WO2015099223A1 - 강도와 연성이 우수한 경량강판 및 그 제조방법 - Google Patents
강도와 연성이 우수한 경량강판 및 그 제조방법 Download PDFInfo
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- WO2015099223A1 WO2015099223A1 PCT/KR2013/012168 KR2013012168W WO2015099223A1 WO 2015099223 A1 WO2015099223 A1 WO 2015099223A1 KR 2013012168 W KR2013012168 W KR 2013012168W WO 2015099223 A1 WO2015099223 A1 WO 2015099223A1
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- steel sheet
- ductility
- less
- strength
- austenite
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 100
- 239000010959 steel Substances 0.000 title claims abstract description 100
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 238000000034 method Methods 0.000 title claims abstract description 18
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 54
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 16
- 238000010438 heat treatment Methods 0.000 claims abstract description 12
- 229910000859 α-Fe Inorganic materials 0.000 claims description 25
- 238000005098 hot rolling Methods 0.000 claims description 20
- 229910052782 aluminium Inorganic materials 0.000 claims description 15
- 238000005097 cold rolling Methods 0.000 claims description 9
- 238000007747 plating Methods 0.000 claims description 9
- 229910052787 antimony Inorganic materials 0.000 claims description 7
- 229910052796 boron Inorganic materials 0.000 claims description 7
- 239000010960 cold rolled steel Substances 0.000 claims description 7
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- 238000001953 recrystallisation Methods 0.000 claims description 7
- 238000001816 cooling Methods 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- 230000000717 retained effect Effects 0.000 claims description 6
- 239000011159 matrix material Substances 0.000 claims description 5
- 230000009467 reduction Effects 0.000 claims description 5
- 238000003303 reheating Methods 0.000 claims description 5
- 229910052725 zinc Inorganic materials 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 4
- 229910052717 sulfur Inorganic materials 0.000 claims description 4
- 238000004804 winding Methods 0.000 claims description 3
- 229910018134 Al-Mg Inorganic materials 0.000 claims description 2
- 229910018467 Al—Mg Inorganic materials 0.000 claims description 2
- 229910018464 Al—Mg—Si Inorganic materials 0.000 claims description 2
- 229910009369 Zn Mg Inorganic materials 0.000 claims description 2
- 229910007570 Zn-Al Inorganic materials 0.000 claims description 2
- 229910007573 Zn-Mg Inorganic materials 0.000 claims description 2
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 abstract description 32
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 30
- 238000005261 decarburization Methods 0.000 abstract description 30
- 239000011572 manganese Substances 0.000 abstract description 17
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 abstract description 10
- 230000002401 inhibitory effect Effects 0.000 abstract description 3
- 230000000052 comparative effect Effects 0.000 description 18
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 15
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 10
- 239000010949 copper Substances 0.000 description 8
- 230000002829 reductive effect Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 230000005484 gravity Effects 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 6
- 238000005204 segregation Methods 0.000 description 6
- 238000000137 annealing Methods 0.000 description 5
- 238000009792 diffusion process Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- 230000008569 process Effects 0.000 description 4
- 239000011701 zinc Substances 0.000 description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 229910052749 magnesium Inorganic materials 0.000 description 3
- 239000011777 magnesium Substances 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 229910001335 Galvanized steel Inorganic materials 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 2
- 230000002159 abnormal effect Effects 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000005262 decarbonization Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- -1 ferrous metals Chemical class 0.000 description 2
- 239000008397 galvanized steel Substances 0.000 description 2
- 230000008595 infiltration Effects 0.000 description 2
- 238000001764 infiltration Methods 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 230000007246 mechanism Effects 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- DHKVCYCWBUNNQH-UHFFFAOYSA-N 2-[5-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-1,3,4-oxadiazol-2-yl]-1-(1,4,5,7-tetrahydropyrazolo[3,4-c]pyridin-6-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C1=NN=C(O1)CC(=O)N1CC2=C(CC1)C=NN2 DHKVCYCWBUNNQH-UHFFFAOYSA-N 0.000 description 1
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910015372 FeAl Inorganic materials 0.000 description 1
- 229910001035 Soft ferrite Inorganic materials 0.000 description 1
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000005324 grain boundary diffusion Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000003562 lightweight material Substances 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 239000010731 rolling oil Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Images
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- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous 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
- C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
- C21D3/02—Extraction of non-metals
- C21D3/04—Decarburising
-
- 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
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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
- 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
- C21D8/0236—Cold rolling
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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
- 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
- C21D8/0263—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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- 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
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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
- 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
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
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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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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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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
- 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
Definitions
- the present invention relates to a steel sheet used for automobile structural members, inner and outer plates, and more particularly, to a light steel sheet having excellent strength and ductility.
