TWI440724B - 成形性優異之高強度熔融鍍鋅鋼板及其製造方法 - Google Patents
成形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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- TWI440724B TWI440724B TW099106396A TW99106396A TWI440724B TW I440724 B TWI440724 B TW I440724B TW 099106396 A TW099106396 A TW 099106396A TW 99106396 A TW99106396 A TW 99106396A TW I440724 B TWI440724 B TW I440724B
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- 229910001335 Galvanized steel Inorganic materials 0.000 title claims description 33
- 239000008397 galvanized steel Substances 0.000 title claims description 33
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 238000000034 method Methods 0.000 title description 21
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 294
- 229910052742 iron Inorganic materials 0.000 claims description 143
- 238000001816 cooling Methods 0.000 claims description 52
- 239000008187 granular material Substances 0.000 claims description 33
- 238000005246 galvanizing Methods 0.000 claims description 32
- 238000010438 heat treatment Methods 0.000 claims description 25
- 238000005496 tempering Methods 0.000 claims description 24
- 238000005096 rolling process Methods 0.000 claims description 22
- 229910000859 α-Fe Inorganic materials 0.000 claims description 21
- 238000011282 treatment Methods 0.000 claims description 17
- 238000005098 hot rolling Methods 0.000 claims description 16
- 239000012535 impurity Substances 0.000 claims description 11
- 238000005275 alloying Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 10
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 230000009467 reduction Effects 0.000 claims description 8
- 238000005097 cold rolling Methods 0.000 claims description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims description 6
- 229910052717 sulfur Inorganic materials 0.000 claims description 6
- 230000009466 transformation Effects 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 4
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 229910000831 Steel Inorganic materials 0.000 description 31
