TW201317366A - 高強度熔融鍍鋅鋼板及其製造方法 - Google Patents
高強度熔融鍍鋅鋼板及其製造方法 Download PDFInfo
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- TW201317366A TW201317366A TW101135893A TW101135893A TW201317366A TW 201317366 A TW201317366 A TW 201317366A TW 101135893 A TW101135893 A TW 101135893A TW 101135893 A TW101135893 A TW 101135893A TW 201317366 A TW201317366 A TW 201317366A
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- Prior art keywords
- less
- steel sheet
- iron
- hot
- dip galvanized
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- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 28
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 28
- 238000000034 method Methods 0.000 title description 18
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 68
- 239000010959 steel Substances 0.000 claims abstract description 68
- 239000002245 particle Substances 0.000 claims abstract description 27
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 23
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 250
- 229910052742 iron Inorganic materials 0.000 claims description 121
- 238000005452 bending Methods 0.000 claims description 34
- 238000001816 cooling Methods 0.000 claims description 23
- 238000004519 manufacturing process Methods 0.000 claims description 18
- 238000005096 rolling process Methods 0.000 claims description 18
- 238000000137 annealing Methods 0.000 claims description 14
- 239000000463 material Substances 0.000 claims description 13
- 238000007747 plating Methods 0.000 claims description 12
- 238000005098 hot rolling Methods 0.000 claims description 10
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 229910052799 carbon Inorganic materials 0.000 claims description 5
- 229910052717 sulfur Inorganic materials 0.000 claims description 5
- 238000005097 cold rolling Methods 0.000 claims description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 238000005246 galvanizing Methods 0.000 claims description 2
- 229910052750 molybdenum Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 229910052720 vanadium Inorganic materials 0.000 claims description 2
- 229910052760 oxygen Inorganic materials 0.000 claims 2
- 210000001161 mammalian embryo Anatomy 0.000 claims 1
- 229910052758 niobium Inorganic materials 0.000 claims 1
- 229910001566 austenite Inorganic materials 0.000 abstract 2
- 229910001563 bainite Inorganic materials 0.000 abstract 1
- 229910000734 martensite Inorganic materials 0.000 abstract 1
- 229910001562 pearlite Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 24
- 238000005728 strengthening Methods 0.000 description 17
- 238000000691 measurement method Methods 0.000 description 8
- 230000002411 adverse Effects 0.000 description 5
- 238000005275 alloying Methods 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 5
- 238000005259 measurement Methods 0.000 description 5
- 229910052761 rare earth metal Inorganic materials 0.000 description 5
- 238000001953 recrystallisation Methods 0.000 description 5
- 239000011701 zinc Substances 0.000 description 5
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 4
- 239000003153 chemical reaction reagent Substances 0.000 description 4
- 230000006866 deterioration Effects 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 229920006395 saturated elastomer Polymers 0.000 description 4
- 229910052684 Cerium Inorganic materials 0.000 description 3
