TW201713778A - 合金化熔融鍍鋅鋼板及其之製造方法 - Google Patents
合金化熔融鍍鋅鋼板及其之製造方法 Download PDFInfo
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- TW201713778A TW201713778A TW105118877A TW105118877A TW201713778A TW 201713778 A TW201713778 A TW 201713778A TW 105118877 A TW105118877 A TW 105118877A TW 105118877 A TW105118877 A TW 105118877A TW 201713778 A TW201713778 A TW 201713778A
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- Prior art keywords
- steel sheet
- hot
- dip galvanized
- iron
- temperature
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 169
- 239000010959 steel Substances 0.000 title claims abstract description 169
- 238000004519 manufacturing process Methods 0.000 title claims description 37
- 238000000034 method Methods 0.000 title description 29
- 239000000203 mixture Substances 0.000 claims abstract description 26
- 239000000126 substance Substances 0.000 claims abstract description 23
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 11
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 11
- 229910052802 copper Inorganic materials 0.000 claims abstract description 10
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 10
- 229910052787 antimony Inorganic materials 0.000 claims abstract description 9
- 229910052785 arsenic Inorganic materials 0.000 claims abstract description 9
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 9
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 9
- 229910052718 tin Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052796 boron Inorganic materials 0.000 claims abstract description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 512
- 229910052742 iron Inorganic materials 0.000 claims description 248
- 238000001816 cooling Methods 0.000 claims description 114
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 95
- 239000008397 galvanized steel Substances 0.000 claims description 95
- 239000010410 layer Substances 0.000 claims description 73
- 238000005275 alloying Methods 0.000 claims description 50
- 238000005496 tempering Methods 0.000 claims description 43
- 239000010960 cold rolled steel Substances 0.000 claims description 36
- 238000005246 galvanizing Methods 0.000 claims description 31
- 238000000137 annealing Methods 0.000 claims description 29
- 238000010438 heat treatment Methods 0.000 claims description 28
- 238000005096 rolling process Methods 0.000 claims description 22
- 238000005097 cold rolling Methods 0.000 claims description 20
- 239000002344 surface layer Substances 0.000 claims description 17
- 238000005098 hot rolling Methods 0.000 claims description 16
- 210000001161 mammalian embryo Anatomy 0.000 claims description 16
- 238000002844 melting Methods 0.000 claims description 16
- 230000008018 melting Effects 0.000 claims description 16
- 229910052751 metal Inorganic materials 0.000 claims description 14
- 239000002184 metal Substances 0.000 claims description 14
- 238000005554 pickling Methods 0.000 claims description 10
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 8
- 238000004804 winding Methods 0.000 claims description 8
- 229910052714 tellurium Inorganic materials 0.000 claims description 7
- 229910052727 yttrium Inorganic materials 0.000 claims description 7
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 229910052760 oxygen Inorganic materials 0.000 claims description 2
- 229910052717 sulfur Inorganic materials 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 claims 4
- 239000000956 alloy Substances 0.000 claims 4
- 229910000734 martensite Inorganic materials 0.000 abstract 4
- 229910001563 bainite Inorganic materials 0.000 abstract 2
- 238000005244 galvannealing Methods 0.000 abstract 1
- 238000007747 plating Methods 0.000 description 43
- 230000000694 effects Effects 0.000 description 36
- 238000012360 testing method Methods 0.000 description 33
- 239000000047 product Substances 0.000 description 22
- 229910000859 α-Fe Inorganic materials 0.000 description 16
- 230000006872 improvement Effects 0.000 description 10
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- 238000005259 measurement Methods 0.000 description 8
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- 229910000794 TRIP steel Inorganic materials 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
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- 239000013078 crystal Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 230000001737 promoting effect Effects 0.000 description 6
- 229920006395 saturated elastomer Polymers 0.000 description 6
- 239000008187 granular material Substances 0.000 description 5