- 239000010959 steel Substances 0.000 description 31
- 230000000694 effects Effects 0.000 description 22
- 238000000137 annealing Methods 0.000 description 15
- 238000007747 plating Methods 0.000 description 12
- 238000002791 soaking Methods 0.000 description 11
- 230000008520 organization Effects 0.000 description 10
- 230000008569 process Effects 0.000 description 10
- 230000015572 biosynthetic process Effects 0.000 description 9
- 239000012467 final product Substances 0.000 description 8
- 230000001965 increasing effect Effects 0.000 description 8
- 239000010410 layer Substances 0.000 description 7
- 238000005452 bending Methods 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 5
- 238000005260 corrosion Methods 0.000 description 5
- 230000006872 improvement Effects 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- 239000002131 composite material Substances 0.000 description 4
- 230000029052 metamorphosis Effects 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 230000002159 abnormal effect Effects 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 230000032683 aging Effects 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000000446 fuel Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000004080 punching Methods 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 244000025254 Cannabis sativa Species 0.000 description 1
- 235000012766 Cannabis sativa ssp. sativa var. sativa Nutrition 0.000 description 1
- 235000012765 Cannabis sativa ssp. sativa var. spontanea Nutrition 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
- 230000009471 action Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 235000009120 camo Nutrition 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 235000005607 chanvre indien Nutrition 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 230000005294 ferromagnetic effect Effects 0.000 description 1
- 239000003337 fertilizer Substances 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 229910052595 hematite Inorganic materials 0.000 description 1
