TW201623654A - 罐用鋼板以及罐用鋼板之製造方法 - Google Patents
罐用鋼板以及罐用鋼板之製造方法 Download PDFInfo
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- TW201623654A TW201623654A TW104134539A TW104134539A TW201623654A TW 201623654 A TW201623654 A TW 201623654A TW 104134539 A TW104134539 A TW 104134539A TW 104134539 A TW104134539 A TW 104134539A TW 201623654 A TW201623654 A TW 201623654A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 98
- 239000010959 steel Substances 0.000 title claims abstract description 98
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 238000000034 method Methods 0.000 title description 20
- 239000000203 mixture Substances 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 102
- 229910052742 iron Inorganic materials 0.000 claims description 48
- 238000000137 annealing Methods 0.000 claims description 33
- 238000005097 cold rolling Methods 0.000 claims description 25
- 238000005096 rolling process Methods 0.000 claims description 20
- 238000001816 cooling Methods 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 claims description 8
- 238000005098 hot rolling Methods 0.000 claims description 8
- 238000005554 pickling Methods 0.000 claims description 5
- 238000000746 purification Methods 0.000 claims description 5
- 239000002994 raw material Substances 0.000 claims 1
- 229910000859 α-Fe Inorganic materials 0.000 abstract description 12
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 229910000734 martensite Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 14
- 230000015572 biosynthetic process Effects 0.000 description 10
- 238000007747 plating Methods 0.000 description 10
- 239000011651 chromium Substances 0.000 description 9
- 239000006104 solid solution Substances 0.000 description 9
- 238000012545 processing Methods 0.000 description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 6
- OKKJLVBELUTLKV-UHFFFAOYSA-N Methanol Chemical compound OC OKKJLVBELUTLKV-UHFFFAOYSA-N 0.000 description 6