- 230000002829 reductive effect Effects 0.000 description 5
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 4
- 230000009471 action Effects 0.000 description 4
- 239000012141 concentrate Substances 0.000 description 4
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- 230000029052 metamorphosis Effects 0.000 description 4
- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 description 4
- 229910017604 nitric acid Inorganic materials 0.000 description 4
- 230000036961 partial effect Effects 0.000 description 4
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- 238000003466 welding Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910017488 Cu K Inorganic materials 0.000 description 2
- 229910017541 Cu-K Inorganic materials 0.000 description 2
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000000354 decomposition reaction Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
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- 238000007373 indentation Methods 0.000 description 2
- 229910052747 lanthanoid Inorganic materials 0.000 description 2
- 150000002602 lanthanoids Chemical class 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
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- 239000002994 raw material Substances 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- 239000011701 zinc Substances 0.000 description 2
- 229910001021 Ferroalloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910001122 Mischmetal Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
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- 238000005261 decarburization Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
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- 229910052739 hydrogen Inorganic materials 0.000 description 1
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- 230000000670 limiting effect Effects 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
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- 150000004767 nitrides Chemical class 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
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- 238000002203 pretreatment Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000012552 review Methods 0.000 description 1
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- 229910052814 silicon oxide Inorganic materials 0.000 description 1
- 229910021647 smectite Inorganic materials 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
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- 230000002195 synergetic effect Effects 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- 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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- B32B15/00—Layered products comprising a layer of metal
- B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
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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
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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
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- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
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Abstract
一種合金化熔融鍍鋅鋼板,其係在鋼板之表面上具備合金化熔融鍍鋅層之合金化熔融鍍鋅鋼板,前述鋼板之化學組成以質量%表示,C:0.25~0.70%、Si:0.25~2.50%、Mn:1.00~5.00%、Al:0.005~3.50%、P:0.15%以下、S:0.03%以下、N≦0.02%、O≦0.01%,視需要包含由Ti、Nb、V、Cr、Mo、Cu、Ni、B、Ca、REM、Mg、W、Zr、Sb、Sn、As、Te、Y、Hf及Co所選出的1種以上,剩餘部分:Fe及雜質,金屬組織以體積%表示,殘留γ:10.0~60.0%、高溫回火麻田散鐵≧5.0%、低溫回火麻田散鐵≧5.0%、麻田散鐵(martensite)≦10.0%、α:0~15.0%、P:0~10.0%、剩餘部分:變韌鐵(bainite),回火麻田散鐵與變韌鐵之合計體積率為30.0%以上,拉伸強度為1470MPa以上,拉伸強度與均勻伸長率之積為13000MPa%以上,拉伸強度與局部伸長率之積為5000MPa%以上。
Description
本發明關於合金化熔融鍍鋅鋼板及其之製造方法。
近年來,為了地球環境保護,以汽車的燃油性能提高為目的,要求車體的輕量化。此外,由於必須確保乘車人員的安全性,而對於高強度鋼板的需求升高。最近,亦希望具有1470MPa以上的拉伸強度之鋼板。然而,供汽車用構件之鋼板僅高強度係不夠,而要求良好的加壓成形性。
為了提高鋼板的加壓成形性,必須提高鋼板的延展性。然而,拉伸強度與延展性係相反的要素,通常難以同時提高拉伸強度及延展性這兩者。再者,於汽車用構件中,要求耐蝕性以及點焊的連續打點性。因此,有必須藉由使用合金化熔融鍍鋅鋼板,達成高強度與良好的加壓成形性。
作為高強度同時具有良好的均勻伸長率之鋼板,已知利用殘留沃斯田鐵之TRIP效果的鋼板。例如,
專利文獻1中揭示加工性良好的高強度合金化熔融鍍鋅鋼板與其之製造方法。
又,專利文獻2中揭示具備鍍敷潤濕性及鍍敷密著性優異的合金化熔融鍍鋅層,且具有590MPa以上的拉伸強度之高強度的合金化熔融鍍鋅鋼板以及其之製造方法。
再者,專利文獻3中揭示具有優異的加工性及耐蝕性之高強度合金化熔融鍍鋅鋼板與其之製造方法。而且,專利文獻4中揭示藉由熱處理而具有超高強度,同時具有優異的延展性之成形構件用鋼板、成形構件及其之製造方法。
[專利文獻1]日本特開平11-279691號公報
[專利文獻2]國際公開第2014/073520號
[專利文獻3]日本特開2011-168816號公報
[專利文獻4]日本特表2014-508854號公報
專利文獻1中記載藉由將C、Si、Mn之比最合適化,而即使進行合金化處理用的再加熱,也得到高強
度同時加壓加工性優異之合金化熔融鍍鋅鋼板。
可是,於TRIP鋼板中,為了使沃斯田鐵殘留,必須含有Si。然而,此Si係大地妨礙鍍敷性,尤其鍍鋅之合金化。專利文獻1記載的技術中之設想強度水準由於為880MPa以下,C含量係低到0.15質量%以下。C含量若變高,則進一步抑制合金化,故難以一邊促進合金化,一邊使強度與伸長率的平衡並存。
於TRIP鋼板中,作為促進合金化之技術,已知如專利文獻2中記載,控制鍍敷前的退火時之環境的方法。藉由此技術,由於Si的氧化物係不在鋼板之表面而形成在內部,故鋅及鐵的合金化變容易進行。
