JP2676581B2 - Steel sheet suitable for thinned deep-drawing can and its manufacturing method - Google Patents
Steel sheet suitable for thinned deep-drawing can and its manufacturing methodInfo
- Publication number
- JP2676581B2 JP2676581B2 JP5197825A JP19782593A JP2676581B2 JP 2676581 B2 JP2676581 B2 JP 2676581B2 JP 5197825 A JP5197825 A JP 5197825A JP 19782593 A JP19782593 A JP 19782593A JP 2676581 B2 JP2676581 B2 JP 2676581B2
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- rolling
- thin
- rolled
- hot
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
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- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Description
【0001】[0001]
【産業上の利用分野】本発明は食品缶、飲料缶等の容器
材料に関し、特に深絞り加工性に優れ、肌荒れ性が良
く、耐食性の優れた薄肉化深絞り缶用途に適した鋼板お
よびその製造法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a container material for food cans, beverage cans and the like, and more particularly to a steel plate suitable for use in a thin-walled deep-drawing can having excellent deep-drawing workability, good surface roughness and excellent corrosion resistance. It concerns the manufacturing method.
【0002】[0002]
【従来の技術】従来、側面無継目(サイドシームレス)
缶の成形法として、表面処理鋼板を成形した後の缶の内
外に有機塗料を施す方法と、成形前の金属板にあらかじ
め樹脂フィルムを被覆し、樹脂フィルムを一種の成形潤
滑剤とし、缶側壁となる部分の金属板を薄肉化する、い
わゆる薄肉化絞り缶成形法とがある。後者の例として、
本発明者らは先に、金属板の平均結晶粒径及び平均表面
粗さを特定することにより、製缶後の耐肌荒れ性および
耐食性に優れた薄肉化絞り缶用の金属板を提案した(特
開平4−314535号参照)。2. Description of the Related Art Conventionally, a side seam is seamless.
As a method of forming a can, a method of applying an organic paint to the inside and outside of the can after forming a surface-treated steel sheet, a method of coating a metal sheet before forming with a resin film in advance, using the resin film as a kind of forming lubricant, There is a so-called thinned draw can molding method for reducing the thickness of a metal plate in a portion to be formed. As an example of the latter,
The present inventors have previously proposed a metal plate for a thinned drawn can having excellent surface roughness and corrosion resistance after can making by specifying the average crystal grain size and the average surface roughness of the metal plate ( JP-A-4-314535).
【0003】[0003]
【発明が解決しようとする課題】しかしながら、従来の
あらかじめ樹脂フィルムを被覆した金属板を用いて薄肉
化絞り缶を成形すると、完成後の缶側壁が極めて肌荒れ
しやすいという問題がある。すなわち、ダイスとポンチ
のクリアランスが缶側壁の厚みより大きく、加工時にお
いて缶側壁がポンチとダイスに拘束されず、いわゆる自
由表面となっているので、DI(Draw and I
roning)成形法と比べ缶側壁が肌荒れしやすいと
いう問題がある。この肌荒れ状態が生ずると、原板とフ
ィルムの密着力が減少し、フィルム剥離の一因ともな
る。また肌荒れは、輸送中の缶同士の接触などの外部か
らの衝撃が引き金になり、フィルム面に微細なクラック
を生じさせ、ひいては耐食性の劣化を招くという問題も
ある。通常、薄肉化深絞り缶は被覆金属板を円板状に打
ち抜き、これを二段階の絞り加工によって成形される。
この二段目の絞り加工(再絞り加工)時においては、フ
ランジ部に高いしわ押え力を加え、缶側壁の絞り−張り
出し加工を行なうことにより、缶側壁の厚みを減少させ
ている。上記の加工法において、再絞り加工は極めて過
酷な成形法であるため、連続成形時に破胴が起こりやす
いという問題があった。このような破胴が起こると高速
製缶加工の生産性を損なうため、破胴が起こりにくく、
しかも加工性に優れた薄肉化深絞り缶用途に適した鋼板
を開発することは急務であった。本発明は上記問題点を
解決することを目的とし、肌荒れ性、耐食性が優れ、連
続高速製缶加工時において、破胴が起きず、しかも加工
性に優れた薄肉化深絞り缶用途に適した鋼板およびその
製造法を提供することを目的とする。However, when a thinned drawn can is formed by using a conventional metal plate previously coated with a resin film, there is a problem that the completed can side wall is extremely rough. That is, since the clearance between the die and the punch is larger than the thickness of the can side wall, and the can side wall is not restricted by the punch and the die during processing, and has a so-called free surface, DI (Draw and I)
There is a problem that the side wall of the can is easily roughened as compared with the molding method. When this rough surface state occurs, the adhesion between the original plate and the film decreases, which also contributes to film peeling. In addition, there is also a problem that the roughened surface is triggered by an external impact such as contact between cans during transportation, which causes fine cracks on the film surface, and eventually causes deterioration of corrosion resistance. Normally, a thin-walled deep-drawing can is formed by punching a coated metal plate into a disk shape and performing a two-stage drawing process.
In the second-stage drawing (redrawing), the thickness of the can side wall is reduced by applying a high wrinkle holding force to the flange portion and performing the drawing-extending process of the can side wall. In the above-mentioned processing method, redrawing is an extremely severe forming method, so that there is a problem that a broken body is likely to occur during continuous forming. If such a fracture occurs, the productivity of high-speed can manufacturing is impaired.
