JPH07252615A - Production of aluminum alloy sheet for drawing - Google Patents
Production of aluminum alloy sheet for drawingInfo
- Publication number
- JPH07252615A JPH07252615A JP4726094A JP4726094A JPH07252615A JP H07252615 A JPH07252615 A JP H07252615A JP 4726094 A JP4726094 A JP 4726094A JP 4726094 A JP4726094 A JP 4726094A JP H07252615 A JPH07252615 A JP H07252615A
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- hot rolling
- temperature
- continuous casting
- cold
- 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.)
- Withdrawn
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- Metal Rolling (AREA)
- Continuous Casting (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、絞り成形用のＡｌ合金
板の製造方法に関し、特にＭｎおよびＭｇを合金元素と
して含有するＡｌ合金を用いて連続鋳造した後熱間圧延
し、更に冷間圧延をなってＡｌ合金板を製造する際にお
いて、連続鋳造時および熱間圧延後の冷却速度を規定す
ると共に、熱間圧延後の冷間圧延工程中適正な温度で連
続中間焼鈍を行なうことによって、強度、焼き付け塗装
硬化性、および絞り成形性を一段と高める方法に関する
ものである。そして本発明によって得られるＡｌ合金板
は、その優れた特性を生かして、飲・食用の缶材を初め
として様々の成形加工用途に利用することができる。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an Al alloy sheet for draw forming, and particularly to continuous casting using an Al alloy containing Mn and Mg as alloying elements, followed by hot rolling and further cold rolling. In producing an Al alloy sheet by rolling, by regulating the cooling rate during continuous casting and after hot rolling, by performing continuous intermediate annealing at an appropriate temperature during the cold rolling step after hot rolling, , Strength, baking paint curability, and draw formability. The Al alloy plate obtained according to the present invention can be utilized for various forming applications including can materials for drinking and eating by taking advantage of its excellent characteristics.
【０００２】[0002]
【従来の技術】たとえば食料用缶や飲料用缶などとして
使用される成形用Ａｌ合金板の製法として従来から一般
的に実施されているのは、半連続鋳造法等によって製造
した鋳塊に面削処理や均質化熱処理を施した後、熱間圧
延、冷間圧延、焼鈍等を順次行なう方法であり、この様
な工程を経て製造される従来の成形用Ａｌ合金板は絞り
成形性が良好であると共に、ある程度の強度も備えてお
り、需要者の要求を一応満足している。2. Description of the Related Art A conventional method for producing an Al alloy sheet for forming, which is used as, for example, food cans and beverage cans, has been generally practiced so far since it is used for ingots produced by a semi-continuous casting method or the like. This is a method of sequentially performing hot rolling, cold rolling, annealing, etc. after subjecting to cutting treatment and homogenizing heat treatment, and the conventional forming Al alloy plate manufactured through such steps has good draw formability. In addition, it also has a certain level of strength, and satisfies the demands of consumers for the time being.
【０００３】ところが近年における需要者の要求は一段
と厳しくなってきており、軽量化を増進するため更に高
い強度を求める傾向があるばかりでなく、成形性におい
ても一層の向上が望まれており、更には生産性向上によ
るコストダウンの要求も次第に高まってきている。However, in recent years, the demands of consumers have become more severe, and there is a tendency not only to demand higher strength in order to promote weight reduction, but further improvement in moldability is also desired. The demand for cost reduction by improving productivity is gradually increasing.
【０００４】こうした要望に沿う比較的新しいＡｌ合金
板製造技術として、連続鋳造により移動帯板とした後直
ちに圧延工程に送って熱間圧延および冷間圧延を行なう
手法（以下、連鋳・直送圧延法ということがある）を採
用し、面削や均質化熱処理を省略する方法が検討されて
いる（特開昭５５−２７４９７号、特公昭６２−５４１
８２号等）。この方法によれば、面削や均質化熱処理の
省略によるコストダウンが図れると共に、鋳造工程で過
飽和に固溶した固溶元素が均質化熱処理時に析出すると
いったことも起こらなくなるため、固溶強化による高強
度化も増進されるといった利点を得ることができる。As a relatively new Al alloy sheet manufacturing technique that meets such demands, a method of performing hot rolling and cold rolling by immediately sending to a rolling step after forming a moving strip by continuous casting (hereinafter referred to as continuous casting / direct rolling Method) and omitting chamfering and homogenizing heat treatment (Japanese Patent Laid-Open No. 55-27497, Japanese Patent Publication No. 62-541).
