクロムの量は0.3~0.7%であってもよい。クロムの量が0.3%未満であると、目標とする引張強度を得ることが難しくなり、上限である0.7%を超えると、ベイナイトの変態速度が遅くなって高い穴拡げ性を得ることが難しくなる。したがって、本発明におけるクロムの含有量は、0.3~0.7%に制限することが好ましい。上記Crの下限は0.4%であることがより好ましく、上記Crの上限は0.6%であることがより好ましい。
本発明におけるアルミニウムの量は0.01~0.3%であってもよい。アルミニウムの添加量が0.01%未満であると、鋼材の脱酸が十分に行われず、清浄性を損なうようになる。これに対し、0.3%を超えて添加すると、鋼材の鋳造性を損なうようになる。したがって、本発明におけるアルミニウムの含有量は、0.01~0.3%に制限することが好ましい。上記Alの下限は0.03%であることがより好ましく、上記Alの上限は0.2%であることがより好ましい。
本発明では、鋼材の硬化能を高めるために0.01~0.03%のチタン及び0.001~0.003%のホウ素を添加してもよい。チタンの含有量が0.01%未満であると、ホウ素が窒素と結合するようになり、ホウ素の硬化能強化効果が消失し、0.03%を超えて含有されると、鋼材の鋳造性が悪くなる。一方、ホウ素含有量が0.001%未満であると、有効な硬化能強化効果を得ることができず、0.003%を超えて含有されると、ホウ素炭化物が形成されるおそれがあり、却って硬化能を損なうようになる。したがって、本発明におけるチタンの含有量は0.01~0.03%、ホウ素の含有量は0.001~0.003%に制限することが好ましい。上記Tiの下限は0.015%であることがより好ましく、上記Tiの上限は0.025%であることがより好ましい。上記Bの下限は0.015%であることがより好ましく、上記Bの上限は0.0025%であることがより好ましい。
リンは、鋼中に不純物として存在し、その含有量をできるだけ低く制御することが有利であるが、鋼材の強度を高めるために意図的に添加することもある。しかし、上記リンが過度に添加されると、鋼材の靭性が悪化するため、本発明ではこれを防止するために上限を0.04%に制限することが好ましい。上記Pの含有量は、0.01%以下であることがより好ましい。
硫黄は上記リンと同様に鋼中に不純物として存在し、その含有量をできるだけ低く制御することが有利である。また、硫黄は鋼材の延性及び衝撃特性を悪化させるため、その上限を0.02%以下に制限することが好ましい。上記Sの含有量は、0.003%以下であることがより好ましい。
本発明において窒素は不純物として鋼材に含まれており、その含有量をできるだけ低く制御することが有利である。上記窒素が多量に添加されると、窒化物を形成し過ぎて過度の組織微細化による圧延性の低下を招き、目標とする組織制御が不可能になり、衝撃特性などの最終品質も損なわれるようになるため、その上限を0.01%以下に制限することが好ましい。上記Nの含有量は、0.0060%以下であることがより好ましい。
銅、ニッケル、及びモリブデンは、鋼材の強度を高める元素であって、本発明では選択成分として含み、各元素の添加上限を0.1%に制限する。これら元素は、鋼材の強度と硬化能を高める元素であるが、過度に多い量を添加すると、目標とする強度レベルを超える可能性があり、高価の元素であるため、経済的な側面で添加上限を0.1%に制限することが好ましい。一方、上記の銅、ニッケル、及びモリブデンは、固溶強化のために作用するため、0.03%未満添加すると、固溶強化効果が僅かであるおそれがあることから、添加する場合にはその下限を0.03%以上に制限することができる。上記Cu、Ni及びMoのそれぞれの上限は0.06%であることがより好ましい。