In addition, there was an urgent need to develop a steel sheet that is excellent in workability and suitable for thinning deep drawing cans. The present invention aims to solve the above-mentioned problems, and is suitable for use in thin-walled deep-drawing cans having excellent surface roughness, excellent corrosion resistance, no breakage during continuous high-speed can-making, and excellent workability. An object of the present invention is to provide a steel sheet and a method for manufacturing the same.
【0004】[0004]
【課題解決のための手段】本発明の薄肉化深絞り缶用途
に適した鋼板は、C:0.01〜0.15%、Si≦
0.05%、Mn≦0.9%、P≦0.04%、S≦
0.04%、Al:0.015〜0.10%、N:0.
002〜0.015%、残部Fe及び不可避的不純物か
らなる熱延鋼板を、冷間圧延、過時効処理を含むヒート
サイクルでの焼鈍、圧下率20〜50%でのDR圧延、
を順次行いDR圧延後の鋼板の平均結晶粒径が6.0μ
m以下である薄肉化深絞り缶用途に適した鋼板である。
また、C:0.01〜0.15%、Si≦0.05%、
Mn≦0.9%、P≦0.04%、S≦0.04%、A
l:0.015〜0.10%、N:0.002〜0.0
15%、Nb:0.001〜0.020%、残部Fe及
び不可避的不純物からなる熱延鋼板を、冷間圧延、過時
効処理を含むヒートサイクルでの焼鈍、圧下率20〜5
0%でのDR圧延、を順次行いDR圧延後の鋼板の平均
結晶粒径が6.0μm以下であることも望ましい。次ぎ
に、本発明の薄肉化深絞り缶用途に適した鋼板の製造法
は、C:0.01〜0.15%、Si≦0.05%、M
n≦0.9%、P≦0.04%、S≦0.04%、A
l:0.015〜0.10%、N:0.002〜0.0
15%、残部Fe及び不可避的不純物からなる熱延鋼板
を、冷間圧延、過時効処理を含むヒートサイクルでの焼
鈍、圧下率20〜50%でのDR圧延、を順次行う薄肉
化深絞り缶用途に適した鋼板の製造法であり、また、
C:0.01〜0.15%、Si≦0.05%、Mn≦
0.9%、P≦0.04%、S≦0.04%、Al:
0.015〜0.10%、N:0.002〜0.015
%、Nb:0.001〜0.020%、残部Fe及び不
可避的不純物からなる熱延鋼板を、冷間圧延、過時効処
理を含むヒートサイクルでの焼鈍、圧下率20〜50%
でのDR圧延、を順次行うことも望ましい。A steel sheet suitable for use in a thin-walled deep-drawn can of the present invention is C: 0.01 to 0.15%, Si ≦.
0.05%, Mn ≦ 0.9%, P ≦ 0.04%, S ≦
0.04%, Al: 0.015 to 0.10%, N: 0.
Hot-rolled steel sheet consisting of 002 to 0.015%, balance Fe and unavoidable impurities, cold rolling, annealing in a heat cycle including overaging treatment, DR rolling with a reduction rate of 20 to 50%,
And the average crystal grain size of the steel sheet after DR rolling is 6.0μ.
A steel sheet having a thickness of m or less, which is suitable for thin-walled deep drawing can applications .
Further, C: 0.01 to 0.15%, Si ≦ 0.05%,
Mn ≦ 0.9%, P ≦ 0.04%, S ≦ 0.04%, A
1: 0.015-0.10%, N: 0.002-0.0
15%, Nb: 0.001 to 0.020%, a hot-rolled steel sheet consisting of balance Fe and unavoidable impurities, cold-rolled, annealed in a heat cycle including overaging treatment, a reduction ratio of 20 to 5
It is also preferable that the average grain size of the steel sheet after DR rolling is sequentially performed by 0% DR rolling to be 6.0 μm or less. Next, the manufacturing method of the steel sheet suitable for use in the thin-walled deep drawing can of the present invention is as follows: C: 0.01 to 0.15%, Si ≦ 0.05%, M
n ≦ 0.9%, P ≦ 0.04%, S ≦ 0.04%, A
1: 0.015-0.10%, N: 0.002-0.0
A thin-walled deep-drawn can in which a hot-rolled steel sheet consisting of 15%, balance Fe and unavoidable impurities is sequentially subjected to cold rolling, annealing in a heat cycle including overaging treatment, and DR rolling at a reduction rate of 20 to 50%. a method of producing steel sheets suitable for use, also,
C: 0.01 to 0.15%, Si ≦ 0.05%, Mn ≦
0.9%, P ≦ 0.04%, S ≦ 0.04%, Al:
0.015 to 0.10%, N: 0.002 to 0.015
%, Nb: 0.001 to 0.020%, the balance of Fe and unavoidable impurities in a hot rolled steel sheet is annealed in a heat cycle including cold rolling and overaging, and a reduction rate of 20 to 50%.
It is also desirable to sequentially perform the DR rolling in.