- 239000011019 hematite Substances 0.000 description 1
- 239000011487 hemp Substances 0.000 description 1
- LIKBJVNGSGBSGK-UHFFFAOYSA-N iron(3+);oxygen(2-) Chemical compound [O-2].[O-2].[O-2].[Fe+3].[Fe+3] LIKBJVNGSGBSGK-UHFFFAOYSA-N 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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- C—CHEMISTRY; METALLURGY
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- 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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- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
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- C21D8/0436—Cold rolling
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Description
本發明係關於主要適合於汽車之結構構件之成形性優異之高強度熔融鍍鋅鋼板,尤其係關於具有780 MPa以上之拉伸強度TS,且具有優異之伸長特性、擴孔性、彎曲性之成形性優異之高強度熔融鍍鋅鋼板及其製造方法。
近年來,以確保碰撞時之乘客之安全性及藉由車身輕量化而改善燃料費為目的,正積極地朝汽車結構構件應用TS(tensile strength,拉伸強度)為780 MPa以上、且板厚較薄之高強度鋼板進展。尤其於最近,亦研究應用具有980 MPa等級、1180 MPa等級之TS之極高強度之高強度鋼板。
然而,一般而言,鋼板之高強度化會導致鋼板之伸長特性、擴孔性、彎曲性等降低,從而導致成形性降低,因此當前期望兼具高強度與優異之成形性,進而耐腐蝕性亦優異之熔融鍍鋅鋼板。
針對該期望,例如專利文獻1中提出了一種成形性及鍍敷密著性優異之高強度合金化熔融鍍鋅鋼板,該鋼板以質量%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%,且剩餘部分由Fe及不可避免之雜質所構成,於該鋼板之表層具有合金化鍍鋅層,合金化熔融鍍鋅層中之Fe%為5~25%,且鋼板之組織為肥粒鐵相與麻田散鐵相之混合組織,TS為800 MPa以上。專利文獻2中提出了一種成形性良好之高強度合金化熔融鍍鋅鋼板,該鋼板中以質量%計而具有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,且剩餘部分由Fe及不可避免之雜質所構成,進而滿足(Mn%)/(C%)≧15且(Si%)/(C%)≧4,於肥粒鐵相中含有以體積率計為3~20%之麻田散鐵相及殘留沃斯田鐵相。專利文獻3中提出了一種擴孔性優異、低降伏比且高強度之鍍敷鋼板,該鋼板以質量%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,進而滿足(Ti%)/(S%)≧5,剩餘部分由Fe及不可避免之雜質所構成,當麻田散鐵相與殘留沃斯田鐵相之體積率合計為6%以上,且設麻田散鐵相、殘留沃斯田鐵相及變韌鐵相之硬質相組織之體積率為α%時,α≦50000×{(Ti%)/48+(Nb%)/93+(Mo%)/96+(V%)/51}。專利文獻4中提出了一種成形時之鍍敷密著性及延伸性優異之高強度熔融鍍鋅鋼板,該鋼板係以質量%計而含有C:0.001~0.3%、Si:0.01~2.5%、Mn:0.01~3%、Al:0.001~4%,且剩餘部分由Fe及不可避免之雜質所構成,於該鋼板之表面具有鍍敷層,該鍍敷層以質量%計而含有Al:0.001~0.5%、Mn:0.001~2%,且剩餘部分由Zn及不可避免之雜質所構成,且鋼之Si含有率:X質量%、鋼之Mn含有率:Y質量%、鋼之Al含有率:Z質量%、鍍敷層之Al含有率:A質量%、及鍍敷層之Mn含有率:B質量%,係滿足0≦3-(X+Y/10+Z/3)-12.5×(A-B),鋼板之微組織包含以體積率計為70~97%之肥粒鐵主相,且其平均粒徑為20 μm以下,作為第2相係以體積率計為3~30%之沃斯田鐵相及/或麻田散鐵相,第2相之平均粒徑為10 μm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中記載之高強度熔融鍍鋅鋼板未必能獲得優異之伸長特性、擴孔性及彎曲性。