此處,專利文獻2之技術係關於C含量未達0.3質量%之比較低的鋼,但為了達成更高強度化,必須使C含量成為0.3質量%以上。然而,若使C含量成為0.3質量%以上,則合金化變難以進行,故即使採用專利文獻2記載之技術,也難以確保殘留沃斯田鐵同時使充分的合金化進行。
另一方面,於專利文獻3記載於TRIP鋼板中,在合金化處理所伴隨的再加熱時中,抑制殘留沃斯田鐵的分解之方法。依照專利文獻3記載之方法,降低合金化處理前的沃斯田鐵中的C量,降低自沃斯田鐵生成碳化物之驅動力,可確保沃斯田鐵。
然而,於專利文獻3之方法的情況,由於殘留沃斯田鐵中的C量變低,沃斯田鐵變不安定,有局部伸
長率降低之傾向。特別地,於1470MPa以上的高強度鋼中,由於較佳為除了均勻伸長率還至少提高局部伸長率,故無法採用專利文獻3記載之方法。
於專利文獻4記載之方法中,在加熱後,對鋼施施予加壓,然後施予熱處理,而製造以回火麻田散鐵為主體之含有殘留沃斯田鐵的TRIP鋼,達成高強度與高延展性。
然而,於專利文獻4之方法中,由於在加熱中鋅熔化,而無法以連續退火生產線實施,無法進行大量生產。再者,於專利文獻4之方法中,由於回火溫度未達480℃,推測鍍敷之合金化係幾乎不發生。
如以上,於上述習知的技術中,關於一邊充分地進行合金化,一邊得到具備高強度與延展性的合金化熔融鍍鋅鋼板,留下改良之餘地。
本發明係為了解決上述問題點而完成者,目的在於提供均勻變形性(均勻伸長率)及局部變形性(局部伸長率)優異之合金化熔融鍍鋅鋼板及其之製造方法。
本發明係為了解決上述問題而完成者,要旨為下述的合金化熔融鍍鋅鋼板及其之製造方法。
(1)一種合金化熔融鍍鋅鋼板,其係在鋼板之表面上具備合金化熔融鍍鋅層之合金化熔融鍍鋅鋼板,前述鋼板之化學組成以質量%表示,C:0.25~0.70%、
Si:0.25~2.50%、Mn:1.00~5.00%、Al:0.005~3.50%、P:0.15%以下、S:0.03%以下、N:0.02%以下、O:0.01%以下、Ti:0~0.50%、Nb:0~0.50%、V:0~0.50%、Cr:0~1.50%、Mo:0~1.50%、Cu:0~5.00%、Ni:0~5.00%、B:0~0.003% Ca:0~0.05%、REM:0~0.05%、Mg:0~0.05%、W:0~0.50%、Zr:0~0.05%、Sb:0~0.50%、Sn:0~0.50%、As:0~0.05%、Te:0~0.05%、
Y:0~0.20%、Hf:0~0.20%、Co:0~1.00%、剩餘部分:Fe及雜質;前述鋼板之板厚1/4位置的金屬組織以體積%表示,殘留沃斯田鐵:10.0~60.0%、高溫回火麻田散鐵:5.0%以上、低溫回火麻田散鐵:5.0%以上、新鮮麻田散鐵:10.0%以下、肥粒鐵:0~15.0%、波來鐵:0~10.0%、剩餘部分:變韌鐵;高溫回火麻田散鐵、低溫回火麻田散鐵與變韌鐵之合計體積率為30.0%以上,拉伸強度為1470MPa以上,拉伸強度與均勻伸長率之積為13000MPa%以上,拉伸強度與局部伸長率之積為5000MPa%以上。
(2)如上述(1)記載之合金化熔融鍍鋅鋼板,其中前述化學組成以質量%表示,Si+Al:0.80%以上。
(3)如上述(1)或(2)記載之合金化熔融鍍鋅鋼板,其中前述化學組成以質量%表示,含有由以下所選出的1種以上,Ti:0.005~0.50%、
Nb:0.005~0.50%、V:0.005~0.50%、Cr:0.01~1.50%、Mo:0.01~1.50%、Cu:0.01~5.00%、Ni:0.01~5.00%、B:0.0001~0.003%、Ca:0.0001~0.05%、REM:0.0005~0.05%、Mg:0.0001~0.05%、W:0.005~0.50%、Zr:0.005~0.05%、Sb:0.005~0.50%、Sn:0.005~0.50%、As:0.005~0.05%、Te:0.001~0.05%、Y:0.001~0.20%、Hf:0.001~0.20%、及Co:0.001~1.00%。
(4)如上述(1)至(3)中任一項記載之合金化熔融鍍鋅鋼板,其中前述殘留沃斯田鐵中所含有的C量為0.85質量%以上。
(5)如上述(1)至(4)中任一項記載之合金化熔融鍍鋅鋼板,其中前述合金化熔融鍍鋅層中所含有的Fe量
為3.0~20.0質量%。
(6)如上述(1)至(5)中任一項記載之合金化熔融鍍鋅鋼板,其中前述鋼板係在表層具備表層軟質層,該表層軟質層具有自板厚1/4位置起到板厚1/2位置為止的區域之平均硬度的0.9倍以下之硬度,前述表層軟質層之自前述合金化熔融鍍鋅層與前述鋼板之界面起的厚度係超過1.0μm。
(7)如上述(1)至(5)中任一項記載之合金化熔融鍍鋅鋼板,其中前述鋼板係在表層具備表層軟質層,該表層軟質層具有自板厚1/4位置起到板厚1/2表層位置為止的區域之平均硬度的0.9倍以下之硬度,前述表層軟質層之自前述合金化熔融鍍鋅層與前述鋼板之界面起的厚度為10μm以下,前述鋼板的疲勞限度相對於拉伸強度之比為0.30以上。
(8)一種合金化熔融鍍鋅鋼板之製造方法,其係製造如上述(1)至(5)中任一項記載之合金化熔融鍍鋅鋼板之方法,依順序進行下述(a)至(l)之步驟,包含:(a)熔製具有上述(1)至(3)中任一項記載之化學組成的鋼塊或扁胚之熔製步驟,(b)加熱前述鋼塊或扁胚,施予熱軋而成為熱軋鋼板之熱軋步驟,(c)冷卻前述熱軋鋼板之第1冷卻步驟,(d)捲取前述熱軋鋼板之捲取步驟,
(e)退捲前述熱軋鋼板,酸洗後,施予冷軋而成為冷軋鋼板之冷軋步驟,(f)將前述冷軋鋼板在Ac1點~920℃的溫度範圍中保持5s以上之退火步驟,(g)將前述冷軋鋼板以1℃/s以上之平均冷卻速度冷卻到100~600℃的溫度範圍為止之第2冷卻步驟,(h)將前述冷軋鋼板冷卻或加熱到熔融鍍鋅浴溫度為止之前處理步驟,(i)將前述冷軋鋼板浸漬於熔融鍍鋅浴中,對鋼板施予熔融鍍鋅而成為熔融鍍鋅鋼板之鍍敷步驟,(j)將前述熔融鍍鋅鋼板加熱至480~600℃,將熔融鍍鋅合金化而成為合金化熔融鍍鋅鋼板之合金化步驟,(k)將前述合金化熔融鍍鋅鋼板以1℃/s以上之平均冷卻速度冷卻到80~300℃的溫度範圍為止之第3冷卻步驟,及(l)將前述合金化熔融鍍鋅鋼板在100~450℃的溫度範圍中保持1s以上48h以下之回火步驟。
(9)一種合金化熔融鍍鋅鋼板之製造方法,其係製造如上述(6)記載之合金化熔融鍍鋅鋼板之方法,依順序進行下述(a)至(l)之步驟,包含:(a)熔製具有上述(1)至(3)中任一項記載之化學組成的鋼塊或扁胚之熔製步驟,(b)加熱前述鋼塊或扁胚,施予熱軋而成為熱軋鋼板之熱軋步驟,
(c)冷卻前述熱軋鋼板之第1冷卻步驟,(d)捲取前述熱軋鋼板之捲取步驟,(e)退捲前述熱軋鋼板,酸洗後,施予冷軋而成為冷軋鋼板之冷軋步驟,(f)將前述冷軋鋼板在露點為-25℃以上的環境下,於Ac1點~920℃的溫度範圍中保持5s以上之退火步驟,(g)將前述冷軋鋼板以1℃/s以上之平均冷卻速度冷卻到100~600℃的溫度範圍為止之第2冷卻步驟,(h)將前述冷軋鋼板冷卻或加熱到熔融鍍鋅浴溫度為止之前處理步驟,(i)將前述冷軋鋼板浸漬於熔融鍍鋅浴中,對鋼板施予熔融鍍鋅而成為熔融鍍鋅鋼板之鍍敷步驟,(j)將前述熔融鍍鋅鋼板加熱至480~600℃,將熔融鍍鋅合金化而成為合金化熔融鍍鋅鋼板之合金化步驟,(k)將前述合金化熔融鍍鋅鋼板以1℃/s以上之平均冷卻速度冷卻到80~300℃的溫度範圍為止之第3冷卻步驟,及(l)將前述合金化熔融鍍鋅鋼板在100~450℃的溫度範圍中保持1s以上48h以下之回火步驟。
(10)一種合金化熔融鍍鋅鋼板之製造方法,其係製造如上述(7)記載之合金化熔融鍍鋅鋼板之方法,依順序進行下述(a)至(l)之步驟,包含:(a)熔製具有上述(1)至(3)中任一項記載之化學組成的鋼塊或扁胚之熔製步驟,
(b)加熱前述鋼塊或扁胚,施予熱軋而成為熱軋鋼板之熱軋步驟,(c)冷卻前述熱軋鋼板之第1冷卻步驟,(d)捲取前述熱軋鋼板之捲取步驟,(e)退捲前述熱軋鋼板,酸洗後,施予冷軋而成為冷軋鋼板之冷軋步驟,(f)將前述冷軋鋼板在露點為-25℃以上的環境下,於Ac1點~920℃的溫度範圍中保持5s以上之退火步驟,(g)將前述冷軋鋼板以1℃/s以上之平均冷卻速度冷卻到100~600℃的溫度範圍為止之第2冷卻步驟,(h)將前述冷軋鋼板冷卻或加熱到熔融鍍鋅浴溫度為止之前處理步驟,(i)將前述冷軋鋼板浸漬於熔融鍍鋅浴中,對鋼板施予熔融鍍鋅而成為熔融鍍鋅鋼板之鍍敷步驟,(j)將前述熔融鍍鋅鋼板加熱至480~600℃,將熔融鍍鋅合金化而成為合金化熔融鍍鋅鋼板之合金化步驟,(k)將前述合金化熔融鍍鋅鋼板以1℃/s以上之平均冷卻速度冷卻到80~300℃的溫度範圍為止之第3冷卻步驟,及(l)將前述合金化熔融鍍鋅鋼板在100~450℃的溫度範圍中保持1s以上48h以下之回火步驟。
依照本發明,可得到一邊具有1470MPa以上
的高拉伸強度,一邊均勻變形性(均勻伸長率)及局部變形性(局部伸長率)優異之合金化熔融鍍鋅鋼板。
本發明者們對於一邊充分地進行合金化,一邊得到具有高強度且延展性優異的合金化熔融鍍鋅鋼板之方法,進行專心致力的檢討,結果得到以下的知識見解。
如前述,由於殘留沃斯田鐵之確保與充分的合金化之進行係相反者,而難以製造具備高強度與延展性這兩者之合金化熔融鍍鋅鋼。本發明者們對於得到具有充分的伸長率與1470MPa以上的拉伸強度之合金化熔融鍍鋅鋼板之方法,徹底地進行檢討。
結果,成功得到:鋼板中的C含量為0.3質量%以上,殘留沃斯田鐵為10體積%以上,拉伸強度為1470MPa以上,拉伸強度與均勻伸長率之積為13000MPa%以上,拉伸強度與局部伸長率之積為5000MPa%以上之高強度且高延展性的合金化熔融鍍鋅鋼板。
說明其手法。作為慣例,鍍敷係在造入鋼板的金屬組織後進行。因此,製作TRIP鋼時,於鍍敷處理前,使C在沃斯田鐵中濃化。然而,施予鍍敷後,若提高合金化處理用的溫度,則在500℃以上碳化物析出。
因此,本發明者們在合金化處理之階段中,不使C在沃斯田鐵中濃化。再者,發現於合金化處理後,
施予進行變態用的熱處理。藉由此熱處理,使C在沃斯田鐵中濃化,可得到含有安定的殘留沃斯田鐵之TRIP鋼。
再者,為了得到一邊具有1470MPa以上的高拉伸強度一邊得到高延展性,發現使後述的高溫回火麻田散鐵及低溫回火麻田散鐵各自以指定的體積率存在者係有效。而且,本發明者們為了以指定的體積率使高溫回火麻田散鐵及低溫回火麻田散鐵各自存在,發現於合金化處理前在指定的加熱條件及冷卻條件下進行退火處理者係有效果的。
本發明係以上述的知識見解為基礎而完成者。以下,詳細說明本發明之各要件。
(A)化學組成
各元素的限定理由係如下述。再者,以下說明中的含量之「%」係意指「質量%」。
C:0.25~0.70%
C係為了得到高強度之有效元素。又,C亦係將有助於鋼板的延展性的提高之殘留沃斯田鐵予以安定化之元素。C含量未達0.25%時,不充分地展現上述效果,難以得到必要的拉伸強度(1470MPa以上)。另一方面,C含量若超過0.70%,則變過硬,冷軋變困難。因此,C含量係設為0.25~0.70%。