82). According to this method, it is possible to reduce costs by omitting chamfering and homogenization heat treatment, and to prevent solid-solution elements that are solid-soluted in supersaturation during the casting process from precipitating during homogenization heat treatment. It is possible to obtain an advantage that the strength is enhanced.
【０００５】こうした連鋳・直送圧延法を行なうときに
採用される連続鋳造法として現在実用化されているの
は、水冷式連続鋳造法（固定式の水冷式連鋳鋳型から板
状に成形されて出てくる連鋳片を冷却水で直接冷却固化
し、連続的に鋳造する方法）、ハンターエンジニアリン
グ社で開発された双ロール鋳造法（回転する一対の冷却
ロール間に溶湯を供給し、該ロール間で冷却固化するこ
とにより連続的に鋳造する方法）、ハザレー社で開発さ
れたベルト式連続鋳造法（可動式の２つのベルト状冷却
部材の間に溶湯を供給し、該ベルト間で冷却固化させな
がら連続的に板状に鋳造する方法）、スイス・アルミニ
ウム社で開発されたブロック式連続鋳造法（可動式の２
つのブロック状冷却部材の間に溶湯を供給し、該ブロッ
ク間で冷却固化させながら連続的に板状に鋳造する方
法）などである。The continuous casting method adopted at the time of performing such continuous casting / direct rolling method is currently put into practical use is a water-cooled continuous casting method (formed from a fixed water-cooled continuous casting mold into a plate shape). The continuous cast piece that comes out is directly cooled and solidified with cooling water and continuously cast), a twin roll casting method developed by Hunter Engineering Co., Ltd. (the molten metal is supplied between a pair of rotating cooling rolls, Continuous casting method by cooling and solidifying between rolls), belt-type continuous casting method developed by Hatherley Co., Ltd. (supplying molten metal between two movable belt-shaped cooling members and cooling between the belts) Continuous solid plate casting while solidifying), Block type continuous casting method (movable type 2) developed by Swiss Aluminum Co.
A method of supplying a molten metal between two block-shaped cooling members and continuously casting in a plate shape while cooling and solidifying between the blocks).
【０００６】[0006]
【発明が解決しようとする課題】ところが現在実用化さ
れている連鋳・直送圧延法では、連続鋳造および熱間圧
延後に行なわれる冷間圧延工程で、加工割れなどを防止
するために３５０〜５００℃程度の比較的低温で中間焼
鈍が行なわれるが、この中間焼鈍工程で、過飽和固溶元
素の析出が起こり、最終冷間圧延製品の高強度化を阻害
するという問題が生じてくる。However, in the continuous casting / direct rolling method which has been put into practical use at present, in the cold rolling step performed after continuous casting and hot rolling, 350 to 500 is used in order to prevent work cracking or the like in the cold rolling step. Although intermediate annealing is performed at a relatively low temperature of about C, precipitation of supersaturated solid solution elements occurs in this intermediate annealing step, which causes a problem of hindering the strengthening of the final cold rolled product.