【0005】[0005]
【作用】本発明の鋼板に、ポリエステル等の樹脂フィル
ムを被覆し、円板状に打ち抜き、これを二段階絞りの連
続高速製缶加工を行っても、破胴が起きず、しかも加工
性に優れた薄肉化深絞り缶を成形できる。特に、近年に
おける著しく薄肉化され、また、その分高強度化された
缶用途の鋼板においても、二段階の過酷な深絞りの際の
破胴を生じないための加工性と強度とを兼ね備え、かつ
成形品として肌荒れや耐食性の条件を満たすことができ
る。即ち、薄肉化深絞り加工においては極薄鋼板を素材
としで、再絞り工程で強いバックテンションとポンチ力
の負荷のもとで曲率半径の小さいダイスコーナーで強度
の引張曲げ加工を受けて薄肉化されるため、これらの薄
肉化深絞りの要求に応える高度な加工性と共にその際破
胴発生に至らないための強度が必要であり、このため缶
強度と加工性の兼ね合いが重要である。本発明において
は、冷延後の過時効処理を含むヒートサイクル後にDR
圧延を組合せることにより、冷延後の過度効処理による
固溶C、Nの低減が図られ、伸び特性が向上して加工性
が向上するという作用と過時効後の圧下率の大きなDR
圧延による板強度の向上とが相俟って、缶用極薄鋼板に
おいて十分な加工性と破胴を生じない強度とを付与する
ことができる。また、Nbの添加は一般に結晶粒微細化
及び固溶C、Nの低減に寄与することが知られていると
ころであるが、冷延後の過時効処理を含む本発明のヒー
トサイクルと組合わされることにより、過時効処理によ
り固溶C、Nの低減が図られ、伸び特性を含む加工性の
向上が図られることと相俟って、過時効処理の際の固溶
C、Nの低減作用が著しく増進されるのであって、その
結晶粒の粗大化防止効果と相俟って、肌荒れ防止と共に
薄肉化深絞り加工における破胴防止効果を達成すること
ができる。そして、これらの作用・効果は、その特定の
成分組成による性質に基づいて発揮されるのであって、
特にC量の規制とNbの微量の含有がこれらの処理工程
と相俟って、肌荒れ性の向上に寄与する結晶粒の細粒化
が達成できる。 The steel sheet of the present invention is coated with a resin film such as polyester and punched into a disk shape, and even if it is subjected to continuous high-speed can-making processing by two-step drawing, no crushing occurs and the workability is improved. Can form excellent thin-walled deep-drawn cans. Especially in recent years
The thickness was significantly reduced and the strength was increased accordingly.
Even for steel sheets for cans, it can be used for deep deep drawing in two stages.
Combines workability and strength to prevent breakage, and
As a molded product, it can meet the conditions of rough skin and corrosion resistance.
You . That is, ultra-thin steel sheet is used
And, in the redrawing process, strong back tension and punch force
Strength at a die corner with a small radius of curvature under the load of
These thin films are thinned by the tensile bending process of
Highly workable to meet the demands of deep drawing
It is necessary to have enough strength to prevent the formation of a barrel.
The balance between strength and workability is important. In the present invention
DR after heat cycle including overaging treatment after cold rolling
By combining rolling, it is possible to use over-effect treatment after cold rolling.
The solid solution C and N are reduced, the elongation characteristics are improved, and the workability is improved.
DR with a large reduction rate after overaging
Combined with the improvement of plate strength by rolling, it becomes an ultra-thin steel plate for cans.
Gives sufficient workability and strength that does not cause crushing
be able to. Also, the addition of Nb generally refines the crystal grains.
And that it is known to contribute to the reduction of solute C and N
However, the heat treatment of the present invention including overaging treatment after cold rolling is performed.
By combining with the cycle,
Resolved C and N are reduced, and workability including elongation characteristics is improved.
Combined with improvement, solid solution during overaging treatment
The effect of reducing C and N is remarkably enhanced.
Combined with the effect of preventing coarsening of crystal grains, it also prevents rough skin.
Achievement of collapsing prevention effect in thinning deep drawing
Can be . And these actions and effects are
It is exerted based on the properties of the component composition,
Especially, the amount of C and the small amount of Nb are contained in these treatment steps.
Combined with the refinement of crystal grains that contribute to the improvement of rough skin
Can be achieved.
【0006】[0006]
【実施例】熱延鋼板の成分 鋼成分は、C:0.01〜0.15%、Si≦0.05
%、Mn≦0.9%、P≦0.04%、S≦0.04
%、Al:0.015〜0.10%、N:0.002〜
0.015%、残部Fe及び不可避的不純物より成る。
また、上記成分にNbを0.001〜0.02%加えた
ものも好適に用いられる。以下に鋼成分の規制理由を述
べる。Cは、0.01%より少なくなると結晶粒の粗大
化を招き、下限を0.01%とした。一方、0.15%
を越えると絞り加工性が劣化することから、範囲を0.
01〜0.15%とした。Siは、缶用材料として耐食
性に有害な元素であるが、Alキルド鋼としては不可避
的に含有される元素であり、上限を0.05%とした。
Mnは、不純物であるSによる熱延中の赤熱脆性を防止
するために必要な成分であるが、一方0.9%を越える
と絞り加工性を劣化することから上限を0.9%とし
た。Pは、結晶粒微細化に有効な成分であり、また原板
の強度を高めることから一定の割合で添加されるが、一
方で耐食性を阻害する。本発明用途の缶用鋼板としては
Pが0.04%を越えると耐食性、特に耐孔明性が著し
く低下するため上限を0.04%とした。Sは、熱延中
の赤熱脆性を生じる不純物成分であり、極力少ないこと
が望ましいが、不可避的に含有される元素であり、上限
を0.04%とした。Alは製鋼に際し、脱酸剤として
鋼浴中に添加され、スラグとして除かれるが、添加量が
少ないと安定した脱酸効果が得られないため、0.01
5%以上必要とする。またAlは固溶Nと反応してAl
Nとして析出し、結晶粒の細粒化に寄与する。一方で
0.10%を越える添加は技術上の効果が少なく、経済
上好ましくないので上限を0.10%とした。NはAl
及びNbと窒化物を形成し、結晶粒の細粒化に有効な成
分であるが、0.002%より少ないと窒化物の析出が
少なく、細粒化の効果がなくなり、一方0.015%を
越えるとスラブ表面に割れが生じ易く、構造欠陥になる
ため範囲を0.002〜0.015%とした。Nbは結
晶粒の細粒化に効果があり、固溶C、Nの低減に寄与す
る。0.001%より少ないと細粒化の効果がなく、一
方、0.020%を越えると固溶Nb量が増して逆に絞
り加工性の劣化を招くため上限を0.020%とした。[Examples] Components of hot-rolled steel sheet The steel components are C: 0.01 to 0.15%, Si ≤ 0.05.