ニオブ及びバナジウムは、析出硬化によって鋼材の降伏強度を高める元素であって、本発明では降伏強度を高めるために選択的に添加してもよい。但し、その含有量が多すぎると、延伸率が低くなり過ぎて、鋼材の脆性を誘発するおそれがあるため、本発明ではニオブ及びバナジウムの上限をそれぞれ0.03%及び0.01%以下に制限する。一方、ニオブ及びバナジウムは、析出硬化を起こすため、少量添加でも効果があるが、0.005%未満で添加すると、その効果が僅かであるおそれがあるため、添加する場合にはその下限を0.005%以上に制限することができる。上記Nb及びVの上限は、それぞれ0.02%、0.008%であることがより好ましい。
数式(1):[C]+([Si]+[Al])/5≦0.35%
(ここで、[C]、[Si]、[Al]は、それぞれC、Si、Alの重量%を意味する。)
まず、上述した合金組成を有し、数式(1)を満たすスラブを準備して上記スラブを1150℃~1250℃の温度まで加熱する。このとき、スラブ温度が1150℃未満であると、次の段階である熱間圧延の実行が不可能になり、これに対し、1250℃を超えると、スラブ温度を高めるために多くのエネルギーが必要以上にかかる。したがって、上記加熱温度は1150~1250℃の温度に制限することが好ましい。上記加熱温度の下限は1190℃であることがより好ましく、上記加熱温度の上限は1230℃であることがより好ましい。
上記加熱されたスラブを仕上げ圧延温度(FDT)が900℃~980℃になる条件で意図した目的に合う厚さまで熱間圧延する。上記仕上げ圧延温度(FDT)が900℃未満であると、圧延負荷が大きく、形状不良が増加して生産性が悪くなる。これに対し、上記仕上げ圧延温度が980℃を超えると、過度の高温作業による酸化物の増加により表面品質が悪くなる。したがって、上記仕上げ圧延温度が900~980℃である条件で熱間圧延することが好ましい。上記仕上げ圧延温度の下限は910℃であることがより好ましく、上記仕上げ圧延温度の上限は950℃であることがより好ましい。
上記熱間圧延された鋼板を10℃/s~100℃/sの平均冷却速度で巻取り温度まで冷却し、500~700℃の標準的な温度領域で巻取りを行う。巻取り後、熱延鋼板を30~60%の冷間圧下率で圧延して冷延鋼板を得る。上記平均冷却速度が10℃/s未満の場合には、熱間圧延の生産性が過度に低下する欠点があり、100℃/sを超える場合には、エッジ部の強度が上昇し、幅方向の材質ばらつきが大きくなるおそれがある。上記平均冷却速度の下限は20℃/sであることが好ましく、上記平均冷却速度の上限は80℃/sであることが好ましい。上記巻取り温度の下限は550℃であることが好ましく、上記巻取り温度の上限は650℃であることが好ましい。上記冷間圧下率が30%未満であると、目標とする厚さ精度を確保し難いだけでなく、鋼板の形状矯正が難しくなる。これに対し、冷間圧下率が60%を超えると、鋼板のエッジ(edge)部にクラックが発生する可能性が高くなり、冷間圧延の負荷が過度に大きくなる問題点が発生する。したがって、本発明では冷間圧延の段階における冷間圧下率を30~60%に制限することが好ましい。上記冷間圧下率の下限は35%であることがより好ましく、上記冷間圧下率の上限は50%であることがより好ましい。
本発明では、上記冷間圧延された鋼板を(Ae3+30℃~Ae3+80℃)の温度範囲で連続焼鈍を実施する。より好ましくは、830~880℃の温度範囲で連続焼鈍を行うことができる。また、上記連続焼鈍は、連続合金化溶融めっき連続炉で行うことができる。連続焼鈍段階は、オーステナイト単相域まで加熱して100%に近いオーステナイトを形成し、この後の相変態に利用するためである。仮に、上記連続焼鈍温度がAe3+30℃未満または830℃未満であると、十分なオーステナイト変態が行われず、焼鈍後の目的とするマルテンサイト及びベイナイト分率を確保することができない。これに対し、上記連続焼鈍温度がAe3+80℃超過または880℃超過であると、生産性が低下し、粗大なオーステナイトが形成されて材質が劣化する。また、焼鈍中に酸化物が成長してめっき材の表面品質を確保し難い。上記Ae3は、当該技術分野で標準的に利用されるCALPHAD(Computer Coupling of Phase Diagrams and Thermochemistry)法を活用した熱力学ソフトウェアを用いて計算することができる。