- the ferritic steels contain 0.8 to 1.2 wt% of carbon, and include 10 to 30 wt% of manganese and 8 to 12 wt% of aluminum (Patent Document 1), 0.2 wt% or less of carbon, and 2.5 to 10 wt%.
- Aluminum was added, and the stiffness was secured through controlling the precipitates and the texture of the structure, but the ductility was secured to some extent, but the tensile strength was low at the level of 400 MPa, and the elongation was only 25%.
- Duplex lightweight steel sheet which has no leasing, and has excellent strength and ductility by generating transformation induced plasticity and controlling ferrite texture, including a large amount of retained austenite. It became (patent document 2).
- Patent Document 1 Japanese Unexamined Patent Publication No. 2006-176843
- Patent Document 2 Japanese Unexamined Patent Publication No. 2009-287114
- One aspect of the present invention is to suppress the decarburization generated during the heat treatment process for the steel sheet containing austenite, thereby preventing the loss of austenite by decarburization, ensuring high strength and ductility even if a small amount of carbon and manganese are added It is to provide a lightweight steel sheet and a method of manufacturing the same.
- the present invention includes, by weight, C: 0.1 to 1.2%, Mn: 2 to 10%, Al: 3 to 10%, P: 0.1% or less, S: 0.01% or less, Ni: 5.0% or less, Cu : 5.0% or less, Sb: 0.01% to 0.05% and B: 0.01% or less selected from the group consisting of, the remainder is composed of Fe and inevitable impurities, the value of the following B * satisfies 2-10 It provides a lightweight steel sheet with excellent strength and ductility.
- the present invention comprises the steps of reheating the steel slab satisfying the composition and B * at 1000 ⁇ 1200 °C;
- It provides a method of manufacturing a lightweight steel sheet having excellent strength and ductility comprising the step of cold rolling the hot rolled steel sheet at a cold reduction rate of 40% or more.
- decarburization of a lightweight steel sheet having an ideal structure containing austenite is effectively suppressed to obtain sufficient retained austenite even if a small amount of alloying element is added, and the retained austenite and carbide are dispersed in the ferrite matrix.
- Tensile strength with less material anisotropy is 700MPa or more and elongation is 30% or more, so the strength and ductility are excellent, as well as the hot rolled steel sheet having excellent formability, as well as cold rolled steel plate and plated steel sheet, thereby providing a remarkable effect on the weight reduction of automobile bodies.
- Figure 1 is a schematic diagram showing the decarburization mechanism of the Duplex steel.
- Figure 2 is a tissue photograph and carbon concentration distribution graph after maintaining 30 minutes at 700 °C of Comparative Example 4.
- Figure 4 is a photograph showing the change in the structure according to the cold rolling before the invention example 4.
- the decarburization mechanism of the austenite and ferrite Duplex tissue steels is shown schematically in FIG. 1.
- carbon reacts with oxygen on the surface of the ferrite in a high temperature oxidizing atmosphere to form CO 2 or CO.
- the ferrite on the steel surface has a lower carbon than the equilibrium concentration, and the carbon is diffused to the surface by the concentration gradient so that decarburization is continuously performed.
- the gradient of carbon concentration is not large, decarburization does not occur much.
