TW201718906A - 合金化熔融鍍鋅鋼板及其製造方法 - Google Patents
合金化熔融鍍鋅鋼板及其製造方法 Download PDFInfo
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- TW201718906A TW201718906A TW105127089A TW105127089A TW201718906A TW 201718906 A TW201718906 A TW 201718906A TW 105127089 A TW105127089 A TW 105127089A TW 105127089 A TW105127089 A TW 105127089A TW 201718906 A TW201718906 A TW 201718906A
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- Prior art keywords
- steel sheet
- hot
- base material
- content
- dip galvanized
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 141
- 239000010959 steel Substances 0.000 title claims abstract description 141
- 238000005275 alloying Methods 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims description 20
- 238000007747 plating Methods 0.000 claims abstract description 65
- 239000000203 mixture Substances 0.000 claims abstract description 32
- 239000000126 substance Substances 0.000 claims abstract description 31
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 10
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052796 boron Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 claims description 70
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 56
- 239000008397 galvanized steel Substances 0.000 claims description 56
- 210000001161 mammalian embryo Anatomy 0.000 claims description 55
- 238000000137 annealing Methods 0.000 claims description 40
- 238000005246 galvanizing Methods 0.000 claims description 40
- 239000010960 cold rolled steel Substances 0.000 claims description 22
- 238000005098 hot rolling Methods 0.000 claims description 11
- 238000005097 cold rolling Methods 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 10
- 238000005336 cracking Methods 0.000 abstract description 31
- 229910052742 iron Inorganic materials 0.000 abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 abstract description 5
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 238000012360 testing method Methods 0.000 description 84
- 239000010936 titanium Substances 0.000 description 39
- 238000011156 evaluation Methods 0.000 description 35
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 28
- 239000006104 solid solution Substances 0.000 description 22
- 238000012545 processing Methods 0.000 description 19
- 239000011572 manganese Substances 0.000 description 18
- 239000010955 niobium Substances 0.000 description 18
- 238000005096 rolling process Methods 0.000 description 18
- 238000000034 method Methods 0.000 description 11
- 239000011701 zinc Substances 0.000 description 11
- 239000013078 crystal Substances 0.000 description 7
- 230000007704 transition Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 5
- 229910052725 zinc Inorganic materials 0.000 description 5
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 230000001681 protective effect Effects 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 210000002257 embryonic structure Anatomy 0.000 description 3