鋼板之強度係後述的回火麻田散鐵及變韌鐵
擔當,但若C含量低,則此等組織變柔軟,有得不到所要的拉伸強度之情況。因此,C含量較佳為0.28%以上,更佳為0.30%以上。又,C含量較佳為0.60%以下,更佳為0.50%以下。
Si:0.25~2.50%
Si除了是將鋼板予以高強度化之元素,還藉由將肥粒鐵強化,將組織均勻化,而是有效於加工性的改善之元素。又,Si係抑制雪明碳鐵(cementite)之析出,完成促進沃斯田鐵的殘留之作用的元素。
Si含量未達0.25%時,不充分地展現上述效果。另一方面,Si含量若超過2.50%,則韌性大幅降低,製造變困難。因此,Si含量係設為0.25~2.50%。Si含量較佳為0.30%以上,更佳為0.60%以上。又,Si含量較佳為2.30%以下,更佳為2.00%以下。
Mn:1.00~5.00%
Mn係使M-A(Martensite-Austenite Constituent)生成,謀求強度與伸長率的並存所必須之元素。Mn含量未達1.00%時,不充分地展現上述效果。另一方面,Mn含量若超過5.00%,則變韌鐵變態之進行變慢,沃斯田鐵中C不濃化。而且,結果沃斯田鐵係不安定化,最終地新鮮麻田散鐵的體積率成為過剩。因此,Mn含量係設為1.00~5.00%。Mn含量較佳為1.20%以上,更佳為1.50%以
上。又,Mn含量較佳為4.5%以下,更佳為4.00%以下。
Al:0.005~3.50%
Al係脫氧元素,同時與Si同樣地,抑制雪明碳鐵之析出,有效於殘留沃斯田鐵之增加的元素。Al含量未達0.005%時,不充分地展現上述效果。另一方面,Al含量若超過3.50%,則夾雜物增加,加工性變差。因此,Al含量係設為0.005~3.50%。Al含量較佳為0.010%以上,更佳為0.020%以上。又,Al含量較佳為3.30%以下,更佳為3.00%以下。
Si+Al:0.80%以上
即使Si及Al各自的含量滿足上述之範圍,若Si+Al未達0.80%,則Si與Al之相乘效果不充分,於變韌鐵變態時,析出雪明碳鐵,有殘留沃斯田鐵不安定化之虞。因此,為了使殘留沃斯田鐵更安定化,Si及Al之合計含量較佳為0.80%以上,更佳為0.90%以上,尤佳為1.00%以上。
P:0.15%以下
P係雜質元素,偏析而使韌性變差之元素。P含量若超過0.15%,則韌性顯著變差。因此,P含量係設為0.15%以下。P含量較佳為0.12%以下,更佳為0.10%以下。再者,為了將P含量減低至未達0.003%,製造成本
係大幅上升。因此,0.003%成為實質的P含量之下限。
S:0.03%以下
S係雜質元素,形成MnS而阻礙伸長率之元素。S含量若超過0.03%,則伸長率顯著降低。因此,S含量係設為0.03%以下。S含量較佳為0.02%以下,更佳為0.01%以下。再者,為了將S含量減低至未達0.0002%,製造成本係大幅上升。因此,0.0002%成為實質的S含量之下限。
N:0.02%以下
N係雜質元素,於連續鑄造中形成成為扁胚之龜裂原因的氮化物之元素。若超過0.02%,則扁胚之龜裂變顯著。因此,N含量係設為0.02%以下。N含量較佳為0.01%以下。再者,為了將N含量減低至未達0.0007%,製造成本係大幅上升。因此,0.0007%成為實質的N之下限。
O:0.01%以下
O係形成夾雜物,阻礙局部延展性及韌性之元素。O含量若超過0.01,則局部延展性及韌性顯著降低。因此,O含量係設為0.01%以下。O含量較佳為0.008%以下,更佳為0.006%以下。再者,為了將O含量減低至未達0.0001%,製造成本係大幅上升。因此,0.0001%成為實質
的O之下限。
於本發明之合金化熔融鍍鋅鋼板中,除了上述元素,可進一步含有下述所示之量的由Ti、Nb、V、Cr、Mo、Cu、Ni、B、Ca、REM、Mg、W、Zr、Sb、Sn、As、Te、Y、Hf及Co所選出的1種以上之元素。
Ti:0~0.50%
Nb:0~0.50%
V:0~0.50%
Ti、Nb及V由於是形成析出物,將結晶粒微細化,有助於強度及韌性升高之元素,故可視需要含有。然而,若任一元素超過0.50%含有,則上述效果飽和,製造成本上升。因此,將Ti、Nb及V之含量皆設為0.50%以下。此等元素之含量較佳皆為0.35%以下。
為了得到上述效果,較佳為含有0.005%以上的由Ti、Nb及V所選出的1種以上。Ti及Nb係為了將沃斯田鐵細粒化,使沃斯田鐵安定化,更佳為含有0.010%以上的Ti及Nb之1種或2種,尤佳為含有0.030%以上。
Cr:0~1.50%
Mo:0~1.50%
Cr及Mo係與Mn同樣,將沃斯田鐵安定化,促進變態強化,有效於鋼板的高強度化之元素。又,Cr及Mo亦
係在合金化處理時,具有抑制沃斯田鐵的分解之作用的元素。因此,可視需要含有此等的元素。然而,若任一元素超過1.50%含有,則變韌鐵變態之進行變慢,沃斯田鐵中C不濃化。而且,結果,沃斯田鐵不安定化,最終地新鮮麻田散鐵之體積率成為過剩。因此,將Cr及Mo之含量皆設為1.50%以下。此等元素之含量較佳皆為1.30%以下。又,Cr含量更佳為1.20%以下,Mo含量更佳為1.00%以下。
為了得到上述效果,較佳為含有0.01%以上的由Cr及Mo所選出的1種以上。又,Cr更佳為0.10%以上含有,Mo更佳為0.05%以上含有。
Cu:0~5.00%
Ni:0~5.00%
Cu及Ni係具有抑制腐蝕的作用之元素。又,Cu及Ni係在鋼板之表面濃化,抑制氫往鋼板內之侵入,具有抑制延遲破壞之作用,同時亦有助於沃斯田鐵的安定化之元素。因此,可視需要含有此等的元素。然而,若任一元素超過5.00%含有,則上述效果飽和,製造成本上升。因此,將Cu及Ni之含量皆設為5.00%以下。此等元素之含量較佳皆為4.00%以下。
為了得到上述效果,較佳為含有0.01%以上的由Cu及Ni所選出的1種以上,更佳為含有0.02%以上。
B:0~0.003%
B係由於是抑制以粒界為起點之核生成,提高淬火性,有助於高強度化之元素,故可視需要含有。然而,若B含量超過0.003%,則上述效果飽和,製造成本上升。因此,B含量係設為0.003%以下。B含量較佳為0.002%以下。為了得到上述效果,B含量較佳為0.0001%以上,更佳為0.0002%以上。
Ca:0~0.05%
REM:0~0.05%
Mg:0~0.05%
Ca、REM及Mg由於是將硫化物球狀化,有助於鋼板的局部伸長率提高之元素,故可視需要含有。然而,若任一元素超過0.05%含有,則上述效果飽和,製造成本上升。因此,將Ca、REM及Mg之含量皆設為0.05%以下。此等元素之含量較佳皆為0.04%以下。
為了得到上述效果,較佳對於Ca及Mg以0.0001%以上,對於REM以0.0005%以上,含有由Ca、REM及Mg所選出的1種以上。
此處,於本發明中,REM係指Sc及鑭系元素之合計16元素,前述REM之含量係意指此等元素之合計含量。再者,鑭系元素係在工業上以密鈰合金(misch metal)之形式添加。
W:0~0.50%
W由於是提高淬火性,有助於鋼板強度的提高之元素,故可視需要含有。然而,若W含量超過0.50%,則上述效果飽和,製造成本上升。因此,W含量係設為0.50%以下。W含量較佳為0.35%以下。為了得到上述效果,W含量較佳為0.005%以上,更佳為0.010%以上。
Zr:0~0.05%
Zr由於是提高淬火性,有助於鋼板強度的提高之元素,故可視需要含有。然而,若Zr含量超過0.05%,則上述效果飽和,製造成本上升。因此,Zr含量係設為0.05%以下。Zr含量較佳為0.03%以下。為了得到上述效果,Zr含量較佳為0.005%以上,更佳為0.07%以上。
Sb:0~0.50%
Sn:0~0.50%
Sb及Sn由於是有助於鍍敷潤濕性與鍍敷密著性的提高,同時具有防止鋼之脫碳的作用之元素,故可視需要含有。然而,若任一元素超過0.50%含有,則在鋼板發生熱脆化,於熱加工時發生裂紋,有在鋼板發生表面疲勞之虞,而且在剪切等的冷加工時亦有發生裂紋之虞。因此,將Sb及Sn之含量皆設為0.50%以下。此等元素之含量較佳皆為0.35%以下。
為了得到上述效果,較佳為含有0.005%以上
的由Sb及Sn所選出的1種以上,更佳為含有0.010%以上。
As:0~0.05%
Te:0~0.05%
As及Te由於是有助於鋼板之機械強度的提高之元素,故可視需要含有。然而,若任一元素超過0.05%含有,則有局部變形能力降低之虞。因此,將As及Te之含量皆設為0.05%以下。此等元素之含量較佳皆為0.03%以下。
為了得到上述效果,含有由As及Te所選出的1種以上,As較佳為0.005%以上,Te較佳為0.001%以上,As更佳為0.010%以上,Te更佳為0.007%以上。
Y:0~0.20%
Hf:0~0.20%
Y及Hf由於是有效於鋼板之耐蝕性的提高之元素,故可視需要含有。然而,若任一元素超過0.20%含有,則有鋼板的局部伸長率大地變差之虞。因此,將Y及Hf之含量皆設為0.20%以下。此等元素之含量較佳皆為0.15%以下。
為了得到上述效果,較佳為含有0.001%以上的由Y及Hf所選出之1種以上,更佳為含有0.005%以上。
Co:0~1.00%
Co係具有促進變韌鐵變態的作用之元素。為了促進TRIP效果,必須使變韌鐵變態發生,使C往沃斯田鐵中濃化,故Co係有用於TRIP效果的促進之元素。因此,可視需要含有Co。然而,Co含量若超過1.00%,則有鋼板的熔接性及局部伸長率大地變差之虞。因此,Co含量係設為1.00%以下。Co含量較佳為0.80%以下。為了得到上述效果,Co含量較佳為0.001%以上,更佳為0.008%以上。
於本發明的鋼板之化學組成中,剩餘部分為Fe及雜質。
此處所謂的「雜質」,就是意指在工業上製造鋼板時,因礦石、廢料(scrap)等之原料、製程的種種主要原因而混入的成分,於不對本發明造成不良影響的範圍內可容許者。
(B)鋼板的金屬組織
說明本發明的鋼板之板厚1/4位置的金屬組織。再者,於以下之說明中,「%」係意指「體積%」。
殘留沃斯田鐵:10.0~60.0%
含有殘留沃斯田鐵的鋼板係在加工中,藉由沃斯田鐵變態成麻田散鐵而發生的變態誘發塑性(Transformation
Induced Plasticity:TRIP),而具有優異的伸長率,具體而言具有優異的均勻伸長率。
殘留沃斯田鐵的體積率若未達10.0%,則鋼板的均勻伸長率變不充分。另一方面,殘留沃斯田鐵的體積率若超過60.0%,則有鋼板的局部伸長率降低之虞。因此,殘留沃斯田鐵的體積率係設為10.0~60.0%。由於延展性若高,則汽車車體的碰撞安全係進一步提高,故於欲確保更高的延展性時,殘留沃斯田鐵的體積率較佳設為13.0%以上。又,殘留沃斯田鐵的體積率較佳為50.0%以下,更佳為40.0%以下,尤佳為30.0%以下。