- austenite and ferrite are in contact, a large amount of equilibrium solid solution carbon exists in austenite, and a very low amount of equilibrium solid solution carbon exists in ferrite, so the concentration gradient becomes very large. Accordingly, since a sufficient amount of carbon is supplied from austenite and decarburization is continuously performed, austenite deprived of carbon in the ferrite has a low carbon content and is converted into ferrite, thereby causing a problem of reducing austenite, which is advantageous for workability. .
- the inventors of the present invention recognize that carbon diffusion is actively carried out through grain boundaries, and as a method of suppressing decarburization, 1) adding grain boundary segregation elements to lower the grain diffusion rate of carbon, and 2) using strong oxide elements.
- the formation of oxides at grain boundaries led to a method of preventing infiltration and diffusion of carbon through grain boundaries.
- the present invention through the method of forming the grain boundary and the oxide in the grain boundary, it is possible to effectively prevent the decarburization without deterioration of mechanical properties, through which there is no loss of austenite, the strength and ductility of a small amount of carbon and manganese It is possible to manufacture excellent low specific gravity light steel sheet.
- Light weight steel sheet of the present invention by weight percent, C: 0.1 ⁇ 1.2%, Mn: 2 ⁇ 10%, Al: 3 ⁇ 10%, P: 0.1% or less, S: 0.01% or less, Ni: 5.0% Or less, Cu: 5.0% or less, Sb: 0.01% to 0.05% and B: 0.01% or less selected from the group consisting of, the remainder is made of Fe and unavoidable impurities, the value of the following B * is 2 ⁇ Meets 10
- composition of the present invention will be described in detail (% by weight).
- Carbon in the steel not only stabilizes austenite, but also strengthens dispersion by cementite.
- the columnar tablets formed during continuous casting have fast recrystallization to form coarse structures during hot rolling, and thus, a carbon content of a certain amount or more is required to form high temperature carbide to refine the structure and increase strength.
- the lower limit thereof is preferably 0.1%.
- Manganese promotes high temperature precipitation of carbides by coexisting with carbon, thereby suppressing hot brittleness by suppressing carbides at grain boundaries, and finally contributing to the improvement of strength of the steel sheet.
- manganese lowers the specific gravity of steel because it increases the lattice constant of steel and lowers its density. Therefore, it is preferable to make the lower limit of manganese 2%.
- the upper limit is preferably set to 10% because manganese brings excessive band structure in the center segregation and hot rolled plate and lowers the ductility.
- Aluminum is the most important element together with C and Mn in the present invention.
- the addition of aluminum reduces the specific gravity of the steel. For this purpose, it is preferable to add 3% or more. It is preferable to add a large amount of aluminum in order to reduce specific gravity.
- an intermetallic compound such as kappa carbide, FeAl, Fe 3 Al increases and the ductility of the steel is lowered, so the upper limit is preferably 10%.
- the composition phase contains austenite 5 area% or more at a high temperature (for example, about 650 to 1250 ° C). If the austenite phase is less than 5 area%, it is impossible to have an abnormal structure (Duplex) at room temperature after steel sheet annealing, and thus, excellent strength and ductility of 700 MPa or more and elongation of 30% or more cannot be obtained.
- a high temperature for example, about 650 to 1250 ° C.
- At least one member selected from the group consisting of Ni: 5.0% or less, Cu: 5.0% or less, Sb: 0.01 to 0.05%, and B: 0.01% or less is used. Include.
- Ni nickel segregates in the ferrite grain boundary and plays a role of preventing carbon diffusion as well as suppressing decarburization.
- the stability of austenite is increased to increase strength and ductility.
- the manufacturing cost of steel increases, It is preferable to make the upper limit into 5% or less.
- Cu copper
- Cu is also a high solubility element in austenite, and forms a molten film on the surface during slab reheating in the hot rolling process, thereby suppressing oxygen infiltration and carbon decarburization.
- the Cu content is too high, fine cracks are generated on the surface of the steel due to grain boundary erosion by molten Cu, causing surface defects such as scrap and sliver on the hot-rolled sheet. It is preferable to set it as%.
- Sb antimony
- Sb is a grain boundary segregation element similar to Ni, but since it has a stronger tendency of grain boundary segregation than Ni, a small amount of 0.01% or more may be added.