- 238000007654 immersion Methods 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 238000004804 winding Methods 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000012937 correction Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 206010067482 No adverse event Diseases 0.000 description 1
- 229910019142 PO4 Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 229910004298 SiO 2 Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- ZCDOYSPFYFSLEW-UHFFFAOYSA-N chromate(2-) Chemical compound [O-][Cr]([O-])(=O)=O ZCDOYSPFYFSLEW-UHFFFAOYSA-N 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000008034 disappearance Effects 0.000 description 1
- 238000009713 electroplating Methods 0.000 description 1
- 230000006355 external stress Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000009616 inductively coupled plasma Methods 0.000 description 1
- 239000003112 inhibitor Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000004020 luminiscence type Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000029052 metamorphosis Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 1
- 239000010452 phosphate Substances 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000012552 review Methods 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 230000037303 wrinkles Effects 0.000 description 1
Classifications
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- B32B15/00—Layered products comprising a layer of metal
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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- C—CHEMISTRY; METALLURGY
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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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C—CHEMISTRY; METALLURGY
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- 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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- C—CHEMISTRY; METALLURGY
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- C—CHEMISTRY; METALLURGY
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- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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Abstract
本發明提供一種合金化熔融鍍鋅鋼板,其具有高強度及優異的深拉性,更且抗扁胚裂紋性及耐二次加工脆性優異。本發明之合金化熔融鍍鋅鋼板的母材鋼板係以質量%表示,含有C:0.0080%以下、Si:0.7%以下、Mn:1.0~2.5%、P:超過0.030~0.048%、S:0.025%以下、Al:0.005~0.20%、N:0.010%以下、Ti:0.005~0.040%、Nb:0.005~0.060%及B:0.0005~0.0030%,剩餘部分係由Fe及雜質所構成,具有滿足式(1)~式(4)之化學組成。合金化熔融鍍鋅層含有7~15質量%的Fe。25×P+4×Si≦3.6 (1) B-X1≧0.0005 (2) C-(12/93)×Nb-X2≧-0.0035 (3) 110×Si+48×Mn+550×P≧120 (4)
Description
本發明關於合金化熔融鍍鋅鋼板及其製造方法,更詳細而言,關於具有440MPa以上的拉伸強度之高強度的合金化熔融鍍鋅鋼板及其製造方法。
最近,為了二氧化碳的排出量之減低及燃料消耗率減低,要求汽車的輕量化。再者,對於汽車的碰撞安全性之提高的要求係升高。鋼材的高強度化係有效於汽車的輕量化及碰撞安全性之提高。
於汽車零件之中,在面板零件係要求高的衝壓成形性(深拉性)。因此,以往於面板零件中,使用加工性高的軟質鋼板。然而,於面板零件中,亦要求上述的高強度化。
專利文獻1~3中提案具有高強度且深拉性優異之冷軋鋼板。於此等之文獻所揭示的冷軋鋼板中,下式定義的平均r值rm高。
rm=(rL+2×r45+rC)/4
上述式中的rL係在冷軋鋼板中,平行於軋製
方向的方向之r值。r45係相對於軋製方向而言45°方向之r值。rC係垂直於軋製方向的方向之r值。r值係稱為蘭克福特值(Lankford value),表示鋼板的塑性各向異性。