- 229910052718 tin Inorganic materials 0.000 description 6
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 5
- 238000005259 measurement Methods 0.000 description 5
- 238000001953 recrystallisation Methods 0.000 description 5
- 239000000243 solution Substances 0.000 description 5
- 235000013361 beverage Nutrition 0.000 description 4
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- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- 239000011347 resin Substances 0.000 description 3
- 229920005989 resin Polymers 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 101100432802 Drosophila melanogaster Ypel gene Proteins 0.000 description 2
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 2
- 238000009924 canning Methods 0.000 description 2
- 238000005530 etching Methods 0.000 description 2
- 238000000605 extraction Methods 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 229910017604 nitric acid Inorganic materials 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000004080 punching Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- QAOWNCQODCNURD-UHFFFAOYSA-N sulfuric acid Substances OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 238000004381 surface treatment Methods 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000006243 chemical reaction 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
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000012611 container material Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 239000007888 film coating Substances 0.000 description 1
- 238000009501 film coating Methods 0.000 description 1
- ZZUFCTLCJUWOSV-UHFFFAOYSA-N furosemide Chemical compound C1=C(Cl)C(S(=O)(=O)N)=CC(C(O)=O)=C1NCC1=CC=CO1 ZZUFCTLCJUWOSV-UHFFFAOYSA-N 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 230000037303 wrinkles Effects 0.000 description 1
Classifications
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C21D1/26—Methods of annealing