上記連続焼鈍された鋼板を560~700℃の温度範囲まで10℃/s以下の平均冷却速度で1次冷却し、270~330℃の温度範囲まで10℃/s以上の平均冷却速度で2次冷却してマルテンサイトを導入する。ここで、上記1次冷却終了温度は、1次冷却で適用しない急冷設備がさらに適用されて急冷が開始される時点と定義することができる。冷却工程を1次及び2次冷却に分けて段階的に実行すると、徐冷段階で鋼板の温度分布を均一にして、最終的な温度及び材質ばらつきを減少させることができ、必要な相構成を得る上でも有利である。
上記冷却された鋼板を再び、380~460℃の温度範囲まで5℃/s以下の昇温速度で再加熱し、以前の段階で得られたマルテンサイトを焼戻し、ベイナイト変態誘導及びベイナイトに隣接している未変態オーステナイトに炭素を濃縮させる。このとき、再加熱温度を380~460℃に制御することが重要であり、380℃より低いか、460℃を超えると、ベイナイトの相変態量が少なく、最終冷却過程で多すぎるフレッシュマルテンサイトが形成されて延伸率及び穴拡げ性を大きく損なうようになる。上記再加熱温度の下限は440℃であることがより好ましく、上記再加熱温度の上限は440℃であることがより好ましい。上記再加熱時の昇温速度が5℃/sを超える場合には、2次冷却時に形成されたマルテンサイト相の焼戻しが不足となり、昇温中にベイナイト相変態が十分に得られないおそれがある。
下記表1の合金組成を有するスラブを準備した後、表2及び3に記載された条件で鋼スラブ加熱-熱間圧延-冷却-巻取り-冷間圧延-連続焼鈍-1次及び2次冷却-再加熱工程を経て冷延鋼板を製造した。一方、下記表2及び3に記載されたFDTは仕上げ圧延温度、CTは熱延巻取り温度、SSは連続焼鈍温度、SCSは1次冷却終了温度、RCSは2次冷却終了温度、RHSは再加熱温度を意味する。
Claims (8)
- 重量%で、炭素(C):0.17~0.21%、ケイ素(Si):0.3~0.8%、マンガン(Mn):2.7~3.3%、クロム(Cr):0.3~0.7%、アルミニウム(Al):0.01~0.3%、チタン(Ti):0.01~0.03%、ホウ素(B):0.001~0.003%、リン(P):0.04%以下、硫黄(S):0.02%以下、窒素(N):0.01%以下、銅(Cu):0.1%以下、ニッケル(Ni):0.1%以下、モリブデン(Mo):0.1%以下、ニオブ(Nb):0.03%以下、バナジウム(V):0.01%以下、残部鉄(Fe)及びその他の不可避不純物からなり、
前記炭素(C)、ケイ素(Si)及びアルミニウム(Al)の含有量は、下記数式(1)を満たし、
微細組織が面積分率で残留オーステナイト3~7%、フレッシュマルテンサイト5~15%、フェライト5%以下(0%を含む)、残部はベイナイトまたは焼戻しマルテンサイトを含み、
前記ベイナイトのラス(lath)の間、または焼戻しマルテンサイト相のラス、もしくは結晶粒の境界に第2相としてセメンタイト相が、体積分率で1~3%析出して分布する高強度冷延鋼板。
[数式(1)][C]+([Si]+[Al])/5≦0.35%
(ここで、[C]、[Si]、[Al]は、それぞれC、Si、Alの重量%を意味する。) - 1180MPa以上の引張強度、0.65~0.85の降伏比、25%以上の穴拡げ性(HER)、5~13%の延伸率を有する、請求項1に記載の高強度冷延鋼板。
- 請求項1に記載の高強度冷延鋼板の表面に溶融亜鉛めっき層をさらに含む、高強度溶融亜鉛めっき鋼板。