於上述面板零件之中,對於具有如側框架外部的形狀之零件,亦要求不僅平均r值rm高,而且下式定義的面內各向異性△r值小。
△r=(rL+rC)/2-r45
於側框架外部中之容納門的部位之四角落部分,要求r45高。於門之鉸鏈安裝部分,要求rL高。面內各向異性△r值愈小,愈能滿足此等的要求。專利文獻4中提案平均r值rm及面內各向異性△r值優異之深拉用高強度冷軋鋼板。
可是,作為汽車鋼板用之冷軋鋼板,有利用合金化熔融鍍鋅鋼板之情況。合金化熔融鍍鋅鋼板係在熔融鍍鋅處理後,藉由實施合金化處理而製造。合金化熔融鍍鋅鋼板通常係以蘭吉馬(Zendgimer)法為代表的線內退火方式來製造。於以蘭吉馬法為代表的線內退火方式中,連續地配置退火設備與熔融鍍鋅設備。因此,於退火後,連續地實施熔融鍍鋅處理。再者,合金化熔融鍍鋅鋼板之鍍層係由缺乏變形能力的金屬間化合物所構成,而拘束母材鋼板的變形。因此,合金化熔融鍍鋅鋼板之平均r值係比不具有鍍層的鋼板之平均r值還低。
於高深拉性的高強度冷軋鋼板中,為了得到高強度,Si含量係高。當Si含量高時,Si係在鋼板表面
變濃,而生成Si氧化物(SiO2)。Si氧化物係在熔融鍍鋅處理時容易發生不鍍。
專利文獻5~7提案即使Si含量高也難以發生不鍍的高強度冷軋鋼板之製造方法。於此等文獻中,對於經預先退火的冷軋鋼板,實施預鍍Ni。對於預鍍Ni後的鋼板,急速加熱到430~500℃為止而實施熔融鍍鋅處理。於熔融鍍鋅處理後,加熱到470~550℃而實施合金化處理。於此製造方法之情況中,可一邊維持原板的冷軋鋼板之加工性,一邊製造合金化熔融鍍鋅鋼板。再者,藉由實施預鍍Ni,即使Si含量高,也難以發生不鍍。
可是,於將鑄造後的扁胚冷卻到室溫為止時,有因內部應力(熱應力及變態應力等)而在扁胚中發生裂紋之情況。又,於移動扁胚的扁胚之操作時及扁胚之堆疊時,有外部應力負荷於扁胚而在扁胚中發生裂紋之情況。將如此的裂紋稱為「扁胚裂紋」。將對於扁胚裂紋抗性稱為「抗扁胚裂紋性」。
又,於冷軋鋼板中,當新的張力或衝撃力作用於深拉加工後的成形品之端部時,有發生沿著拉延方向的脆性破壞之情況。將如此的現象稱為「二次加工脆性」。將對於二次加工脆性的耐性稱為「耐二次加工脆性」。
於藉由專利文獻4~7中揭示的製造方法所製造的合金化熔融鍍鋅鋼板中,有上述的抗扁胚裂紋性及耐二次加工脆性低之情況。
專利文獻1:日本特公平8-30217號公報
專利文獻2:日本特公平8-26412號公報
專利文獻3:日本特開2001-131695號公報
專利文獻4:日本發明專利第4094498號公報
專利文獻5:日本發明專利第2526320號公報
專利文獻6:日本發明專利第2526322號公報
專利文獻7:日本特開2015-063729號公報
本發明之目的係在於提供具有高強度及優異的深拉性,更且抗扁胚裂紋性及耐二次加工脆性優異之高強度的合金化熔融鍍鋅鋼板及其製造方法。
本發明之合金化熔融鍍鋅鋼板具備母材鋼板與合金化熔融鍍鋅層。母材鋼板係以質量%表示,含有C:0.0080%以下、Si:0.7%以下、Mn:1.0~2.5%、P:超過0.030~0.048%、S:0.025%以下、Al:0.005~0.20%、N:0.010%以下、Ti:0.005~0.040%、Nb:0.005~0.060%及B:0.0005~0.0030%,剩餘部分由Fe及雜質
所構成,具有滿足式(1)~式(4)的化學組成。合金化熔融鍍鋅層係形成在母材鋼板之表面上,含有7~15質量%的Fe。合金化熔融鍍鋅鋼板的平均r值為1.2以上,面內各向異性△r值為-0.5~0.5,拉伸強度為440MPa以上。
25×P+4×Si≦3.6 (1)
B-X1≧0.0005 (2)
C-(12/93)×Nb-X2≧-0.0035 (3)
110×Si+48×Mn+550×P≧120 (4)
此處,於式中的各元素符號中,代入對應的元素之含量(質量%)。
再者,式(2)中的X1係如以下定義。
N-(14/48)×Ti>0時,X1=(11/14)[N-(14/48)×Ti],N-(14/48)×Ti≦0時,X1=0。
還有,(3)中的X2係如以下定義。
Ti-(48/14)×N>0時,X2=(12/48)[Ti-(48/14)×N],Ti-(48/14)×N≦0時,X2=0。
本發明的合金化熔融鍍鋅鋼板之製造方法具備:對具有上述化學組成的扁胚,以800~950℃的精軋溫度實施熱軋而製造熱軋鋼板,以600~760℃的捲取溫
度捲取熱軋鋼板之步驟,對於熱軋鋼板,實施冷軋而製造冷軋鋼板之步驟,對於前述冷軋鋼板,實施退火處理而製造母材鋼板之步驟,對於母材鋼板,實施熔融鍍鋅之步驟,與對於經熔融鍍鋅處理的母材鋼板,實施以470~620℃的合金化處理溫度保持10~40秒的合金化處理之步驟。
本發明之合金化熔融鍍鋅鋼板係具有高強度及優異的深拉性,更且抗扁胚裂紋性及耐二次加工脆性優異。本發明之製造方法係可製造上述合金化熔融鍍鋅鋼板。
圖1係顯示藉由以與後述的耐二次加工脆性評價試驗相同方法進行預備試驗而得之F1=25×P+4×Si與脆性龜裂長度(mm)的關係之圖。
圖2係顯示實施例中的抗扁胚裂紋性評價試驗所得之延性脆性斷面轉變溫度vTrs(℃)與合金化熔融鍍鋅鋼板的母材鋼板中之P含量(質量%)的關係之圖。
本發明者們係對於在具有高強度及優異的深拉性(高的平均r值及低的面內各向異性△r值)之合金化熔融鍍鋅鋼板中,得到優異的抗扁胚裂紋性及耐二次加工脆性之方法,進行調查及檢討。結果,本發明者們得到以下的知識見解。
(A)為了一邊具有440MPa以上高的拉伸強度,一邊得到優異的耐二次加工脆性,必須抑制合金化熔融鍍鋅鋼板的母材鋼板中之P及Si的含量。
定義F1=25×P+4×Si。於F1中的各元素符號中,代入合金化熔融鍍鋅鋼板的母材鋼板中之對應的元素之含量(質量%)。F1係耐二次加工脆性之指標。
圖1係以後述的耐二次加工脆性評價試驗為基礎而作成,顯示F1與脆性龜裂長度(mm)的關係之圖。圖1係由以下之方法所得。實施後述的耐二次加工脆性評價試驗。試驗材料之化學組成係除了F1為本發明之範圍內,還滿足式(2)~式(4)。當試驗後的試驗片之觀察結果為發生脆性龜裂時,測定脆性龜裂長度。測定結果係F1與脆性龜裂長度的關係如下。F1=1.8的試料之脆性龜裂長度為0。F1=2.5的試料之脆性龜裂長度為0。F1=3.1的試料之脆性龜裂長度為0。F1=3.6的試料之脆性龜裂長度為0。F1=3.8的試料之脆性龜裂長度為85mm。F1=4.2的試料之脆性龜裂長度為168mm。F1=4.6的試料之脆性龜裂長度為210mm。以所得之脆性龜裂長度為基礎,作成圖1。
參照圖1,若F1超過3.6,則隨著F1之增加而脆性龜裂長度顯著地增大。另一方面,若F1為3.6以下,則脆性龜裂係幾乎不發生。因此,合金化熔融鍍鋅鋼板若不滿足式(1),則可一邊具有440MPa以上的高強度,一邊提高耐二次加工脆性。
25×P+4×Si≦3.6 (1)
(B)若提高粒界強度,則可提高抗扁胚裂紋性及耐二次加工脆性。若固溶B及固溶C之量為恰當,則粒界強度升高。具體而言,若滿足式(2)及式(3),則可確保恰當量的固溶B及固溶C,可提高抗扁胚裂紋性及耐二次加工脆性。
