TWI447235B - 成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板及其製造方法 - Google Patents
成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板及其製造方法 Download PDFInfo
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- TWI447235B TWI447235B TW100113120A TW100113120A TWI447235B TW I447235 B TWI447235 B TW I447235B TW 100113120 A TW100113120 A TW 100113120A TW 100113120 A TW100113120 A TW 100113120A TW I447235 B TWI447235 B TW I447235B
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- Prior art keywords
- steel sheet
- galvanized steel
- dip galvanized
- hot
- iron
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- 229910001335 Galvanized steel Inorganic materials 0.000 title claims description 44
- 239000008397 galvanized steel Substances 0.000 title claims description 44
- 238000004519 manufacturing process Methods 0.000 title claims description 14
- 238000000034 method Methods 0.000 title description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 297
- 229910052742 iron Inorganic materials 0.000 claims description 144
- 238000001816 cooling Methods 0.000 claims description 49
- 229910000831 Steel Inorganic materials 0.000 claims description 40
- 239000010959 steel Substances 0.000 claims description 40
- 238000010438 heat treatment Methods 0.000 claims description 39
- 238000005246 galvanizing Methods 0.000 claims description 25
- 239000000203 mixture Substances 0.000 claims description 17
- 239000008187 granular material Substances 0.000 claims description 16
- 229910052748 manganese Inorganic materials 0.000 claims description 14
- 238000002791 soaking Methods 0.000 claims description 14
- 239000002245 particle Substances 0.000 claims description 13
- 229910052796 boron Inorganic materials 0.000 claims description 11
- 238000005275 alloying Methods 0.000 claims description 10
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 8
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 229910052717 sulfur Inorganic materials 0.000 claims description 5
- 229910000734 martensite Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910001563 bainite Inorganic materials 0.000 claims description 2
- 230000001419 dependent effect Effects 0.000 claims 1
- 239000012071 phase Substances 0.000 description 135
- 238000005496 tempering Methods 0.000 description 24
- 230000000694 effects Effects 0.000 description 23
- 238000000137 annealing Methods 0.000 description 22
- 238000005096 rolling process Methods 0.000 description 22
- 229910000859 α-Fe Inorganic materials 0.000 description 17
- 238000007747 plating Methods 0.000 description 12
- 238000010521 absorption reaction Methods 0.000 description 11
- 238000005728 strengthening Methods 0.000 description 9