- 請求項1に記載の高強度冷延鋼板の表面に合金化溶融亜鉛めっき層をさらに含む、高強度溶融亜鉛めっき鋼板。
- 請求項1に記載の冷延鋼板の製造方法であって、
重量%で、炭素(C):0.17~0.21%、ケイ素(Si):0.3~0.8%、マンガン(Mn):2.7~3.3%、クロム(Cr):0.3~0.7%、アルミニウム(Al):0.01~0.3%、チタン(Ti):0.01~0.03%、ホウ素(B):0.001~0.003%、リン(P):0.04%以下、硫黄(S):0.02%以下、窒素(N):0.01%以下、銅(Cu):0.1%以下、ニッケル(Ni):0.1%以下、モリブデン(Mo):0.1%以下、ニオブ(Nb):0.03%以下、バナジウム(V):0.01%以下、残部鉄(Fe)及びその他の不可避不純物からなり、前記炭素(C)、前記ケイ素(Si)及び前記アルミニウム(Al)の含有量が下記数式(1)を満たすスラブを準備する段階;
前記スラブを1150~1250℃の温度範囲まで加熱する段階;
加熱された前記スラブを900~980℃の仕上げ圧延温度(FDT)範囲で仕上げ熱間圧延する段階;
前記仕上げ熱間圧延後、10℃/sec~100℃/secの平均冷却速度で冷却する段階;
500~700℃の温度範囲で巻取る段階;
30~60%の冷間圧下率で冷間圧延して冷延鋼板を得る段階;
前記冷延鋼板を(Ae3+30℃~Ae3+80℃)の温度範囲で連続焼鈍する段階;
連続焼鈍した鋼板を560~700℃の温度範囲まで10℃/s以下の平均冷却速度で1次冷却し、270~330℃の温度範囲まで10℃/s以上の平均冷却速度で2次冷却する段階;及び
冷却された鋼板を380~460℃の温度範囲まで5℃/s以下の昇温速度で再加熱する段階;を含む高強度冷延鋼板の製造方法。
[数式(1)][C]+([Si]+[Al])/5≦0.35%
(ここで、[C]、[Si]、[Al]は、それぞれC、Si、Alの重量%を意味する。) - 前記連続焼鈍する段階は、830~880℃の温度範囲で行われる、請求項5に記載の高強度冷延鋼板の製造方法。
- 請求項5に記載の再加熱された冷延鋼板に対し、430~490℃の温度範囲で溶融亜鉛めっき処理する段階をさらに含む、高強度溶融亜鉛めっき鋼板の製造方法。
- 前記溶融亜鉛めっき処理する段階の後、合金化熱処理を行った後に常温まで冷却を実施する、請求項7に記載の高強度溶融亜鉛めっき鋼板の製造方法。
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- 2019-09-27 CN CN201980063783.9A patent/CN112752862B/zh active Active
- 2019-09-27 JP JP2021516770A patent/JP7410936B2/ja active Active
- 2019-09-27 US US17/280,524 patent/US11753693B2/en active Active
- 2019-09-27 WO PCT/KR2019/012563 patent/WO2020067752A1/ko unknown
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US11753693B2 (en) | 2023-09-12 |
JP2022501510A (ja) | 2022-01-06 |
WO2020067752A1 (ko) | 2020-04-02 |
US20220033926A1 (en) | 2022-02-03 |
CN112752862B (zh) | 2022-05-06 |
CN112752862A (zh) | 2021-05-04 |
US20230340633A1 (en) | 2023-10-26 |
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