- C21D1/28—Normalising
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- C—CHEMISTRY; METALLURGY
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- B65D85/00—Containers, packaging elements or packages, specially adapted for particular articles or materials
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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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- C21D2211/005—Ferrite
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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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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- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
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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
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/54—Furnaces for treating strips or wire
- C21D9/56—Continuous furnaces for strip or wire
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Abstract
本發明是提供:具有高強度及優異的成形性之罐用鋼板以及罐用鋼板的製造方法。
本發明的罐用鋼板,其組成分以質量%計,係含有C:0.015%以上0.150%以下、Si:0.04%以下、Mn:1.0%以上2.0%以下、P:0.025%以下、S:0.015%以下、Al:0.01%以上0.10%以下、N:0.0005%以上且未達0.0050%、Ti:0.003%以上0.015%以下、B:0.0010%以上0.0040%以下,其餘部分是Fe以及不可避免的雜質,並且其鋼板組織,係以肥粒鐵相作為主相,第2相則是由麻田散鐵相與殘留沃斯田鐵相所組成的至少其中一方,該第2相以面積百分率計,合計係含有1.0%以上,拉伸強度為480MPa以上,總伸長率為12%以上,降伏伸長率為2.0%以下。
Description
本發明係關於:適合主要是被用在食品罐和飲料罐的罐容器材料之罐用鋼板及其製造方法。
近年來,基於減輕環境負荷以及削減成本的觀點考量,乃要求削減食品罐和飲料罐所用的鋼板的使用量,無論是兩片式罐、三片式罐都在進行鋼板的薄型化。
此外,為了彌補薄型化後的罐體強度,在罐身部進行凸波紋加工或者將罐身部製作成幾何形狀的異形罐的情況變多。兩片式罐的異形罐,是利用衝拉加工或引縮加工,先實施過加工度較高的成形之後,又對於罐身部進行加工,因此是對於鋼板要求較高的成形性。
另一方面,加工度較低的罐底部,因加工硬化所導致的強度上昇很小,因此將其薄型化的情況下,鋼板的高強度化是必要的。尤其是在罐底部的形狀為平坦的情況下,也就是在加工度極小的情況下,更為高強度化是必要的。
此外,在進行製罐加工中,發生拉伸變形紋
(皺紋)的話,將導致外觀不良,所以鋼板的降伏伸長率必須是夠小。
一般而言,鋼板是隨著高強度化而使成形性變差。針對於這種課題,為了要實現既有高強度又兼具有良好的成形性之鋼板,乃就將硬質的第2相加以活用的鋼板進行檢討。
專利文獻1所揭示的製罐用高強度且加工性良好的冷軋鋼板,其組成分係含有C:0.15wt%以下、Si:0.10wt%以下、Mn:3.00wt%以下、Al:0.150wt%以下、P:0.100wt%以下、S:0.010wt%以下以及N:0.0100wt%以下,其餘部分是鐵以及不可避免的雜質,鋼板組織是具有:肥粒鐵與麻田散鐵或變韌鐵的混合組織,其拉伸強度(TS)為40kgf/mm2以上,伸長率(El)為15%以上,烘烤硬化量(BH)為5kgf/mm2以上。