- 239000011575 calcium Substances 0.000 description 8
- 230000006872 improvement Effects 0.000 description 8
- 230000008569 process Effects 0.000 description 8
- 239000013078 crystal Substances 0.000 description 7
- 229920006395 saturated elastomer Polymers 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 239000002131 composite material Substances 0.000 description 5
- 238000005098 hot rolling Methods 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- 238000005097 cold rolling Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 239000000446 fuel Substances 0.000 description 4
- 229910052698 phosphorus Inorganic materials 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 230000029052 metamorphosis Effects 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 239000013585 weight reducing agent Substances 0.000 description 3
- 230000032683 aging Effects 0.000 description 2
- 230000037396 body weight Effects 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 230000008520 organization Effects 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 239000011701 zinc Substances 0.000 description 2
- 238000012935 Averaging Methods 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000005294 ferromagnetic effect Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 229910001568 polygonal ferrite Inorganic materials 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000000644 propagated effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 229910052712 strontium Inorganic materials 0.000 description 1
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium atom Chemical compound [Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Classifications
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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
-
- 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
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
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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
- C21D6/00—Heat treatment 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/001—Heat treatment of ferrous alloys containing Ni
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
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- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C21D8/0221—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
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- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
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- 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
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- C—CHEMISTRY; METALLURGY