B-X1≧0.0005 (2)
C-(12/93)×Nb-X2≧-0.0035 (3)
此處,於式中的各元素符號中,代入對應的元素之含量(質量%)。
式(2)中的X1係如以下定義。
N-(14/48)×Ti>0時,X1=(11/14)[N-(14/48)×Ti],N-(14/48)×Ti≦0時,X1=0。
(3)中的X2係如以下定義。
Ti-(48/14)×N>0時,X2=(12/48)[Ti-(48/14)×N],Ti-(48/14)×N≦0時,
X2=0。
定義F2=B-X1。定義F3=C-(12/93)×Nb-X2。F2係固溶B量之指標,F3係固溶C量之指標。若F2為0.0005以上,則有助於粒界強化的固溶B量係在鋼中充分地存在。又,若F3為-0.0035以上,則有助於粒界強度的固溶C量係在鋼中充分地存在。因此,滿足式(1)的合金化熔融鍍鋅鋼板之母材鋼板若進一步滿足式(2)及式(3),則粒界強度升高,抗扁胚裂紋性及耐二次加工脆性升高。
(C)為了一邊滿足上述式(1)~式(3),一邊使拉伸強度成為440MPa以上,合金化熔融鍍鋅鋼板的母材鋼板係滿足式(4)。
110×Si+48×Mn+550×P≧120 (4)
定義F4=110×Si+48×Mn+550×P。F4係鋼板的拉伸強度之指標。若F4為120以上,則滿足式(1)~式(3)的合金化熔融鍍鋅鋼板之拉伸強度係成為440MPa以上。
(D)本發明者們發現藉由進一步將合金化熔融鍍鋅鋼板的母材鋼板中之P含量設為0.048%以下,而於合金化熔融鍍鋅鋼板中,顯著地提高抗扁胚裂紋性。以下,說明此點。
圖2係顯示後述的抗扁胚裂紋性評價試驗所得之延性脆性斷面轉變溫度vTrs(℃)與合金化熔融鍍鋅鋼板中之P含量(質量%)的關係之圖。
參照圖2,P含量小於0.048%時,隨著P含量之降低,延性脆性斷面轉變溫度vTrs係顯著地降低,而成為-20℃以下。另一方面,當P含量成為0.048%以下時,即使P含量降低,延性脆性斷面轉變溫度vTrs也沒有如自-20℃起那麼地降低。即,於圖2中,反曲點存在於P含量=0.048%附近。
因此,若P含量為0.048%以下,則得到優異的抗扁胚裂紋性。另一方面,P係為了提高鋼的強度,P含量若為0.030%以下,則拉伸強度成為未達440MPa。因此,若滿足上述(A)~(D),且P含量為超過0.030%~0.048%以下,則得到一邊具有440MPa以上的拉伸強度及優異的耐二次加工脆性,一邊抗扁胚裂紋性優異的合金化熔融鍍鋅鋼板。
(E)將滿足上述式(1)~式(4)的化學組成之扁胚予以熱軋時,若精加工溫度FT(℃)為800~950℃,且捲取溫度CT(℃)為600~760℃,則得到優異的深拉性。即,平均r值為1.2以上,且面內各向異性△r值為-0.5~0.5。
基於以上的知識見解而完成的本發明之合金化熔融鍍鋅鋼板,係具備母材鋼板與合金化熔融鍍鋅層。母材鋼板係以質量%表示,含有C:0.0080%以下、Si:0.7%以下、Mn:1.0~2.5%、P:超過0.030~0.048%、S:0.025%以下、Al:0.005~0.20%、N:0.010%以下、Ti:0.005~0.040%、Nb:0.005~0.060%及B:0.0005~
0.0030%,剩餘部分由Fe及雜質所構成,具有滿足式(1)~式(4)的化學組成。合金化熔融鍍鋅層係形成在母材鋼板之表面上,含有7~15質量%的Fe。合金化熔融鍍鋅鋼板的平均r值為1.2以上,面內各向異性△r值為-0.5~0.5,拉伸強度為440MPa以上。
25×P+4×Si≦3.6 (1)
B-X1≧0.0005 (2)
C-(12/93)×Nb-X2≧-0.0035 (3)
110×Si+48×Mn+550×P≧120 (4)
此處,於式中的各元素符號中,代入對應的元素之含量(質量%)。
再者,式(2)中的X1係如以下定義。
N-(14/48)×Ti>0時,X1=(11/14)[N-(14/48)×Ti],N-(14/48)×Ti≦0時,X1=0。
還有,式(3)中的X2係如以下定義。
Ti-(48/14)×N>0時,X2=(12/48)[Ti-(48/14)×N],Ti-(48/14)×N≦0時,X2=0。
上述化學組成亦可含有C:未達0.0040%、Ti:0.005~0.035%、及Nb:0.005~0.035%。
上述化學組成也可含有C:0.0040~0.0080%
、Ti:0.005~0.040%、及Nb:0.005~0.060%。此時,式(3)之值較佳為-0.0002以上。
本發明的合金化熔融鍍鋅鋼板之製造方法具備:對具有上述化學組成的扁胚,以800~950℃的精軋溫度實施熱軋而製造熱軋鋼板,以600~760℃的捲取溫度捲取熱軋鋼板之步驟,對於熱軋鋼板,實施冷軋而製造冷軋鋼板之步驟,對於冷軋鋼板,實施退火處理而製造母材鋼板之步驟,對於母材鋼板,實施熔融鍍鋅之步驟,與對於經熔融鍍鋅處理的母材鋼板,實施以470~620℃的合金化處理溫度保持10~40秒的合金化處理之步驟。
關於上述的製造母材鋼板之步驟及實施熔融鍍鋅之步驟,可於實施所謂的蘭吉馬法等之線內退火後,於保護氣氛下將母材鋼板(鋼帶)導入至熔融鍍鋅浴中。又,亦可將退火處理後的冷軋鋼板(即母材鋼板)取出至爐外(所謂的線外退火),實施恰當的前洗淨後,視需要實施預鍍Ni處理等的前處理,於保護氣氛下加熱到430~480℃後,將母材鋼板導入至熔融鍍鋅浴中。
實施上述的線內退火時,Si等之易氧化性元素係在表面變濃。因此,若對於Si含量為0.25%以上的冷軋鋼板實施線內退火,則容易發生不鍍。因此,當Si含量為0.25%以上時,較佳為實施線外退火而製造母材鋼板,對於經由線外退火所製造的母材鋼板,實施預鍍Ni處理。此時,可一邊抑制不鍍之發生,一邊實施熔融鍍鋅處理。再者,對於Si含量未達0.25%的母材鋼板,即使實
施預鍍Ni處理,也毫無不良影響。
以下,詳述本發明的合金化熔融鍍鋅鋼板。與元素有關的「%」,只要沒有特別預先指明,則意指質量%。
本發明之合金化熔融鍍鋅鋼板具備母材鋼板與合金化熔融鍍鋅層。合金化熔融鍍鋅層係形成在母材鋼板之表面上。
母材鋼板之化學組成係具有以下的元素。
C:0.0080%以下
碳(C)係無可避免地含有。C係提高鋼的強度。C更作為固溶C而偏析至粒界,抑制鋼的二次加工脆性及抗扁胚裂紋性。然而,C含量若過高,則鋼的深拉性降低。具體而言,TiC及NbC過剩地生成而面內各向異性△r值升高。TiC及NbC更抑制退火時的粒成長,降低平均r值。因此,C含量為0.0080%以下。
為了將高強度及耐二次加工脆性予以進一步提高,C含量的較佳下限為0.0008%,更佳為0.0021%。再者,為了得到優異的深拉性,C含量的較佳上限為0.0070%,更佳為0.0050%。
使高強度及耐二次加工脆性特別提高時,較
佳的C含量為0.0040~0.0080%。使深拉性特別提高時,較佳的C含量為未達0.0040%。
Si:0.7%以下