%, Mn ≦ 0.9%, P ≦ 0.04%, S ≦ 0.04
%, Al: 0.015 to 0.10%, N: 0.002 to
0.015%, balance Fe and unavoidable impurities.
Further, those obtained by adding 0.001 to 0.02% of Nb to the above components are also preferably used. The reasons for the regulation of steel components are described below. If C is less than 0.01%, the crystal grains are coarsened, and the lower limit is made 0.01%. On the other hand, 0.15%
If it exceeds 1.0 , the drawability deteriorates, so the range is set to 0.
It was set to 01 to 0.15%. Si is an element harmful to corrosion resistance as a material for cans, but is an unavoidable element in Al-killed steel, and the upper limit is 0.05%.
Mn is a component necessary to prevent red hot embrittlement due to impurities S during hot rolling. On the other hand, if it exceeds 0.9%, drawability deteriorates, so the upper limit was made 0.9%. . P is an effective component for refining the crystal grains, and is added at a certain ratio to increase the strength of the original sheet, but impairs corrosion resistance. As a steel sheet for cans for use in the present invention, if P exceeds 0.04%, corrosion resistance, particularly puncture resistance remarkably decreases, so the upper limit was made 0.04%. S is an impurity component that causes red hot embrittlement during hot rolling, and is desirably as small as possible. However, S is an element inevitably contained, and the upper limit is set to 0.04%. Al is added as a deoxidizing agent in the steel bath during steelmaking and is removed as slag. However, if the added amount is too small, a stable deoxidizing effect cannot be obtained.
5% or more is required. Also, Al reacts with solid solution N to form Al
Precipitates as N and contributes to grain refinement. On the other hand, addition of more than 0.10% has little technical effect and is economically unfavorable, so the upper limit was made 0.10%. N is Al
It is a component that forms nitrides with Nb and N, and is an effective component for grain refinement, but if it is less than 0.002%, the precipitation of nitrides is small and the grain refinement effect disappears, while 0.015% If it exceeds 0.1%, cracks are likely to occur on the slab surface, causing structural defects, so the range was made 0.002 to 0.015%. Nb is effective in refining crystal grains, and contributes to reduction of solid solution C and N. If it is less than 0.001%, there is no effect of grain refining, while if it exceeds 0.020%, the amount of solid solution Nb increases and conversely deteriorates drawability, so the upper limit was made 0.020%.
【0007】スラブ加熱温度、熱間圧延条件は、本発明
では特定するものではないが、スラブ加熱温度は、Nの
積極的分解固溶および熱間圧延温度の安定的確保の見地
から、1100℃以上とするのが望ましい。熱間圧延仕
上げ温度をAr3 点以下にすると、熱延板の結晶組織が
混粒化するとともに粗大化するので、熱間圧延仕上げ温
度はAr3 点以上とした。また巻取温度は熱延時のコイ
ル幅方向および長手方向の品質安定性を考慮して下限を
450℃とし、650℃を越えると結晶粒が粗大化し、
肌荒れが生じるため、巻取温度は450〜650℃の範
囲が望ましい。Although the slab heating temperature and the hot rolling conditions are not specified in the present invention, the slab heating temperature is set to 1100 ° C. from the viewpoint of the active decomposition of N and the stable securing of the hot rolling temperature. It is desirable to make the above. If the hot rolling finish temperature is lower than the Ar3 point, the crystal structure of the hot-rolled sheet is mixed and coarsened, so the hot rolling finish temperature is higher than the Ar3 point. In addition, the lower limit of the winding temperature is set to 450 ° C. in consideration of the quality stability in the coil width direction and the longitudinal direction at the time of hot rolling.
Since the skin becomes rough, the winding temperature is preferably in the range of 450 to 650 ° C.
【0008】冷間圧延工程 圧下率が75%未満では、焼鈍工程で鋼板の結晶粒粗大
化もしくは混粒化をもたらし、結晶粒を十分細粒化する
ことができないので、冷間圧延の圧下率は75%を下限
とすることが望ましい。[0008] If the rolling reduction is less than 75%, the annealing step results in coarsening or mixing of the grains of the steel sheet, and the grains cannot be sufficiently refined. Is preferably set to 75% as the lower limit.