本發明係有鑑於上述情況,旨在提供具有780 MPa以上之TS,且具有優異之伸長特性、擴孔性及彎曲性之成形性優異之高強度熔融鍍鋅鋼板及其製造方法。
本發明者等為達成上述目的而進行了以下之研究。
實驗性地以真空熔解爐將以質量%計含有C:0.103%、Si:1.29%、Mn:2.41%、P:0.011%、S:0.0021%、Al:0.029%、N:0.0031、Cr:0.31%、Mo:0.12%,且剩餘部分由Fe及不可避免之雜質所構成之鋼熔化而製成鋼坯。以1250℃對該等鋼坯進行加熱後,於880℃之精軋溫度進行熱軋後,經過0.5 s後,以10~250℃/s之平均冷卻速度水冷至550℃以下,再於500~700℃之溫度下捲取,進行相當熱處理而製成熱軋鋼板。藉由酸洗而將該等熱軋鋼板之鏽皮除去後,以軋縮率50%進行冷軋,並仿照熔融鍍鋅生產線,以5℃/s以上之平均加熱速度加熱至700℃,繼而於700~900℃之溫度區域均熱120 s,再以10℃/s之平均冷卻速度冷卻至520℃以下之溫度區域而退火後,將該等熱軋鋼板於含有0.13%之Al之475℃之鍍鋅浴中浸漬3 s,進行熔融鍍鋅處理,從而於鋼板表面上形成附著量為45 g/m2
之鍍鋅。繼而以550℃進行鍍鋅之合金化處理,之後,以15℃/s之平均冷卻速度冷卻至室溫而製成熔融鍍鋅鋼板。
針對以上述方式獲得之熔融鍍鋅鋼板,以下述方法進行微組織之解析及強度TS、總伸長率El、擴孔率λ之測定。
微組織之解析:針對與鋼板之輥軋方向平行之板厚剖面,藉由硝太蝕劑(nital)進行腐蝕之後,以掃描式電子顯微鏡(SEM,scanning electron microscope)於1000~5000倍之10個視野下進行觀察,而鑑定肥粒鐵相、麻田散鐵相及麻田散鐵相中之回火麻田散鐵相,並藉由影像解析軟體(Image-Pro;Cybernetics公司製造)進行解析,計算出肥粒鐵相及麻田散鐵相占組織全體之面積率。又,亦計算出回火麻田散鐵相占麻田散鐵相全體之面積率。
再者,可根據腐蝕後之表面形態而判別未回火之麻田散鐵相與回火麻田散鐵相。即,麻田散鐵相呈現出平滑之表面,而回火麻田散鐵相則可於晶粒內觀察到因腐蝕而形成之結構(凹凸)。可採用該方法,以晶粒為單位鑑定麻田散鐵相與回火麻田散鐵相,且可以上述方法求出各個相之面積率及整個麻田散鐵相中之回火麻田散鐵相之比例。
TS與El之測定:為了對強度、伸長特性進行評估,於與輥軋方向成直角之方向上,取出JIS5號拉伸測試片,依照JIS Z 2241並以20 mm/min之十字頭(cross head)速度進行拉伸測試,而測定出TS及El。
擴孔率λ之測定:為了對擴孔性進行評估,採用100 mm×100 mm之測試片,依照JFS T 1001(鐵連標準)而進行3次擴孔測試,計算出平均之擴孔率λ(%)。
其結果如圖1所示,得知當回火麻田散鐵相占麻田散鐵相全體之面積率為70%以上時,麻田散鐵相占組織全體之面積率為30~50%之範圍可獲得較高之TS×El及較高之λ。
又,同時亦得知下述情況。
優異之伸長特性、擴孔性、彎曲性係藉由如下方式而獲得:將優化了成分組成之鋼坯於熱軋後之2 s以內,以50℃/s以上之平均冷卻速度冷卻至600℃以下,再以由成分組成所規定之特定捲取溫度進行捲取,繼而以軋縮率40%以上進行冷軋,之後,以5℃/s以上之平均加熱速度加熱至Ac1
變態點以上之溫度區域,繼而於(Ac1
變態點+50℃)以上且Ac3
變態點以下之溫度區域均熱30~500 s,再以3~30℃/s之平均冷卻速度冷卻至600℃以下之溫度區域而進行退火,之後,實施熔融鍍鋅處理。
本發明係基於上述之發現而完成者,其提供一種成形性優異之高強度熔融鍍鋅鋼板,該鋼板具有以質量%計含有C:0.05~0.2%、Si:0.5~2.5%、Mn:1.5~3.0%、P:0.001~0.05%、S:0.0001~0.01%、Al:0.001~0.1%、N:0.0005~0.01%,且剩餘部分由Fe及不可避免之雜質所構之成分組成;其具有如下之微組織:含有肥粒鐵相與包含回火麻田散鐵相之麻田散鐵相,上述肥粒鐵相占組織全體之面積率為30%以上,上述麻田散鐵相占組織全體之面積率為30~50%,且上述回火麻田散鐵相占麻田散鐵相全體之面積率為70%以上。
較佳的是,本發明之高強度熔融鍍鋅鋼板中,進而以質量%計單獨或者組合含有Cr:0.01~1.5%;或Ti:0.0005~0.1%與B:0.0003~0.003%中之至少1種元素;或Nb:0.0005~0.05%;或自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。