殘留沃斯田鐵中所含有的C量(Cγ):0.85質量%以上
為了使殘留沃斯田鐵安定地存在,C較佳為在殘留沃斯田鐵中濃化。若Cγ未達0.85質量%,則殘留沃斯田鐵變不安定,容易消失。結果,難以將殘留沃斯田鐵確保在10.0%以上,有無法確保所要的均勻伸長率與局部伸長率之情況。因此,Cγ較佳為0.85質量%以上,更佳為0.90質量%以上,尤佳為0.95質量%以上。
Cγ之上限係沒有特別的規定,但若超過1.50質量%,則在變形中沃斯田鐵不往麻田散鐵變態,無法得到TRIP效果,有延展性變差之虞。因此,Cγ較佳為1.50質量%以下。
高溫回火麻田散鐵:5.0%以上
高溫回火麻田散鐵係經480~600℃的溫度所回火之麻田散鐵。高溫回火麻田散鐵係比肥粒鐵硬質,而且比後述的低溫回火麻田散鐵軟質,推斷有效於延展性之提高。為了得到上述效果,必須將高溫回火麻田散鐵的體積率設為5.0%以上。高溫回火麻田散鐵的體積率較佳為10.0%以上。然而,高溫回火麻田散鐵的體積率若過剩,則無法確保低溫回火麻田散鐵、殘留沃斯田鐵及變韌鐵的體積率,故較佳設為70.0%以下。
低溫回火麻田散鐵:5.0%以上
低溫回火麻田散鐵係經100~450℃的溫度所回火之麻田散鐵。低溫回火麻田散鐵係比前述的高溫回火麻田散鐵硬質,故係為了確保1470MPa以上的拉伸強度而必要的組織。因此,必須將低溫回火麻田散鐵的體積率設為5.0%以上。低溫回火麻田散鐵的體積率較佳為10.0%以上,更佳為15.0%以上。然而,低溫回火麻田散鐵的體積率若過剩,則無法確保高溫回火麻田散鐵、殘留沃斯田鐵及變韌鐵的體積率,故較佳設70.0%以下。
新鮮麻田散鐵:10.0%以下
於製造高強度的鋼板時,通常增多新鮮麻田散鐵(未回火的麻田散鐵),但於本發明的鍍敷鋼板之情況,新鮮麻田散鐵的體積率若超過10.0%,則由於鋼板的局部延展性及降伏比降低而不宜。因此,將新鮮麻田散鐵的體積率
設為10.0%以下。新鮮麻田散鐵的體積率較佳為7.0%以下。
肥粒鐵:0~15.0%
肥粒鐵由於是軟質組織,其體積率若超過15.0%,則無法得到1470MPa以上的拉伸強度。因此,肥粒鐵的體積率係設為15.0%以下。
波來鐵:0~10.0%
於合金化處理時若發生波來鐵,則有減少殘留沃斯田鐵的體積率之虞。又,由於是比回火麻田散鐵更軟質之組織,強度降低。因此,波來鐵的體積率係設為10.0%以下。波來鐵的體積率愈低愈佳,較佳為5.0%以下,更佳為0%。
於本發明的鋼板之板層1/4位置的金屬組織中,剩餘部分為變韌鐵。
高溫回火麻田散鐵、低溫回火麻田散鐵與變韌鐵之合計體積率:30.0%以上
回火麻田散鐵(於以下之說明中,亦將「高溫回火麻田散鐵」及「低溫回火麻田散鐵」總稱為「回火麻田散鐵」)與變韌鐵之合計體積率未達30.0%時,若欲確保1470MPa的拉伸強度,則必須提高新鮮麻田散鐵的體積率。然而,若提高新鮮麻田散鐵的體積率,則局部延展性
降低。因此,從一邊維持1470MPa以上的拉伸強度一邊確保所要的局部延展性之點來看,將上述之合計體積率設為30.0%以上。
又,為了使殘留沃斯田鐵的體積率成為10.0%以上,於變韌鐵變態時或麻田散鐵之回火時,必須使C往殘留沃斯田鐵中濃化。為了得到此效果,亦將回火麻田散鐵與變韌鐵之合計體積率設為30.0%以上。從局部變形能力及強度的提高之觀點來看,回火麻田散鐵與變韌鐵之合計體積率較佳設為40.0%以上。
再者,由於回火麻田散鐵及變韌鐵不僅有助於拉伸強度之提高,而且亦有助於降伏強度之提高,故藉由將上述之合計體積率成設在指定值以上,可使降伏比成為0.58以上。因此,本發明的鍍敷鋼板係適合作為汽車用構件。
以下說明於本發明中求得上述各組織的體積率之方法。
殘留沃斯田鐵的體積率(Vγ)係可自使用Mo-K α線所得之數據,藉由下式算出。
V γ=(2/3){100/(0.7×α(111)/γ(200)+1)}+(1/3){100/(0.78×α(211)/γ(311)+1)}
惟,α(211)、γ(200)、α(211)及γ(311)表示面強度。
又,殘留沃斯田鐵的C量(Cγ)係可藉由Cu-K α線的X射解析,自沃斯田鐵的(200)面、(220)面及(311)面之反射角,求得晶格常數(單位為埃),依照下式算
出。
Cγ=(晶格常數-3.572)/0.033
接著,用F.S.Lepera:Journal of Metals 32,No.3,(1980)38-39中記載之方法,腐蝕輥軋方向的剖面,使新鮮麻田散鐵及殘留沃斯田鐵出現。然後,於板厚1/4位置中,使用光學顯微鏡以1000倍的倍率觀察,將組織照片予以影像處理,測定新鮮麻田散鐵及殘留沃斯田鐵之合計面積率(%),將其當作合計體積率。
然後,自新鮮麻田散鐵及殘留沃斯田鐵之合計體積率的值,扣除藉由上述之方法所測定之殘留沃斯田鐵的體積率,求得新鮮麻田散鐵的體積率。
再者,切出垂直於輥軋方向之剖面,鏡面研磨後,對於經電解研磨的樣品,用SEM-EBSD以0.1step間隔測定100μm×100μm以上之區域。然後,使用股份有限公司TSL Solutions的分析軟體,算出各個結晶粒中的粒內之Image Quality的平均值(Grain Average Image Quality:GAIQ值)。
然後,將GAIQ值為5000以下的結晶粒之分率當作低溫回火麻田散鐵與新鮮麻田散鐵之合計體積率。藉由自此值扣除新鮮麻田散鐵的體積率,求得低溫回火麻田散鐵的體積率。
又,切出垂直於輥軋方向之剖面,鏡面研磨後,用硝酸腐蝕液進行腐蝕。對於該樣品進行SEM觀
察,求得板條狀的組織且含有雪明碳鐵者之分率作為高溫回火麻田散鐵與低溫回火麻田散鐵之合計面積率,將其當作合計體積率。SEM觀察係以5000倍的倍率進行,測定區域係使25μm×20μm之區域成為4個視野以上。藉由自此值扣除低溫回火麻田散鐵的體積率,求得高溫回火麻田散鐵的體積率。
變韌鐵與回火麻田散鐵之合計亦藉由SEM觀察求得。將觀察到變韌鐵或麻田散鐵之區塊者當作變韌鐵或回火麻田散鐵。然後,測定變韌鐵與回火麻田散鐵之合計面積率,將其當作合計體積率。
對於肥粒鐵及波來鐵,亦同樣地進行硝酸腐蝕液腐蝕後,用SEM觀察,不是下部組織,將被挖的區域當作肥粒鐵,將看得見層狀組織者當作波來鐵。而且,求得肥粒鐵及波來鐵各自的面積率,將其當作體積率。
(C)合金化熔融鍍鋅層
合金化熔融鍍鋅層中所含有的Fe量:3.0~20.0質量%
合金化熔融鍍鋅層係可為通常的合金化熔融鍍鋅層。然而,鍍敷層中所含有的Fe量若未達3.0質量%,則有合金化熔融鍍鋅鋼板的熔接性及滑動性變不充分之情況。因此,鍍敷層的Fe量較佳為3.0質量%以上。另一方面,從確保耐粉化性之觀點來看,鍍敷層的Fe量較佳為20.0質量%以下。
鍍敷層的Fe量更佳為5.0質量%以上,尤佳為7.0質量%以上。又,鍍敷層的Fe量更佳為15.0質量%以下。再者,鍍敷層的Fe量係可藉由熔融鍍鋅後的熱處理(合金化處理)之條件進行調整。
(D)機械特性
本發明之合金化熔融鍍鋅鋼板,從確保充分的衝撃吸收性之觀點來看,係設為具有1470MPa以上的拉伸強度者。拉伸強度之上限係沒有特別的限定。拉伸強度只要是按照用途,在1470~2200MPa之範圍內適宜選擇即可。
又,考慮對於要求成形性的汽車零件之適用,將拉伸強度與均勻伸長率之積設為13000MPa%以上,將拉伸強度與局部伸長率之積設為5000MPa%以上。汽車用零件由於需要均勻變形特性及局部變形特性,而有滿足此2者之必要。
降伏比係影響將鋼板成形所得之機械零件的強度。例如,為了提高汽車零件的碰撞安全性(提高碰撞能量),要求高的降伏比。因此,本發明的鍍敷鋼板之降伏比較佳為0.58以上,更佳為0.70以上,尤佳為0.80以上。又,基於同樣的觀點,本發明之鍍敷鋼板較佳為具有850MPa以上的降伏強度。
再者,於本發明中,作為拉伸強度及降伏強度,採用輥軋直角方向的拉伸試驗中所求得之值。所謂的輥軋直角方向,就是指垂直於鋼板的輥軋方向及厚度方向
之方向,即寬度方向。
再者,使用本發明之合金化熔融鍍鋅鋼板作為遭受重複的負荷之汽車用零件的原料鋼板時,除了優異的均勻變形特性及局部變形特性,還要求優異的疲勞特性。欲確保指定的疲勞特性時,較佳將疲勞限度相對於拉伸強度之比設為0.30以上,更佳設為0.35以上。再者,鋼板之疲勞限度係藉由將應力比設為-1,將重複頻率設為25Hz,將最大重複數設為2×106次而測定。
(E)鋼板的表層組織
本發明之合金化熔融鍍鋅鋼板具備表層軟質層。所謂的表層軟質層,就是意指存在於鋼板表層且具有自板厚1/4位置起到板厚1/2位置為止的區域中之平均硬度的0.9倍以下之硬度的層。
於本發明中,由於藉由控制化學組成與板厚1/4位置的金屬組織,可得到高強度與優異的成形性,故表層軟質層之厚度係沒有特別的限制。然而,藉由按照用途適宜地調整表層軟質層之厚度,可得到附加的特性。
例如,於熔接施有鍍鋅的汽車用鋼板時,在熔接部會發生液體金屬脆性裂紋。此液體金屬脆性裂紋係鋼板強度愈成為高強度愈容易發生。然而,藉由除了上述化學組成及金屬組織之規定,還將表層軟質層之厚度設為超過10μm,可確保優異的耐液體金屬脆性裂紋性。
另一方面,如上述,使用鍍敷鋼板作為遭受
重複的負荷之汽車用零件的原料鋼板時,要求優異的疲勞特性。藉由除了上述化學組成及金屬組織之規定,還將表層軟質層之厚度設為10μm以下,可提高疲勞特性,可使疲勞限度相對於拉伸強度之比成為0.30以上。
再者,表層軟質層之厚度係藉由以下之程序求得。首先,切出垂直於輥軋方向的剖面,鏡面研磨。然後,自該樣品的鍍敷層與鋼板之界面起10μm的位置到板厚之中心(板厚1/2位置)為止,以10μm間距依順序測定微維氏硬度。試驗力只要是按照組織的硬度適宜選擇即可,例如可設為2~25gf。又,當壓痕重疊時,在垂直於板厚之方向中挪移測定。
自上述的測定結果,求得自板厚1/4位置起到板厚1/2位置為止的區域之平均硬度,界定成為其硬度的0.9倍之位置。然後,將自鍍敷層與鋼板之界面起到成為上述平均硬度的0.9倍之位置為止之距離定義為表層軟質層之厚度。
惟,當自鍍敷層與鋼板之界面起10μm的位置之硬度超過自板厚1/4位置起到板厚1/2位置為止的區域之平均硬度的0.9倍時,難以藉由上述之方法測定表層軟質層之厚度。當時,藉由SEM觀察調查組織分率的變化,求得表層軟質層之厚度。
具體而言,以500~1000倍之倍率測定表層的組織,在垂直於板厚方向之方向中,於100~200μm之範圍內觀察金屬組織。然後,分別求得自鍍敷層與鋼板之
界面起2、4、6、8、10μm之位置的硬質組織之分率。又,求得自板厚1/4位置起到板厚1/2位置為止的區域之硬質組織的平均分率,界定成為上述平均分率的0.9倍之位置,將該位置與鍍敷層及鋼板之界面的距離定義為表層軟質層之厚度。此處,所謂硬質組織之分率,就是指肥粒鐵及波來鐵以外的組織之合計面積率。
(F)製造方法