專利文獻2所揭示的製罐用高強度薄鋼板,是製品板厚t為0.1~0.5mm的製罐用高強度薄鋼板,其特徵為:其鋼的組成分以質量%計,係含有C:0.04~0.13、Si:超過0.01~0.03、Mn:0.1~0.6、P:0.02以下、S:0.02以下、Al:0.01~0.2、N:0.001~0.02,其餘部分是Fe以及不可避免的雜質,其鋼板組織是由:以肥粒鐵相為主體的肥粒鐵相與麻田散鐵相的複合組織,麻田散鐵相的百分率為5%以上且未達30%,麻田散鐵粒徑d(μm)與製品板厚t(mm)係符合下列數式(A),且30T硬度為60以上,
1.0<(1-EXP(-t*3.0))*4/d‧‧‧‧數式(A)
專利文獻1:日本特開平4-337049號公報
專利文獻2:日本特開2009-84687號公報
然而,前述習知技術係可舉出下列的問題。
專利文獻1所記載的發明,是利用兩次冷軋、兩次退火來製造鋼板,因此能源成本將會上昇。此外,也很難穩定地抑制拉伸變形紋的發生,也就是,很難獲得低的降伏伸長率。
專利文獻2所記載的發明,在退火工序中,需要進行急速冷卻,所以鋼板內的溫度不一致的現象很容易變大,難以獲得穩定且良好的成形性。此外,因為Mn含量很低只有0.1~0.6%而已,所以無法充分地減少降伏伸長率,這是其技術課題。
本發明係有鑑於這種情事而開發完成的,是以提供:具有高強度以及優異的成形性之罐用鋼板以及罐用鋼板的製造方法,當作本發明所欲解決的技術課題。尤其是以提供:可適用於兩片式異形罐的成形的罐用鋼板以
及罐用鋼板的製造方法,當作本發明所欲解決的技術課題。
本發明人等,為了解決上述課題而不斷努力地進行研究。具體而言,是為了達到兼具:罐底部所被要求的高強度、以及罐身部所被要求的優異的成形性,而不斷努力地進行研究。其結果終於找到了一種創見,就是:將組成分、鋼板組織、拉伸強度(以下,也稱TS)、總伸長率、降伏伸長率(以下,也稱YP-EL)予以調整在特定的範圍內的話即可解決上述課題,並且依據這種創見,本發明人等終於完成了本發明。此外,本發明人等也特別針對於製造條件努力地進行研究,因而找到了一種創見,就是將退火條件以及2次冷軋條件控制在特定的範圍內的作法,就控制金屬組織的觀點而言,是較佳的作法。本發明的要旨係如下所述。
〔1〕一種罐用鋼板,其組成分以質量%計,係含有C:0.015%以上0.150%以下、Si:0.04%以下、Mn:1.0%以上2.0%以下、P:0.025%以下、S:0.015%以下、Al:0.01%以上0.10%以下、N:0.0005%以上且未達0.0050%、Ti:0.003%以上0.015%以下、B:0.0010%以上0.0040%以下,其餘部分是Fe以及不可避免的雜質;其鋼板組織,係以肥粒鐵相作為主相,第2相則是由麻田散鐵相與殘留沃斯田鐵相所組成的至少其中一方,該
第2相以面積百分率計,合計是含有1.0%以上;拉伸強度為480MPa以上;總伸長率為12%以上;並且降伏伸長率為2.0%以下。
〔2〕如前述〔1〕所記載的罐用鋼板,其中除了前述組成分之外,又含有Cr:0.03%以上0.30%以下、Mo:0.01%以上0.10%以下的一種以上。
〔3〕一種罐用鋼板的製造方法,係將具有前述〔1〕或〔2〕所記載的組成分的胚料,以加熱溫度為1130℃以上的條件來進行加熱,以精製溫度為820℃以上930℃以下的條件來進行熱軋之後,以捲取溫度為640℃以下的條件來進行捲取,進行酸洗之後,以85%以上的軋縮率進行一次冷軋,以退火溫度為720℃以上780℃以下的條件來進行連續退火,然後以1.0%以上10%以下的軋縮率進行二次冷軋。
〔4〕如前述〔3〕所記載的罐用鋼板的製造方法,係在前述連續退火之後,以2℃/秒以上且未達70℃/秒的冷卻速度,從前述退火溫度進行冷卻直到400℃,然後,進行前述的二次冷軋。
本發明的罐用鋼板係具有高強度以及優異的成形性。
此外,使用本發明的罐用鋼板的話,係可容易進行製造兩片式異形罐。
根據本發明,可使得食品罐和飲料罐等所使用的鋼板更薄型化,而可達成省資源化以及低成本化,具有產業上可利用性的效果。
以下將詳細說明本發明。但本發明並不限定在以下的實施方式。