又,本發明之高強度熔融鍍鋅鋼板中,亦可使鍍鋅為合金化鍍鋅。
本發明之高強度熔融鍍鋅鋼板可藉由如下方法而製造:例如,將具有上述成分組成之鋼坯加熱至1150~1300℃之加熱溫度後,以800~950℃之精軋溫度實施熱軋,再於上述熱軋後2 s以內,以50℃/s以上之平均冷卻速度冷卻至600℃以下,繼而以未滿Tct℃之捲取溫度進行捲取,再以軋縮率40%以上進行冷軋後,以5℃/s以上之平均加熱速度加熱至Ac1
變態點以上之溫度區域,繼而於(Ac1
變態點+50℃)以上且AC3
變態點以下之溫度區域均熱30~500 s後,以3~30℃/s之平均冷卻速度冷卻至600℃以下之溫度區域而進行退火,之後,實施熔融鍍鋅處理,繼而以30℃/s以下之平均冷卻速度進行冷卻。
其中,Tct=810-300×[C]-60×[Si]-60×[Mn]-70×[Cr]-80×[Mo]-40×[Ni]-70×[Cu],[M]表示元素M之含量(質量%),於元素M為不可避免之雜質之情形時設為[M]=0。
本發明之高強度熔融鍍鋅鋼板之製造方法中,亦可於實施熔融鍍鋅處理之後,於450~600℃之溫度區域實施鍍鋅之合金化處理。
本發明係製造具有780 MPa以上之TS,且具有優異之伸長特性、擴孔性、彎曲性之成形性優異之高強度熔融鍍鋅鋼板。可藉由將本發明之高強度熔融鍍鋅鋼板應用於汽車結構構件中,而實現更進一步之乘客安全性之確保及藉由車身大幅輕量化而帶來之燃料費改善。
以下對本發明之詳細內容進行說明。再者,表示成分元素之含量之「%」於未特別限定之情形下係指「質量%」。
C係使鋼強化時重要之元素,係具有高固溶強化能力,並且於利用麻田散鐵相來強化組織時,用以調整其面積率或硬度所不可缺少之元素。於C量未滿0.05%時,難以獲得必需之面積率之麻田散鐵相,並且無法使麻田散鐵相硬質化,因此無法獲得充分之強度。另一方面,當C量超過0.2%時,熔接性劣化,並且會因偏析層之形成而導致成形性降低。因此,將C量設為0.05~0.2%。
Si係本發明中極為重要之元素,其於退火時之冷卻過程中,促進肥粒鐵變態,並且自肥粒鐵相向沃斯田鐵相排出固溶C而使肥粒鐵相淨化,於提高延伸性之同時,使沃斯田鐵相穩定化,因此即便係難以急冷之熔融鍍鋅生產線,亦可容易地生成麻田散鐵相,且可容易地複合組織化。尤其,藉由冷卻過程中之沃斯田鐵相之穩定化而抑制生成波來鐵相或變韌鐵相,並促進生成麻田散鐵相。又,固溶於肥粒鐵相之Si促進加工硬化而提高延伸性,並且改善應力集中部位之應力傳播性而提高彎曲性。進而,Si將肥粒鐵相固溶強化而降低肥粒鐵相與麻田散鐵相之硬度差,抑制於其界面上生成龜裂並改善局部變形能力,從而有助於提高擴孔性或彎曲性。為了獲得此種效果,必需將Si量設為0.5%以上。另一方面,當Si量超過2.5%時,變態點之上升顯著,不僅阻礙生產穩定性,異常組織亦發達而導致成形性降低。因此,將Si量設定為0.5~2.5%。
Mn可有效地防止鋼之熱脆化及確保鋼之強度。又,可容易地提高淬火性而實現複合組織化。進而,可增加退火時之第2相之比例,減少未變態沃斯田鐵相中之C量,於熔融鍍鋅處理後之冷卻過程中容易產生自身回火,藉由降低最終製品之麻田散鐵相之硬度而抑制局部變形,從而有助於提高擴孔性或彎曲性。同時,Mn具有抑制冷卻過程中生成波來鐵相或變韌鐵相之作用,且使自沃斯田鐵相向麻田散鐵相之變態變得容易,之後可以充分之比例生成自身回火之麻田散鐵相。為了獲得此種效果,必需將Mn量設為1.5%以上。另一方面,當Mn量超過3.0%時,會導致成形性劣化。因此,將Mn量設為1.5~3.0%。
P係具有固溶強化之作用,且可根據所需強度而添加之元素。又,其係用以促進肥粒鐵變態且對複合組織化亦有效之元素。為了獲得此種效果,必需將P量設為0.001%以上。另一方面,當P量超過0.05%時,會導致熔接性劣化,並且於將鍍鋅進行合金化處理時,使合金化速度降低,有損鍍鋅之品質。因此,將P量設為0.001~0.05%。
S係向粒界偏析而使得鋼於熱加工時脆化,並且作為硫化物存在而導致局部變形能力降低。因此,必需將該S量設為0.01%以下,較佳的是0.003%以下,更佳的是0.001%以下。然而,因生產技術上之限制,S量必需為0.0001%以上。因此,將S量設為0.0001~0.01%,較佳的是0.0001~0.003%,更佳的是0.0001~0.001%。
Al係使肥粒鐵相生成,對提高強度與延伸性之均衡性為有效之元素。為了獲得此種效果,必需將Al量設為0.001%以上。另一方面,當Al量超過0.1%時,會導致表面性狀劣化。因此,將Al量設為0.001~0.1%。
N係導致鋼之耐時效性劣化之元素。尤其,當N量超過0.01%時,耐時效性之劣化變得顯著。其量越少越好,但因生產技術上之限制,N量必需為0.0005%以上。因此,將N量設為0.0005~0.01%。