本發明的合金化熔融鍍鋅鋼板之製造條件係沒有特別的限制,但可藉由以下所示的製造方法來製造。於以下的製造方法中,依順序進行下述(a)至(l)之步驟。詳細說明各步驟。
(a)熔製步驟
熔製具有上述化學組成的鋼塊或扁胚。熔製步驟的條件係沒有特別的限制,可使用通常之方法。
(b)熱軋步驟
加熱鋼塊或扁胚,施予熱軋而成為熱軋鋼板。熱軋步驟之條件亦不設特別的限制,例如較佳將熱軋前的加熱溫度設為1000~1300℃,將熱軋的加工溫度設為800~1000℃。
加熱溫度未達1000℃時,在熱軋之前的搬送期間溫度降低,有無法以所要的溫度完成加工輥軋之虞。
另一方面,加熱溫度若超過1300℃,則有達到具有上述化學組成的鋼之熔點而熔化之虞。
又,具有本發明所規定的化學組成之鋼由於硬,若加工溫度未達800℃,則對於輥軋機造成的大的負荷,有熱軋變困難之虞。另一方面,加工溫度若超過1000℃,則輥軋後的鋼板之結晶變粗大,有最終所得之合金化熔融鍍敷鋼板的各種特性降低之虞。
(c)第1冷卻步驟
冷卻加工輥軋結束後的熱軋鋼板。第1冷卻步驟的冷卻條件係不設特別的限制,但較佳為以10℃/s以上之平均冷卻速度進行冷卻,於300~700℃的溫度範圍中停止冷卻。
熱軋鋼板之組織若微細,則容易得到Mn濃化的效果,但平均冷卻速度若未達10℃/s,則相變態係在高溫發生,有組織粗大化之虞。平均冷卻速度之上限係沒有特別的限定,但工業上平均冷卻速度若超過200℃/s,則冷卻停止溫度之控制變困難,發生材質的偏差。因此,平均冷卻速度較佳設為200℃/s以下,更佳設為100℃/s以下,尤佳設為60℃/s以下。
又,冷卻停止溫度若未達300℃,則鋼板之組織變成麻田散鐵主體,有捲取變困難之虞。另一方面,冷卻停止溫度若超過700℃,則鋼板之表面所生成的鱗皮(scale)係到達鋼板內部,有酸洗變困難之虞。再者,於製
造上成為問題者係熱軋鋼板之強度及酸洗的容易性,故可考慮此等,適宜設定冷卻停止溫度。
(d)捲取步驟
捲取冷卻停止後的熱軋鋼板。捲取溫度亦沒有特別的限定,但較佳為700℃以下。捲取溫度亦與前述第1冷卻步驟的冷卻停止溫度同樣,可考慮熱軋鋼板之強度及酸洗之容易性來適宜設定。
(e)冷軋步驟
將經捲取的熱軋鋼板再退捲,於酸洗後,施予冷軋而成為冷軋鋼板。冷軋步驟之條件亦不設特別的限制。惟,由於具有本發明規定的化學組成之鋼係硬,若軋縮率超過90%,則以短時間結束冷軋者係變難。因此,冷軋步驟的軋縮率較佳為90%以下。以軋縮率為90%以下之範圍,考慮所望之板厚及輥軋機之能力而適宜設定即可。
(f)退火步驟
對於冷軋後的冷軋鋼板,施予在Ac1點~920℃的溫度範圍中保持5s以上之退火。退火溫度若未達Ac1點,則由於雪明碳鐵不變成沃斯田鐵,無法得到變韌鐵、殘留沃斯田鐵及回火麻田散鐵作為最終組織,故必須Ac1點以上。另一方面,退火溫度愈高溫則在鋼板表面上所生成的鱗皮愈厚,鍍敷時的潤濕性變差。又,從抑制粒徑的粗大
化而確保良好的韌性之觀點,及從減低能量成本之觀點來看,退火溫度係設為920℃以下。退火溫度較佳設為900℃以下。
又,若在上述的退火溫度保持的保持時間未達5s,則取決於鋼板之場所,發生溫度不均,無法使組織充分地均勻化,難以得到充分的局部伸長率。因此,保持時間係設為5s以上。保持時間較佳設為10s以上。
退火環境係不設特別的限制。然而,為了調整鋼板的表層軟質層之厚度,宜按照退火溫度來露點控制退火環境。如上述,當表層軟質層之厚度為10μm以下時,鋼板的疲勞限度相對於拉伸強度之比變高,疲勞特性升高。當表層軟質層之厚度超過10μm時,鋼板之耐液體金屬脆性裂紋性升高。
具體而言,為了使表層軟質層之厚度超過10μm,較佳為將退火環境之露點設為-25℃以上,更佳設為超過-15℃,尤佳設為超過-10℃。另一方面,為了使表層軟質層之厚度成為10μm以下,較佳為將退火環境之露點設為-15℃以下,更佳設為-20℃以下,尤佳設為-25℃以下。
(g)第2冷卻步驟
將退火後的冷軋鋼板以1℃/s以上之平均冷卻速度冷卻到100~350℃的溫度範圍為止。第2冷卻步驟的平均冷卻速度若未達1℃/s,則發生在鋼板中雪明碳鐵析出之
虞。平均冷卻速度較佳為5℃/s以上,更佳為8℃/s以上。
惟,由於平均冷卻速度若超過100℃/s,則冷卻速度過快,故在殘留沃斯田鐵發生的溫度範圍(100~350℃)中誘導鋼板者變困難。因此,平均冷卻速度較佳為容易控制在目的之冷卻停止溫度的速度,較佳設為100℃/s以下,更佳設為50℃/s以下。
又,冷卻停止溫度若未達100℃,則沃斯田鐵幾乎都變態成麻田散鐵,有無法確保10體積%以上的最終組織中之殘留沃斯田鐵之虞。另一方面,冷卻停止溫度若超過350℃,則麻田散鐵變態量變少,有無法確保5體積%以上的其後所得之高溫回火麻田散鐵之虞。因此,冷卻停止溫度係設為100~350℃。
冷卻停止溫度之下限係可按照鋼種類或熱處理條件而適宜設定,較佳設為130℃以上,更佳設為150℃以上,尤佳設為175℃以上,特佳設為200℃以上。又,冷卻停止溫度較佳設為300℃以下。
(b)前處理步驟
於對冷軋鋼板施予熔融鍍鋅之前,施予將冷軋鋼板冷卻或加熱至熔融鍍鋅浴溫度為止之前處理。鋼板的溫度若大地脫離鍍敷溫度,則將鋼板浸漬於鍍敷浴中時,有造成外觀不良之可能性。再者,未必需要使冷軋鋼板的溫度與鍍敷浴溫度嚴密地一致,若為50℃左右之差的範圍內則
容許。
(i)鍍敷步驟
於前處理完成後,將冷軋鋼板浸漬於熔融鍍鋅浴中,對鋼板施予熔融鍍鋅而成為熔融鍍鋅鋼板。熔融鍍鋅浴之浴組成、浴溫度及鍍敷附著量係沒有特別的限定,可按照所欲的熔融鍍鋅層之組成及厚度來適宜設定。鍍敷附著量例如可將每單面的鍍敷附著量設為20~80g/m2之範圍內。
(j)合金化步驟
藉由將熔融鍍鋅鋼板加熱至480~600℃,將熔融鍍鋅合金化而成為合金化熔融鍍鋅鋼板。合金化處理之條件只要是以將合金化熔融鍍鋅層中之Fe量確保在指定量以上之方式適宜設定即可。例如,當每單面的鍍敷附著量為20~80g/m2之範圍內時,較佳為將熔融鍍鋅鋼板加熱至490~560℃,保持5~60s。
(k)第3冷卻步驟
於合金化處理之後,將合金化熔融鍍鋅鋼板以1℃/s以上之平均冷卻速度冷卻到80~300℃的的溫度範圍為止。第3冷卻步驟的冷卻開始溫度係合金化步驟結束時的鋼板溫度。
藉由第3冷卻步驟之冷卻,促進麻田散鐵的
一部分生成,同時促進C從變韌鐵變態與麻田散鐵到沃斯田鐵之分配,使殘留沃斯田鐵安定化。於第3冷卻步驟後之回火步驟中,為了確保10體積%以上的殘留沃斯田鐵,必須在第3冷卻步驟之結束時間點,沃斯田鐵以10體積%以上存在於鋼板中。
平均冷卻速度若未達1℃/s,則有得不到上述效果之虞。平均冷卻速度較佳設為5℃/s以上。平均冷卻速度之上限係沒有特別的限定,但從經濟性之觀點來看,較佳設為500℃/s以下。
又,冷卻停止溫度若未達80℃或超過300℃,則同樣地有得不到上述效果之虞。冷卻停止溫度較佳設為110℃以上。由於冷卻停止溫度愈低強度愈高,冷卻結束溫度較佳設為250℃以下。
(l)回火步驟
對於冷卻停止後的合金化熔融鍍鋅鋼板,施予在100~450℃的溫度範圍中保持1s以上48h以下之回火處理。回火係為了得到將麻田散鐵回火之效果、促進變韌鐵變態之效果、以及使C自麻田散鐵及變韌鐵往殘留沃斯田鐵濃化之效果而進行。
回火溫度若未達100℃,則有得不到上述效果之虞。另一方面,回火溫度若超過450℃,則變成高溫回火麻田散鐵,強度大幅變差。又,C已濃化的沃斯田鐵係分解成波來鐵。因此,回火溫度係設為100~450℃。回
火溫度較佳設為120℃以上,更佳設為140℃以上。又,回火溫度較佳設為430℃以下。
又,回火時間(保持時間)若未達1s,則得不到回火效果。另一方面,回火時間若超過48h,則即使將回火溫度設為100~450℃,也碳化物析出,有殘留沃斯田鐵大幅減少之虞。因此,回火時間係設為1s以上48h以下。回火時間較佳設為10s以上,更佳設為30s以上。又,回火時間較佳設為45h以下,更佳設為40h以下。
(m)其他
於回火步驟之後,為了改善合金化熔融鍍鋅鋼板之平坦性,可對鋼板施予平整軋壓或調平處理。再者,於合金化熔融鍍鋅鋼板上,亦可形成具有塗油或潤滑作用之皮膜。
如以上說明,藉由使用上述製造方法,即使鋼板含有0.25質量%以上的C,也可製造1470MPa級以上且高延展性之合金化熔融鍍鋅鋼板。
以下,藉由實施例更具體地說明本發明,惟本發明不受此等實施例所限定。
熔製具有表1中所示之化學組成的鋼,製作厚度40mm的扁胚。將此扁胚在表2~4中所示的條件下熱軋,製造熱軋鋼板。
接著,以表2~4中所示的速度(第1冷卻速度),用噴水將上述熱軋鋼板冷卻到捲取溫度為止。然後,裝入爐內,在捲取溫度保持60min,藉由以20℃/h之平均冷卻速度在爐內冷卻到100℃以下的溫度為止,模擬捲取。對於所得之熱軋鋼板,酸洗而去除鱗皮後,於表2~4所示的條件下冷軋。
[表1]
自所得之冷軋鋼板採集試驗材。進行將試驗材加熱到指定的溫度為止而保持之退火,接著,以指定的速度(第2冷卻速度)冷卻。表2~4中一併顯示退火步驟之最高退火溫度、退火時間及露點、以及第2冷卻步驟之第2冷卻速度及第2冷卻停止溫度。
然後,對於一部分的試驗材,進行等溫保持後,以5℃/s加熱或冷卻到熔融鍍敷浴溫之460℃為止,進行熔融鍍鋅。然後,以表2~4中所示的GA條件進行合金化處理,接著以10℃/s之速度(第3冷卻速度),冷卻到第3冷卻停止溫度為止。冷卻後,以10℃/s之速度加熱,以表2~4中所示之條件進行回火處理後,以10℃/s之冷卻速度冷卻到室溫為止。
為了比較,亦以表5中所示的以往之製造條件,製作合金化熔融鍍鋅鋼板。到冷軋步驟為止係與上述相同之步驟。於冷軋步驟之後進行退火,然後進行第2冷卻。然後,以10℃/s之速度加熱到回火溫度為止,進行回火處理。然後,直接升溫,以表5中所示之GA條件進行合金化處理,接著以10℃/s之速度(第3冷卻速度),冷卻到第3冷卻停止溫度為止。
接著,進行所得之合金化熔融鍍鋅鋼板的金屬組織觀察,進行各組織的體積率及殘留沃斯田鐵中的C量之測定。
殘留沃斯田鐵的體積率(Vγ)係使用Mo-K α線所得之數據,藉由下式算出。
V γ=(2/3){100/(0.7×α(111)/γ(200)+1)}+(1/3){100/(0.78×α(211)/γ(311)+1)}
惟,α(211)、γ(200)、α(211)及γ(311)表示面強度。
又,殘留沃斯田鐵的C量(Cγ)係藉由Cu-K α線的X射解析,自沃斯田鐵的(200)面、(220)面及(311)面之反射角,求得晶格常數(單位為埃),依照下式算出。
Cγ=(晶格常數-3.572)/0.033
接著,用F.S.Lepera:Journal of Metals 32,No.3,(1980)38-39中記載之方法,腐蝕輥軋方向的剖面,使新鮮麻田散鐵及殘留沃斯田鐵出現。然後,於板厚1/4位置中,使用光學顯微鏡以1000倍的倍率觀察,將組織照片予以影像處理,測定新鮮麻田散鐵及殘留沃斯田鐵之合計面積率(%),將其當作合計體積率。