矽(Si)係無可避免地含有。Si係藉由固溶強化而提高鋼板的強度。然而,Si含量若過高,則耐二次加工脆性降低,同時熔融鍍鋅步驟(線內退火之情況)中的不鍍變容易發生。Si含量若過高,則熱加工後的鱗皮剝離性降低,而且閃光對焊(flash butt)熔接性降低。因此,Si含量為0.7%以下。Si含量超過0.7%時,即使實施預鍍Ni,也有發生不鍍之情況。Si含量的較佳下限為0.1%,更佳為0.2%,尤佳為0.3%。Si含量的較佳上限為0.6%,更佳為0.5%。
Mn:1.0~2.5%
錳(Mn)係藉由固溶強化而提高鋼板的強度。Mn進一步降低Ar3變態點。Ar3變態點若降低,則由於可降低熱軋的精加工溫度(FT),而可將熱軋鋼板的肥粒鐵粒予以微細化。Mn含量若過低,則得不到此等的效果。另一方面,Mn含量若過高,則鋼板的韌性降低。因此,Mn含量為1.0~2.5%。Mn含量的較佳下限為1.2%,更佳為1.4%。Mn含量的較佳上限為2.3%,更佳為2.1%。
P:超過0.030~0.048%
磷(P)係藉由固溶強化而提高鋼板的強度。P含量若過低,則於本發明之化學組成中,確保440MPa的拉伸長強度者變困難。另一方面,P含量若過高,則P偏析至
粒界而粒界強度降低。此時,抗扁胚裂紋性及耐二次加工脆性降低,特別地如圖2中所示,抗扁胚裂紋性降低。因此,P含量為超過0.030%~0.048%。P含量的較佳下限為0.033%,更佳為0.035%。P含量的較佳上限為0.047%,更佳為0.045%。
S:0.025%以下
硫(S)係無可避免地含有。S係降低鋼的熱加工性及韌性。因此,S含量為0.025%以下。S含量的較佳上限為0.010%,更佳為0.005%。S含量較佳為儘量低。惟,考慮脫硫所需要的成本時,S含量的較佳下限為0.0005%。
Al:0.005~0.20%
鋁(Al)係將鋼脫氧。Al係進一步形成AlN而抑制結晶粒的粗大化。Al更與Si相同,為肥粒鐵安定化元素,可作為Si的代替物而含有。Al含量若過低,則得不到此等的效果。另一方面,Al含量若過高,則鋼的韌性降低。因此,Al含量為0.005~0.20%。Al含量的較佳下限為0.01%,更佳為0.02%。Al含量的較佳上限為0.10%,更佳為0.06%。
N:0.010%以下
氮(N)係無可避免地含有。N係形成氮化物(AlN)而抑制結晶粒的粗大化。然而,N含量若過高,則鋼的韌性降低。因此,N含量為0.010%以下。N含量的較佳上限為0.007%,更佳為0.005%。N係形成Al或Ti
的碳氮化物等而抑制結晶粒的粗大化。因此,N含量的較佳下限為0.001%。
Ti:0.005~0.040%、鈦(Ti)係形成微細的Ti碳氮化物,抑制結晶粒的粗大化。Ti係進一步形成TiN而減低固溶N,抑制BN之析出。藉此,固溶B所致的抗扁胚裂紋性及耐二次加工脆性係升高。Ti含量若過低,則得不到此等的效果。另一方面,Ti含量若過高,則Ti碳氮化物係粗大化而鋼的韌性降低。再者,生成TiP而平均r值降低。因此,Ti含量為0.005~0.040%。Ti含量的較佳下限為0.010%,更佳為0.015%。Ti含量的較佳上限為0.035%,更佳為0.030%。
C含量未達0.0040%時,Ti含量的較佳範圍為0.005~0.035%。C含量為0.0040~0.0080%時,Ti含量的較佳範圍為0.005~0.040%。
Nb:0.005~0.060%
鈮(Nb)係形成微細的Nb碳氮化物,抑制結晶粒的粗大化。Nb含量若過低,則得不到此效果。另一方面,Nb含量若過高,則因析出至粒界的NbC,而抗扁胚裂紋性及耐二次加工脆性降低。因此,Nb含量為0.005~0.060%。Nb含量的較佳下限為0.010%,更佳為0.015%。Nb含量的較佳上限為0.040%,更佳為0.035%。
C含量未達0.0040%時,Nb含量的較佳範圍為0.005~0.035%。C含量為0.0040~0.0080%時,Nb含量的較佳範圍為0.005~0.060%。
B:0.0005~0.0030%
硼(B)係固溶而偏析至粒界,抑制P及S偏析至粒界者。藉此,抗扁胚裂紋性及耐二次加工脆性升高。B含量若過低,則得不到此效果。另一方面,B含量若過高,則在粒界生成粗大的氮化物(BN),鋼的抗扁胚裂紋性及耐二次加工脆性降低。析出至粒界的粗大BN更降低鋼的熱加工性及韌性。因此,B含量為0.0005~0.0030%。B含量的較佳下限為0.0010%,更佳為0.0015%。B含量的較佳上限為0.0025%,更佳為0.0020%。
本發明之合金化熔融鍍鋅鋼板的母材鋼板之化學組成的剩餘部分係由Fe及雜質所構成。此處,所謂的雜質,就是指工業上製造上述母材鋼板時,自作為原料的礦石、廢料或製造環境等所混入者,在對於上述母材鋼板不造成不良影響的範圍內可容許者。
上述母材鋼板之化學組成係進一步滿足下式(1)~式(4)。
25×P+4×Si≦3.6 (1)
B-X1≧0.0005 (2)
C-(12/93)×Nb-X2≧-0.0035 (3)
110×Si+48×Mn+550×P≧120 (4)
此處,於式中的各元素符號中,代入對應的元素之含量(質量%)。
上述母材鋼板之化學組成係滿足式(1)。
25×P+4×Si≦3.6 (1)
定義F1=25×P+4×Si。F1係耐二次加工脆性之指標。如圖1中所示,F1若超過3.6,則脆性龜裂長度顯著地變長,耐二次加工脆性降低。F1若為3.6以下,則充分抑制脆性龜裂之發生,耐二次加工脆性升高。
上述母材鋼板之化學組成係進一步滿足式(2)。
B-X1≧0.0005 (2)
此處,式(2)中的X1係如以下定義。
N-(14/48)×Ti>0時,X1=(11/14)[N-(14/48)×Ti]。N-(14/48)×Ti≦0時,X1=0。
定義F2=B-X1。F2係固溶B量之指標,且為抗扁胚裂紋性及耐二次加工脆性之指標。X1比0更大時,理論上不藉由Ti而充分地固定N,意指與B能結合的N係存在。X1為0以下時,理論上藉由Ti而充分地固定N,意指與B能結合的N係不存在。
F2未達0.0005時,固溶B係無法充分地偏析至粒界。此時,由於P及S偏析至粒界,而扁胚裂紋或二次加工脆性容易發生。F2為0.0005以上時,固溶B係充分地偏析至粒界,抑制P及S的粒界偏析。因此,粒界強
度升高,得到具有優異的抗扁胚裂紋性及耐二次加工脆性。
上述母材鋼板之化學組成係進一步滿足式(3)。
C-(12/93)×Nb-X2≧-0.0035 (3)
此處,式(3)中的X2係如以下定義。
Ti-(48/14)×N>0時,X2=(12/48)[Ti-(48/14)×N]。Ti-(48/14)×N≦0時,X2=0。
定義F3=C-(12/93)×Nb-X2。F3係固溶C量之指標,且為抗扁胚裂紋性及耐二次加工脆性之指標。X2比0更大時,理論上Ti係比與N結合的量更多地存在,意指與C能結合的Ti係存在。X2為0以下時,理論上全部的Ti係結合至N,意指與C能結合的Ti係不存在。