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 238000000354 decomposition reaction Methods 0.000 description 3
- 229910052746 lanthanum Inorganic materials 0.000 description 3
- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 230000003287 optical effect Effects 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 230000000717 retained effect Effects 0.000 description 3
- 230000001629 suppression Effects 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910002651 NO3 Inorganic materials 0.000 description 2
- NHNBFGGVMKEFGY-UHFFFAOYSA-N Nitrate Chemical compound [O-][N+]([O-])=O NHNBFGGVMKEFGY-UHFFFAOYSA-N 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 239000010410 layer Substances 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 230000029052 metamorphosis Effects 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000011002 quantification Methods 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- YPFNIPKMNMDDDB-UHFFFAOYSA-K 2-[2-[bis(carboxylatomethyl)amino]ethyl-(2-hydroxyethyl)amino]acetate;iron(3+) Chemical compound [Fe+3].OCCN(CC([O-])=O)CCN(CC([O-])=O)CC([O-])=O YPFNIPKMNMDDDB-UHFFFAOYSA-K 0.000 description 1
- 208000010392 Bone Fractures Diseases 0.000 description 1
- 206010017076 Fracture Diseases 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000004453 electron probe microanalysis Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005294 ferromagnetic effect Effects 0.000 description 1
- 239000003337 fertilizer Substances 0.000 description 1
- 238000000445 field-emission scanning electron microscopy Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 150000002603 lanthanum Chemical class 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000000399 optical microscopy Methods 0.000 description 1
- 239000007800 oxidant agent Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000011295 pitch Substances 0.000 description 1
- 229910001568 polygonal ferrite Inorganic materials 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000012552 review Methods 0.000 description 1
- 150000003303 ruthenium Chemical class 0.000 description 1
- 238000004626 scanning electron microscopy Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000004627 transmission electron microscopy Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
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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
-
- 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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- 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
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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
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
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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
- 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
- C21D8/0284—Application of a separating or insulating coating
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- C—CHEMISTRY; METALLURGY
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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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- 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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- C—CHEMISTRY; METALLURGY
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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