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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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- 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
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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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
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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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
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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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
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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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- C23C2/0224—Two or more thermal pretreatments
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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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- 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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- 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
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
- C23C2/29—Cooling or quenching
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Description
本發明係關於主要適用於汽車構造構件的成形性優異之高強度熔融鍍鋅鋼板,特別係關於具有980MPa以上拉伸強度TS,且擴孔性等成形性、與依高速進行變形時的衝擊吸收性均優異的高強度熔融鍍鋅鋼板及其製造方法。
近年,在衝撞時對駕駛員的安全性確保、以及藉由車體輕量化達到燃料消耗改善之目的下,TS(拉伸強度)為980MPa以上、且板厚較薄的高強度鋼板對於汽車構造構件的應用正積極進展。然而,一般因為鋼板的高強度化會導致鋼板的擴孔性等降低,因而期盼兼具高強度與優異成形性的鋼板。且,因為隨鋼板的高強度化而衍生之軋延性降低,會導致衝撞時的塑性變形能力受損,因而能量吸收量會隨之減少,故期待高速變形下的能量吸收能力提升。
針對此種需求,例如專利文獻1提案有:成形性及鍍敷密接性均優異的高強度合金化熔融鍍鋅鋼板,其係在依質量%計,含有:C:0.04~0.1%、Si:0.4~2.0%、Mn:1.5~3.0%、B:0.0005~0.005%、P≦0.1%、4N<Ti≦0.05%、Nb≦0.1%,其餘部分為Fe及不可避免的雜質構成的鋼板表層上,設有合金化鍍鋅層,而合金化熔融鍍鋅層中的Fe%為5~25%,且鋼板的組織係屬於肥粒鐵(ferrite)相與麻田散鐵(martensite)相之混合組織的TS為800MPa以上。
專利文獻2提案有:成形性佳的高強度合金化熔融鍍鋅鋼板,其係由依質量%計,C:0.05~0.15%、Si:0.3~1.5%、Mn:1.5~2.8%、P:0.03%以下、S:0.02%以下、Al:0.005~0.5%、N:0.0060%以下、其餘部分為Fe及不可避免的雜質構成,並滿足(Mn%)/(C%)≧15、且(Si%)/(C%)≧4,肥粒鐵相中,依體積率計含有3~20%的麻田散鐵相與殘留沃斯田鐵(retained austenite)相。
專利文獻3提案有:擴孔性優異且低降伏比的高強度冷軋鋼板與高強度鍍敷鋼板,其係由依質量%計,含有:C:0.04~0.14%、Si:0.4~2.2%、Mn:1.2~2.4%、P:0.02%以下、S:0.01%以下、Al:0.002~0.5%、Ti:0.005~0.1%、N:0.006%以下,且滿足(Ti%)/(S%)≧5,其餘部分由Fe及不可避免的雜質構成,麻田散鐵相與殘留沃斯田鐵相的體積率合計為6%以上,且將麻田散鐵相、殘留沃斯田鐵相及變韌鐵(bainite)相的硬質相組織之體積率設為α%時,
α≦50000×{(Ti%)/48+(Nb%)/93+(Mo%)/96+(V%)/51}。
專利文獻4提案有:成形時的鍍敷密接性及軋延性均優異之高強度熔融鍍鋅鋼板,其係在依質量%計,含有:C:0.001~0.3%、Si:0.01~2.5%、Mn:0.01~3%、Al:0.001~4%,其餘部分為Fe及不可避免的雜質構成的鋼板表面上,設有由依質量%計,含有:Al:0.001~0.5%、Mn:0.001~2%,其餘部分為Zn及不可避免的雜質所構成鍍敷層的熔融鍍鋅鋼板,其中,鋼的Si含有率:X質量%、鋼的Mn含有率:Y質量%、鋼的Al含有率:Z質量%、鍍敷層的Al含有率:A質量%、鍍敷層的Mn含有率:B質量%,係滿足0≦3-(X+Y/10+Z/3)-12.5×(A-B),鋼板的微觀組織係依體積率計為70~97%的肥粒鐵主相,且其平均粒徑在20μm以下,第2相係依體積率計由3~30%的沃斯田鐵相及/或麻田散鐵相構成,第2相的平均粒徑為10μm以下。