F3比-0.0035更低時,由於固溶C量為不充分,粒界的強度不充分地升高。此時,抗扁胚裂紋性及耐二次加工脆性降低。F3為-0.0035以上時,提高粒界強度用的固溶C量係充分地存在。因此,抗扁胚裂紋性及耐二次加工脆性升高。F3的較佳下限為-0.0015,更佳為0.0002。F3較佳為0.0025,更佳為0.0018以下。此時,深拉性係進一步升高。
C含量為0.0040~0.0080%時,F3的較佳下限為-0.0002。
上述鋼板之化學組成係進一步滿足式(4)。
110×Si+48×Mn+550×P≧120 (4)
定義F4=110×Si+48×Mn+550×P。F4係C含量、Ti含量及Nb含量為上述之範圍內時,鋼板的拉伸強度之指標。F4未達120時,鋼板的拉伸強度未達440MPa,得不到高強度。F4若為120以上,則元素為上述範圍,且滿足上述式(1)~式(3)的化學組成之鋼板的拉伸強度係成為440MPa以上。F4較佳為130以上。
合金化熔融鍍鋅層係形成在上述母材鋼板之表面上。合金化熔融鍍鋅層含有7~15質量%的Fe。Fe含量未達7%時,點焊性降低。另一方面,Fe含量超過15%時,合金化熔融鍍鋅層之密著性降低。Fe含量若為7~15%,則點焊性及密著性優異。若實施後述條件的合金化處理,則合金化熔融鍍鋅層中的Fe含量成為上述範圍。合金化熔融鍍鋅層的Fe含量的較佳下限為8%,較佳的上限為12%。
合金化熔融鍍鋅層之化學組成含有上述的Fe與Al,剩餘部分係由Zn及雜質所構成。Al係含於上述的熔融鍍鋅浴中。於製造步驟中,實施後述的預鍍Ni處理時,合金化熔融鍍鋅層之化學組成亦可含有Ni。
合金化熔融鍍鋅層之鍍敷附著量係沒有特別
的限定。從耐蝕性之觀點來看,合金化熔融鍍鋅層的較佳鍍敷附著量以Zn的單面附著量計為5g/m2以上。從合金化熔融鍍鋅層的加工性及密著性之觀點來看,合金化熔融鍍鋅層之Zn單面附著量的較佳上限為100g/m2。
於本發明之合金化熔融鍍鋅鋼板中,以式(A)所定義的平均r值rm為1.2以上。
rm=(rL+2×r45+rC)/4 (A)
上述式(A)中之rL係在合金化熔融鍍鋅鋼板中,平行於軋製方向的方向之r值。r45係相對於軋製方向而言45°方向之值。rC係垂直於軋製方向的方向之r值。r值係稱為蘭克福特值,表示鋼板的塑性各向異性。
於本發明之合金化熔融鍍鋅鋼板中,進一步地以式(B)所定義的面內各向異性△r值為-0.5~0.5。
△r=(rL+rC)/2-r45 (B)
於以側框架外部等為代表的加工度高之汽車零件中,要求優異的深拉性。平均r值rm若為1.2以上,則得到優異的深拉性。
再者,於側框架外部中之容納門的部位之四角落部分,要求r45高。於門之鉸鏈安裝部分,要求rL高。面內各向異性△r值若為-0.5~0.5,則可滿足此等之要求,得到優異的深拉性。
於本發明之合金化熔融鍍鋅鋼板中,從塗裝性及熔接性之觀點來看,可將上層鍍層形成在上述的合金化熔融鍍鋅層上。又,對於本發明之合金化熔融鍍鋅鋼板,從塗裝性、耐蝕性、潤滑性、熔接性等的提高之觀點來看,亦可實施鉻酸鹽處理、磷酸鹽處理、其他的各種化成處理。
本發明的合金化熔融鍍鋅鋼板之製造方法的一例係如以下。
本製造方法包含熱軋步驟、冷軋步驟、退火步驟、熔融鍍鋅處理步驟與合金化處理步驟。以下,詳述各步驟。
於熱軋步驟中,首先以周知的方法製造具有上述的化學組成(滿足式(1)~式(4))之熔鋼。以周知的方法鑄造所製造的熔鋼,而製造扁胚。鑄造時之冷卻方法例如係周知的徐冷或空氣冷卻。
對於所製造的扁胚,實施熱軋而製造熱軋鋼板。捲取所製造的熱軋鋼板,而成為捲料。熱軋步驟中的精加工溫度FT及捲取溫度CT係如以下。
精加工溫度FT:800~950℃
於熱軋中,使用粗軋機來實施粗軋後,使用精軋機來
實施精軋。精軋機係具備排成一列的複數之機台。各機台包含一對的軋輥。
於熱軋中,將精軋機中之軋延鋼板的最終機台之出側的鋼板之表面溫度定義為精加工溫度FT(℃)。於本發明中,精加工溫度FT為800~950℃。
精加工溫度FT未達800℃時,成為沃斯田鐵與肥粒鐵的2相域輥軋,精加工溫度FT超過950℃時,熱軋鋼板的結晶粒變粗大。於此等之情況中,平均r值rm變低,面內各向異性△r變大。精加工溫度FT若為800~950℃,則熱軋鋼板的肥粒鐵粒變微細。結果,以滿足其他的條件(化學組成及製造條件)者作為條件,平均r值rm成為1.2以上,面內各向異性△r值成為-0.5~0.5。
再者,熱軋時的扁胚之加熱溫度,係以滿足上述精加工溫度FT者作為條件,較佳為儘量低。扁胚之加熱溫度若低,則可提高平均r值rm。
捲取溫度CT:600~760℃
捲取精軋後的熱軋鋼板,而成為捲料。將捲取開始時的熱軋鋼板之表面溫度定義為捲取溫度CT(℃)。於本發明中,捲取溫度CT為600~760℃。捲取溫度CT未達600℃時及捲取溫度CT超過760℃時,Ti碳氮化物及Nb碳氮化物的析出量不成為恰當量。此時,由於固溶C量過低,耐二次加工脆性會降低,或結晶粒不微細,平均r值rm會變低。
捲取溫度CT若為600~760℃,Ti碳氮化物
及Nb碳氮化物的析出量成為恰當量,有助於粒界強度的固溶C量亦成為恰當量。結果,耐二次加工脆性升高,平均r值rm亦變大。
對於所製造的熱軋鋼板,實施冷軋。冷軋步驟之軋縮率係未必要限定。冷軋步驟的軋縮率為75~83%。此時,平均r值rm變更高,且面內各向異性△r值變更低。惟,軋縮率係沒有特別限定於上述範圍之必要。使用周知的條件,能實施冷軋的話就夠了。
對於所製造的冷軋鋼板,實施退火處理,而製造母材鋼板。退火溫度為再結晶溫度以上,較佳為Ac1變態溫度以下。退火溫度若為再結晶溫度以上,則促進再結晶,母材鋼板的深拉加工性升高,耐二次加工脆性升高。
退火溫度若為上述之範圍,則沒有特別的限定,例如為750~850℃。退火溫度的較佳下限為800℃。此時,平均r值rm變更高。退火溫度的較佳上限為830℃。此時,於連續退火中,進一步抑制板擠紋之發生。所謂的「板擠紋」,就是指在往連續退火爐的通板時,鋼帶挫曲,在鋼帶中發生皺紋或裂紋之現象。
母材鋼板的Si含量為0.25%以上時,較佳為對於母材鋼板,實施利用在熔融鍍鋅線外所配置的退火設備之線外退火,然後對於母材鋼板,實施預鍍Ni處理,加熱預鍍Ni處理後的母材鋼板後,實施熔融鍍鋅處理。預鍍Ni處理之方法係未必要限定。預鍍Ni處理係可電鍍處理,也可浸漬鍍敷處理,於附著量控制的容易性之觀點中,較佳為使用電鍍處理。藉由預鍍Ni處理,於母材鋼板上形成Ni鍍層。實施鍍Ni處理時,不鍍係被顯著地抑制。Ni鍍層的較佳鍍敷附著量為0.2~2g/m2。此時,藉由預鍍Ni處理,相當於已析出至母材鋼板的表面之Ni的30~65%之量係包含於合金化處理後的鍍層中。作為Ni電鍍的鍍浴,例如可使用濕浴,但未必要受此所限定。
再者,於本製造方法中,亦可不實施預鍍Ni處理。此時,於退火步驟後,實施熔融鍍鋅處理步驟及合金化處理步驟。
藉由蘭吉馬法等之所謂的線內退火時,於保護氣氛下,將經退火的母材鋼板(鋼帶)冷卻到熔融鋅浴溫或其附近溫度,將母材鋼板浸入熔融鋅浴中。惟,當母材鋼板的Si含量為0.25%以上時,容易發生不鍍。因此,當為Si含量高的母材鋼板時,較佳為實施上述的線外退火。