- 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
- C21D8/0436—Cold rolling
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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
- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
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- C22C—ALLOYS
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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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- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- 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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
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- 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
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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
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- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
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- C—CHEMISTRY; METALLURGY
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- 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
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- C—CHEMISTRY; METALLURGY
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- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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- C23C2/06—Zinc or cadmium or alloys based thereon
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- 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
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- C23C2/29—Cooling or quenching
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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
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
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- C—CHEMISTRY; METALLURGY
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Abstract
本發明係一種高強度熔融鍍鋅鋼板,其含有主要成分,並且以質量%計,鋼板係以體積分率計將肥粒鐵40%以上作為主相,且含有殘留沃斯田鐵8%以上~60%以下,並且剩餘部分之組織係由變韌鐵、麻田散鐵、波來鐵中之1種或2種以上所構成者。於該熔融鍍鋅鋼板中,沃斯田鐵粒之平均殘留應力σR滿足式(1)之範圍的沃斯田鐵粒係50%以上,並於該鋼板表面具有含有小於7質量%之Fe,且剩餘部分係由Zn、Al及不可避免的不純物所構成的熔融鍍鋅層。-400MPa≦σR≦200MPa (1)
Description
本發明係有關於使用於汽車用構造材等之彎曲性優異的高強度(例如,抗拉強度980MPa以上)之熔融鍍鋅鋼板及製造方法。
以提升汽車之燃料費及衝撞安全性為目的,除了對車體骨架構造追求高強度化,隨著材料強度之提升,因材料之成形性下降,故對所使用之鋼板要求兼具高加壓加工性與強度。
於高強度鋼板中,眾所周知的是於組織具有殘留沃斯田鐵之殘留沃斯田鐵鋼利用TRIP效果,不僅係高強度,亦具有非常高的伸長。於該殘留沃斯田鐵鋼中,為更加提高伸長,例如,專利文獻1中揭示有一種可一面確保高殘留沃斯田鐵分率,一面控制2種肥粒鐵(變韌肥粒鐵、多邊形肥粒鐵)以確保伸長之技術。
另一方面,於抗拉強度980MPa以上之高強度鋼板的成形中,並非係抗拉強度440MPa以下之低強度鋼板成形時作為主體的沖壓成形,多以彎曲成形為中心地加工。於高強度鋼板中,與伸長同樣地亦要求彎曲性之提升。
以往,可知V彎曲性與局部延性相關,而提高局部延性之技術,專利文獻1中揭示了一種測量組織之均一
化,並析出強化肥粒鐵單相,以高強度化的技術,專利文獻2中揭示了一種藉以變韌鐵作為主體之組織,而同樣地測量組織的均一化之技術。
又,專利文獻3中,揭示了一種以體積分率計,包含30~90%之肥粒鐵相、5%以上之變韌鐵、10%以下之麻田散鐵、及5~30%之殘留沃斯田鐵相的高強度高延性熔融鍍鋅鋼板。專利文獻4中,揭示了一種鋼板所含之差排密度係8×1011(個/mm2)以下,由應變速率0.0067(s-1)下之半靜力強度(FS1)與應變速率1000(s-1)下之動力強度(FS2)的比所構成之靜動比(=FS2/FS1)係1.05以上的高強度冷軋鋼板。
然而,現今,於高強度鋼板中亦要求更高之強度、加工性,但對應該等要求之兼具充分高程度之伸長與V彎曲性的技術係尚未得知。
專利文獻1:日本專利特開2003-306746號公報
專利文獻2:日本專利特開平4-88125號公報
專利文獻3:日本專利特開2005-133201號公報
專利文獻4:日本專利特開2002-30403號公報
本發明係用以解決以往之問題點而作成者,係重複地致力檢討於具有抗拉強度980MPa以上之殘留沃斯田
鐵鋼中,可提升V彎曲性後,結果,發現的一種技術,並以提供伸長與V彎曲性優異之高強度熔融鍍鋅鋼板及其製造方法作為課題。
本發明人致力研究之結果,發現藉由賦與殘留沃斯田鐵相壓縮之殘留應力,可較以往提高殘留沃斯田鐵之穩定性,而有效地對彎曲外側之抗拉應力部彎曲內側的壓縮應力部彎曲之局部變形作用。
本發明人依據前述觀察所得知識更加進行研究之結果,發現為賦與殘留沃斯田鐵相壓縮之殘留應力,藉由較佳地控制過時效(OA)處理時重複彎曲中的輥徑、張力、道次(pass)數,以控制沃斯田鐵相中之殘留應力,對伸長、V彎曲性可得充分的效果。本發明人更加依據前述觀察所得知識更加進行研究之結果,發現藉使過時效(OA)處理時重複彎曲中的條件控制,配合沃斯田鐵相中之濃化及粒徑的控制,可提高殘留沃斯田鐵相之穩定性,故對伸長、V彎曲性更有效。