剩餘部分係Fe及不可避免之雜質,但因以下之理由,較佳的是單獨或者組合含有Cr:0.01~1.5%;或Ti:0.0005~0.1%與B:0.0003~0.003%中之至少1種元素;或Nb:0.0005~0.05%;或自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。
Cr於退火時使第2相之比例增加,且使未變態沃斯田鐵相中之C量減少,藉此於熔融鍍鋅處理後之冷卻過程中容易產生自身回火,從而使最終製品之麻田散鐵相之硬度降低,抑制局部變形而有助於提高擴孔性或彎曲性。進而,藉由Cr向碳化物固溶而容易生成碳化物,可於短時間內進行自身回火。同時,Cr具有抑制在冷卻過程中生成波來鐵相或變韌鐵相之作用,可使自沃斯田鐵相向麻田散鐵相之變態變得容易,之後可以充分之比例生成自身回火之麻田散鐵相。為了獲得此種效果,必需將Cr量設為0.01%以上。另一方面,當Cr量超過1.5%時,第2相之比例增大,或過多地生成Cr碳化物等,從而導致延伸性降低。因此,將Cr量設為0.01~1.5%。
Ti係與C、S、N形成析出物而有效地幫助提高強度及韌性。又,當添加有B時,會使N作為TiN而析出,因此可抑制BN之析出,且可有效地表現以下說明之B之效果。為了獲得此種效果,必需將Ti量設為0.0005%以上。另一方面,當Ti量超過0.1%時,過度地析出強化,導致延伸性降低。因此,將Ti量設為0.0005~0.1%。
B係抑制自沃斯田鐵相生成波來鐵相或變韌鐵相,具有使沃斯田鐵相之穩定度提高之作用,因此可增強於熔融鍍鋅處理後之冷卻過程中容易進行麻田散鐵變態、繼而自身回火之效果。為了獲得此種效果,必需將B量設為0.0003%以上。另一方面,當B量超過0.003%時,會導致延伸性降低。因此,將B量設為0.0003~0.003%。
Nb具有提高鋼板強度之效果,為確保所需之強度,可根據需要而添加。藉由添加適當量,可使在熔融鍍鋅生產線之退火時以逆變態生成之沃斯田鐵相微細化,因此亦使退火後之微組織微細化而提昇強度。又,於熱軋時或者熔融鍍鋅生產線之退火時形成微細之析出物而提昇強度。為了獲得此種效果,必需添加0.0005%以上之Nb量。另一方面,當Nb量超過0.05時,組織過度微細化而無法獲得後述之較佳組織。因此,將Nb量設為0.0005~0.05%。
Mo、Ni、Cu不僅有作為固溶強化元素之作用,於退火時之冷卻過程中,亦可使沃斯田鐵相穩定化而容易地實現複合組織化。為了獲得此種效果,必需將Mo量、Ni量、Cu量分別設為0.01%以上。另一方面,當Mo量超過1.0%、Ni量超過2.0%、Cu量超過2.0%時,會導致鍍敷性、成形性、點熔接性劣化。因此,將Mo量設為0.01~1.0%,將Ni量設為0.01~2.0%,將Cu量設為0.01~2.0%。
本發明之高強度熔融鍍鋅鋼板包含於富有延伸性之軟質肥粒鐵相中主要分散有硬質之麻田散鐵相的複合組織。為了確保充分之延伸性,而需要占組織全體之面積率為30%以上之肥粒鐵相。
為了達成780 MPa以上之TS,而必需使包含回火麻田散鐵相之麻田散鐵相占組織全體之面積率為30%以上。另一方面,當該麻田散鐵相之面積率超過50%時,無法獲得充分之延伸性。因此,將麻田散鐵相占組織全體之面積率設為30~50%。
回火麻田散鐵相與未回火之麻田散鐵相比較係為軟質,藉由降低肥粒鐵相與麻田散鐵相之硬度差而提高局部變形能力,從而可提高擴孔性或彎曲性。尤其,以上述之肥粒鐵相與麻田散鐵相之面積率,藉由使均勻變形能力與局部變形能力適當地均衡,便可提高擴孔性或彎曲性而又不會損害伸長特性。為了充分地呈現該效果,必需將回火麻田散鐵相占麻田散鐵相全體之面積率設為70%以上。
於此,肥粒鐵相或麻田散鐵相占組織全體之面積率、及回火麻田散鐵相占麻田散鐵相全體之面積率,係以上述方法求得之面積率。
此處之未回火之麻田散鐵相,係指具有與變態前之沃斯田鐵相相同之化學組成、且具有過飽和地固溶有C之體心立方結構之組織,且係具有板條(lath)、板條束(packet)、板條塊(block)等之微觀結構之高差排密度的硬質相。回火麻田散鐵相係指自麻田散鐵相作為碳化物而析出過飽和之固溶C的維持母相微觀結構之高差排密度之肥粒鐵相。又,回火麻田散鐵相無需由用以獲得其之熱歷程(例如「淬火-回火」或「自身回火」等)而特別地加以區分。
再者,本發明之微組織即便除包含肥粒鐵相與麻田散鐵相以外,還包含以占組織全體之合計面積率計而為20%以下之範圍之殘留沃斯田鐵相、波來鐵相、變韌鐵相,亦不會損害本發明之效果。