[專利文獻1]日本專利特開平9-13147號公報
[專利文獻2]日本專利特開平11-279691號公報
[專利文獻3]日本專利特開2002-69574號公報
[專利文獻4]日本專利特開2003-55751號公報
然而,專利文獻1~4所記載的高強度冷軋鋼板與高強度熔融鍍鋅鋼板,若欲獲得980MPa以上的TS,則勢必無法獲得優異的擴孔性等成形性。且,對於衝撞時的能量吸收能力均無任何考慮。
本發明之目的在於提供:具有980MPa以上的TS,且擴孔性等成形性良好,且高速變形時的能量吸收能力(耐衝擊性)優異之高強度熔融鍍鋅鋼板及其製造方法。
本發明者等針對具有980MPa以上的TS,呈現良好的軋延性與擴孔性,且衝撞時的能量吸收能力優異之高強度熔融鍍鋅鋼板不斷進行深入鑽研,結果發現下述事項:
i)使成分組成依滿足特定關係之方式進行適當化,並藉由以30%以上的面積率單獨含有回火麻田散鐵(tempered-martensite)相、或含有回火麻田散鐵相與變韌鐵相2種的合計,且將回火麻田散鐵相的最靠近間距離設為10μm以下,便可達成980MPa以上的TS、良好的軋延性與擴孔性、以及優異的能量吸收能力。
ii)此種微觀組織係藉由依5℃/s以上的平均加熱速度加熱至Ac1
變態點以上的溫度域,然後依未滿5℃/s的平均加熱速度加熱至(Ac3
-50)℃以上,接著,在(Ac3
-50)℃以上且(Ac3
+50)℃以下的溫度域中施行30~500s均熱,再依3~30℃/s的平均冷卻速度施行一次冷卻至600℃以下的溫度域,接著,施行熔融鍍鋅後,在200℃~400℃溫度域中依成為15℃/s以下的平均冷卻速度之方式施行二次冷卻,便可獲得。
本發明係根據上述發現而完成,解決上述課題的本發明手段係如下述。
[1]一種成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其特徵為,成分組成依質量%計,係含有:C:0.03~0.13%、Si:1.0~2.0%、Mn:2.4~3.5%、P:0.001~0.05%、S:0.0001~0.01%、Al:0.001~0.1%、N:0.0005~0.01%、B:0.0003~0.01%,且C、Mn、B的含有量滿足下式(1),其餘部分由Fe及不可避免的雜質構成,組織係回火麻田散鐵相與變韌鐵相依合計面積率計含有30%以上(當沒有變韌鐵相時則為回火麻田散鐵相依面積率計含有30%以上),且回火麻田散鐵相的最靠近間距離係10μm以下。
(%Mn)+1000×(%B)≧35×(%C)…(1)
[2]如[1]所記載的成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,上述回火麻田散鐵相的平均粒徑係2.0μm以上。
[3]如[1]或[2]所記載的成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,成分組成依質量%計,係進一步含有從Ti:0.0005~0.1%、Nb:0.0005~0.05%中選擇之至少1種元素。
[4]如[1]~[3]項中任一項所記載的成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,成分組成依質量%計,係進一步含有從Cr:0.01~1.0%、Mo:0.01~1.0%、Ni:0.01~2.0%、Cu:0.01~2.0%中選擇之至少1種元素。
[5]如[1]~[4]項中任一項所記載的成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,成分組成依質量%計,係進一步含有Ca:0.001~0.005%。
[6]如[1]~[5]項中任一項所記載的成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,高強度熔融鍍鋅鋼板係高強度合金化熔融鍍鋅鋼板。
[7]一種成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板之製造方法,係將具有[1]、[3]~[5]項中任一項所記載成分組成的鋼板,依5℃/s以上的平均加熱速度加熱至Ac1
變態點以上的溫度域,然後依未滿5℃/s的平均加熱速度加熱至(Ac3
-50)℃以上,接著在(Ac3
-50)℃以上且(Ac3
+50)℃以下的溫度域中施行30~500s均熱,再依3~30℃/s的平均冷卻速度施行一次冷卻至600℃以下的溫度域,接著,施行熔融鍍鋅後,在200℃~400℃溫度域中依成為15℃/s以下的平均冷卻速度之方式施行二次冷卻。
[8]如[7]所記載的成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板之製造方法,其中,在上述一次冷卻後、且施行上述熔融鍍鋅前,在300~550℃溫度域中保持20~150s。
[9]如[7]或[8]所記載的成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板之製造方法,其中,在施行上述熔融鍍鋅後、且上述二次冷卻前,在450~600℃溫度域中施行鍍鋅的合金化處理。
根據本發明,可製造具有980MPa以上的TS,且擴孔性等成形性良好,且高速變形時的能量吸收能力優異之高強度熔融鍍鋅鋼板。藉由將本發明的高強度熔融鍍鋅鋼板應用於汽車構造構件,便可圖謀更進一步的駕駛員安全性確保、以及利用大幅度車體輕量化所得之燃料消耗改善。
以下,針對本發明的詳細內容進行說明。另外,表示成分元素含有量的「%」,在無特別聲明的前提下係指「質量%」。
1)成分組成
C:0.03~0.13%
C係在強化鋼時的重要元素,具有高固溶強化能力,且當利用由麻田散鐵相所造成的組織強化時,屬於為調整其面積率與硬度而不可或缺的元素。若C量未滿0.03%,便難以獲得必要面積率的麻田散鐵相,且因為麻田散鐵相不會硬質化,因而無法獲得充分的強度。另一方面,若C量超過0.13%,則熔接性會劣化,且麻田散鐵相會明顯硬化,且自行回火作用受抑制,導致成形性(特別係擴孔性)降低。故,C量係設為0.03~0.13%。