依據本發明人之觀察所得知識,可如以下推測本發明可得前述效果的機制。
殘留沃斯田鐵鋼係控制退火中之肥粒鐵變態、變韌鐵變態,以提高沃斯田鐵中的C濃度,於製品之鋼組織殘留沃斯田鐵,藉由該殘留沃斯田鐵之TRIP效果,具有高伸長的高強度鋼板。然而,因係混合組織,故推測如此之殘留沃斯田鐵鋼並非彎曲性優異的鋼。
相對於此,本發明人等認為應使TRIP效果有效地對彎曲性產生作用,故於實驗室中對經改變C、Si、Mn量之各種鋼進行熔解、熱軋、冷軋、退火、熔融鍍鋅,檢討用以得到所需之抗拉強度、延性、V彎曲性、鍍敷性的各種方法。
經如此之致力檢討,結果,發現不僅需特定對前述目的有效的各種成分,賦與對殘留沃斯田鐵相之壓縮的殘留應力,不僅可較以往提高殘留沃斯田鐵之穩定性,對彎曲外側之抗拉應力部彎曲內側的壓縮應力部彎曲之局部變形亦有效地作用。
本發明係依據前述觀察所得之知識所完成者。
本發明係例如,可包含以下知態樣。
[1]一種熔融鍍鋅鋼板,係以質量%計,含有:C:0.10%以上且0.4%以下、Si:0.01%以上且0.5%以下、Mn:1.0%以上且3.0%以下、O:0.006%以下、P:0.04%以下、S:0.01%以下、Al:0.1以上且3.0%以下、N:0.01%以下、及Si+Al≧0.5%,並由剩餘部分之Fe及不可避免的不純物所構成的鋼板;進而該鋼板係以體積分率計,將肥粒鐵40%以上作為主相,且含有殘留沃斯田鐵8%以上~60%以下,並且剩餘部分之組織係由變韌鐵、麻田散鐵、波來鐵中之1種或2種以上所構成的高強度熔融鍍鋅鋼板;前述沃斯田鐵中,平均殘留應力σR滿足式(1)之範圍的沃斯田鐵粒係50%以上,-400MPa≦σR≦200MPa (1);於前述鋼板表面具有含有小於7質量%之Fe,且剩餘部
分係由Zn、Al及不可避免的不純物所構成的熔融鍍鋅層。
[2]如[1]記載之熔融鍍鋅鋼板,其中前述沃斯田鐵之平均粒徑係10μm以下,沃斯田鐵中之平均C濃度以質量%計係0.7%以上且1.5%以下。
[3]如[1]或[2]記載之熔融鍍鋅鋼板,其中前述沃斯田鐵粒之相對於軋延方向的平均長寬比係0.5以上且0.95以下。
[4]如[1]~[3]之任1項記載的熔融鍍鋅鋼板,其以質量%計,更含有:Mo:0.02%以上且0.5%以下、Nb:0.01%以上且0.10%以下、Ti:0.01%以上且0.20%以下、V:0.005%以上且0.10%以下、Cr:0.1%以上且2.0%以下、Ca:0.0005%以上且0.05%以下、Mg:0.0005%以上且0.05%以下、REM:0.0005%以上且0.05%以下、Cu:0.04%以上且2.0%以下、Ni:0.02%以上且1.0%以下、B:0.0003%以上且0.007%以下之1種或2種以上的元素。
[5]一種熔融鍍鋅鋼板之製造方法,其係對以質量%計,含有:C:0.10%以上且0.4%以下、Si:0.01%以上且0.5%以下、Mn:1.0%以上且3.0%以下、O:0.006%以下且P:0.04%以下、S:0.01%以下、Al:0.1以上且3.0%以下、N:0.01%以下、Si+Al≧0.5%,並由剩餘部分之Fe及不可避免的不純物所構成的鋼材,進行下述步驟:於熱軋扁鋼胚溫度為1100℃以上,且完成溫度為850~970℃下施行熱軋延處理;將前述熱軋延後之鋼板以平均10~200℃/秒冷卻至
650℃以下的溫度域為止,並於650℃以下之溫度範圍捲取;對該鋼板以軋縮率為40%以上施行冷軋延;以退火時之最高溫度為700~900℃進行退火,並以平均0.1~200℃/秒之冷卻速度冷卻至350℃~550℃之溫度域內,之後,於該溫度域內保持1秒以上且1000秒以下;將於該溫度域內保持後之鋼板浸漬於熔融鍍鋅浴,並於該鍍敷處理後,於470~580℃之溫度範圍施行合金化處理;且於將前述鋼板保持於350℃~550℃之溫度域內時,藉由使用輥徑為50~2000mm之輥將鋼板重複折彎,來賦與該鋼板應變;並且該重複折彎時所施加於前述鋼板之長度方向的平均應力係2~50MPa。
[6]如[5]記載之熔融鍍鋅鋼板之製造方法,其中前述重複折彎時的道次數係2~6道次。
依據本發明,可提供一種延性與V彎曲性優異之高強度熔融鍍鋅鋼板。該熔融鍍鋅鋼板之製造亦可較容易且穩定地實施。因此,本發明之熔融鍍鋅鋼板特別是可最佳地使用於近年目標輕量化之汽車用鋼板,於產業上之價值極大。
圖1係顯示殘留沃斯田鐵相中之殘留應力與最小彎曲半徑R之關係的圖表。
圖2係顯示沃斯田鐵粒之平均殘留應力σR滿足式(1)之範圍的圖表。
圖3係顯示滿足式(1)之沃斯田鐵粒的比例與最小彎曲半徑R之關係的圖表。
圖4係顯示殘留沃斯田鐵之平均粒徑與最小彎曲半徑R之關係的圖表。
圖5係顯示殘留沃斯田鐵粒之長寬比與最小彎曲半徑R之關係的圖表。
圖6係顯示C濃度與最小彎曲半徑R之關係的圖表。
本發明之高強度薄鋼板係著眼於殘留沃斯田鐵鋼中可提高殘留沃斯田鐵相之穩定性者。如前述,本發明係依據經發現藉控制殘留沃斯田鐵相之殘留應力及長寬比,將穩定性提高至極限,可高程度地兼具強度與伸長與V彎曲者。
本發明之熔融鍍鋅鋼板中的組織係以肥粒鐵相與變韌鐵相作為主體,且需含有3%以上之殘留沃斯田鐵相。於要求更高之強度時,亦可含有麻田散鐵,但若非以肥粒鐵相與變韌鐵相作為主體時,有伸長顯著地下降的傾向。
殘留沃斯田鐵相中之殘留應力係本發明中最重要者之一。如圖1所示,殘留沃斯田鐵相中之殘留應力越低,特別是15MPa以下時,最小彎曲半徑R變得最小。藉於
製造步驟中賦與各殘留沃斯田鐵粒壓縮的殘留應力,加工中之麻田散鐵變態變慢,結果,提高相全體的穩定性。
為達成前述,如圖2所示,於該沃斯田鐵粒之平均殘留應力σR滿足式(1)的範圍內Σr係最小。又,如圖3所示,滿足該式(1)之沃斯田鐵粒為50%以上時,係為穩定,最小彎曲半徑R係最小。
-400MPa≦σR≦200MPa (1)
此處,殘留沃斯田鐵率測定方法只要是可以保證精度之測定方法的話,可用任何方法,例如,於自被測材料板之表層至1/4厚度的經化學研磨之面進行,利用經單色化的MoKα線自肥粒鐵之(200)及(211)面積分強度與沃斯田鐵之(200)、(220)及(311)面積分強度,定量殘留沃斯田鐵。又,σR只要於可正確地得到殘留應力之條件下,並可保證精度的測定方法的話,可使用任何方法,例如,本發明中,於自被測材料板之表層至1/4厚度的經化學研磨之面,使用利用具有5μm 的光束系之高精度輻射光X射線繞射的應力測定法,仔細地測定任意之50個殘留沃斯田鐵粒的殘留應力,可得於式(1)範圍內之殘留沃斯田鐵粒的比例。
於本發明中,殘留沃斯田鐵之平均粒徑以10μm以下為佳。如圖4所示,大於10μm時,殘留沃斯田鐵相之分散大,無法充分地發揮TRIP效果,故伸長下降。此處,平均粒徑(平均圓等效直徑)之測定只要是可保證精度之測定方法的話,可使用任何方法,例如,利用硝太蝕劑試劑腐蝕鋼板軋延方向截面或與軋延方向成直角之截面,並藉
由500倍之光學顯微鏡觀察定量化。
又,如圖5所示,若殘留沃斯田鐵粒之長寬比相對於軋延方向係0.5以上且0.95以下,最小彎曲半徑係最小而為佳。大於0.95或小於0.5時,彎曲變形時殘留沃斯田鐵之穩定性將不均衡。此處,長寬比之測定方法若為可保證精度之測定方法,可使用任何方法,例如,利用硝太蝕劑試劑腐蝕鋼板軋延方向截面或與軋延方向成直角之截面,並藉由500倍之光學顯微鏡觀察定量化後,對30個殘留沃斯田鐵粒,使用影像處理軟體測定軋延方向之粒徑及軋延直角方向之粒徑,求出長寬比後,將該等之平均值作為材料的代表值。
殘留沃斯田鐵之平均C濃度亦大幅地有助於殘留沃斯田鐵的穩定性。如圖6所示,平均C濃度以質量%計小於0.7%時,殘留沃斯田鐵之穩定性變得極低,故無法有效地得到TRIP效果,伸長劣化。另一方面,即使大於1.5%,不僅伸長改善效果達到飽和,用以製造其之成本增加,故以0.7%以上且1.5%以下為佳。此處,C濃度只要是於可正確地得到分解濃度之條件下,可保證精度的測定方法的話,可為任何之測定方法,例如,可藉由使用附屬有FE-SEM的EPMA,以0.5μm以下節距仔細注意C濃度地測定,即可得C濃度。