如上述般,本發明之高強度熔融鍍鋅鋼板係藉由以下方法而製造:例如將具有上述成分組成之鋼坯加熱至1150~1300℃之加熱溫度後,以800~950℃之精軋溫度實施熱軋,再於上述熱軋後2 s以內,以50℃/s以上之平均冷卻速度冷卻至600℃以下,繼而以未滿Tct℃之捲取溫度進行捲取後,以軋縮率40%以上進行冷軋,之後,以5℃/s以上之平均加熱速度加熱至Ac1
變態點以上之溫度區域,繼而於(Ac1
變態點+50℃)以上且Ac3
變態點以下之溫度區域均熱30~500 s後,以3~30℃/s之平均冷卻速度冷卻至600℃以下之溫度區域而進行退火後,實施熔融鍍鋅處理,繼而以30℃/s以下之平均冷卻速度進行冷卻。
自確保熱軋時之溫度之觀點考慮,必需將鋼坯加熱溫度設為1150℃以上。另一方面,當加熱溫度過高時,會引起伴隨氧化重量之增加而使鏽皮損耗増大等問題,因此將鋼坯加熱溫度之上限設為1300℃。
為防止巨觀偏析,較佳的是以連續鑄造法製造鋼坯,但亦可藉由造塊法等而製造鋼坯。
加熱後之鋼坯藉由粗軋及精軋進行熱軋而製成熱軋鋼板。此時,若精軋溫度過高,則粒變得粗大,最終製品之成形性降低,並且容易產生鏽皮缺陷。為此,將精軋溫度設為950℃以下。另一方面,若精軋溫度未滿800℃則輥軋負重增大而輥軋負載變大,或沃斯田鐵相於未再結晶狀態之軋縮率變高,異常之集合組織發達,自最終製品之材質之均勻性之觀點考慮係欠佳。因此,將精軋溫度設為800~950℃,較好的是840~920℃。
再者,鋼坯於通常之條件下藉由粗軋而成為板片(sheet bar),但於使加熱溫度降低之情形時,自防止熱軋時之問題之觀點考慮,較好的是於精軋前使用板帶加熱器(bar heater)等對板片進行加熱。
本發明中,熱軋鋼板之微組織較佳的是以肥粒鐵相與變韌鐵相為主相之組織。變韌鐵相或以比較低之溫度生成之肥粒鐵相包含較多之差排而成為沃斯田鐵逆變態之起點,因此最終製品中可以既定之比例包含麻田散鐵相。
當熱軋後至開始冷卻前經過超過2秒鐘之時間時,於輸出輥道上容易不均勻地生成肥粒鐵相,從而無法獲得本發明中較佳之以肥粒鐵相與變韌鐵相為主體之均勻之熱軋鋼板的微組織。又,當平均冷卻速度低於50℃/s時或未冷卻至600℃以下時,亦會產生同樣之問題。
如上述般定義之Tct℃係本發明者等經驗性地導出之捲取溫度之實驗式,藉由使捲取溫度未滿Tct℃,可形成本發明中較佳之以肥粒鐵相與變韌鐵相為主體之熱軋鋼板的微組織。
當軋縮率未滿40%時,於接下來之退火時成為沃斯田鐵相之逆變態之核的粒界或差排於每單位體積之總數減少,難以獲得上述之最終製品之微組織。又,微組織會產生不均勻,伸長特性、擴孔性及彎曲性降低。
藉由以5℃/s以上之平均加熱速度加熱至Ac1
變態點以上之溫度區域,可抑制加熱中之回復或肥粒鐵相之再結晶,因下一次均熱時於包含較多之差排之狀態下生成逆變態,故而沃斯田鐵相高密度且均勻地分散,因此可提高最終製品之擴孔性或彎曲性。
藉由在均熱時提高沃斯田鐵相之比例,沃斯田鐵相中之C濃度降低,Ms點上升,因此可呈現出熔融鍍鋅處理後之冷卻過程之自身回火效果。又,最終製品之麻田散鐵相之比例增加,因此即便藉由回火而使麻田散鐵相之硬度降低,仍可達成充分之強度,從而可兼顧充分之強度與良好之局部延伸性。為此,必需於(Ac1
變態點+50℃)以上且Ac3
變態點以下之溫度區域進行均熱處理。當均熱溫度低於(Ac1
變態點+50℃)時,沃斯田鐵相之比例不充分,無法呈現自身回火之效果,因此不僅會導致擴孔性或彎曲性降低,亦會導致強度降低。當均熱溫度超過Ac3
變態點時,肥粒鐵相之生成不充分,延伸性降低。
又,當均熱時間未滿30 s時,向沃斯田鐵相之逆變態不充分,無法獲得必需之沃斯田鐵相之比例。當均熱時間超過500 s時,均熱之效果飽和,並且妨礙生產率。
均熱後,必需於均熱溫度至600℃以下之溫度區域(冷卻停止溫度),以3~30℃/s之平均冷卻速度冷卻。當平均冷卻速度未滿3℃/s時,冷卻中進行肥粒鐵變態而導致未變態沃斯田鐵相中之C增濃,無法呈現自身回火之效果,因此導致擴孔性或彎曲性降低。當平均冷卻速度超過30℃/s時,抑制肥粒鐵變態之效果飽和,並且於設備上亦難以實現。又,當冷卻停止溫度超過600℃時,由於肥粒鐵相或波來鐵相之生成而使麻田散鐵相之比例顯著降低,使得該麻田散鐵相占組織全體之面積率未滿30%,從而無法獲得780 MPa以上之TS。
於熔融鍍鋅處理後之冷卻過程中進行麻田散鐵相之自身回火。當平均冷卻速度超過30℃/s時,所進行之自身回火並不充分,因此擴孔性或彎曲性降低。
製造方法之其他條件並無特別限定,自生產率之觀點考慮,較佳的是於連續熔融鍍鋅生產線上,進行上述之退火、熔融鍍鋅、鍍鋅合金化處理等之一系列處理。又,於熔融鍍鋅時,較佳的是使用包含0.10~0.20%之Al量之鍍鋅浴。於鍍敷後,為了調整鍍敷之所需量而可進行擦拭。
藉由轉爐而將表1所示之成分組成之鋼No.A~I熔化,並以連續鑄造法而製成鋼坯。