Si:1.0~2.0%
Si在本發明中係極重要元素,在退火時會促進肥粒鐵變態,且將固溶C從肥粒鐵相排出於沃斯田鐵相,俾將肥粒鐵相潔淨化,而提升軋延性,同時將沃斯田鐵相安定化,因而即便在難以施行急冷的連續熔融鍍鋅生產線上施行退火之情況,仍會生成麻田散鐵相,使複合組織化較為容易。又,Si係將肥粒鐵相予以固溶強化,降低肥粒鐵相與麻田散鐵相的硬度差,抑制在其界面處生成龜裂,改善局部變形能力,對擴孔性的提升具貢獻。且,固溶於肥粒鐵相中的Si會促進加工硬化而提高軋延性,且會改善應變集中部位的應變傳播性,俾提升擴孔性,並抑制高速變形時的局部性破壞。為能獲得此種效果,必須將Si量設為1.0%以上。另一方面,若Si量超過2.0%,則效果已飽和,且表面性狀會出現頗大的問題。故,Si量係設為1.0~2.0%。
Mn:2.4~3.5%
Mn係有效於防止鋼的熱脆化、以及確保強度,且提升淬火性俾使複合組織化較為容易。且,在退火時使未變態沃斯田鐵相的比例增加,使其C濃度減少,容易產生在退火時的冷卻過程、與熔融鍍鋅處理後的冷卻過程所生成麻田散鐵相的自行回火,降低最終組織中的麻田散鐵相硬度,抑制局部變形,對擴孔性的提升具頗大貢獻。且,Mn的添加會使變態點降低,促進加熱時朝沃斯田鐵的逆變態,使麻田散鐵相呈緻密分散。為能獲得此種效果,必須將Mn量設為2.4%以上。另一方面,若Mn量超過3.5%,會明顯生成偏析層,導致成形性劣化。故,Mn量係設為2.4~3.5%。
P:0.001~0.05%
P係配合所需強度可添加的元素,且因為會促進肥粒鐵變態,因而亦屬於複合組織化的有效元素。為能獲得此種效果,必須將P量設為0.001%以上。另一方面,若P量超過0.05%,會導致熔接性劣化,且當將鍍鋅施行合金化處理時,會造成合金化速度降低,而損及鍍鋅的品質。故,P量係設為0.001~0.05%。
S:0.0001~0.01%
S會偏析於粒界導致在熱加工時使鋼脆化,且依硫化物形式存在導致局部變形能力降低,因而其量必須設在0.01%以下、較佳係0.003%以下、更佳係0.001%以下。但是,就從生產技術上的限制觀點而言,S量必須達0.0001%以上。故,S量設為0.0001~0.01%、較佳0.0001~0.003%、更佳0.0001~0.001%。
Al:0.001~0.1%
Al係使肥粒鐵相生成,對強度-軋延性均衡的提升屬有效的元素。為能獲得此種效果,必須將Al量設為0.001%以上。另一方面,若Al量超過0.1%,會導致表面性狀劣化。故,Al量係設為0.001~0.1%。
N:0.0005~0.01%
N係會使鋼的抗老化性劣化之元素。特別係若N量超過0.01%,抗老化性的劣化會趨於明顯。其量係越少越佳,但就從生產技術上的限制而言,N量必須達0.0005%以上。故,N量係設為0.0005~0.01%。
B:0.0003~0.01%
B係提升淬火性俾使複合組織化較為容易。且,抑制冷卻時的肥粒鐵與波來鐵(pearlite)等擴散變態,使未變態沃斯田鐵相的比例增加,俾使其C濃度減少,容易產生在退火時的冷卻過程、與熔融鍍鋅處理後的冷卻過程中所生成麻田散鐵相的自行回火,俾降低最終組織中的麻田散鐵相硬度,抑制局部變形,對擴孔性提升具頗大貢獻。為能獲得此種效果,B量必須達0.0003%以上。另一方面,若B量超過0.01%,會導致軋延性降低。故,B量係設為0.0003~0.01%。
(%Mn)+1000×(%B)≧35×(%C)
回火麻田散鐵相主要係在熔融鍍鋅後的二次冷卻過程中,利用與麻田散鐵變態同時引發回火的自行回火而生成,為能有效率地產生此現象時,便依使Ms點上升的方式,未變態沃斯田鐵中的C濃度越小越佳。變韌鐵相係在均熱後的一次冷卻或者接著的保持過程中生成,而為能有效率地產生此現象,便依使未變態沃斯田鐵呈不安定的方式,C濃度越小越佳。
所以,為能依既定分率獲得回火麻田散鐵相與變韌鐵相,必須調整退火時的未變態沃斯田鐵量、與其中的C濃度。未變態沃斯田鐵量係利用成分元素控制變態點便可進行調整,特別係必須嚴格控制影響較大的Mn與B之添加量。未變態沃斯田鐵中的C濃度係除在鋼中的添加量之外,尚有C元素在均熱時會被分配於未變態沃斯田鐵中的傾向,因而強烈依存於未變態沃斯田鐵量。考慮該等因素,為能在上述成分組成範圍內,可依既定分率獲得回火麻田散鐵相與變韌鐵相,Mn、B、C的添加量必須控制於經驗求得的下式範圍內。
(%Mn)+1000×(%B)≧35×(%C)
其餘部分係Fe及不可避免的雜質,由於以下的理由,較佳係含有:從Ti:0.0005~0.1%、Nb:0.0005~0.05%中選擇之至少1種元素、或從Cr:0.01~1.0%、Mo:0.01~1.0%、Ni:0.01~2.0%、Cu:0.01~2.0%中選擇之至少1種元素、或Ca:0.001~0.005%。
Ti:0.0005~0.1%
Ti會與C、S、N形成析出物,對強度及韌性的提升具有效貢獻。又,因為利用析出強化而強化鋼,因而可配合所需強度進行添加。又,Ti係當與B同時含有的情況,因為會使N依TiN形式析出,因而BN的析出受抑制,俾有效地顯現出上述B的效果。為能獲得此種效果,必須將Ti量設為0.0005%以上。另一方面,若Ti量超過0.1%,析出強化會過度作用,反將導致軋延性降低。故,Ti量係設為0.0005~0.1%。
Nb:0.0005~0.05%
Nb係利用析出強化而強化鋼,因而可配合所需強度進行添加。為能獲得此種效果,Nb量必須添加0.0005%以上。若Nb量超過0.05%,析出強化會過度作用,反將導致軋延性降低。故,Nb量係設為0.0005~0.05%。
Cr:0.01~1.0%、Mo:0.01~1.0%、Ni:0.01~2.0%、Cu:0.01~2.0%
Cr、Mo、Ni、Cu不僅具有當作固溶強化元素的功用,在退火時的冷卻過程,會使沃斯田鐵相呈安定化,使複合組織化較為容易。為能獲得此種效果,Cr量、Mo量、Ni量及Cu量分別必須設為0.01%以上。另一方面,若Cr量超過1.0%、Mo量超過1.0%、Ni量超過2.0%、Cu量超過2.0%,則鍍敷性、成形性及點熔接性會劣化。故,Cr量係設為0.01~1.0%、Mo量係設為0.01~1.0%、Ni量係設為0.01~2.0%、Cu量係設為0.01~2.0%。
Ca:0.001~0.005%