【0009】焼鈍工程 本発明では、過時効処理を含むヒートサイクルでの焼鈍
を採用することにより、破胴に効果があることが判明し
た。これは固溶C、Nが低減したことによると考えられ
る。焼鈍は、連続焼鈍後、そのまま連続焼鈍処理で過時
効処理を行う場合と、一旦降温し、改めて箱焼鈍処理を
行う場合の、いずれの処理方法でもよい。前段階の連続
焼鈍の処理温度は、再結晶温度以上あれば良いが、75
0℃を越えると結晶粒の粗大化が起きるので好ましくな
い。なお、ここで言う過時効処理とは、一般の焼鈍処理
に比較して、低温、長時間での熱処理を言う。過時効処
理は連続焼鈍に続けて行う場合は、400〜550℃で
1〜3分間均熱処理を行う。400℃未満では、固溶
C、Nが低減できず、550℃を越えると結晶粒が粗大
化する。また、1分未満では、固溶C、Nの低減が十分
図れず、3分を越えると炉長が長大化するため、1〜3
分の範囲とする。また、過時効処理は、箱焼鈍でもよ
い。箱焼鈍による場合は、一旦下げた温度を400〜5
50℃に上げ、2〜10時間均熱処理を行う。400℃
未満では、過時効処理としての品質が安定せず、特性が
ばらつく。550℃を越えると、連続焼鈍と同様結晶粒
が粗大化する。2時間未満では、過時効処理としての品
質が安定せず、特性がばらつく。一方、10時間を越す
処理は経済上得策ではない。Annealing Step In the present invention, it has been found that the adoption of annealing in a heat cycle including overaging treatment has an effect on fracture. This is considered to be due to a decrease in solid solution C and N. Annealing may be carried out by any of the following methods: continuous aging followed by over-aging after continuous annealing, and case where the temperature is once lowered and box annealing is performed again. The treatment temperature of the continuous annealing in the preceding stage may be at least the recrystallization temperature,
If the temperature exceeds 0 ° C., the crystal grains become coarse, which is not preferable. Here, the overaging treatment means a heat treatment at a low temperature for a long time as compared with a general annealing treatment. When the overaging treatment is performed after the continuous annealing, the soaking is performed at 400 to 550 ° C for 1 to 3 minutes. If the temperature is lower than 400 ° C., solid solution C and N cannot be reduced. If the temperature exceeds 550 ° C., crystal grains become coarse. If it is less than 1 minute, the solid solution C and N cannot be sufficiently reduced, and if it exceeds 3 minutes, the furnace length becomes long, so
Minute range. The overaging treatment may be box annealing. In case of box annealing, lower the temperature once to 400 ~ 5.
The temperature is raised to 50 ° C., and the soaking is performed for 2 to 10 hours. 400 ° C
When the amount is less than the above, the quality as overaging treatment is not stable and the characteristics vary. If it exceeds 550 ° C., the crystal grains become coarse as in continuous annealing. If the time is less than 2 hours, the quality as the overaging treatment is not stable, and the characteristics vary. On the other hand, treatment exceeding 10 hours is not economically advantageous.
【0010】過時効処理の効果 一般に、固溶C、Nの増加により全伸びが低下し、一様
伸びも劣化する。これは、伸び時に発生するくびれや、
ボイドの連結機構に固溶C、Nが作用しているためと考
えられる。過時効処理は鋼中の固溶C、Nを低減させ、
鋼の軟質化に効果がある、過時効処理を行うことによ
り、鋼中固溶C、Nを低減させ、くびれの発生やボイド
の連結が抑制され、結果的に破断・破胴感受性を低減さ
せると考えられる。本発明の鋼成分範囲は、これらの過
時効処理における作用を発揮させる上で必要であって、
前記の各成分の作用はこの過時効処理を通じて達成され
るものである。C量の下限値やAl、Nb等の存在は結
晶粒の細粒化によって肌荒れ防止するが、特に、微量の
Nb添加はその固溶C、Nの低減作用を過時効処理と相
俟って発揮することにより加工性を向上する。[0010] In general, the effect of overage treatment decreases the total elongation and the uniform elongation by increasing the amount of solid solution C and N. This is due to the constriction that occurs when stretching,
It is considered that solid solution C and N act on the void connection mechanism. Overaging treatment reduces solid solution C and N in steel,
By overaging, which has the effect of softening the steel, the solid solution C and N in the steel is reduced, the occurrence of necking and the connection of voids are suppressed, and as a result, the susceptibility to fracture and shattering is reduced. it is conceivable that. The range of steel composition of the present invention is
It is necessary to exert the action in aging treatment,
The action of each of the above components is achieved through this overaging treatment.
Things. The lower limit of C content and the presence of Al, Nb, etc.
It prevents rough skin by making the crystal grains fine, but
Addition of Nb has the effect of reducing the solute C and N by overaging treatment.
Workability is improved by taking advantage of this .
【0011】調質圧延 調質圧延(SR,Single Reduce Rol
lingの略)は、伸び率が0.5〜2.0%の範囲で
あれば、ストレッチャストレインの発生が防止されるた
め、この範囲が適当である。Temper Rolling Temper rolling (SR, Single Reduce Roll
(Ling is an abbreviation for ling), since the occurrence of stretcher strain is prevented if the elongation percentage is in the range of 0.5 to 2.0%.