本發明的罐用鋼板,其組成分以質量%計,係含有C:0.015%以上0.150%以下、Si:0.04%以下、Mn:1.0%以上2.0%以下、P:0.025%以下、S:0.015%以下、Al:0.01%以上0.10%以下、N:0.0005%以上且未達0.0050%、Ti:0.003%以上0.015%以下、B:0.0010%以上0.0040%以下,其餘部分是Fe以及不可避免的雜質;其鋼板組織,係以肥粒鐵相作為主相,第2相則是由麻田散鐵相與殘留沃斯田鐵相所組成的至少其中一方,該第2相以面積百分率計,合計是含有1.0%以上;拉伸強度為480MPa以上;總伸長率為12%以上;並且降伏伸長率為2.0%以下。
此外,適合用來製造罐用鋼板之本發明的製造方法,係將具有上述組成分的胚料,以加熱溫度為1130℃以上的條件來進行加熱,以精製溫度為820℃以上930℃以下的條件來進行熱軋之後,以捲取溫度為640℃以下的條件來進行捲取,進行酸洗之後,以85%以上的軋縮率進行一次冷軋,以退火溫度為720℃以上780℃以下的條件來進
行連續退火,然後以1.0%以上10%以下的軋縮率進行二次冷軋之罐用鋼板的製造方法。
以下,將依序地說明本發明的罐用鋼板的組成分、鋼板組織、鋼板特性、製造方法。首先係就本發明的罐用鋼板的組成分進行說明。在組成分的說明中,各成分的含量是質量%。
C:0.015%以上0.150%以下
C是形成鋼板組織中的第2相以及提昇拉伸強度的重要元素,藉由將含量設定為0.015%以上,可使得第2相達到1.0%以上,可使拉伸強度達到480MPa以上。此外,藉由生成第2相,可使YP-EL降低成2.0%以下。C含量愈多第2相就愈增加,對於高強度化有助益,因此C含量是0.030%以上為佳。另一方面,C含量若超過0.150%的話,總伸長率將會變差成未達12%,並且降伏伸長率變大,成形性變差。因此,C含量的上限必須設定在0.150%。基於成形性的觀點考量,將C含量設定在0.080%以下為宜,設定在0.060%以下更好。
Si:0.04%以下
Si添加多量的話,將會因為表面濃化而導致表面處理性惡化,耐腐蝕性變差,因此必須將Si含量設定在0.04%以下。Si含量較好是設定在0.03%以下。
Mn:1.0%以上2.0%以下
Mn是用來生成第2相,達成高強度化的重要元素。此外,也具有藉由減少在退火過程中的固溶C而使降伏伸
長率降低的效果。想要獲得這種效果,必須將Mn含量設定在1.0%以上。基於想要穩定地生成第2相的觀點考量,係將Mn含量設定在1.5%以上為宜。更好是設定在1.6%以上。但是Mn含量若超過2.0%的話,中央偏析將會變得明顯,總伸長率會變差,因此係將Mn含量設定在2.0%以下。
P:0.025%以下
P添加多量的話,將導致過剩的硬質化和因為中央偏析而使得成形性變差,此外,耐腐蝕性也會變差。因此,係將P含量的上限設定在0.025%。P含量較好是在0.020%以下。P係可提昇淬火硬化性,對於第2相的生成有助益,因此將P含量設定在0.010%以上為宜。
S:0.015%以下
S是會在鋼中形成硫化物而導致熱軋性變差。因此,將S含量設定在0.015%以下。S含量較佳是設定在0.012%以下。
Al:0.01%以上0.10%以下
Al係適合作為脫氧元素,因此必須含有0.01%以上。過剩含有的話,將會產生多量的氧化鋁殘留在鋼板內而導致成形性變差,因此必須將Al含量設定在0.10%以下。Al含量較佳為0.08%以下。
N:0.0005%以上且未達0.0050%
N若是作為固溶N存在的話,降伏伸長率會增加而使成形性變差,因此必須將N含量設定成未達0.0050%。N
含量較佳為0.0040%以下,更優是0.0030%以下。最好是除了上述N總含量之外,也規定固溶N含量,將該固溶N含量規定為未達0.001%。固溶N含量的測定方法,是可藉由:從N總含量減去:以10%Br甲醇溶液進行萃取分析所測得的NaS氮化物含量而獲得。另一方面,想要使N總含量穩定地未達0.0005%,是很困難,製造成本也會上昇,因此將N含量的下限設定在0.0005%。
Ti:0.003%以上0.015%以下
Ti係可將N予以固定成TiN,而具有可降低YP-EL的效果。此外,藉由優先的生成TiN的話,即可抑制BN的生成,以確保固溶B,因此具有對於第2相的生成有助益的效果,所以Ti含量必須為0.003%以上。Ti含量較好為0.005%以上。Ti含量若超過0.015%的話,將生成TiC而將C固定下來,第2相的面積百分率變少,肥粒鐵相的再結晶溫度將會上昇而導致在退火過程中無法充分進行再結晶,導致總伸長率變差。因此,必須將Ti含量設定在0.015%以下。
B:0.0010%以上0.0040%以下
B係與N形成BN而使固溶N減少,而具有減少降伏伸長率的效果,除此之外,也會當作固溶B存在而提昇淬火硬化性,對於第2相的形成有助益,因此必須將B含量設定在0.0010%以上。B過剩含有的話,不僅是上述的效果趨於飽和,就連總伸長率也會變差,異方性也會惡化而導致成形性變差,因此必須將B含量的上限設定在