首先,說鋼板之成分的限定理由。另,%係質量%之意。
C:C係可提升鋼板強度之元素。然而,小於0.1%時,
將不易兼具980MPa以上之抗拉強度與加工性。另一方面,大於0.40%時,確保點熔接性變得困難。因此,將C含量範圍設為0.1~0.40%以下。C含量以0.1~0.38為佳,以0.13~0.38更佳。
Si:Si係強化元素,並有效提升鋼板之強度。又,因可抑制雪明碳鐵之析出,故需添加以有助於殘留沃斯田鐵的穩定化。小於0.01%時,高強度化之效果小,又,大於0.5%時,加工性下降。因此,Si含量係設為0.01~0.5%之範圍。Si含量以0.02~0.5%為佳,以0.1~0.45%更佳。
Mn:Mn係強化元素,係有效提升鋼板之強度。然而,小於1.0%時,欲得到980MPa以上之抗拉強度係為困難。反之,較多時將助長與P、S的共偏析,導致加工性之顯著劣化,故將上限設為3.0%。Mn含量以1.0~2.8%為佳,以1.2~2.8%更佳。
O:O因形成氧化物,使伸長、彎曲性或擴孔性劣化,故需抑制添加量。特別是,氧化物多作為夾雜物存在,存在於衝孔端面、或切截面時,將於端面形成缺口狀之傷痕或粗大之凹坑,故於擴孔時或硬化加工時,將導致應力集中,成為龜裂形成的起點,造成大幅之擴孔性或彎曲性的劣化。這是因為於O大於0.006%時,該傾向將變得顯著,故將O含量之上限設為0.006%以下。換言之,O係作為不純物限制為0.006%以下。O含量之上限以0.005%以下為佳,以0.004%以下更佳。另一方面,O含量小於0.0001%時,將導致成本過高,於經濟上不佳,故將其作為實質之
下限。
P:P有於鋼板之板厚中央部偏析的傾向,使熔接部脆化。大於0.04%時,因熔接部之脆化變得顯著,故將其適當範圍設為0.04%以下。換言之,P係作為不純物限制為0.04%以下。P含量以0.03%以下為佳,以0.02%以下更佳。P之下限值並未特別限定,但小於0.0001%時,於經濟上係不利,以將該值作為下限值為佳。
S:S係對熔接性及鑄造時與熱軋時之製造性造成不良影響。因此,將其上限值設為0.01%以下。換言之,S係作為不純物限制為0.01%以下。S含量以0.004%以下為佳,以0.003%以下更佳。S之下限值並未特別限定,但小於0.0001%時,於經濟上係不利,故以將該值作為下限值為佳。又,S將與Mn連結形成粗大之MnS,使彎曲性或擴孔性劣化,故需儘量減少。
Al:Al可促進肥粒鐵形成,提升延性,故亦可添加。又,亦可活用作為脫氧材。小於0.1%時,該效果係不充分。另一方面,過剩之添加將增大Al系之粗大夾雜物的個數,成為擴孔性劣化或表面傷痕的原因。因此,將Al添加之上限設為3.0%。Al含量以0.1~2.9%為佳,以0.15~2.9%更佳。
於本發明中,Al+Si係0.5%以上。該Al+Si以0.5~4%為佳,以0.51~3.5%更佳。
N:N將形成粗大之氮化物,使彎曲性或擴孔性劣化,故需抑制添加量。這是因為,於N大於0.01%時,該
傾向將變得顯著,故將N含量之範圍設為0.01%以下。此外,因將成為熔接時氣孔產生的原因,故N含量以少為佳。N含量以0.005%以下為佳,以0.004%以下更佳。下限不需特別限定即可發揮本發明之效果,但N含量小於0.0005%時,將導致製造成本的大幅增加,故其係實質之下限。
Mo:Mo係強化元素,並對提升可硬化性係為重要。然而,小於0.02%時,因無法得到該等之效果,故將下限值設為0.02%。反之,含有大於0.5%時,因對製造時及熱軋時之製造性造成不良影響,故將上限值設為0.5%。
Nb:Nb係強化元素。於析出物強化、利用抑制肥粒鐵結晶粒之成長的細粒強化及透過抑制再結晶之差排強化中,有助於提升鋼板之強度。添加量小於0.01%時,因無法得到該等之效果,故將下限值設為0.01%。於含有大於0.1%時,因碳氮化物之析出變多,成形性劣化,故將上限值設為0.1%。
Ti:Ti係強化元素。於析出物強化、利用抑制肥粒鐵結晶粒之成長的細粒強化及透過抑制再結晶之差排強化中,有助於提升鋼板之強度。添加量小於0.01%時,因無法得到該等之效果,故將下限值設為0.01%。於含有大於0.2%時,因碳氮化物之析出變多,成形性劣化,故將上限值設為0.2%。
V:V係強化元素。於析出物強化、利用抑制肥粒鐵結晶粒之成長的細粒強化及透過抑制再結晶之差排強化中,有助於提升鋼板之強度。添加量小於0.005%時,因
無法得到該等之效果,故將下限值設為0.005%。於含有大於0.1%時,因碳氮化物之析出變多,成形性劣化,故將上限值設為0.1%。
Cr:Cr係強化元素,並對提升可硬化性係為重要。然而,小於0.1%時,因無法得到該等之效果,故將下限值設為0.1%。反之,含有大於2.0%時,因對製造時及熱軋時之製造性造成不良影響,故將上限值設為2.0%。
可添加合計0.0005~0.05%之選自於Ca、Mg、REM之1種或2種以上的元素。Ca、Mg及REM係用以脫氧之元素,以含有1種或2種以上合計0.0005%以上為佳。REM係指Rare Earth Metal(稀土金屬)。然而,於含量的合計大於0.05%時,將成為成形加工性惡化之原因。因此,將含量之合計設為0.0005~0.05%。另,於本發明中,REM係多添加於稀土金屬合金,除了La或Ce以外,有複合地含有鑭系列之元素的情形。不可避免的不純物方面,即使包含該等La或Ce以外之鑭系列之元素亦可發揮本發明的效果。但,即便添加金屬La或Ce仍可發揮本發明之效果。
Cu:Cu係強化元素,並對提升可硬化性係為重要。此外,因可提升熔融鍍敷之濕潤性或促進合金化反應,故亦可添加Cu。然而,小於0.04%時,因無法得到該等之效果,故將下限值設為0.04%。反之,含有大於2.0%時,因對製造時及熱軋時之製造性造成不良影響,故將上限值設為2.0%。
Ni:Ni係強化元素,並對提升可硬化性係為重
要。此外,因可提升熔融鍍敷之濕潤性或促進合金化反應,故亦可添加Ni。然而,小於0.02%時,因無法得到該等之效果,故將下限值設為0.02%。反之,含有大於1%時,因對製造時及熱軋時之製造性造成不良影響,故將上限值設為1.0%。
B於添加0.0003%以上時係有助於粒界強化或鋼材之強度化,但其添加量大於0.07%時,不僅該效果達飽和,亦使熱軋時之製造性下降,故將其上限設為0.07%。
接著,說明鋼板之組織。
本鋼板中藉以肥粒鐵作為主相,並使體積率8%以上之殘留沃斯田鐵分散,確保980MPa以上的抗拉最大強度。因此,需包含殘留沃斯田鐵。肥粒鐵相之形態除了多邊形肥粒鐵以外,亦可包含粒狀肥粒鐵。以肥粒鐵作為主相,係因藉以富有延性之肥粒鐵作為主相,可提升延性。主相肥粒鐵相小於40%時未能確保充分之延性,而不實用,故將主相肥粒鐵之體積分率設為40%以上。
第二相藉由包含殘留沃斯田鐵,可同時達成高強度化與更加提升延性。體積分率小於8%時,因不易得到該效果,故將其下限設為小於8%。將上限設為60%以下,係因大於60%時,主相肥粒鐵相的體積分率小於40%,而無法確保充分之延性。變韌鐵組織因活用於殘留沃斯田鐵的穩定化,故係不可避免地含有。為更高強度化,亦可含有麻田散鐵。
另外,前述微觀組織之各相、肥粒鐵、麻田散鐵、
變韌鐵、沃斯田鐵、波來鐵及剩餘部分之組織的判別、存在位置之觀察及面積率的測定,可藉由硝太蝕劑試劑及日本專利特開59-219473號公報所揭示的試劑,腐蝕鋼板軋延方向截面或與軋延方向成直角方向之截面,並利用1000倍之光學顯微鏡觀察及1000~100000倍之掃描式及穿透式電子顯微鏡定量化。進行各20視野以上之觀察,藉由計點法或影像解析可求得各組織的面積率。
於以下說明本發明之高強度熔融鍍鋅鋼板的製造方法。
將熱軋延前之扁鋼胚於連續鑄造後施行通常之熱軋。
例如,保持連續鑄造後之原樣、或藉由再加熱而為1100℃以上。小於該溫度時,均質處理將不充分,產生強度與V彎曲性的下降。
接著,熱軋延扁鋼胚使完成溫度為850℃以上且970℃以下。這是因為,完成溫度小於850℃時將成為(α+γ)2相域軋延,導致延性下降,大於970℃時沃斯田鐵粒徑將變得粗大,肥粒鐵相分率變小,延性下降。