線外退火時,較佳為對於母材鋼板,實施預鍍Ni處理步驟後,實施熔融鍍鋅處理。熔融鍍鋅處理只
要是以周知的條件實施就夠了。於熔融鍍鋅處理中,將經預鍍Ni處理的母材鋼板在保護氣氛下,例如以20℃/秒以上的加熱速度,較佳加熱到430~480℃為止。將經加熱的母材鋼板浸漬於熔融鍍鋅浴中,而使熔融鍍鋅層附著於母材鋼板表面。從熔融鍍鋅浴中提起熔融鍍鋅層已附著的母材鋼板。
藉由以周知的方法調整母材鋼板的提起速度或拂拭的氣體之流量,可調整鍍敷附著量。關於附著量控制,線內退火或線外退火係本質上無差異。
熔融鍍鋅浴中的Al濃度係沒有特別的限定,但較佳為0.05~0.25%。Al濃度高時抑制合金化,低時促進合金化。
鋼板浸入熔融鋅浴中的溫度較佳為450~475℃。浸入溫度低時,有發生不鍍之虞。浸入溫度過高時,浮渣的發生量增加。
對於形成有熔融鍍鋅層的母材鋼板,加熱到470~620℃的合金化處理溫度。於加熱後,在處理溫度保持10~40秒,而實施合金化處理。加熱速度例如為20℃/秒以上。
合金化處理溫度若未達470℃,則合金化容易變不充分,合金化熔融鍍鋅層中的Fe含量容易成為未達7%。另一方面,合金化處理溫度若超過620℃,則合金化
容易過剩地進行,合金化熔融鍍鋅層的密著性降低之虞係變大。在合金化處理溫度的保持時間若未達10秒,則合金化容易變不充分。保持時間若超過40秒,則合金化容易過剩地進行,合金化熔融鍍鋅層的密著性降低之虞係變大。
藉由以上之步驟,可製造合金化熔融鍍鋅鋼板。
將經線外退火的冷軋鋼板當作母材鋼板,於預鍍Ni處理後,進行熔融鍍鋅處理之情況,可在預鍍Ni處理步驟前,實施酸洗處理步驟。此時,可去除因退火處理而形成在母材鋼板之表面上的氧化被膜。
又,可於退火處理步驟後,在熔融鍍鋅處理前實施(實施預鍍Ni處理步驟之情況,在退火處理步驟後,於預鍍Ni處理步驟前),實施以形狀矯正及降伏點伸長的消失為目的之調質軋製步驟。實施調質輥軋步驟時,較佳的伸長率為0.1~2%。伸長率若為0.1%以上,則充分得到形狀矯正及降伏點伸長的消失。伸長率若為2%以下,則於合金化熔融鍍鋅鋼板中,能維持優異的伸長率(全伸長率)。
上述調質輥軋步驟亦可在合金化處理後實施。此時,在調質輥軋步驟的較佳伸長率為0.1~2%。
製造表1中所示的化學組成之熔鋼,將熔鋼鑄造而製造扁胚。
對於各鋼編號的扁胚,以表2中所示的精加工溫度FT(℃)及捲取溫度CT(℃)來製造熱軋鋼板。對於熱軋鋼板,以80%的輥軋率實施冷軋,而製造冷軋鋼板。對於冷軋鋼板,以表2中所示的退火溫度(℃)來實施退火處理,而製造母材鋼板。對於試驗編號49及50以外的其他試驗編號之母材鋼板,於退火後,進行酸洗處理後,實施預鍍Ni處理,而在母材鋼板之表面上形成鍍敷附著量0.5g/m2之Ni鍍層。對於預鍍Ni處理後的母材鋼板,實施熔融鍍鋅處理(將每一面的Zn附著量設定在45g/m2,Zn浴中的Al濃度為0.14~0.17%,浴溫455~460℃)。具體而言,以20℃/秒的加熱速度將母材鋼板加熱到460℃為止後,於鍍鋅浴中浸漬母材鋼板而實施熔融鍍鋅處理。
對於試驗編號49及50的母材鋼板,不實施預鍍Ni處理,而以能線內退火的熔融鍍鋅設備,於與上述相同之條件下實施熔融鍍鋅處理。
對於熔融鍍鋅處理後的母材鋼板,以表2中所示的合金化處理溫度(℃)及保持時間(秒)來實施合金化處理。對於合金化處理後的鋼板,實施1.0%的伸長率之調質輥軋,製造具有0.7mm的板厚之合金化熔融鍍鋅鋼板。
[表2]
自各鋼編號的扁胚(鑄片),採集JIS Z 2242(2005)中規定的V缺口標準試驗片。使用此試驗片,依據JIS Z 2242(2005),實施夏皮(Charpy)衝撃試驗,測定延性脆性斷面轉變溫度vTrs(℃)。延性脆性斷面轉變溫度vTrs(℃)若為-20℃以下,則評價為抗扁胚裂紋性優異。
自各試驗編號的合金化熔融鍍鋅鋼板之板厚中央部,採集拉伸試驗片。使用所採集的試驗片,於常溫(25℃)的大氣中實施依據JIS Z 2241(2011)的拉伸試驗,求得降伏強度YP(0.2%耐力)及拉伸強度ST(MPa)。
自各試驗編號的合金化熔融鍍鋅鋼板之板厚中央部,採集拉伸試驗片。使用所採集的試驗片,實施依據JIS Z 2254(2008)的塑性應變比試驗,求得rL值、r45值、rC值。使用所得之rL值、r45值、rC值,根據式(A),求得平均r值。再者,使用所得之rL值、r45值、rC值,根據式(B),求得面內各向異性△r值。平均r值為1.2以上而且面內各向異性△r值為-0.5~0.5時,評價為深拉性優異。
目視判斷於各試驗編號的合金化熔融鍍鋅鋼板之表面上是否發生不鍍。
自各試驗編號的合金化熔融鍍鋅鋼板,採集包含合金化熔融鍍鋅層的樣品。以加有Inhibitor(朝日化學工業股份有限公司製700BK,0.3%)的10%鹽酸,溶解去除GA的鍍層,自其前後的重量差來算出鍍敷附著量。再者,自已溶解的液,以感應耦合電漿發光分光(1CP-AES)分析,測定Zn、Fe、Al、Ni量,算出Zn附著量及鍍敷皮膜中的Fe含量(合金化度)。Fe含量若為7~15%,則判斷已得到優異的合金化熔融鍍鋅層。
對於各試驗編號的合金化熔融鍍鋅鋼板,實施25mm杯深拉試驗。試驗後,測定膠帶試驗所致的黑化度。黑化度愈低,鍍敷密著性愈高。於本實施例中,黑化度未達30%時,判斷鍍敷密著性優異(表3中記載為「E」(優良))。黑化度為30%以上時,判斷密著性低(表3中記載為「NA」(不被接受))。
自各試驗編號的合金化熔融鍍鋅鋼板來製作直徑45mm的坯料。對於坯料,使用衝頭直徑為20.64mm的球頭衝頭,實施深拉成形(深拉比為2.2)。然後,於-40℃的乙醇中,以側面成為水平的方式浸漬,藉由加壓機進行加壓而擠壓坯料。在加壓後的坯料上,藉由目視判斷有無脆性龜裂。
表3中顯示評價結果。
[表3]
參照表3,試驗編號1、3、5、6、8、9、27、28、31、32、49~53之化學組成為恰當,製造條件亦恰當。因此,於此等試驗編號的合金化熔融鍍鋅鋼板
中,拉伸強度TS為440MPa以上,平均r值rm為1.2以上,面內各向異性△r為-0.5~0.5之範圍內。再者,合金化熔融鍍鋅層中的Fe含量為7~15%之範圍內。即,得到高強度且深拉性優異之合金化熔融鍍鋅鋼板。還有,於此等試驗編號中,延性脆性斷面轉變溫度vTrs(℃)為-20℃以下,得到優異的抗扁胚裂紋性。再者,於耐二次加工脆性評價試驗中,看不到脆性龜裂,得到優異的耐二次加工脆性。
再者,於此等試驗編號中,全伸長率為30%以上。又,皆不發生不鍍。還有,於鍍敷密著性試驗中,於任一試驗編號中皆黑化度未達30%,鍍敷密著性優異。
另一方面,於試驗編號2、4、7、29、30中,P含量過高。因此,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。
於試驗編號10中,P含量過高,F1不滿足式(1),F3不滿足式(3)。因此,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號11中,Si含量過高。再者,F1不滿足式(1)。因此,發生不鍍。再者,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。還有,於耐二次加工脆性評價