0.0040%。
本發明的罐用鋼板,除了上述的成分之外,又含有Cr:0.03%以上0.30%以下、Mo:0.01%以上0.10%以下之中的一種以上為佳。
Cr:0.03%以上0.30%以下
Cr係可提昇淬火硬化性而對於第2相的生成有助益,具有高強度化和降低YPEL的效果。因此,將Cr含量設定在0.03%以上為宜。Cr含量若超過0.30%的話,不僅是效果趨於飽和,耐腐蝕性也會變差,因此係將Cr含量設定在0.30%以下為宜。
Mo:0.01%以上0.10%以下
Mo是可藉由提昇淬火硬化性而對於第2相的生成有助益,具有高強度化和降低YPEL的效果。因此,將Mo含量設定在0.01%以上為宜。Mo含量若超過0.10%的話,不僅是效果趨於飽和,有時候,肥粒鐵相的再結晶溫度將會上昇,退火時的再結晶受到阻礙,總伸長率變差,因此係將Mo含量設定在0.10%以下為宜。
罐用鋼板的組成分的其餘部分是Fe以及不可避免的雜質。
其次,說明本發明的罐用鋼板的鋼板組織。
本發明的罐用鋼板,係以肥粒鐵相作為主相。基於成形性的觀點考量,肥粒鐵相的面積百分率係80%以上為
宜,90%以上更好,95%以上更優。
第2相則是由麻田散鐵相與殘留沃斯田鐵相所形成的至少其中一方,以面積百分率計,合計是佔1.0%以上
本發明的罐用鋼板,係以肥粒鐵相作為主相,並且係以由麻田散鐵相與殘留沃斯田鐵相所組成的至少其中一方作為第2相。本發明的罐用鋼板,第2相以面積百分率計,係含有1.0%以上。藉由將第2相設定為1.0%以上,可以達成拉伸強度為480MPa以上的高強度化以及降伏伸長率為2.0%以下的低降伏伸長率化。第2相的較佳含量,以面積百分率計係含有2.0%以上。雖然第2相的上限並未特別限定,但是第2相過多的話,成形性會有變差的虞慮,因此將第2相的面積百分率設定在20%以下為宜,設定在10%以下更好。
本發明的罐用鋼板,也可以是:鋼板組織係由肥粒鐵相、麻田散鐵相、以及殘留沃斯田鐵相所組成的鋼板。另一方面,雖然亦可含有不是肥粒鐵相、麻田散鐵相、以及殘留沃斯田鐵相的例如:雪明鐵、變韌鐵相之類的其他種類的相,但是其他種類的相的面積百分率必須少於第2相。例如:其他種類的相的面積百分率,合計是未達1.0%為宜。
本發明,為了可以觀察到鋼板中之與輥軋方向平行的垂直斷面,乃將樣本裁切出來之後,埋入樹脂內進行研磨後,利用硝酸腐蝕液進行腐蝕而使鋼板組織浮現
出來,然後,利用掃描型電子顯微鏡對於鋼板組織進行拍攝,利用圖像處理來測定肥粒鐵相以及第2相(麻田散鐵相以及殘留沃斯田鐵相的合計)等的鋼板組織的面積百分率。
其次,說明本發明的罐用鋼板的鋼板特性。
拉伸強度:480MPa以上、總伸長率:12%以上、降伏伸長率:2.0%以下
為了確保罐底部的充分的強度,必須將鋼板的拉伸強度設定在480MPa以上。拉伸強度更好是490MPa以上。除了進行衝拉暨引縮加工之外,為了確保凸波紋之類的罐身加工性,總伸長率必須設定在12%以上。總伸長率較好是15%以上。為了防止製罐時的拉伸變形紋,必須將降伏伸長率設定在2.0%以下。降伏伸長率更好是1.0%以下。
本發明中,拉伸強度、總伸長率、以及降伏伸長率的評量方法,係從輥軋方向採取出日本工業規格JIS 5號拉伸試驗片,根據日本工業規格JIS Z 2241所規定的方法來進行評量。
雖然本發明的罐用鋼板的板厚並未特別限定,但是以0.40mm以下為宜。本發明的罐用鋼板係可達到極薄的縮減厚度,因此基於省資源化以及低成本化的觀點考量,將板厚設定在0.10~0.20mm更好。
其次,說明本發明的罐用鋼板的製造方法。本發明的罐用鋼板的製造方法雖然並未特別限定,但是以
採用以下所述的條件來進行製造罐用鋼板為宜。此外,亦可根據必要,又適當地實施:鍍Sn、鍍Ni、鍍Cr等的鍍膜工序、化成處理工序、包膜等的樹脂膜披覆工序之類的工序。
加熱溫度:1130℃以上
熱軋前之胚料的加熱溫度太低的話,TiN的一部分無法熔解,將會有因產生粗大的TiN而導致成形性變差之虞慮,因此係將加熱溫度設定在1130℃以上。加熱溫度較好是1150℃以上。上限雖然並未特別規定,但是胚料的加熱溫度太高的話,則會有因產生過多的鏽皮而導致製品表面缺陷之虞慮,因此係將上限設定在1260℃為宜。
熱軋的精製溫度:820℃以上930℃以下
熱軋的精製溫度較之930℃更高的話,將促進鏽皮的生成而會有導致表面性狀惡化之虞慮。因此,將精製溫度的上限設定在930℃。熱軋的精製溫度未達820℃的話,拉伸特性的異方性會變大,成形性會有變差之虞慮,因此將精製溫度的下限設定在820℃。精製溫度的較佳下限是860℃。