之後,以平均10℃/秒以上且200℃/秒以下冷卻至650℃以下的溫度域。之後,於650℃以下之溫度範圍捲取。小於該冷卻速度、大於該捲取溫度時,將生成使彎曲性顯著地劣化的波來鐵相。平均冷卻速度大於200℃/秒時,波來鐵抑制效果達飽和,又,冷卻終點溫度之差異變大,變得不易確保穩定之材質。因此,設為200℃/秒以下。
酸洗後可於試作材施行40%以上之冷軋延。小於其
時,退火中之再結晶或逆變態受到抑制,造成伸長之下降。
退火時之最高溫度係700℃以上且900℃以下。小於700℃時,因退火中之肥粒鐵相的再結晶變慢,引起伸長之下降。另一方面,較其高溫時,麻田散鐵分率增加,造成伸長的劣化。
於退火步驟之均熱處理後的冷卻中,為凍結組織,有效地引起變韌鐵變態,以冷卻速度快為佳。但,小於0.1℃/秒時無法控制變態。另一方面,即使大於200℃/秒,該效果達飽和,又,使殘留沃斯田鐵生成最重要之冷卻終點溫度的溫度控制性顯著地劣化。因此,退火後之冷卻速度以平均0.1℃/秒以上且200℃/秒以下為佳。該冷卻速度以平均1.2℃/秒以上且14℃/秒以下更佳,以1.8秒以上且11℃/秒以下特佳。
冷卻終點溫度及其後之保持或放冷係控制變韌鐵生成、決定殘留沃斯田鐵之C濃度的重要之技術。冷卻終點溫度小於350℃時,將生成多量之麻田散鐵,過剩地提高鋼強度,此外,不易殘留沃斯田鐵,故伸長之劣化變得極大。另一方面,大於550℃時,變韌鐵變態變慢,此外,於保持或放冷中將造成雪明碳鐵之生成,殘留沃斯田鐵中之C的濃化下降。因此,可生成8%以上具有高C濃度之殘留沃斯田鐵的冷卻停止溫度、及保持或放冷溫度以350℃以上且550℃以下為佳。
保持或放冷時間由對殘留沃斯田鐵之C濃化的點來看,以長為佳。小於1秒時,無法充分地產生變韌鐵變
態,C濃化變得不充分。另一方面,大於1000秒時,將於沃斯田鐵相中生成雪明碳鐵,藉此,變得容易產生C濃度之下降。因此,保持或放冷時間以1秒以上且1000秒以下為佳。該保持或放冷時間以110~800秒為佳,以150~400秒更佳。
藉由保持時間(過時效(OA)處理時)中之重複彎曲中的輥徑、張力、道次數之最佳控制,可控制沃斯田鐵相中之殘留應力及殘留沃斯田鐵粒之長寬比,但於將過時效(OA)處理溫度設為350℃至550℃時,需完全滿足以下要件。輥徑因賦與某一定之應變,故以小為佳。但,50mm以下時,輥剛性下降,而無法賦與穩定之應變。另一方面,大於2000mm時,面接觸部分變多,而不易局部地賦與大之應變。因此,輥徑以50mm以上且2000mm以下為佳。更佳者是下限為350mm以上。上限以1000mm以下為佳。
又,張力係藉由該值除以板截面積(板厚×板寬)之值的長度平均應力所整理,係用以決定長度方向之長寬比的重要之值,但於過時效(OA)溫度時為350℃至550℃時的鋼板強度(TS)大於50%時,斷裂之危險性高。因350℃下之980MPa鋼的強度係100MPa左右,故張力(長度平均應力)以50MPa以下為適當。該張力(長度平均應力)以45MPa以下為佳,以40MPa以下更佳。下限並未特別規定,但考量到鋼板之通板性,特別是考量到蛇行後,以2MPa以上為佳,以10MPa以上更佳。
此外,道次數方面,數量越多彎曲.回彎之次數增加,而容易控制殘留應力,但1道次時該效果小。因此,通常以
2道次以上為佳。該彎曲次數以6道次以下為佳,以5道次以下更佳。
之後,浸漬於熔融鋅層。又,本技術亦可於浸漬後施行合金化處理。此時,於470℃以上且580℃之範圍進行鍍敷之合金化處理。較其低之溫度中合金化變得不充分,大於其時變得過度合金,耐蝕性顯著地劣化。
以下,依據實施例詳細地說明本發明。
製造具有表1所示之成分組成的鋼,冷卻凝固後再加熱至1200℃,以880℃進行最後軋延,以平均冷卻速度60℃/秒冷卻至550℃後,以表2之捲取溫度進行捲取。之後,對該熱軋板施行50%之冷軋延。之後於連續退火中以表2所示的條件進行退火處理。
假設實際生產線中過時效(OA)處理時之重複彎曲的輥徑、張力、道次數之效果,於退火處理之OA時賦與複數相異的曲率、張力、次數,評價對殘留應力之影響。
之後,浸漬於經控制預定之條件的鋅鍍敷浴,之後冷卻至室溫。鍍敷浴中之有效Al濃度係0.09~0.17mass%的範圍。一部分之鋼板係於浸漬於鋅鍍敷浴後,以各條件進行合金化處理,再冷卻至室溫。此時之目標量係兩面均約35g/m2。最後,對所得之鋼板以0.4%之軋縮率進行表皮輥軋(skin pass rolling)。於退火.鍍敷處理後進行1%之表皮輥軋,以抑制降伏點伸長。
於表2顯示前述熱處理條件及鍍敷處理條件。抗拉特性係以JIS5號抗拉試驗片之C方向抗拉評價。組織之判別、存在位置之觀察及平均粒徑(平均圓等效直徑)與占有率的測定,係藉由硝太蝕劑試劑腐蝕鋼板軋延方向截面或與軋延方向成直角之截面,利用500倍~1000倍的光學顯微鏡觀察而定量化。
V彎曲特性係進行依據JISZ2248之試驗,對衝孔R0.5mm、1mm、2mm實施,並以目視觀察如下述地判斷,以「○」作為合格。
○:無破裂
△:些微破裂產生(於彎曲外表面產生複數裂痕)
×:產生破裂
殘留沃斯田鐵率測定方法係於自被測材料板之表層至1/4厚度的經化學研磨之面進行,利用經單色化的MoKα線自肥粒鐵之(200)及(211)面積分強度與沃斯田鐵之(200)、(220)及(311)面積分強度,定量殘留沃斯田鐵。
殘留沃斯田鐵相之殘留應力(σR)的測定方法係於自被測材料板之表層至1/4厚度的經化學研磨之面進行,並利用高分解能X射線繞射裝置,由10處之平均值求出。本次實驗中使用之高分解能X射線繞射裝置係Bruker AXS社製的D8 DISCOVER Hybrid Super Speed Solution。使用由該裝置之繞射面間隔分布求得之應變(εR)與鋼材之楊氏模數(E),藉由以下式(2)求出殘留應力(σR)。
σR=εR×E (2)
實驗No.“a”~“o”係本發明例,任一特性均係合格,可得目標之特性的鋼板。另一方面,成分或製造方法係本發明範圍外之實驗No.“p”~“ag”的任一特性均係不合格。
依據本發明,可提供一種伸長及V彎曲性優異之高強度熔融鍍鋅鋼板。該熔融鍍鋅鋼板之製造亦可較容易且穩定地實施。因此,本發明之熔融鍍鋅鋼板,特別地,最適合作為近年以輕量化作為目標的汽車用鋼板使用,產業上之價值極大。
圖1係顯示殘留沃斯田鐵相中之殘留應力與最小彎曲
半徑R之關係的圖表。
圖2係顯示沃斯田鐵粒之平均殘留應力σR滿足式(1)之範圍的圖表。
圖3係顯示滿足式(1)之沃斯田鐵粒的比例與最小彎曲半徑R之關係的圖表。
圖4係顯示殘留沃斯田鐵之平均粒徑與最小彎曲半徑R之關係的圖表。
圖5係顯示殘留沃斯田鐵粒之長寬比與最小彎曲半徑R之關係的圖表。
圖6係顯示C濃度與最小彎曲半徑R之關係的圖表。
Claims (6)
- 一種熔融鍍鋅鋼板,其特徵在於,其係以質量%計,含有:C:0.10%以上且0.4%以下、Si:0.01%以上且0.5%以下、Mn:1.0%以上且3.0%以下、O:0.006%以下、P:0.04%以下、S:0.01%以下、Al:0.1以上且3.0%以下、N:0.01%以下、及Si+Al≧0.5%,並由剩餘部分之Fe及不可避免的不純物所構成的鋼板;進而該鋼板係以體積分率計,將肥粒鐵40%以上作為主相,且含有殘留沃斯田鐵8%以上~60%以下,並且剩餘部分之組織係由變韌鐵、麻田散鐵、波來鐵中之1種或2種以上所構成的高強度熔融鍍鋅鋼板;前述沃斯田鐵中,平均殘留應力σR滿足式(1)之範圍的沃斯田鐵粒係50%以上,-400MPa≦σR≦200MPa (1);於前述鋼板表面具有含有小於7質量%之Fe,且剩餘部分係由Zn、Al及不可避免的不純物所構成的熔融鍍鋅層。
- 如申請專利範圍第1項之熔融鍍鋅鋼板,其中前述沃斯 田鐵之平均粒徑係10μm以下,沃斯田鐵中之平均C濃度以質量%計係0.7%以上且1.5%以下。
- 如申請專利範圍第1或2項之熔融鍍鋅鋼板,其中前述沃斯田鐵粒之相對於軋延方向的平均長寬比係0.5以上且0.95以下。