- Sb in addition to grain boundary segregation, Sb newly forms a grain boundary oxide having ductility at a high temperature of Mn 2 Sb 2 O 7 , and these oxides newly prevent the penetration of oxygen and the diffusion of carbon by grain boundary diffusion.
- the upper limit is preferably 0.05%.
- B boron
- Sb boron
- the tendency to segregate in the austenite grain boundary is strong, so the decarburization inhibitory effect is not as high as that of Sb.
- oxides such as B 2 O 3 on the surface
- the upper limit thereof is preferably 0.01%.
- the remainder contains Fe and unavoidable impurities.
- the content of Ni, Cu, Sb, and B is preferably a value satisfying 2 to 10 defined by the following B *.
- the B * is to adjust the content of the component in order to take into account the mechanical properties and the economics of the alloy required in the present invention, and to ensure the optimum decarburization effect.
- Ni has a problem in that the steelmaking cost rises when a large amount is added, and other elements have a problem that may cause surface defects and room temperature cracking. Therefore, in consideration of this, it is important to optimize the component elements.
- the B * value is 2 or more, the effect of suppressing decarburization is realized, but if it exceeds 10, there is a problem in that ductility decreases due to an increase in alloy cost and an increase in grain boundary oxide, so that the value does not exceed 10. desirable.
- the lightweight steel sheet of the present invention preferably contains residual austenite in the ferrite matrix.
- the residual austenite is preferably 10 to 50% by area fraction.
- Light weight steel sheet of the present invention can secure sufficient residual austenite even if the addition of a small amount of alloying elements than the existing, can provide a steel sheet excellent in strength and ductility of tensile strength less than 700MPa, elongation of 30% or more less material anisotropy .
- the steel sheet includes a cold rolled steel sheet and a plated steel sheet.
- a steel ingot or slab (hereinafter referred to as slab) that satisfies the composition and the value of B * is prepared, and the slab is reheated to 1000 to 1200 ° C.
- the reheating temperature is preferably set to 1000 ⁇ 1200 °C so as to ensure the normal hot rolling temperature.
- the finish rolling temperature is a temperature having a Duplex structure at a high temperature, the rolling can be made well by the ferrite excellent in ductility, and the lower the finishing rolling temperature increases the rolling load, it is preferably performed at 700 °C or more Do.
- the winding is carried out by a conventional method to produce a hot rolled steel sheet.
- the steel slab preferably contains 5% or more of austenite structure as an area fraction. Including 5% or more of the austenite structure does not produce sufficient carbide at the temperature at which hot rolling is performed,
- the decarburized layer is preferably 10 ⁇ m or less. After the surface of the hot-rolled steel sheet was ground to remove the oxide layer, and then maintained at 700 ° C. for 30 minutes in an air atmosphere, when the decarburized layer was evaluated, when the decarburized layer was 10 ⁇ m or less, the austenite disappeared, resulting in excellent strength. You will have ductility with.
- the hot-rolled steel sheet may be heat treated at a temperature of 500 to 800 ° C. for at least 1 hour in order to reduce the anisotropy of the steel and to reduce the carbide and austenite band structure.
- Duplex steels, including austenite have a soft, two-phase structure of ferrite and hard austenite, most of which are deformed during hot rolling. This is because the recovery and recrystallization of low strength ferrite is very fast.
- a band-like structure in which carbides or austenite are arranged in layers in the ferrite matrix structure is formed.
- the band structure causes mechanical anisotropy of the steel and impairs workability, and may cause brittle fracture during cold rolling. Therefore, in order to eliminate this, it is preferable to heat-treat at a temperature of 500 ° C. or more for carbide spheroidization and a temperature of 800 ° C. or less for removing austenite bands for 1 hour or more.
- the hot rolled steel sheet may be cold rolled at a cold reduction rate of 40% or more to produce a cold rolled steel sheet.
- Cold rolling is usually performed after pickling, and the cold reduction rate must be 40% or more, so that the accumulated energy can be secured by cold working and a new recrystallized structure can be obtained.