Ca係使S依CaS形式析出,俾抑制會助長龜裂產生與傳播的MnS生成,具有使擴孔性提升的效果。為能獲得此種效果,必須將Ca量設為0.001%以上。另一方面,若Ca量超過0.005%,則此項效果已飽和。故,Ca量係設為0.001~0.005%。
2)微觀組織
回火麻田散鐵相與變韌鐵相的合計面積率(當沒有變韌鐵相時則為回火麻田散鐵相的面積率):30%以上
在微觀組織中,為達成980MPa以上的強度,係含有麻田散鐵相。為能提高諸如擴孔性的局部變形能力,且為使高速變形時的應變傳播性提高,麻田散鐵相係必須含有較軟質之經回火的麻田散鐵相。將回火麻田散鐵其中一部分取代為變韌鐵亦同樣可獲得此種效果。為能有效地顯現該等效果,必須將組織整體中所佔的回火麻田散鐵相與變韌鐵相之合計面積率設為30%以上(當沒有變韌鐵相時則將回火麻田散鐵相的面積率設為30%以上)。麻田散鐵相係可含有未回火麻田散鐵相。另外,當含有回火麻田散鐵相與變韌鐵相二者的情況,就從強度確保的觀點而言,在組織整體中所佔的回火麻田散鐵相比例,較佳係10%以上。
此處所謂「未回火麻田散鐵相」係指具有與變態前的沃斯田鐵相相同之化學組成,具有C過飽和固溶之體心立方結構的組織,且具有條、束、塊等微視構造的高差排密度硬質相。所謂「回火麻田散鐵相」係從麻田散鐵相中將過飽和的固溶C依碳化物形式析出,維持母相微視構造的高差排密度肥粒鐵相。又,回火麻田散鐵相係無須依照用以獲得其的熱經歷,例如淬火-回火與自行回火等,而特別區分。
回火麻田散鐵相的最靠近間距離:10μm以下
即便回火麻田散鐵滿足上述面積率,但當粗大且稀疏分佈的情況,在與該等鄰接異相間的界面處容易進行龜裂傳播,特別係會使高速變形下的軋延性降低,無法獲得充分的能量吸收能力。當回火麻田散鐵細微且緻密分佈時,各個回火麻田散鐵粒會成為龜裂傳播的阻力,特別係會使高速變形下的軋延性上升,俾提升能量吸收能力。為能充分獲得此項效果,必須將回火麻田散鐵相的最靠近間距離設為10μm以下。
回火麻田散鐵相的平均粒徑:2.0μm以上
若回火麻田散鐵相的粒徑過度細微,產生局部性龜裂的起點便會呈高密度,容易導致局部變形能力降低,因而較佳係將其平均粒徑設為2.0μm以上。
另外,除上述相以外的相,較佳係主要為肥粒鐵相。除此之外,即便含有殘留沃斯田鐵相、波來鐵相,仍不會損及本發明效果。
此處所謂「各相的面積率」係指在觀察視野面積中所佔的各相面積比例。如本發明的鋼板,因為三維的組織呈均勻,因而可採用與體積率同值。依此各相的面積率、最靠近間距離及回火麻田散鐵相的平均粒徑,係將平行於鋼板軋延方向的板厚截面施行研磨後,再利用3%Nital施行腐蝕,然後使用SEM(掃描式電子顯微鏡)依2000倍的倍率觀察10視野,並使用市售影像處理軟體(例如Media Cybernetics公司的Image-Pro)便可求得。未回火麻田散鐵相、與回火麻田散鐵相的判別係可利用Nital腐蝕後的表面形態實施。即,未回火麻田散鐵相係呈平滑表面,而回火麻田散鐵相係結晶粒內會觀察到因腐蝕形成的構造(凹凸)。利用該方法依照結晶粒單位鑑定未回火麻田散鐵相、與回火麻田散鐵相。具體而言,從利用SEM所拍攝到的微觀組織相片,鑑定回火麻田散鐵相與變韌鐵相的相,再利用影像處理軟體,依每個各相施行二值化處理,便可求得各相的面積率。
再者,回火麻田散鐵相的平均粒徑係導出各個結晶粒的圓相當直徑,再將該等予以平均便可求得。
回火麻田散鐵相的最靠近間距離係藉由將回火麻田散鐵相的面積率除以各個回火麻田散鐵粒的面積率,便可求得每單位體積的回火麻田散鐵結晶粒個數,計算出回火麻田散鐵結晶粒每1個所佔的平均佔有面積,再開立方根便可求得。即,依下式進行計算。
LTM
=(dM
/2)×(4π/3f)1/3
LTM
:最靠近間距離
dM
:回火麻田散鐵平均粒徑
f:回火麻田散鐵面積率
3)製造條件
本發明的高強度熔融鍍鋅鋼板係如上述,例如藉由將具有上述成分組成的鋼板,依5℃/s以上的平均加熱速度,加熱至Ac1
變態點以上的溫度域之後,再依未滿5℃/s的平均加熱速度加熱至(Ac3
-50)℃以上的溫度域,接著在(Ac3
-50)℃~(Ac3
+50)℃溫度域中施行30~500s均熱,再以依3~30℃/s的平均冷卻速度施行一次冷卻至600℃以下溫度域的條件施行退火後,施行熔融鍍鋅處理,再於200℃~400℃溫度域中依15℃/s以下的平均冷卻速度施行二次冷卻之方法便可製造。
退火時的加熱條件1:依5℃/s以上的平均加熱速度加熱至Ac1
變態點以上的溫度域
藉由依5℃/s以上的平均加熱速度加熱至Ac1
變態點以上的溫度域,便可在抑制回復與再結晶肥粒鐵相生成的情況下,引發沃斯田鐵變態,因而可增加沃斯田鐵相的比例,最終便容易獲得麻田散鐵相的既定面積率。又,因為可將麻田散鐵相均勻分散,因而可縮短回火麻田散鐵相的最靠近間距離。結果,可在確保必要的強度、提升擴孔性之情況下,提高高速變形下的吸收能量。當直到Ac1
變態點的平均加熱速度係未滿5℃/s的情況、或加熱溫度未滿Ac1
變態點的情況,回復、再結晶會明顯進行,頗難達成必要的回火麻田散鐵與變韌鐵之面積率、以及既定回火麻田散鐵相的最靠近間距離。
退火時的加熱條件2:依未滿5℃/s的平均加熱速度加熱至(Ac3
-50)℃以上
為達成既定的麻田散鐵相面積率與粒徑,必須在從加熱開始的均熱中,使沃斯田鐵相成長至適當尺寸。但是,當高溫域中的平均加熱速度偏大時,因為沃斯田鐵相會細微分散,因而各個沃斯田鐵相無法成長,導致難以依既定面積率獲得最終組織中的回火麻田散鐵相。因而,將朝(Ac3
-50)℃以上的高溫域之平均加熱速度設為未滿5℃/s。當加熱溫度偏低的情況,即便降低加熱速度,未變態沃斯田鐵仍不會成長,因而無法獲得既定的回火麻田散鐵面積率。故,加熱溫度係設為(Ac3
-50)℃以上。
退火時的均熱條件:在(Ac3
-50)℃以上且(Ac3
+50)℃以下的溫度域施行30~500s均熱
藉由在均熱時提高沃斯田鐵相的比例,便可降低沃斯田鐵相中的C量,俾使Ms點上升,可獲得熔融鍍鋅處理後的冷卻過程中之自行回火效果,且即便因回火而降低麻田散鐵相的硬度,仍可達成充分的強度,可獲得980MPa以上之TS、與優異擴孔性、以及高速變形時較高的吸收能量。但是,若均熱溫度超過(Ac3
+50)℃,未變態沃斯田鐵的結晶粒徑會粗大化,導致無法滿足既定的最靠近間距離。又,當均熱時間未滿30s的情況,因為未變態沃斯田鐵不會充分成長,因而無法獲得既定的麻田散鐵相面積率與粒徑。另一方面,當均熱時間超過500s的情況,效果已達飽和,且會抑制生產性。