然後,自新鮮麻田散鐵及殘留沃斯田鐵之合計體積率的值,扣除藉由上述之方法所測定之殘留沃斯田鐵的體積率,求得新鮮麻田散鐵的體積率。
再者,切出垂直於輥軋方向之剖面,鏡面研磨後,對於經電解研磨的樣品,用SEM-EBSD以0.1step間隔測定100μm×100μm以上之區域。然後,使用股份有限公司TSL Solutions的分析軟體,算出各個結晶粒中的粒內之Image Quality的平均值(Grain Average Image Quality:GAIQ值)。
然後,將GAIQ值為5000以下的結晶粒之分率當作低溫回火麻田散鐵與新鮮麻田散鐵之合計體積率。藉由自此值扣除新鮮麻田散鐵的體積率,求得低溫回火麻田散鐵的體積率。
又,切出垂直於輥軋方向之剖面,鏡面研磨後,用硝酸腐蝕液進行腐蝕。對於該樣品進行SEM觀察,求得板條狀的組織且含有雪明碳鐵者之分率作為高溫回火麻田散鐵與低溫回火麻田散鐵之合計面積率,將其當
作合計體積率。SEM觀察係以5000倍的倍率進行,測定區域係使25μm×20μm之區域成為4個視野以上。藉由自此值扣除低溫回火麻田散鐵的體積率,求得高溫回火麻田散鐵的體積率。
變韌鐵與回火麻田散鐵之合計亦藉由SEM觀察求得。將觀察到變韌鐵或麻田散鐵之區塊者當作變韌鐵或回火麻田散鐵。然後,測定變韌鐵與回火麻田散鐵之合計面積率,將其當作合計體積率。
對於肥粒鐵及波來鐵,亦同樣地進行硝酸腐蝕液腐蝕後,用SEM觀察,不是下部組織,將被挖的區域當作肥粒鐵,將看得見層狀組織者當作波來鐵。而且,求得肥粒鐵及波來鐵各自的面積率,將其當作體積率。
又,進行各合金化熔融鍍鋅鋼板之鍍敷層中所含有的Fe量之測定。具體而言,以熔融鍍鋅層與母材之界面作為起點,使用能量分散型X射線分析裝置(EDX)測定(1/8×鍍敷層厚度)~(7/8×鍍敷層厚度)的區域之Fe濃度(質量%)。然後,算出其平均值,當作鍍敷層中所含有的Fe量。
再者,使用各合金化熔融鍍鋅鋼板,藉由以下的程序進行表層軟質層之厚度的測定。
首先,切出垂直於輥軋方向的剖面,鏡面研磨。然後,自該樣品的鍍敷層與鋼板之界面起10μm的位置到板厚之中心(板厚1/2位置)為止,以10μm間距依順序測定微維氏硬度。試驗力係按照組織的硬度,在2~
25gf之範圍調整。又,當壓痕重疊時,在垂直於板厚之方向中挪移測定。
自上述的測定結果,求得自板厚1/4位置起到板厚1/2位置為止的區域之平均硬度,界定成為其硬度的0.9倍之位置。然後,求得自鍍敷層與鋼板之界面起到成為上述平均硬度的0.9倍之位置為止之距離作為表層軟質層之厚度。
惟,當自鍍敷層與鋼板之界面起10μm的位置之硬度超過自板厚1/4位置起到板厚1/2位置為止的區域之平均硬度的0.9倍時,藉由SEM觀察調查組織分率的變化,求得表層軟質層之厚度。
具體而言,以500~1000倍之倍率測定表層的組織,在垂直於板厚方向之方向中,於100~200μm之範圍內觀察金屬組織。然後,分別求得自鍍敷層與鋼板之界面起2、4、6、8、10μm之位置的硬質組織之分率。又,求得自板厚1/4位置起到板厚1/2位置為止的區域之硬質組織的平均分率,界定成為上述平均分率的0.9倍之位置,將該位置與鍍敷層及鋼板之界面的距離當作表層軟質層之厚度。
表6~9中彙總顯示上述之觀察結果及測定結果。
[表6]
[表7]
[表8]
接著,進行所得之合金化熔融鍍鋅鋼板的機械特性之測定。自施有熱處理的試驗材,以輥軋方向及對於寬度方向而言垂直方向成為拉伸方向之方式,採集JIS5號拉伸試驗片,測定降伏強度(YS)、拉伸強度(TS)、均勻伸長率(uEL)、總伸長率(tEL)。又,將總伸長率與均勻伸長率之差當作局部伸長率(1EL)。
又,使用各合金化熔融鍍鋅鋼板,進行疲勞特性之評價。疲勞限度係使用JIS1號試驗片,藉由平面
彎曲疲勞試驗測定。而且,將應力比設為-1,將重複頻率設為25Hz。首先,對於各鋼板,進行施加拉伸強度的0.6倍應力之疲勞試驗。結果,由於全部的鋼板在未達2×106次之重複數斷裂,自該應力起每20MPa下降,重複進行同樣的疲勞試驗。而且,當成為在2×106次不發生斷裂的應力時,升高10MPa的應力進行試驗。於其亦不斷裂時,升高5MPa上的應力進行試驗,當斷裂時,降低5MPa的應力進行試驗。於以上述要領進行的疲勞試驗之中,將在最大重複數為2×106次時不發生斷裂的最大應力當作疲勞限度。
再者,使用各合金化熔融鍍鋅鋼板,藉由以下之程序進行耐液體金屬脆性裂紋性之評價。
重疊2片相同的鋼板,以點焊接合,以SEM觀察接合部之剖面,調查液體金屬脆性裂紋之態樣。點焊係使用Cr-Cu電極,對於2片重疊的鋼板以5°的打角進行。通電模式係使用50Hz的電源,將加壓力設為250~750kgf,將熔核(nugget)直徑成為5.5~6.0mm之電流以40循環通電之通電模式。
液體金屬脆性裂紋之態樣,係研磨包含熔核之中心的鋼板剖面,以SEM觀察,用以下的裂紋評分評價裂紋的程度。
1:於板組之內側發生裂紋,裂紋的長度超過10μm。
2:於板組之內側發生裂紋,但裂紋的長度為10μm
以下。
3:裂紋進展到熔核為止,或在與熔核距離300μm的位置之板組的外側發生裂紋。
4:僅在電極所接觸的鋼板之表面部分與熔核之間發生裂紋。
5:無裂紋。
表10~13中顯示機械特性之測定結果以及疲勞特性及耐液體金屬脆性裂紋性之評價結果。
[表10]
[表11]
[表12]
於本發明例之試驗No.1-4、9~16、23、24、28~30、33~71及80~85中,可知TS超過1470MPa,拉伸強度與均勻伸長率之積為13000MPa%以上,拉伸強度與局部伸長率之積為5000MP%以上,具有優異的成形性,而且於鍍敷層中亦完成充分的合金化。
相對於其,試驗No.5、18、19及25由於第2冷卻停止溫度高,而得不到高溫回火麻田散鐵,拉伸強度
與均勻伸長率之積變低。試驗No.6由於最高退火溫度低,而大量地發生肥粒鐵-波來鐵變態,拉伸強度變低。試驗No.7由於第2冷卻速度慢,而於冷卻途中,進行波來鐵變態,故殘留沃斯田鐵分率變低,拉伸強度與均勻伸長率之積變低。
試驗No.8由於回火處理之時間長,殘留沃斯田鐵往含碳化物的變韌鐵分解,而殘留沃斯田鐵量變少,拉伸強度與均勻伸長率之積變低。試驗No.17由於第2冷卻停止溫度低,於此溫度麻田散鐵變態大量地進行,而沃斯田鐵幾乎不殘留,拉伸強度與均勻伸長率之積變低。
試驗No.20由於回火處理溫度高,沃斯田鐵分解成含碳化物的變韌鐵,而殘留沃斯田鐵少,拉伸強度與均勻伸長率之積變低。試驗No.21由於回火處理溫度低,且試驗No.22由於不施予回火處理,而C皆不往沃斯田鐵中濃化,新鮮麻田散鐵變多,拉伸強度與局部伸長率之積變低。
試驗No.26雖然機械特性優異,但起因於合金化溫度低,鍍敷層之合金化變不充分。試驗No.27由於合金化溫度高,大量地發生波來鐵,而殘留沃斯田鐵分率變低,拉伸強度與均勻伸長率之積變低。
試驗No.31係第3冷卻停止溫度高,回火麻田散鐵量少,更且其後亦不進行變韌鐵變態,結果C不在沃斯田鐵中濃化,最終地發生新鮮麻田散鐵,故拉伸強度與均勻伸長率之積及拉伸強度與局部伸長率之積皆變低。
又,試驗No.32由於第3冷卻停止溫度低,於此時間點大量地發生麻田散鐵,沃斯田鐵變少,故拉伸強度與均勻伸長率之積及拉伸強度與局部伸長率之積皆變低。
試驗No.72係C含量比規定範圍更低,拉伸強度變低。試驗No.73係C含量比規定範圍更高,殘留沃斯田鐵成為過剩,於拉伸試驗開始後立即斷裂。試驗No.74係Si含量比規定範圍更低,無法確保殘留沃斯田鐵,拉伸強度與均勻伸長率之積變低。
試驗No.75係Si含量比規定範圍更高,於冷軋時斷裂。試驗No.76係Mn含量比規定範圍更低,於第2冷卻中進行波來鐵變態,無法確保殘留沃斯田鐵,拉伸強度變低。試驗No.77~79各自由於Mn、Cr及Mo之含量比規定範圍更高,而不進行變韌鐵變態,C不往沃斯田鐵中濃化,麻田散鐵大量地殘留,拉伸強度與局部伸長率之積變低。
試驗No.86~89係依照以往的手法於回火處理後進行合金化處理之例。於試驗No.86及87中,雖然由於合金化溫度充分而合金化進行,但殘留沃斯田鐵及低溫回火麻田散鐵的體積率變低,拉伸強度及拉伸強度與均勻伸長率之積變低。試驗No.88中雖然亦合金化進行某程度,但低溫回火麻田散鐵的體積率變低,拉伸強度及拉伸強度與均勻伸長率之積變低。試驗No.89中由於合金化溫度低,而除了合金化變不充分,還有低溫回火麻田散鐵的體積率低,故拉伸強度變低。根據以上,於以往的手法
中,強度-延展性平衡與充分的合金化之並存係困難。
再者,於本發明例中,在退火步驟中露點設為-25℃以下的試驗No.2、12、24、29、66~68、84及85,係表層軟質層之厚度成為10μm以下,疲勞限度相對於拉伸強度之比變高,成為疲勞特性優異之結果。
另一方面,退火步驟中露點設為-10℃以上的試驗No.1、3、4、9~11、13~16、23、28、30、33~65、69~71及80~83,係表層軟質層之厚度超過10μm,裂紋評分成為4以上,成為耐液體金屬脆性裂紋性優異之結果。
依照本發明,可得到一邊具有1470MPa以上的高拉伸強度,一邊均勻變形性(均勻伸長率)及局部變形性(局部伸長率)優異之合金化熔融鍍鋅鋼板。
Claims (10)
- 一種合金化熔融鍍鋅鋼板,其係在鋼板之表面上具備合金化熔融鍍鋅層之合金化熔融鍍鋅鋼板,前述鋼板之化學組成以質量%表示,C:0.25~0.70%、Si:0.25~2.50%、Mn:1.00~5.00%、Al:0.005~3.50%、P:0.15%以下、S:0.03%以下、N:0.02%以下、O:0.01%以下、Ti:0~0.50%、Nb:0~0.50%、V:0~0.50%、Cr:0~1.50%、Mo:0~1.50%、Cu:0~5.00%、Ni:0~5.00%、B:0~0.003% Ca:0~0.05%、REM:0~0.05%、Mg:0~0.05%、W:0~0.50%、 Zr:0~0.05%、Sb:0~0.50%、Sn:0~0.50%、As:0~0.05%、Te:0~0.05%、Y:0~0.20%、Hf:0~0.20%、Co:0~1.00%、剩餘部分:Fe及雜質;前述鋼板之板厚1/4位置的金屬組織以體積%表示,殘留沃斯田鐵:10.0~60.0%、高溫回火麻田散鐵:5.0%以上、低溫回火麻田散鐵:5.0%以上、新鮮麻田散鐵:10.0%以下、肥粒鐵:0~15.0%、波來鐵:0~10.0%、剩餘部分:變韌鐵;高溫回火麻田散鐵、低溫回火麻田散鐵與變韌鐵之合計體積率為30.0%以上,拉伸強度為1470MPa以上,拉伸強度與均勻伸長率之積為13000MPa%以上,拉伸強度與局部伸長率之積為5000MPa%以上。
- 如請求項1之合金化熔融鍍鋅鋼板,其中前述化學組成以質量%表示, Si+Al:0.80%以上。