- the cold rolled steel sheet may be formed into a plated steel sheet by removing rolling oil on the surface and performing continuous annealing or plating.
- the continuous annealing is heated at a heating rate of 1 ⁇ 20 °C / s, annealing for 10 to 180 seconds at a temperature of more than the recrystallization temperature 900 °C or less, and then cooled to 400 °C at a cooling rate of 1 ⁇ 100 °C / s. desirable.
- the recrystallization temperature is preferably maintained for at least 10 seconds to be cracked so that sufficient recrystallization and grain growth at a temperature of 900 °C, if it exceeds 180 seconds, the productivity is lowered, and the zinc bath and alloying treatment time in the subsequent plating process Since this can be increased, there is a fear that the corrosion resistance and the surface properties deteriorate.
- the plating is not particularly limited, zinc-based plating, aluminum-based, metal alloy plating may be applied to ensure corrosion resistance.
- plating layers such as Zn, Zn-Fe, Zn-Al, Zn-Mg, Zn-Al-Mg, Al-Si, Al-Mg-Si, can be formed.
- the plating layer is preferable in view of ensuring sufficient corrosion resistance to be carried out at a thickness of 10 to 200 ⁇ m per side.
- B * means Ni + 0.5Cu + 100Sb + 500B.
- the cold rolled steel sheet was heated to 800 ° C. at a heating rate of 5 ° C./s for 60 seconds, then slowly cooled to 600 to 680 ° C. and quenched to 400 ° C. again at a cooling rate of 20 ° C./s for 100 seconds. Then, zinc plating was performed in a hot dip galvanizing bath at 400 to 500 ° C. to produce a galvanized steel sheet.
- Figure 2 shows the structure photograph and carbon concentration distribution after maintaining the hot-rolled steel sheet of Comparative Steel 4 at 700 °C 30 minutes in the air atmosphere.
- the hot rolled steel sheet of Comparative Steel 4 has already undergone considerable decarburization, and in order to sufficiently remove the decarburization layer, it is ground to a thickness of 1.2 mm, and then maintained in a furnace heated to a temperature of 700 ° C. in an air atmosphere for 30 minutes, and then the structure is secondary Observation with an electron microscope. Although the average depth of the decarburized layer is seen to be 170 ⁇ m on the tissue photograph, the carbon concentration is evaluated from the surface, and the decarburization is performed deeply up to about 400 ⁇ m.
- the retained austenite is considerably lost to about 400 ⁇ m, so that the ductility is not high, and the austenite having a low C content is deteriorated in thermal stability and transforms into ferrite containing martensite or carbide during cooling to room temperature.
- FIG. 3 is a tissue photograph of surface decarburization after maintaining hot-rolled steel sheets of Inventive Example 4 and Comparative Example 4 at 700 ° C. for 30 minutes in an air atmosphere.
- the hot rolled steel sheet of Inventive Steel 4 of FIG. 3 (a) has almost no decarburization with a decarburization depth of 7 ⁇ m, and thus, it can be seen that a larger amount of stable austenite remains up to room temperature, so that both strength and ductility are excellent. It can be seen that the hot rolled steel sheet of Comparative Example 4 of FIG. 3 (b) has a severe decarburization at a depth of 170 ⁇ m.
- Figure 4 is a photograph showing the change in texture according to the heat treatment before cold rolling of the inventive steel 4.
- the hot rolled steel sheet of the inventive steel 4 was pickled to remove oxides formed on the surface, and then subjected to carbide spheroidization and austenite band removing heat treatment at a temperature of 700 ° C. for 5 hours.
- Inventive steel 4 has the advantage of being able to perform such heat treatment because it has a decarburization prevention effect. Thereafter, cold rolling was performed at 67%, heated to 800 ° C., cracked for 60 seconds, annealed, and microstructures were observed by a secondary electron microscope.