- 如申請專利範圍第1或2項之熔融鍍鋅鋼板,其以質量%計,更含有:Mo:0.02%以上且0.5%以下、Nb:0.01%以上且0.10%以下、Ti:0.01%以上且0.20%以下、V:0.005%以上且0.10%以下、Cr:0.1%以上且2.0%以下、Ca:0.0005%以上且0.05%以下、Mg:0.0005%以上且0.05%以下、REM:0.0005%以上且0.05%以下、Cu:0.04%以上且2.0%以下、Ni:0.02%以上且1.0%以下、及B:0.0003%以上且0.007%以下之1種或2種以上的元素。
- 一種熔融鍍鋅鋼板之製造方法,其特徵在於,其係對以質量%計,含有:C:0.10%以上且0.4%以下、Si:0.01%以上且0.5%以下、Mn:1.0%以上且3.0%以下、O:0.006%以下、P:0.04%以下、S:0.01%以下、Al:0.1以上且3.0%以下、N:0.01%以下、及Si+Al≧0.5%,並由剩餘部分之Fe及不可避免的不 純物所構成的鋼材,進行下述步驟:於熱軋扁鋼胚溫度為1100℃以上,且完成溫度為850~970℃下施行熱軋延處理;將前述熱軋延後之鋼板以平均10~200℃/秒冷卻至650℃以下的溫度域為止,並於650℃以下之溫度範圍捲取;對該鋼板以軋縮率為40%以上施行冷軋延;以退火時之最高溫度為700~900℃進行退火,並以平均0.1~200℃/秒之冷卻速度冷卻至350℃~550℃之溫度域內,之後,於該溫度域內保持1秒以上且1000秒以下;將於該溫度域內保持後之鋼板浸漬於熔融鍍鋅浴,並於該鍍敷處理後,於470~580℃之溫度範圍施行合金化處理;且於將前述鋼板保持於350℃~550℃之溫度域內時,藉由使用輥徑為50~2000mm之輥將鋼板重複折彎,來賦與該鋼板應變;並且該重複折彎時所施加於前述鋼板之長度方向的平均應力係2~50MPa。
- 如申請專利範圍第5項之熔融鍍鋅鋼板之製造方法,其中前述重複折彎時的道次數係2~6道次。
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Publication number | Priority date | Publication date | Assignee | Title |
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TWI829576B (zh) * | 2022-04-20 | 2024-01-11 | 日商日本製鐵股份有限公司 | 熔融鍍敷鋼材 |
Families Citing this family (20)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP6119655B2 (ja) * | 2014-03-31 | 2017-04-26 | Jfeスチール株式会社 | 鋼帯内における材質のバラツキが小さい成形性に優れた高強度合金化溶融亜鉛めっき鋼帯およびその製造方法 |
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US10626485B2 (en) * | 2015-02-17 | 2020-04-21 | Jfe Steel Corporation | Thin high-strength cold-rolled steel sheet and method of producing the same |
JP6348435B2 (ja) * | 2015-02-27 | 2018-06-27 | 株式会社神戸製鋼所 | 高強度高延性鋼板 |
CN105986175B (zh) * | 2015-03-02 | 2018-01-16 | 中国钢铁股份有限公司 | 高强度高延展性钢材的制造方法 |
MX2018007185A (es) | 2015-12-15 | 2018-08-01 | Tata Steel Ijmuiden Bv | Cinta de acero galvanizada por inmersion en caliente de alta resistencia. |
WO2017125773A1 (en) * | 2016-01-18 | 2017-07-27 | Arcelormittal | High strength steel sheet having excellent formability and a method of manufacturing the same |
MX2018008543A (es) | 2016-02-25 | 2018-09-19 | Nippon Steel & Sumitomo Metal Corp | Lamina de acero galvanizada por inmersion en caliente, de alta resistencia, con excelente resistencia a la descamacion por impacto y resistencia a la corrosion en la seccion trabajada. |
BR112018073175B1 (pt) * | 2016-05-10 | 2022-08-16 | United States Steel Corporation | Produto de chapa de aço laminada a frio de alta resistência, e, método para produzir um produto de chapa de aço laminada a frio de alta resistência |
US11560606B2 (en) | 2016-05-10 | 2023-01-24 | United States Steel Corporation | Methods of producing continuously cast hot rolled high strength steel sheet products |
US11993823B2 (en) | 2016-05-10 | 2024-05-28 | United States Steel Corporation | High strength annealed steel products and annealing processes for making the same |
CN106801198B (zh) * | 2017-02-07 | 2018-02-09 | 和县隆盛精密机械有限公司 | 一种适用于机械臂弯曲件的合金铸件及其热处理工艺 |
KR102265252B1 (ko) * | 2017-02-28 | 2021-06-14 | 제이에프이 스틸 가부시키가이샤 | 고강도 강판 및 그 제조 방법 |
JP6443594B1 (ja) | 2017-10-20 | 2018-12-26 | Jfeスチール株式会社 | 高強度鋼板およびその製造方法 |
CN111247264A (zh) * | 2017-10-20 | 2020-06-05 | 杰富意钢铁株式会社 | 高强度钢板及其制造方法 |
JP6787523B1 (ja) * | 2019-01-30 | 2020-11-18 | Jfeスチール株式会社 | 高強度鋼板およびその製造方法 |
WO2020179292A1 (ja) * | 2019-03-06 | 2020-09-10 | 日本製鉄株式会社 | 熱延鋼板 |
EP3936630A4 (en) * | 2019-03-06 | 2022-11-02 | Nippon Steel Corporation | HOT ROLLED STEEL SHEET |
CN110202868B (zh) * | 2019-07-15 | 2021-03-23 | 哈尔滨工业大学 | 一种Nb/高Nb-TiAl层状复合材料及其制备方法 |