退火時的冷卻條件:從均熱溫度起,依3~30℃/s的平均冷卻速度施行冷卻至600℃以下的溫度域(一次冷卻)
經均熱後,從均熱溫度起必須依3~30℃/s的平均冷卻速度,施行冷卻至600℃以下的溫度域(冷卻停止溫度),此時若平均冷卻速度未滿3℃/s,在冷卻中會進行肥粒鐵變態,導致無法獲得充分面積率的未變態沃斯田鐵相,且會進行朝未變態沃斯田鐵相中的C濃化,造成不易獲得自行回火效果,導致難以依既定的面積率與最靠近間距離獲得最終組織的回火麻田散鐵相,造成擴孔性降低與高速變形時的能量吸收能力降低。若平均冷卻速度超過30℃/s,抑制肥粒鐵變態的效果已達飽和,且難以依一般的生產設備實現。又,將冷卻停止溫度設定在600℃以下的理由,係若超過600℃,冷卻中的肥粒鐵相生成較為明顯,難以依既定的面積率獲得回火麻田散鐵相與變韌鐵相之緣故。
經退火後,依通常的條件施行熔融鍍鋅處理,但在此之前,較佳係施行如下述的熱處理。
退火後的熱處理條件:在300~550℃溫度域施行20~150s熱處理
經退火後,藉由在300~550℃溫度域施行20~150s熱處理,便會更加促進利用自行回火進行的麻田散鐵相硬度降低,或者藉由出現變韌鐵相,而更有效地縮小各相間的硬度差,俾可更進一步改善擴孔性及高速變形時的能量吸收能力。當熱處理溫度未滿300℃的情況、與熱處理時間未滿20s的情況,此種效果會降低。另一方面,當熱處理溫度超過550℃時,因為會進行肥粒鐵相與波來鐵相的變態,以及C的濃化會過剩,導致阻礙麻田散鐵的自行回火,因而最終組織難以獲得既定的回火麻田散鐵分率。當熱處理時間超過150s的情況,此項效果已達飽和,且會抑制生產性。
熔融鍍鋅後的冷卻條件:在200℃~400℃溫度域中依成為15℃/s以下的平均冷卻速度之方式施行冷卻(二次冷卻)
經施行熔融鍍鋅後,必須在200℃~400℃溫度域中依成為15℃/s以下的平均冷卻速度之方式施行二次冷卻,此係為確保在會產生自行回火的溫度域中之滯留時間。若超過400℃的溫度,麻田散鐵變態便不會充分生成,若未滿200℃的溫度,則不會進行元素的擴散,因而即便將平均冷卻速度設在15℃/s以下,仍不會充分進行自行回火。另一方面,當平均冷卻速度超過15℃/s的情況,即便有生成麻田散鐵變態,但卻無法確保為充分進行自行回火所需要的時間。
再者,當施行鍍鋅的合金化處理時,不管在退火後是否有施行在上述300~550℃溫度域中的熱處理,均可在施行熔融鍍鋅處理後、且二次冷卻前,在450~600℃溫度域將鍍鋅施行合金化處理。藉由在450~600℃溫度域施行合金化處理,鍍敷中的Fe濃度便會成為8~12%,俾提升鍍敷的密接性、以及塗裝後的耐蝕性。若未滿450℃,合金化便不會充分進行,導致犧牲防蝕作用降低、以及滑動性降低,若超過600℃,合金化會過度進行,導致粉化性降低。又,肥粒鐵相與波來鐵相等會大量生成,導致無法達高強度化。
製造方法之其他的條件,並無特別的限定,較佳係依以下的條件實施。
本發明的高強度熔融鍍鋅鋼板所使用之退火前的鋼板,係將具有上述成分組成的鋼胚,經熱軋後,再冷軋至所需板厚便可製得。又,就從生產性的觀點而言,高強度熔融鍍鋅鋼板較佳係利用熔融鍍鋅前的退火、熱處理、熔融鍍鋅、以及鍍鋅的合金化處理等可連續施行一連串處理的連續熔融鍍鋅生產線進行製造。
鋼胚係為防止巨觀偏析,較佳係利用連續鑄造法進行製造,但亦可利用造塊法、薄鋼胚鑄造法進行製造。當將鋼胚施行熱軋時,鋼胚會被再加熱,而為防止軋延荷重增大,較佳係將加熱溫度設為1150℃以上。又,為防止銹皮損失的增大、與燃料原單位的增加,較佳係將加熱溫度的上限設為1300℃。
熱軋係利用粗軋與精軋實施,精軋係為防止冷軋‧退火後的成形性降低,較佳在Ar3
變態點以上的完軋溫度實施。又,為防止因結晶粒粗大化而造成組織不均勻、與發生銹皮缺陷情形,較佳係將完軋溫度設為950℃以下。
熱軋後的鋼板就從防止銹皮缺陷、與確保良好形狀性的觀點而言,較佳在500~650℃的捲取溫度進行捲取。
捲取後的鋼板利用酸洗等去除銹皮之後,為有效率地生成多邊形肥粒鐵相,較佳係依軋縮率40%以上施行冷軋。
熔融鍍鋅時較佳係使用含有0.10~0.20%Al量的鍍鋅浴。又,在鍍敷後,為調整鍍敷的表觀量,可施行擦拭。
利用真空熔解爐熔製表1所示成分組成的鋼No.A~M,並利用分塊軋延形成片條鋼胚(sheet bar slab)。將該等片條鋼胚加熱至1200℃後,在850~920℃(Ar3
變態點以上)的完軋溫度施行熱軋,再施行600℃的捲取處理。接著,經酸洗後,依軋縮率50%施行冷軋成為表2所示板厚,利用紅外加熱爐依表2所示退火條件施行退火後,再施行一次冷卻,對其中一部分的鋼板依表2所示條件施行熱處理後,於含有0.13%Al的475℃鍍鋅浴中浸漬3s,形成附著量45g/m2
的鍍鋅,再於表2所示溫度施行合金化處理,接著再於200℃~400℃溫度域中依成為表2所示平均冷卻速度的方式施行二次冷卻,便製得鍍鋅鋼板No.1~23。另外,如表2所示,其中一部分鍍鋅鋼板並沒有施行合金化處理。
然後,針對所獲得鍍鋅鋼板,依上述方法,以實施方式所記載的方法求取:肥粒鐵相的面積率、回火麻田散鐵相的面積率、變韌鐵相的面積率、回火麻田散鐵相與變韌鐵相的面積總和、回火麻田散鐵相的平均粒徑及最靠近間距離。又,朝軋延方向的直角方向採取JIS5號拉伸試驗片,根據JIS Z 2241,依20mm/min夾頭速度實施拉伸試驗,測定TS及總伸長率El。又,採取100mm×100mm試驗片,根據JFST 1001(日本鋼鐵協會規格)施行3次擴孔試驗,求取平均的擴孔率λ(%),並評估擴孔性。高速變形特性係在應變速度為2000/s的條件下,利用高速拉伸試驗機實施試驗,測定應力-應變曲線,依公稱應變求取截至15%的吸收能量,利用將其除以TS的數值進行評估。另外,高速拉伸試驗係根據「鐵與鋼」、vol.83(1997)p.748所記載方法實施。結果示於表3。
本發明例的鍍鋅鋼板均屬於TS為980MPa以上,且擴孔率λ為40%以上、TS×El≧18000MPa‧%,成形性優異,且將直到應變量為15%的吸收能量除以TS之數值為0.14以上,可知屬於高速變形時的能量吸收能力優異之高強度熔融鍍鋅鋼板。