- Figure 4 (a) is a microstructure before the heat treatment, in the hot rolling temperature region (Duplex) steel has a two-phase structure of soft ferrite and hard austenite, most of the ferrite is deformed during hot rolling. This is because the recovery and recrystallization of low strength ferrite is very fast. As a result, a band-like structure in which carbides or austenite are arranged in layers is formed in the ferrite matrix structure. Such band structure causes mechanical anisotropy of steel, impairs workability, and causes brittle fracture during cold rolling.
- the present invention has the advantage that there is no loss of austenite even if the heat treatment to reduce the carbide spheroidization and austenite band structure through decarburization suppression, it is possible to manufacture a high ductility low specific gravity light steel sheet having much less anisotropy than the prior art.
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Abstract
Description
구분 | C | Mn | P | S | Al | Ni | Cu | Sb | B | B* |
발명예1 | 0.12 | 9.9 | 0.011 | 0.007 | 3.3 | 4.7 | - | 0.02 | - | 6.7 |
발명예2 | 1 | 2.2 | 0.009 | 0.005 | 9.8 | 4.5 | - | 0.05 | - | 9.5 |
발명예3 | 0.5 | 6.1 | 0.011 | 0.003 | 6.1 | - | - | - | 0.005 | 2.5 |
발명예4 | 0.32 | 3.5 | 0.012 | 0.004 | 6.2 | - | - | 0.03 | - | 3 |
발명예5 | 0.31 | 8.2 | 0.011 | 0.005 | 4.8 | - | 4.8 | - | - | 2.4 |
발명예6 | 0.6 | 2.5 | 0.012 | 0.004 | 7.6 | 0.9 | 0.5 | 0.01 | - | 2.15 |
비교예1 | 0.004 | 0.24 | 0.011 | 0.003 | 3.5 | - | - | 0.04 | - | 4 |
비교예2 | 1.2 | 2.7 | 0.011 | 0.006 | 8.7 | - | - | - | 0.002 | 1 |
비교예3 | 0.5 | 7.2 | 0.01 | 0.004 | 5.8 | 1.6 | - | - | - | 1.6 |
비교예4 | 0.3 | 3.5 | 0.012 | 0.004 | 6.2 | - | - | - | - | 0 |
비교예5 | 0.32 | 3.5 | 0.012 | 0.004 | 9.0 | 6.0 | - | - | 0.01 | 11.0 |
구분 | 1000℃에서의 오스테나이트 분율(%) | 탈탄층 깊이(㎛) | 잔류 오스테나이트 분율(%) | 인장강도(MPa) | 연신율(%) |
발명예1 | 87 | 3 | 50 | 1064 | 31.3 |
발명예2 | 26 | 1 | 25 | 998 | 38.4 |
발명예3 | 32 | 6 | 31 | 884 | 35.8 |
발명예4 | 25 | 7 | 23 | 798 | 32.1 |
발명예5 | 55 | 8 | 35 | 837 | 34.6 |
발명예6 | 12 | 9 | 12 | 881 | 37.5 |
비교예1 | 0 | 0 | 0 | 426 | 21.1 |
비교예2 | 46 | 20 | 12 | 742 | 22.2 |
비교예3 | 42 | 16 | 16 | 803 | 27.6 |
비교예4 | 16 | 170 | 5 | 756 | 26.4 |
비교예5 | 45 | 1 | 33 | - | - |
Claims (9)
- 중량%로, C: 0.1~1.2%, Mn: 2~10%, Al: 3~10%, P: 0.1%이하, S:0.01%이하를 포함하고, Ni: 5.0%이하, Cu: 5.0%이하, Sb: 0.01~0.05% 및 B: 0.01%이하로 이루어진 그룹에서 선택된 1종 이상을 포함하고, 나머지는 Fe 및 불가피한 불순물로 이루어지며,하기 B*의 값이 2~10을 만족하는 강도와 연성이 우수한 경량강판.B* = Ni + 0.5Cu + 100Sb + 500B (각 성분의 값은 중량%임)
- 청구항 1에 있어서,상기 강판의 미세조직은 페라이트 기지조직에 잔류 오스테나이트를 면적분율로 10~50% 포함하는 강도와 연성이 우수한 경량강판.