試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號12中,B含量過低。因此,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號13中,F4不滿足式(4)。因此,拉伸強度TS未達440MPa。
於試驗編號14及36中,P含量過低。因此,拉伸強度TS未達440MPa。
於試驗編號15及37中,P含量過高。因此,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。
於試驗編號16及38中,F1不滿足式(1)。因此,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號17及39中,F2不滿足式(2)。因此,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號18及40中,F3不滿足式(3)。因此,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆
性低。
於試驗編號19及41中,F4不滿足式(4)。因此,拉伸長強度TS未達440MPa。
於試驗編號20及42中,精加工溫度FT過高。因此,平均r值rm未達1.2,面內各向異性△r未達-0.5,深拉性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號21及43中,精加工溫度FT過低,結果亦捲取溫度CT亦過低。因此,平均r值rm未達1.2,面內各向異性△r未達-0.5,深拉性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號22及44中,捲取溫度CT過低。因此,平均r值rm未達1.2,面內各向異性△r未達-0.5,深拉性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號23及45中,合金化處理溫度過高。因此,合金化熔融鍍鋅層中的Fe含量超過15%。結果,於鍍敷密著性評價試驗中,黑化度成為30%以上,鍍敷密著性低。
於試驗編號24及46中,合金化處理溫度過低。因此,合金化熔融鍍鋅層中的Fe含量未達7%。
於試驗編號25及47中,在合金化處理溫度的保持時間過長。因此,合金化熔融鍍鋅層中的Fe含量
超過15%。結果,於鍍敷密著性評價試驗中,黑化度成為30%以上,鍍敷密著性低。
於試驗編號26及48中,在合金化處理溫度的保持時間過短。因此,合金化熔融鍍鋅層中的Fe含量未達7%。
於試驗編號33中,P含量過高。再者,F1不滿足式(1)。因此,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。
於試驗編號34中,Si含量及P含量過高。因此,於抗扁胚裂紋性評價試驗中,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。再者,於耐二次加工脆性評價試驗中,發生脆性龜裂,耐二次加工脆性低。還有,發生不鍍。
於試驗編號35中,C含量過高。因此,平均r值過低。再者,延性脆性斷面轉變溫度vTrs(℃)超過-20℃,抗扁胚裂紋性低。
以上,說明本發明之實施形態。然而,上述實施形態只不過是實施本發明用的例示而已。因此,本發明係不受上述實施形態所限定,在不脫離其宗旨之範圍內,可適宜變更上述實施形態而實施。
Claims (5)
- 一種合金化熔融鍍鋅鋼板,其具備:以質量%表示,含有:C:0.0080%以下、Si:0.7%以下、Mn:1.0~2.5%、P:超過0.030~0.048%、S:0.025%以下、Al:0.005~0.20%、N:0.010%以下、Ti:0.005~0.040%、Nb:0.005~0.060%、及B:0.0005~0.0030%,剩餘部分由Fe及雜質所構成,具有滿足式(1)~式(4)的化學組成之母材鋼板,與形成在前述母材鋼板之表面上,含有7~15質量%的Fe之合金化熔融鍍鋅層;且平均r值為1.2以上,面內各向異性△r值為-0.5~0.5,拉伸長強度為440MPa以上;25×P+4×Si≦3.6 (1) B-X1≧0.0005 (2) C-(12/93)×Nb-X2≧-0.0035 (3) 110×Si+48×Mn+550×P≧120 (4) 此處,於式中的各元素符號中,代入對應的元素之含量(質量%);再者,式(2)中的X1係如以下定義;N-(14/48)×Ti>0時,X1=(11/14)[N-(14/48)×Ti],N-(14/48)×Ti≦0時,X1=0;還有,(3)中的X2係如以下定義;Ti-(48/14)×N>0時,X2=(12/48)[Ti-(48/14)×N],Ti-(48/14)×N≦0時,X2=0。
- 如請求項1之合金化熔融鍍鋅鋼板,其中前述化學組成含有:C:未達0.0040%、Ti:0.005~0.035%、及Nb:0.005~0.035%。
- 如請求項1之合金化熔融鍍鋅鋼板,其中前述化學組成含有:C:0.0040~0.0080%、Ti:0.005~0.040%、及Nb:0.005~0.060%,且式(3)之下限值為-0.0002。
- 一種合金化熔融鍍鋅鋼板之製造方法,其具備: 對具有如請求項1~3之化學組成的扁胚,以800~950℃的精軋溫度實施熱軋而製造熱軋鋼板,以600~760℃的捲取溫度捲取前述熱軋鋼板之步驟,對於前述熱軋鋼板,實施冷軋而製造冷軋鋼板之步驟,對於前述冷軋鋼板,實施退火處理而製造母材鋼板之步驟,對於前述母材鋼板,實施熔融鍍鋅處理之步驟,與對於經前述熔融鍍鋅處理的前述母材鋼板,實施以470~620℃的合金化處理溫度保持10~40秒的合金化處理之步驟。
- 如請求項4之合金化熔融鍍鋅鋼板之製造方法,其進一步具備:於前述製造母材鋼板之步驟後,在前述實施熔融鍍鋅處理之步驟前,對前述母材鋼板實施預鍍Ni處理之步驟,與於前述實施預鍍Ni處理之步驟後,在前述實施熔融鍍鋅處理之步驟前,加熱經前述預鍍Ni的前述母材鋼板之步驟。
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EP3342893A1 (en) | 2018-07-04 |
JPWO2017033901A1 (ja) | 2018-06-07 |
US20180258514A1 (en) | 2018-09-13 |
TWI609976B (zh) | 2018-01-01 |
MX2018002264A (es) | 2018-03-23 |
WO2017033901A1 (ja) | 2017-03-02 |
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