捲取溫度:640℃以下
捲取溫度超過640℃的話,會在熱軋鋼板中形成粗大的碳化物,在進行退火時,該粗大的碳化物將會未固溶,而阻礙第2相的生成,會有導致拉伸強度降低、增加YP-EL之虞慮。因此,係將捲取溫度設定在640℃以下。基於要讓碳化物細微地分散在鋼板中的觀點考量,係將捲取溫
度設定在600℃以下為宜,設定在550℃以下更好。捲取溫度的下限雖然並未特別規定,但是如果太低的話,熱軋鋼板會過度地硬化而會有阻礙冷軋的作業性之虞慮,因此,係將捲取溫度設定在400℃以上為宜。
酸洗條件,則是只要能夠將鋼板的表層鏽皮除去的話即可,並未特別地規定其條件。可利用一般常用方法來進行酸洗。
一次冷軋的軋縮率:85%以上
藉由實施冷軋將轉位導入進去,在進行退火過程中促進沃斯田鐵變態,可獲得促進第2相的生成之效果。為了獲得這種效果,係將一次冷軋的軋縮率設定在85%以上。此外,藉由將一次冷軋的軋縮率設定成較大的作法,肥粒鐵相將會細粒化,第2相也變細微,因此可以提昇:拉伸強度與加工性之兩者的均衡性。如果一次冷軋的軋縮率太大的話,拉伸特性的異方性會變大,會有成形性變差之虞慮。因此,係將一次冷軋的軋縮率設定在93%以下為宜。
退火溫度:720℃以上780℃以下
為了要獲得高拉伸強度與高總伸長率、低YP-EL,在退火過程中生成第2相的作法是很重要的。想要使第2相生成,在肥粒鐵+沃斯田鐵的雙相域中,將沃斯田鐵相予以穩定化的作法是很重要的,藉由在720℃以上780℃以下的條件下對於鋼板進行退火,可使第2相生成。為了確
保成形性,必須在退火過程中,使肥粒鐵相充分地再結晶,因此將退火溫度設定在720℃以上。另一方面,退火溫度太高的話,肥粒鐵粒徑將會變粗大化,因此設定在780℃以下。退火方法,基於材質的均一性之觀點考量,係採用連續退火法為宜。退火時間雖然並未特別限定,但是以10秒以上60秒以下為宜。
退火溫度起迄400℃的冷卻速度:2℃/秒以上且未達70℃/秒
為了穩定地生成第2相,係調整退火後的冷卻速度為宜,藉由設定為2℃/秒以上的作法,可使其容易生成面積百分率為1.0%以上的第2相。太快的冷卻速度的話,將導致鋼板內的冷卻不一致而無法穩定地獲得高總伸長率,而且鋼帶捲的移送作業趨於不穩定因而會有難以有效率地進行製造之虞慮,因此係將從退火溫度起迄400℃的冷卻速度設定在未達70℃/秒為宜。
二次冷軋(DR)的軋縮率:1.0%以上10%以下
退火後的鋼板,是藉由實施二次冷軋而被高強度化,並且二次冷軋係有降低鋼板的降伏伸長率之效果。想要獲得這種效果,係將二次冷軋的軋縮率設定在1.0%以上。二次冷軋的軋縮率太高的話,成形性將會惡化,因此係設定在10%以下。在被特別要求成形性的情況下,係將二次冷軋的軋縮率設定在4%以下為佳。
以下將說明本發明的實施例。但是本發明的技術範圍並不是限定在以下的實施例而已。
首先將具有表1所示的鋼記號A~V的成分且其餘部分是Fe以及不可避免的雜質的組成分的鋼進行熔製,而獲得鋼胚料。將所獲得的鋼胚料依據表2所示的條件,進行加熱後,進行熱軋,進行捲取,進行酸洗以除去鏽皮之後,實施一次冷軋,在連續退火爐中依據表2所示的退火溫度進行15秒鐘的退火,依據表2所示的冷卻速度進行冷卻至400℃為止,從400℃起迄室溫為止,係以20℃/秒的速度進行冷卻之後,依據表2所示的軋縮率進行二次冷軋,因而製得板厚度為0.16~0.22mm的鋼板(鋼板記號1~33)。對於該鋼板進行鍍鉻(不含錫)處理作為表面處理之後,製作成披覆有機皮膜的包膜鋼板。
利用濃硫酸將前述包膜鋼板的有機皮膜除去之後,從輥軋方向採取出日本工業規格JIS 5號拉伸試驗片,根據日本工業規格JIS Z 2241的規定進行評量:拉伸強度、總伸長率、降伏伸長率。此處,係為了測定板厚度而將有機皮膜予以除去,但是並未將鍍鉻層除去。這是因為鍍鉻層很薄,屬於板厚測定時的誤差範圍之內,即使不除去鍍鉻層,對於拉伸強度也幾乎沒有影響。此外,針對於拉伸強度、總伸長率、降伏伸長率的評量,也可以是在將鍍鉻層的局部或全部除去之後,才進行評量。將評量結果標示於
表3。
為了能夠觀察到鋼板中之與輥軋方向平行的垂直斷面,將樣本裁切出來之後,埋入樹脂中,進行研磨後,利用硝酸腐蝕液進行腐蝕以使鋼板組織浮現出來,然後,利用掃描型電子顯微鏡拍攝鋼板組織,利用圖像處理技術來測定出肥粒鐵相以及第2相(麻田散鐵相以及殘留沃斯田鐵相的合計)的面積百分率。將測定結果標示於表3。
利用濃硫酸從鋼板上除去有機皮膜以及鍍鉻層之後,藉由:從N總含量減去:以10%Br甲醇溶液進行萃取分析所測得的NaS氮化物含量而測定出固溶N含量。將測定結果標示於表3。