- 청구항 1에 있어서,상기 강판은 인장강도가 700MPa 이상이고, 연신율이 30% 이상인 강도와 연성이 우수한 경량강판.
- 중량%로, C: 0.1~1.2%, Mn: 2~10%, Al: 3~10%, P: 0.1%이하, S:0.01%이하를 포함하고, Ni: 5.0%이하, Cu: 5.0%이하, Sb: 0.01~0.05% 및 B: 0.01%이하로 이루어진 그룹에서 선택된 1종 이상을 포함하고, 나머지는 Fe 및 불가피한 불순물로 이루어지며, 하기 B*의 값이 2~10을 만족하는 강 슬라브를 1000~1200℃로 재가열하는 단계;상기 재가열된 강 슬라브를 열간압연하고, 700℃ 이상에서 마무리 열간압연하는 단계;상기 열간압연 후 권취하여 열연강판을 제조하는 단계; 및상기 열연강판을 40% 이상의 냉간압하율로 냉간압연하는 단계를 포함하는 강도와 연성이 우수한 경량강판의 제조방법.B* = Ni + 0.5Cu + 100Sb + 500B (각 성분의 값은 중량%임)
- 청구항 4에 있어서,상기 열간압연 중 강 슬라브의 미세조직은 오스테나이트가 면적분율로 5% 이상 포함하는 강도와 연성이 우수한 경량강판의 제조방법.
- 청구항 4에 있어서,상기 열연강판은 대기 분위기 700℃의 온도에서 30분간 유지하였을 때, 탈탄층이 10㎛ 이하인 강도와 연성이 우수한 경량강판의 제조방법.
- 청구항 4에 있어서,상기 열연강판을 500~800℃에서 1시간 이상 열처리하는 단계를 포함하는 강도와 연성이 우수한 경량강판의 제조방법.
- 청구항 4에 있어서,상기 냉연강판을 1~20℃/s의 가열속도로 재결정온도~900℃까지 가열하고, 10~180초 동안 유지한 후, 1~100℃/s의 냉각속도로 냉각하는 단계를 포함하는 강도와 연성이 우수한 경량강판의 제조방법.
- 청구항 4에 있어서,상기 냉각 후, Zn,Zn-Fe, Zn-Al, Zn-Mg, Zn-Al-Mg, Al-SI 및 Al-Mg-Si 중 선택된 1종의 도금층을 형성하는 단계를 더 포함하는 강도와 연성이 우수한 경량강판의 제조방법.
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JP5440672B2 (ja) | 2011-09-16 | 2014-03-12 | Jfeスチール株式会社 | 加工性に優れた高強度鋼板およびその製造方法 |
KR20130034727A (ko) | 2011-09-29 | 2013-04-08 | 현대자동차주식회사 | 저비중강판용 합금 및 그 제조방법 |
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- 2013-12-26 JP JP2016542748A patent/JP6307618B2/ja active Active
- 2013-12-26 EP EP13900318.0A patent/EP3088546A4/en not_active Ceased
- 2013-12-26 US US15/107,555 patent/US10273556B2/en active Active
- 2013-12-26 CN CN201380081867.8A patent/CN105899695B/zh active Active
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KR20130006461A (ko) * | 2010-03-16 | 2013-01-16 | 잘쯔기터 플래시슈탈 게엠베하 | 벽 두께에 걸쳐 조절될 수 있는 재료 특성을 갖는 경량 강으로부터 작업물을 제조하는 방법 |
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Also Published As
Publication number | Publication date |
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KR101560940B1 (ko) | 2015-10-15 |
US10273556B2 (en) | 2019-04-30 |
JP2017508068A (ja) | 2017-03-23 |
EP3088546A4 (en) | 2016-12-07 |
CN105899695A (zh) | 2016-08-24 |
US20160312332A1 (en) | 2016-10-27 |
JP6307618B2 (ja) | 2018-04-04 |
KR20150074959A (ko) | 2015-07-02 |
EP3088546A1 (en) | 2016-11-02 |
CN105899695B (zh) | 2018-04-06 |
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