【0012】DR圧延 DR圧延は成形後の缶強度を持たせるために必要である
が、圧下率は20〜50%とする。20%未満では、十
分な缶強度が得られず、50%を越えると鋼板が高強度
となり、缶成形加工に困難を来す。ここでDR圧延と
は、DoubleReduce Rollingの略で
あり、調質圧延よりもより積極的に板厚を減少させ、板
強度を増加させる圧延法である。本発明では、上記調質
圧延とDR圧延とを含めて二次冷延とする。本発明で
は、過時効処理により前記の鋼中の固溶C、Nを低減し
てくびれの発生やボイドの連結を抑制して深絞りにおけ
る加工性を向上して、本発朋の対象である薄肉化深絞り
の加工条件を満たすと共に、DR圧延を行うことによっ
て強度を付与し、これによって、本発明の鋼板は、薄肉
化深絞り加工に求められる高度の加工性に併せて加工時
の破胴発生を生じない板強度を付与することができる。
このように、本発明においては、これら2つの工程が組
み合わされて、加工性と板強度それぞれの条件を達成す
ることができる。また、このDR圧延によって極薄板厚
の缶において求められる所要の缶強度をも達成するもの
である。 DR rolling DR rolling is necessary to give can strength after forming, but the rolling reduction is 20 to 50%. If it is less than 20%, sufficient can strength cannot be obtained, and if it exceeds 50%, the steel sheet has high strength, and it becomes difficult to form a can. Here, the DR rolling is an abbreviation for Double Reduce Rolling, and is a rolling method that more positively reduces the sheet thickness and increases the sheet strength than the temper rolling. In the present invention, the secondary cold rolling includes the above temper rolling and DR rolling. In the present invention
Reduces the solute C and N in the steel by overaging.
It suppresses the necking and void connection and allows deep drawing.
Which is the target of this invention
By performing the DR rolling while satisfying the processing conditions of
To impart strength, which makes the steel sheet of the present invention thin
During processing in accordance with the high workability required for deep drawing
It is possible to provide a plate strength that does not cause breakage of the plate.
Thus, in the present invention, these two steps are combined.
Achieved the conditions of workability and plate strength
Can be In addition, this DR rolling enables ultra-thin plate thickness
Achieving the required can strength required for other cans
It is.
【0013】つぎに、本発明に用いられる鋼板として
は、シ−ト状およびコイル状の鋼板、鋼箔およびそれら
の鋼板等に表面処理を施したものがあげられる。特に、
下層が金属クロム、上層がクロム水和酸化物の2層構造
をもつ電解クロム酸処理鋼板あるいは極薄錫めっき鋼
板、ニッケルめっき鋼板、亜鉛めっき鋼板およびこれら
のめっき鋼板にクロム水和酸化物あるいは上層がクロム
水和酸化物、下層が金属クロム層からなる2層構造をも
つ表面処理をほどこしたものがポリエステル樹脂との接
触性に優れている。Next, examples of the steel sheet used in the present invention include sheet-shaped and coil-shaped steel sheets, steel foils, and those obtained by subjecting these steel sheets to surface treatment. Especially,
Electrolytic chromic acid-treated steel sheet or ultra-thin tin-plated steel sheet, nickel-plated steel sheet, zinc-plated steel sheet having a two-layer structure of chromium metal on the lower layer and hydrated chromium oxide on the upper layer Is a hydrated oxide of chromium, and a surface treatment having a two-layer structure of a metal chromium layer as the lower layer is excellent in contact with the polyester resin.
【0014】平均結晶粒径 結晶粒径の特定について図1および図2に基づいて説明
する。図1は平均結晶粒径と製缶加工後の缶側壁の肌荒
れ性との関係を示したものである。図1から平均結晶粒
径が大きくなると製缶加工後の表面の肌荒れ性が劣化す
ることがわかる。平均結晶粒径が6μmを越えると、表
面の肌荒れ性が劣化し、缶としての見栄えや特性が損な
われる。このため平均結晶粒径は6μmを越えないこと
とする。また図2は平均結晶粒径と耐食性との関係を示
したものである。図2からも平均結晶粒径が6μmを越
えない範囲で耐食性がよいことがわかる。なお、耐食性
の評価は次のようにした。製缶加工後の缶を130℃で
20分の熱処理を行い、水を充填し、37℃、2週間経
時後の缶内面の腐食(黒化)程度を目視で評価した。Average Grain Size The specification of the crystal grain size will be described with reference to FIGS. FIG. 1 shows the relationship between the average crystal grain size and the roughness of the side wall of the can after the can-making process. From FIG. 1, it can be seen that when the average crystal grain size is large, the surface roughness after the can-making process is deteriorated. When the average crystal grain size exceeds 6 μm, the surface roughness is deteriorated, and the appearance and characteristics as a can are impaired. For this reason, the average crystal grain size does not exceed 6 μm. FIG. 2 shows the relationship between the average crystal grain size and the corrosion resistance. FIG. 2 also shows that the corrosion resistance is good when the average crystal grain size does not exceed 6 μm. In addition, evaluation of corrosion resistance was performed as follows. After the can-making process, the can was heat-treated at 130 ° C. for 20 minutes, filled with water, and the degree of corrosion (blackening) of the inner surface of the can after 2 weeks at 37 ° C. was visually evaluated.