- 如請求項1或2之合金化熔融鍍鋅鋼板,其中前述化學組成以質量%表示,含有由以下所選出的1種以上,Ti:0.005~0.50%、Nb:0.005~0.50%、V:0.005~0.50%、Cr:0.01~1.50%、Mo:0.01~1.50%、Cu:0.01~5.00%、Ni:0.01~5.00%、B:0.0001~0.003%、Ca:0.0001~0.05%、REM:0.0005~0.05%、Mg:0.0001~0.05%、W:0.005~0.50%、Zr:0.005~0.05%、Sb:0.005~0.50%、Sn:0.005~0.50%、As:0.005~0.05%、Te:0.001~0.05%、Y:0.001~0.20%、Hf:0.001~0.20%、及Co:0.001~1.00%。
- 如請求項1至3中任一項之合金化熔融鍍鋅鋼板, 其中前述殘留沃斯田鐵中所含有的C量為0.85質量%以上。
- 如請求項1至4中任一項之合金化熔融鍍鋅鋼板,其中前述合金化熔融鍍鋅層中所含有的Fe量為3.0~20.0質量%。
- 如請求項1至5中任一項之合金化熔融鍍鋅鋼板,其中前述鋼板係在表層具備表層軟質層,該表層軟質層具有自板厚1/4位置起到板厚1/2位置為止的區域之平均硬度的0.9倍以下之硬度,前述表層軟質層之自前述合金化熔融鍍鋅層與前述鋼板之界面起的厚度係超過1.0μm。
- 如請求項1至5中任一項之合金化熔融鍍鋅鋼板,其中前述鋼板係在表層具備表層軟質層,該表層軟質層具有自板厚1/4位置起到板厚1/2位置為止的區域之平均硬度的0.9倍以下之硬度,前述表層軟質層之自前述合金化熔融鍍鋅層與前述鋼板之界面起的厚度為10μm以下,前述鋼板的疲勞限度相對於拉伸強度之比為0.30以上。
- 一種合金化熔融鍍鋅鋼板之製造方法,其係製造如請求項1至5中任一項之合金化熔融鍍鋅鋼板之方法,依順序進行下述(a)至(l)之步驟,包含:(a)熔製具有上述(1)至(3)中任一項記載之化學組成的鋼塊或扁胚之熔製步驟, (b)加熱前述鋼塊或扁胚,施予熱軋而成為熱軋鋼板之熱軋步驟,(c)冷卻前述熱軋鋼板之第1冷卻步驟,(d)捲取前述熱軋鋼板之捲取步驟,(e)退捲前述熱軋鋼板,酸洗後,施予冷軋而成為冷軋鋼板之冷軋步驟,(f)將前述冷軋鋼板在Ac1點~920℃的溫度範圍中保持5s以上之退火步驟,(g)將前述冷軋鋼板以1℃/s以上之平均冷卻速度冷卻到100~600℃的溫度範圍為止之第2冷卻步驟,(h)將前述冷軋鋼板冷卻或加熱到熔融鍍鋅浴溫度為止之前處理步驟,(i)將前述冷軋鋼板浸漬於熔融鍍鋅浴中,對鋼板施予熔融鍍鋅而成為熔融鍍鋅鋼板之鍍敷步驟,(j)將前述熔融鍍鋅鋼板加熱至480~600℃,將熔融鍍鋅合金化而成為合金化熔融鍍鋅鋼板之合金化步驟,(k)將前述合金化熔融鍍鋅鋼板以1℃/s以上之平均冷卻速度冷卻到80~300℃的溫度範圍為止之第3冷卻步驟,及(l)將前述合金化熔融鍍鋅鋼板在100~450℃的溫度範圍中保持1s以上48h以下之回火步驟。
- 一種合金化熔融鍍鋅鋼板之製造方法,其係製造如請求項6之合金化熔融鍍鋅鋼板之方法,依順序進行下述(a)至(l)之步驟,包含: (a)熔製具有上述(1)至(3)中任一項記載之化學組成的鋼塊或扁胚之熔製步驟,(b)加熱前述鋼塊或扁胚,施予熱軋而成為熱軋鋼板之熱軋步驟,(c)冷卻前述熱軋鋼板之第1冷卻步驟,(d)捲取前述熱軋鋼板之捲取步驟,(e)退捲前述熱軋鋼板,酸洗後,施予冷軋而成為冷軋鋼板之冷軋步驟,(f)將前述冷軋鋼板在露點為-25℃以上的環境下,於Ac1點~920℃的溫度範圍中保持5s以上之退火步驟,(g)將前述冷軋鋼板以1℃/s以上之平均冷卻速度冷卻到100~600℃的溫度範圍為止之第2冷卻步驟,(h)將前述冷軋鋼板冷卻或加熱到熔融鍍鋅浴溫度為止之前處理步驟,(i)將前述冷軋鋼板浸漬於熔融鍍鋅浴中,對鋼板施予熔融鍍鋅而成為熔融鍍鋅鋼板之鍍敷步驟,(j)將前述熔融鍍鋅鋼板加熱至480~600℃,將熔融鍍鋅合金化而成為合金化熔融鍍鋅鋼板之合金化步驟,(k)將前述合金化熔融鍍鋅鋼板以1℃/s以上之平均冷卻速度冷卻到80~300℃的溫度範圍為止之第3冷卻步驟,及(l)將前述合金化熔融鍍鋅鋼板在100~450℃的溫度範圍中保持1s以上48h以下之回火步驟。
- 一種合金化熔融鍍鋅鋼板之製造方法,其係製造 如請求項7之合金化熔融鍍鋅鋼板之方法,依順序進行下述(a)至(l)之步驟,包含:(a)熔製具有上述(1)至(3)中任一項記載之化學組成的鋼塊或扁胚之熔製步驟,(b)加熱前述鋼塊或扁胚,施予熱軋而成為熱軋鋼板之熱軋步驟,(c)冷卻前述熱軋鋼板之第1冷卻步驟,(d)捲取前述熱軋鋼板之捲取步驟,(e)退捲前述熱軋鋼板,酸洗後,施予冷軋而成為冷軋鋼板之冷軋步驟,(f)將前述冷軋鋼板在露點為-15℃以下的環境下,於Ac1點~920℃的溫度範圍中保持5s以上之退火步驟,(g)將前述冷軋鋼板以1℃/s以上之平均冷卻速度冷卻到100~600℃的溫度範圍為止之第2冷卻步驟,(h)將前述冷軋鋼板冷卻或加熱到熔融鍍鋅浴溫度為止之前處理步驟,(i)將前述冷軋鋼板浸漬於熔融鍍鋅浴中,對鋼板施予熔融鍍鋅而成為熔融鍍鋅鋼板之鍍敷步驟,(j)將前述熔融鍍鋅鋼板加熱至480~600℃,將熔融鍍鋅合金化而成為合金化熔融鍍鋅鋼板之合金化步驟,(k)將前述合金化熔融鍍鋅鋼板以1℃/s以上之平均冷卻速度冷卻到80~300℃的溫度範圍為止之第3冷卻步驟,及(l)將前述合金化熔融鍍鋅鋼板在100~450℃的溫度 範圍中保持1s以上48h以下之回火步驟。
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ES2732799T3 (es) * | 2011-09-30 | 2019-11-26 | Nippon Steel Corp | Chapa de acero galvanizada por inmersión en caliente y método de fabricación de la misma |
EP2762589B8 (en) * | 2011-09-30 | 2017-10-04 | Nippon Steel & Sumitomo Metal Corporation | High-strength hot-dip galvanized steel sheet excellent in impact resistance property and manufacturing method thereof, and high-strength alloyed hot-dip galvanized steel sheet and manufacturing method thereof |
EP2762592B1 (en) | 2011-09-30 | 2018-04-25 | Nippon Steel & Sumitomo Metal Corporation | High-strength hot-dipped galvanized steel sheet and high-strength alloyed hot-dipped galvanized steel sheet, each having tensile strength of 980 mpa or more, excellent plating adhesion, excellent formability and excellent bore expanding properties, and method for producing same |
TWI468534B (zh) | 2012-02-08 | 2015-01-11 | Nippon Steel & Sumitomo Metal Corp | 高強度冷軋鋼板及其製造方法 |
KR101699644B1 (ko) | 2012-11-06 | 2017-01-24 | 신닛테츠스미킨 카부시키카이샤 | 합금화 용융 아연 도금 강판과 그 제조 방법 |
JP6007882B2 (ja) * | 2013-10-15 | 2016-10-19 | 新日鐵住金株式会社 | 引張最大強度780MPaを有する衝突特性に優れた高強度鋼板、高強度溶融亜鉛めっき鋼板、並びに、高強度合金化溶融亜鉛めっき鋼板 |
JP6007881B2 (ja) | 2013-10-15 | 2016-10-12 | 新日鐵住金株式会社 | 引張最大強度780MPa以上を有する衝突特性に優れた高強度鋼板、高強度溶融亜鉛めっき鋼板及び高強度合金化溶融亜鉛めっき鋼板 |
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- 2016-06-10 JP JP2016564653A patent/JP6187710B2/ja active Active
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
TWI650435B (zh) * | 2018-03-30 | 2019-02-11 | 日商新日鐵住金股份有限公司 | 鋼板及其製造方法 |
TWI671409B (zh) * | 2018-08-28 | 2019-09-11 | 日商Jfe鋼鐵股份有限公司 | 鋼板及其製造方法 |
Also Published As
Publication number | Publication date |
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KR102081361B1 (ko) | 2020-02-25 |
US10745775B2 (en) | 2020-08-18 |
JP6187710B2 (ja) | 2017-08-30 |
WO2016199922A1 (ja) | 2016-12-15 |
CN114990431A (zh) | 2022-09-02 |
MX2017015286A (es) | 2018-02-19 |
EP3309273B1 (en) | 2021-05-26 |
JPWO2016199922A1 (ja) | 2017-06-22 |
BR112017025389A2 (pt) | 2018-08-07 |
US20180298462A1 (en) | 2018-10-18 |
EP3309273A1 (en) | 2018-04-18 |
EP3309273A4 (en) | 2018-12-26 |
KR20180016518A (ko) | 2018-02-14 |
CN107636184A (zh) | 2018-01-26 |
TWI602927B (zh) | 2017-10-21 |
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