EP4079943A4 (en) * | 2019-12-20 | 2022-12-21 | Nippon Steel Corporation | NICKEL-PLATED STEEL SHEET AND METHOD OF PRODUCTION OF NICKEL-PLATED STEEL SHEET |
Family Cites Families (25)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS59219473A (ja) | 1983-05-26 | 1984-12-10 | Nippon Steel Corp | カラ−エツチング液及びエツチング方法 |
JPH0762178B2 (ja) | 1990-07-30 | 1995-07-05 | 新日本製鐵株式会社 | 伸びフランジ性と延性の優れた高強度熱延鋼板の製造方法 |
KR960006583B1 (ko) | 1992-05-25 | 1996-05-20 | 십닙폰세이테쭈 카부시키가이샤 | 강대의 연속소둔설비 |
DE69431134T2 (de) | 1994-03-02 | 2002-12-12 | Nippon Steel Corp | Vorrichtung zur Regelung des Bandzuges in Durchlaufglühanlagen für Stahlband |
JP2002030403A (ja) | 2000-07-14 | 2002-01-31 | Sumitomo Metal Ind Ltd | 合金化溶融亜鉛めっき鋼板とその製造方法 |
JP3775334B2 (ja) | 2002-04-18 | 2006-05-17 | Jfeスチール株式会社 | 加工性に優れた高張力鋼板ならびにその製造方法および加工方法 |
EP1431406A1 (en) * | 2002-12-20 | 2004-06-23 | Sidmar N.V. | A steel composition for the production of cold rolled multiphase steel products |
DE602004027803D1 (de) * | 2003-03-31 | 2010-08-05 | Nippon Steel Corp | Nach dem heisstauchverfahren mit legiertem zink beschichtetes stahlblech und herstellungsverfahren dafür |
DE602004027475D1 (de) * | 2003-04-10 | 2010-07-15 | Arcelor France | Ein herstellungsverfahren für feuerverzinktes stahlblech mit hoher festigkeit |
JP4235030B2 (ja) * | 2003-05-21 | 2009-03-04 | 新日本製鐵株式会社 | 局部成形性に優れ溶接部の硬さ上昇を抑制した引張強さが780MPa以上の高強度冷延鋼板および高強度表面処理鋼板 |
JP4325865B2 (ja) | 2003-08-29 | 2009-09-02 | 株式会社神戸製鋼所 | 加工性に優れた高張力鋼板およびその製法 |
JP2006265671A (ja) * | 2005-03-25 | 2006-10-05 | Nisshin Steel Co Ltd | 加工性及び耐溶融金属脆化割れ性に優れた合金化溶融亜鉛めっき高張力鋼板 |
JP5250938B2 (ja) | 2005-03-31 | 2013-07-31 | Jfeスチール株式会社 | 延性に優れる低降伏比型高強度合金化溶融亜鉛めっき鋼板およびその製造方法 |
JP5250939B2 (ja) | 2005-03-31 | 2013-07-31 | Jfeスチール株式会社 | 合金化溶融亜鉛めっき鋼板の製造方法 |
JP4956998B2 (ja) | 2005-05-30 | 2012-06-20 | Jfeスチール株式会社 | 成形性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
RU2418094C2 (ru) * | 2006-01-30 | 2011-05-10 | Ниппон Стил Корпорейшн | Высокопрочный горячеоцинкованный погружением стальной лист и высокопрочный отожженный после цинкования стальной лист с превосходными формуемостью и способностью к нанесению гальванопокрытия и способы изготовления и устройства для изготовления таких листов |
EP1887746A1 (de) | 2006-08-09 | 2008-02-13 | MintNet GmbH | Sicherungssystem und -verfahren für elektronische Post |
JP5070865B2 (ja) | 2007-02-02 | 2012-11-14 | 住友金属工業株式会社 | 局部延性能に優れた熱延鋼板及びその製造方法 |
EP2009129A1 (en) * | 2007-06-29 | 2008-12-31 | ArcelorMittal France | Process for manufacturing a galvannealed steel sheet by DFF regulation |
EP2009127A1 (en) * | 2007-06-29 | 2008-12-31 | ArcelorMittal France | Process for manufacturing a galvanized or a galvannealed steel sheet by DFF regulation |
KR101130837B1 (ko) | 2008-04-10 | 2012-03-28 | 신닛뽄세이테쯔 카부시키카이샤 | 구멍 확장성과 연성의 균형이 극히 양호하고, 피로 내구성도 우수한 고강도 강판과 아연 도금 강판 및 이 강판들의 제조 방법 |
CN102137943B (zh) | 2009-04-22 | 2013-01-09 | 新日铁工程技术株式会社 | 冷轧钢板的制造方法及其制造设备 |
CA2781815C (en) * | 2009-11-30 | 2015-04-14 | Nippon Steel Corporation | High strength steel plate with ultimate tensile strength of 900 mpa or more excellent in hydrogen embrittlement resistance and method of production of same |
JP5651964B2 (ja) * | 2010-02-16 | 2015-01-14 | 新日鐵住金株式会社 | 延性及び穴広げ性並びに耐食性に優れた合金化溶融亜鉛めっき鋼板及びその製造方法 |
JP5488129B2 (ja) * | 2010-03-31 | 2014-05-14 | 新日鐵住金株式会社 | 冷延鋼板およびその製造方法 |
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