【0015】[0015]
【表1】 [Table 1]
【0016】[0016]
【表2】 [Table 2]
【0017】評価 本発明の実施例No.1〜6は発明の成分範囲内で、過
時効処理を実施しており、加工性に優れている。表2に
示すとおり平均結晶粒径が6.0μm以下であり、肌荒
れ性、耐食性とも優れていることが判る。また、本発明
の薄肉化深絞り缶用途として重要な加工性においても優
れた結果となっている。特に実施例No.5及び6は微
量のNb添加により加工性に優れていることが判る。一
方、比較例No.7はC量が本発明範囲の下限以下で少
ないため結晶粒が粗大となり肌荒れ性、耐食性共に不良
となり、過時効処理を施したにもかかわらず加工性にお
いても劣った結果となっている。比較例No.8〜10
は、発明の成分範囲にあるが、過時効処理を実施してお
らず加工性が劣っている。なおここで、評価缶は、それ
ぞれ以下のようにした。肌荒れ性の評価は、薄肉化深絞
り缶成形後の缶内面の缶側壁の表面粗さを測定し、Ra
が1μm以下を◎(最良)とし、1〜1.5μmのもの
を○(良)とし、1.5〜2μmのものを△(やや不
良)とし、2μm以上を×(不良)として評価した。ま
た、耐食性の評価は、薄肉化深絞り缶成形後、130℃
×20分の熱処理を行い、水を充填し、37℃で2週間
経時後の缶内面の腐食(黒化)程度を目視で評価した。
表面が全く黒化していないものを◎(最良)とし、黒化
の程度が微小なものを○(良)とし、黒化の範囲が小の
もの(直径5mm以下)を△(やや不良)とし、大(直
径5mm以上)のものを×(不良)として評価した。加
工性の評価は、薄肉化深絞り缶成形時にしわ押さえ圧を
上げていって、破胴するまでのしわ押さえ圧の大小で評
価した。しわ押さえ圧が5トン以下で破胴したものを△
(やや不良)とし、5〜7トンで破胴したものを○
(良)とし、7トン以上で破胴したものを◎(最良)と
した。Evaluation Example No. 1 of the present invention. Nos. 1 to 6 were overaged within the range of the components of the invention, and were excellent in workability. In Table 2
As shown, the average crystal grain size is 6.0 μm or less, and the skin is rough.
It can be seen that both the corrosion resistance and the corrosion resistance are excellent. In addition, the present invention
It has excellent workability, which is important for thin-walled deep-drawing can applications.
The result has been. In particular, Example No. 5 and 6 are slight
It can be seen that the workability is excellent by adding a certain amount of Nb . one
If, Comparative Example No. 7 is small when the amount of C is below the lower limit of the range of the present invention.
Since it is not present, the crystal grains become coarse and the surface roughness and corrosion resistance are poor.
Therefore, even though overaged, it is easy to process.
The result is inferior. Comparative Example No. 8-10
Is within the range of the components of the invention, but has not been overaged and is inferior in workability. Here, the evaluation cans were as follows. The roughness of the skin is evaluated by measuring the surface roughness of the can side wall on the inner surface of the can after forming the thin-walled deep-drawing can and measuring Ra.
Was evaluated as ⊚ (best), 1 to 1.5 μm as ◯ (good), 1.5 to 2 μm as Δ (slightly bad), and 2 μm or more as x (bad). In addition, the corrosion resistance was evaluated at 130 ° C after forming a thin-walled deep-drawing can.
It was heat treated for 20 minutes, filled with water, and visually evaluated for corrosion (blackening) of the inner surface of the can after 2 weeks at 37 ° C.
If the surface is not blackened at all, it is ◎ (best), if the degree of blackening is minute, it is ○ (good), and if the range of blackening is small (diameter 5 mm or less) is Δ (somewhat bad). , Large (diameter of 5 mm or more) was evaluated as x (poor). The workability was evaluated by increasing the wrinkle holding pressure at the time of forming a thin-walled deep-drawing can, and evaluating the magnitude of the wrinkle holding pressure until breaking. Crumpled with a wrinkle holding pressure of 5 tons or less △
(Slightly bad), crushed with 5 to 7 tons ○
(Good), crushed at 7 tons or more was rated as ◎ (best).
【0018】[0018]
【発明の効果】本発明により、肌荒れ性、耐食性に優
れ、連続高速製缶加工時においても破胴が起きず、しか
も加工性に優れた薄肉化深絞り缶用途に適した鋼板を提
供することができる。なお、本発明により提供される鋼
板は、缶用途として、鋼板単独でも使用可能であるが、
この鋼板に表面処理をして、ぶりき、TFS、ニッケル
めっき鋼板等としても利用できる。さらに、上記の表面
処理鋼板にポリエステル等の樹脂フィルムを被覆しても
よい。また、この鋼板にエポキシ等の塗料をコーティン
グしたものも薄肉化深絞り缶用途に適用できる。According to the present invention, there is provided a steel sheet which is excellent in surface roughness and corrosion resistance, does not break even during continuous high-speed can-making, and is excellent in workability and is suitable for a thin-walled deep drawn can. Can be. In addition, the steel sheet provided by the present invention can be used as a can for a steel sheet alone,
This steel sheet can be surface-treated and used as tinplate, TFS, nickel-plated steel sheet and the like. Further, the surface-treated steel sheet may be covered with a resin film such as polyester. Further, a steel sheet coated with a paint such as epoxy can also be used for thinned deep drawing cans.
【図1】肌荒れ性に及ぼす平均結晶粒径の影響を示すグ
ラフである。FIG. 1 is a graph showing the influence of an average crystal grain size on skin roughness.
【図2】耐食性に及ぼす平均結晶粒径の影響を示すグラ
フである。FIG. 2 is a graph showing the effect of average crystal grain size on corrosion resistance.
Claims (4)
05%、Mn≦0.9%、P≦0.04%、S≦0.0
4%、Al:0.015〜0.10%、N:0.002
〜0.015%、残部Fe及び不可避的不純物からなる
熱延鋼板を、冷間圧延、過時効処理を含むヒートサイク
ルでの焼鈍、圧下率20〜50%でのDR圧延、を順次
行いDR圧延後の鋼板の平均結晶粒径が6.0μm以下
である薄肉化深絞り缶用途に適した鋼板。1. C: 0.01 to 0.15%, Si ≦ 0.