為了評量成形性,先將前述的包膜鋼板衝製成圓形(尺寸:直徑為140mm)之後,實施深衝拉加工、引縮加工等,製罐形成有底的圓筒形(尺寸:直徑50mm×高度100mm)之後,在罐身部的高度中央、以及從高度中央起算的上下10mm處、上下20mm處之合計5個地方的罐圓周方向,進行凸波紋加工,以成形為:與適用於飲料罐的2片式罐相同的罐體。然後依照以下所述的判斷基準,
以目視方式進行評量,將評量結果標示於表3。
將製罐時,未發生破胴且未發現到有拉伸變形紋的測試樣本標示為◎;將雖然未發生破胴,但有發現到對於實用性並不造成問題之輕微的拉伸變形紋的測試樣本標示為○;將發生破胴或者被發現有明顯的拉伸變形紋的測試樣本標示為×。
發明例的每一個都是拉伸強度為480MPa以上,總伸長率為12%以上,降伏伸長率為2.0%以下,以肥粒鐵相作為主相,第2相的面積百分率是1.0%以上。因此,係為總伸長率高且降伏伸長率低之高強度罐用鋼板。並且發明例的每一個在製罐後,罐底部皆可確保充分的強度。
另一方面,比較例係在拉伸強度、總伸長率、降伏伸長率、第2相的面積百分率的其中一項以上的表現不佳,而且成形性不夠充分。
Claims (4)
- 一種罐用鋼板,其組成分以質量%計,係含有C:0.015%以上0.150%以下、Si:0.04%以下、Mn:1.0%以上2.0%以下、P:0.025%以下、S:0.015%以下、Al:0.01%以上0.10%以下、N:0.0005%以上且未達0.0050%、Ti:0.003%以上0.015%以下、B:0.0010%以上0.0040%以下,其餘部分是Fe以及不可避免的雜質;其鋼板組織,係以肥粒鐵相作為主相,第2相則是由麻田散鐵相與殘留沃斯田鐵相所組成的至少其中一方,該第2相以面積百分率計,合計是含有1.0%以上;拉伸強度為480MPa以上;總伸長率為12%以上;並且降伏伸長率為2.0%以下。
- 如請求項1所述的罐用鋼板,除了前述組成分之外,又含有Cr:0.03%以上0.30%以下、Mo:0.01%以上0.10%以下的其中一種以上。
- 一種罐用鋼板的製造方法,係將具有如請求項1或請求項2所記載的組成分之胚料,以加熱溫度為1130℃以上的條件來進行加熱,以精製溫度為820℃以上930℃以下的條件來進行熱軋之後,以捲取溫度為640℃以下的條件來進行捲取,進行酸洗之後,以85%以上的軋縮率進行一次冷軋,以退火溫度為720℃以上780℃以下的條件來進行連續退火,然後以1.0%以上10%以下的軋縮率進行二次冷軋。
- 如請求項3所述的罐用鋼板的製造方法,係在前述連續退火之後,以2℃/秒以上且未達70℃/秒的冷卻速度,從前述退火溫度進行冷卻直到400℃,然後,進行前述的二次冷軋。
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- 2017-03-24 PH PH12017500557A patent/PH12017500557A1/en unknown
Also Published As
Publication number | Publication date |
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JP6048618B2 (ja) | 2016-12-21 |
MY176614A (en) | 2020-08-18 |
CN107109556A (zh) | 2017-08-29 |
CN107109556B (zh) | 2019-01-11 |
EP3187612A4 (en) | 2017-09-20 |
US20170314095A1 (en) | 2017-11-02 |
WO2016075866A1 (ja) | 2016-05-19 |
TWI588271B (zh) | 2017-06-21 |
EP3187612A1 (en) | 2017-07-05 |
JPWO2016075866A1 (ja) | 2017-04-27 |
EP3187612B1 (en) | 2019-06-19 |
US10837076B2 (en) | 2020-11-17 |
KR20170070135A (ko) | 2017-06-21 |
PH12017500557A1 (en) | 2017-08-30 |
KR101918426B1 (ko) | 2018-11-13 |
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