以1250℃對該等鋼坯進行加熱,於表2所示之熱軋條件下製成熱軋鋼板,之後,進行酸洗,再於表2所示之冷軋條件下進行冷軋,藉由連續熔融鍍鋅生產線,於表2所示之退火條件下進行退火後,於包含0.13%之Al之475℃之鍍鋅浴中浸漬3s而形成附著量為45 g/m2
之鍍鋅,繼而以表2所示之溫度進行合金化處理後,以表2所示之平均冷卻速度進行冷卻,從而製作出鍍鋅鋼板No.1~23。再者,如表2所示,一部分鍍鋅鋼板並未進行合金化處理。而且,針對所獲得之鍍鋅鋼板,以上述方法測定肥粒鐵相與麻田散鐵相占組織全體之面積率、及回火麻田散鐵相占麻田散鐵相全體之面積率。又,以上述方法,測定TS、El、λ。再者,於通常之藉由沖孔加工而形成初始孔之情形下、及為了對原材料自身之局部延伸性進行評估而藉由擴孔鑽加工形成初始孔之情形下,進行λ之測定。進而,於與輥軋方向成直角之方向上,採用寬度30 mm×長度120 mm之條帶狀測試片,以表面粗糙度Ry成為1.6~6.3 S之方式使端部平滑後,藉由V形塊法,以90°之彎曲角度進行彎曲測試,求出未產生龜裂或頸縮之最小彎曲半徑即極限彎曲半徑R,並以該極限彎曲半徑R相對於板厚t之比(R/t)來評估彎曲性。
結果示於表3中。得知本發明例之鍍鋅鋼板均係如下之成形性優異之高強度熔融鍍鋅鋼板:TS為780 MPa以上,於TS×E1≧19000 MPa‧%下強度與延伸性之均衡性亦較高,即伸長特性優異,又沖孔加工之λ為50%以上,擴孔鑽加工之λ為70%以上,R/t為1.0以下,擴孔性與彎曲性亦優異。
圖1係表示改變回火麻田散鐵相占麻田散鐵相全體之面積率時,麻田散鐵相占組織全體之面積率與TS×EI、λ之關係圖。
Claims (8)
- 一種成形性優異之高強度熔融鍍鋅鋼板,其特徵在於,具有以質量%計含有C:0.05~0.2%、Si:0.5~2.5%、Mn:1.5~3.0%、P:0.001~0.05%、S:0.0001~0.01%、Al:0.001~0.1%、N:0.0005~0.01%,而剩餘部分由Fe及不可避免之雜質所構成之成分組成;且具有如下之微組織:含有肥粒鐵相與包含回火麻田散鐵相之麻田散鐵相,上述肥粒鐵相占組織全體之面積率為30%以上且未滿70%,上述麻田散鐵相之面積率為30~50%,上述回火麻田散鐵相占麻田散鐵相全體之面積率為70~94%。
- 如申請專利範圍第1項之成形性優異之高強度熔融鍍鋅鋼板,其中,上述組成之外,進一步含有下述群組(A)~(D)之至少一群組;(A)以質量%計含有Cr:0.01~1.5%;(B)以質量%計含有Ti:0.0005~0.1%、B:0.0003~0.003%中之至少1種元素;(C)以質量%計含有Nb:0.0005~0.05%;(D)以質量%計含有Mo:0.01~1.0%、Ni:0.01~2.0%、Cu:0.01~2.0%中之至少1種元素。
- 如申請專利範圍第1或2項之成形性優異之高強度熔融鍍鋅鋼板,其中,鍍鋅為合金化鍍鋅。
- 如申請專利範圍第2項之成形性優異之高強度熔融鍍鋅鋼 板,其中,上述至少一群組為以質量%計含有Cr:0.01~1.5%的群組(A)。
- 如申請專利範圍第2項之成形性優異之高強度熔融鍍鋅鋼板,其中,上述至少一群組為以質量%計含有Ti:0.0005~0.1%、B:0.0003~0.003%中之至少1種元素的群組(B)。
- 如申請專利範圍第2項之成形性優異之高強度熔融鍍鋅鋼板,其中,上述至少一群組為以質量%計含有Cr:0.01~1.5%的群組(A),與以質量%計含有Ti:0.0005~0.1%、B:0.0003~0.003%中之至少1種元素的群組(B)。
- 一種成形性優異之高強度熔融鍍鋅鋼板之製造方法,其特徵在於,將具有申請專利範圍第1、2、4至6項中任一項之成分組成之鋼坯加熱至1150~1300℃之加熱溫度後,以800~950℃之精軋溫度實施熱軋,再於上述熱軋後2s以內,以50℃/s以上之平均冷卻速度冷卻至600℃以下,繼而以未滿Tct℃之捲取溫度進行捲取,再以軋縮率40%以上進行冷軋後,以5℃/s以上之平均加熱速度加熱至Ac1 變態點以上之溫度區域,繼而於(Ac1 變態點+50℃)以上且Ac3 變態點以下之溫度區域均熱30~500s後,以3~30℃/s之平均冷卻速度冷卻至600℃以下之溫度區域而進行退火之後,實施熔融鍍鋅處理,繼而以30℃/s以下之平均冷卻速度進行冷卻;其中,Tct=810-300×[C]-60×[Si]-60×[Mn]-70×[Cr]-80× [Mo]-40×[Ni]-70×[Cu],[M]表示元素M之含量(質量%),於元素M為不可避免之雜質之情形時設為[M]=0。
- 如申請專利範圍第7項之成形性優異之高強度熔融鍍鋅鋼板之製造方法,其中,實施熔融鍍鋅處理之後,於450~600℃之溫度區域實施鍍鋅之合金化處理。
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