05%, Mn ≦ 0.9%, P ≦ 0.04%, S ≦ 0.0
4%, Al: 0.015 to 0.10%, N: 0.002
˜0.015%, balance Fe and unavoidable impurities, hot-rolled steel sheet is sequentially cold-rolled, annealed in a heat cycle including overaging treatment, and DR-rolled at a reduction rate of 20-50%, and then DR-rolled. A steel sheet suitable for thin-walled deep-drawing can applications, in which the subsequent steel sheet has an average crystal grain size of 6.0 μm or less.
05%、Mn≦0.9%、P≦0.04%、S≦0.0
4%、Al:0.015〜0.10%、N:0.002
〜0.015%、Nb:0.001〜0.020%、残
部Fe及び不可避的不純物からなる熱延鋼板を、冷間圧
延、過時効処理を含むヒートサイクルでの焼鈍、圧下率
20〜50%でのDR圧延、を順次行いDR圧延後の鋼
板の平均結晶粒径が6.0μm以下である薄肉化深絞り
缶用途に適した鋼板。2. C: 0.01 to 0.15%, Si ≦ 0.
05%, Mn ≦ 0.9%, P ≦ 0.04%, S ≦ 0.0
4%, Al: 0.015 to 0.10%, N: 0.002
To 0.015%, Nb: 0.001 to 0.020%, the balance of Fe and unavoidable impurities, hot-rolled steel sheet is annealed in a heat cycle including cold rolling and overaging, and a reduction ratio of 20 to 50. %, Which is suitable for thin-walled deep-drawing can applications, in which the average grain size of the steel sheet after DR rolling is 6.0 μm or less.
05%、Mn≦0.9%、P≦0.04%、S≦0.0
4%、Al:0.015〜0.10%、N:0.002
〜0.015%、残部Fe及び不可避的不純物からなる
熱延鋼板を、冷間圧延、過時効処理を含むヒートサイク
ルでの焼鈍、圧下率20〜50%でのDR圧延、を順次
行う薄肉化深絞り缶用途に適した鋼板の製造法。3. C: 0.01 to 0.15%, Si ≦ 0.
05%, Mn ≦ 0.9%, P ≦ 0.04%, S ≦ 0.0
4%, Al: 0.015 to 0.10%, N: 0.002
˜0.015%, balance Fe and unavoidable impurities, hot-rolled steel sheet is sequentially subjected to cold rolling, annealing in a heat cycle including overaging treatment, and DR rolling at a reduction rate of 20 to 50% to reduce the wall thickness. Steel plate manufacturing method suitable for deep drawing can applications.
05%、Mn≦0.9%、P≦0.04%、S≦0.0
4%、Al:0.015〜0.10%、N:0.002
〜0.015%、Nb:0.001〜0.020%、残
部Fe及び不可避的不純物からなる熱延鋼板を、冷間圧
延、過時効処理を含むヒートサイクルでの焼鈍、圧下率
20〜50%でのDR圧延、を順次行う薄肉化深絞り缶
用途に適した鋼板の製造法。4. C: 0.01 to 0.15%, Si ≦ 0.
05%, Mn ≦ 0.9%, P ≦ 0.04%, S ≦ 0.0
4%, Al: 0.015 to 0.10%, N: 0.002
To 0.015%, Nb: 0.001 to 0.020%, the balance of Fe and unavoidable impurities, hot-rolled steel sheet is annealed in a heat cycle including cold rolling and overaging, and a reduction ratio of 20 to 50. % Steel production method suitable for thin-walled deep-drawing can applications in which DR rolling in sequence is performed sequentially.
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FR2795743B1 (en) * | 1999-07-01 | 2001-08-03 | Lorraine Laminage | LOW ALUMINUM STEEL SHEET FOR PACKAGING |
JP2006045590A (en) * | 2004-07-30 | 2006-02-16 | Toyo Kohan Co Ltd | Steel sheet coated with organic resin film for di can, and manufacturing method therefor |
JP5434212B2 (en) * | 2008-04-11 | 2014-03-05 | Jfeスチール株式会社 | Steel plate for high-strength container and manufacturing method thereof |
JP6164273B2 (en) * | 2015-01-09 | 2017-07-19 | Jfeスチール株式会社 | Steel plate for cans and method for producing steel plate for cans |
CN104745785B (en) * | 2015-04-14 | 2017-06-13 | 武汉钢铁(集团)公司 | A kind of production method of superhigh intensity heat-proof corrosion-resistant tie |
CN114635095B (en) * | 2022-03-23 | 2023-04-07 | 邯郸市金泰包装材料有限公司 | Tinning plate containing sunflower pattern for aerosol can bottom cover and production method thereof |
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Publication number | Priority date | Publication date | Assignee | Title |
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JPS5938338A (en) * | 1982-08-30 | 1984-03-02 | Kawasaki Steel Corp | Production of ultra thin steel sheet having high yield strength and drawability |
JPH0480345A (en) * | 1990-07-19 | 1992-03-13 | Nippon Steel Corp | Cold rolled steel sheet excellent in workability, roughening property and earing property and its manufacture |
JP2560168B2 (en) * | 1991-12-18 | 1996-12-04 | 株式会社神戸製鋼所 | Method for producing cold-rolled steel sheet excellent in paint bake hardenability at low temperature |
-
1993
- 1993-07-14 JP JP5197825A patent/JP2676581B2/en not_active Expired - Fee Related
Also Published As
Publication number | Publication date |
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JPH0734192A (en) | 1995-02-03 |
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