根據本發明,可製造具有980MPa以上的TS,且擴孔性等成形性良好,且高速變形時的能量吸收能力優異之高強度熔融鍍鋅鋼板。藉由將本發明的高強度熔融鍍鋅鋼板應用於汽車構造構件,便可圖謀更進一步的駕駛員安全性確保、以及利用大幅度車體輕量化所得之燃料消耗改善。
Claims (9)
- 一種成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其特徵為,成分組成依質量%計,係含有:C:0.03~0.13%、Si:1.0~2.0%、Mn:2.4~3.5%、P:0.001~0.05%、S:0.0001~0.01%、Al:0.001~0.1%、N:0.0005~0.01%、B:0.0003~0.01%,且C、Mn、B的含有量滿足下式(1),其餘部分由Fe及不可避免的雜質構成,組織係回火麻田散鐵(tempered-martensite)相與變韌鐵(bainite)相依合計面積率計含有30%以上(當沒有變韌鐵相時則為回火麻田散鐵相依面積率計含有30%以上),且回火麻田散鐵相的最靠近間距離係10μm以下;(%Mn)+1000×(%B)≧35×(%C)…(1)。
- 如申請專利範圍第1項之成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,上述回火麻田散鐵相的平均粒徑係2.0μm以上。
- 如申請專利範圍第1或2項之成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,成分組成依質量%計,係進一步含有從Ti:0.0005~0.1%、Nb:0.0005~0.05%中選擇之至少1種元素。
- 如申請專利範圍第1或2項之成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,成分組成依質量%計,係進一步含有從Cr:0.01~1.0%、Mo:0.01~1.0%、Ni:0.01~2.0%、Cu:0.01~2.0%中選擇之至少1種元素。
- 如申請專利範圍第1或2項之成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,成分組成依質量%計,係進一步含有Ca:0.001~0.005%。
- 如申請專利範圍第1或2項之成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板,其中,高強度熔融鍍鋅鋼板係高強度合金化熔融鍍鋅鋼板。
- 一種成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板之製造方法,係將具有申請專利範圍第1及3至5項中任一項之成分組成的鋼板,依5℃/s以上的平均加熱速度加熱至Ac1 變態點以上的溫度域,然後依未滿5℃/s的平均加熱速度加熱至(Ac3 -50)℃以上,接著在(Ac3 -50)℃以上且(Ac3 +50)℃以下的溫度域中施行30~500s均熱,再依3~30℃/s的平均冷卻速度施行一次冷卻至600℃以下的溫度域,接著,施行熔融鍍鋅後,在200℃~400℃溫度域中依成為15℃/s以下的平均冷卻速度之方式施行二次冷卻。
- 如申請專利範圍第7項之成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板之製造方法,其中,在上述一次冷卻後、且施行上述熔融鍍鋅前,在300~550℃溫度域中保持20~150s。
- 如申請專利範圍第7或8項之成形性及耐衝擊性優異之高強度熔融鍍鋅鋼板之製造方法,其中,在施行上述熔融鍍鋅後、且上述二次冷卻前,在450~600℃溫度域中施行鍍鋅的合金化處理。
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KR20100046057A (ko) * | 2007-10-25 | 2010-05-04 | 제이에프이 스틸 가부시키가이샤 | 가공성이 우수한 고강도 용융 아연 도금 강판 및 그 제조 방법 |
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JP4894863B2 (ja) * | 2008-02-08 | 2012-03-14 | Jfeスチール株式会社 | 加工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 |
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TW200934881A (en) * | 2008-01-31 | 2009-08-16 | Jfe Steel Corp | High strength galvanized steel sheet excellent in formability and method for manufacturing the same |
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EP2559782A1 (en) | 2013-02-20 |
EP2559782A4 (en) | 2015-10-21 |
CN102859018B (zh) | 2015-05-20 |
TW201142046A (en) | 2011-12-01 |
KR101515695B1 (ko) | 2015-04-27 |
KR20120127671A (ko) | 2012-11-22 |
JP2011225915A (ja) | 2011-11-10 |
US20170130293A1 (en) | 2017-05-11 |
US9982318B2 (en) | 2018-05-29 |
US9617630B2 (en) | 2017-04-11 |
EP2559782B1 (en) | 2017-06-07 |
US20130206288A1 (en) | 2013-08-15 |
CN102859018A (zh) | 2013-01-02 |
JP4893844B2 (ja) | 2012-03-07 |
WO2011129452A1 (ja) | 2011-10-20 |
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