【０００７】本発明は、上記の様な従来技術の問題点に
着目してなされたものであって、その目的は、Ａｌ合金
を連続鋳造された移動帯板を熱間圧延温度以上に保持さ
れた状態で直ちに、あるいは熱間圧延温度に調整してか
ら熱間圧延し、更に冷間圧延を行なってＡｌ合金板を製
造する際において、特に連続鋳造、熱間圧延、冷間圧延
および中間焼鈍の一連の工程における過飽和固溶元素の
析出を可及的に抑制し、最終冷間圧延製品の強度を高め
ると共に、焼き付け塗装硬化性や絞り加工性においても
一層改善することのできる方法を確立しようとするもの
である。The present invention has been made by paying attention to the problems of the prior art as described above, and the purpose thereof is to keep a moving strip made of an Al alloy continuously cast at a temperature higher than the hot rolling temperature. Immediately or after adjusting the hot rolling temperature and then hot rolling, and then cold rolling to produce an Al alloy sheet, especially continuous casting, hot rolling, cold rolling and intermediate annealing. Let's establish a method that can suppress the precipitation of supersaturated solid solution elements in the series of steps as much as possible, enhance the strength of the final cold-rolled product, and further improve the baking coating hardenability and drawability. It is what
【０００８】[0008]
【課題を解決するための手段】上記課題を解決すること
のできた本発明に係る成形性Ａｌ合金板の製造方法の構
成は、 Ｍｎ：０．４〜１．５％ Ｍｇ：０．８〜２．５％ Ｃｕ：０．２５％以下（０％を含む） Ｚｎ：０．２５％以下（０％を含む） Ｆｅ：０．１〜１．０％ Ｓｉ：０．１〜１．０％ の要件を満たすＡｌ合金を、凝固時の冷却速度が Ｒ≧５で、且つＲ≧７．５（［Ｆｅ］＋［Ｓｉ］）＋２ 但し、Ｒ：凝固時の冷却速度（℃／ｓｅｃ） ［Ｆｅ］，［Ｓｉ］：Ａｌ合金中のＦｅ、Ｓｉの含有率
（％） を満足する条件で連続鋳造した後、該鋳片を熱間圧延温
度以上に保持された状態で直ちに、あるいは熱間圧延温
度以上に調整してから熱間圧延し、熱間圧延後１００℃
／分以上の速度で冷却し、次いで冷間圧延と５００℃〜
固相線温度での連続中間焼鈍を行ない、更に冷間圧延す
るところに要旨を有するものである。[Means for Solving the Problems] The structure of the method for producing a formable Al alloy sheet according to the present invention, which was able to solve the above problems, is as follows: Mn: 0.4-1.5% Mg: 0.8-2 0.5% Cu: 0.25% or less (including 0%) Zn: 0.25% or less (including 0%) Fe: 0.1 to 1.0% Si: 0.1 to 1.0% For an Al alloy satisfying the requirements, the cooling rate during solidification is R ≧ 5 and R ≧ 7.5 ([Fe] + [Si]) + 2, where R is the cooling rate during solidification (° C./sec) [Fe ], [Si]: after continuous casting under conditions satisfying the content ratio (%) of Fe and Si in the Al alloy, the slab is immediately or hot rolled in a state where it is kept at a hot rolling temperature or higher. After hot-rolling after adjusting the temperature above 100 ℃ after hot-rolling
Per minute or more, followed by cold rolling and 500 ° C-
The main point is that continuous intermediate annealing is performed at the solidus temperature and further cold rolling is performed.
【０００９】本発明は上記構成を基本思想とするが、こ
の発明の実施について好ましい態様あるいは変形態様を
更に具体化して示すと、下記の通りである。 １．連続鋳造法としては、水冷式連続鋳造法、双ロール
式連続鋳造法、ベルト式連続鋳造法、ブロック式連続鋳
造法などを採用することができるが、連続鋳造から熱間
圧延工程への移行時期は、鋳片内部が固相線温度以下に
まで低下して完全に凝固した後にタイミングを合わせる
のが好ましい。 ２．連続鋳造後に行なわれる熱間圧延の開始温度は３５
０〜５５０℃の範囲が好ましい。 ３．連続鋳造では、通常４〜３０ｍｍ程度の肉厚の板状
鋳片が連続的に製造され、これを熱間圧延によって１〜
５ｍｍ程度に圧延した後、冷間圧延によって０．１〜１
ｍｍ程度の肉厚のＡｌ合金板に圧延される。 ４．本発明は、連続鋳造の後直ちに熱間圧延し、引き続
いて、若しくは一旦巻き取った後、冷間圧延工程へ送る
方法に適用されるが、この他、連続鋳造の後鋳片を一旦
冷却保持して、熱間圧延温度以上に調整してから熱間圧
延を行ない、次いで冷間圧延工程へ送る方法にも適用す
ることができる。 ５．本発明は、連続鋳造して得られる移動帯板の温度を
保持して直ちに熱間圧延し、引き続いて、若しくは一旦
巻き取ってから冷間圧延工程へ送る所謂連鋳・直送圧延
方法に有利に適用されるが、この他連続鋳造の後、一旦
保持し、鋳片温度が実質的に降下しないうちに熱間圧延
へ送り、更に冷間圧延を行なう方法にも適用することが
できる。The present invention is based on the above-mentioned structure as a basic idea, and the preferred embodiment or modified embodiment of the present invention will be described in more detail below. 1. As the continuous casting method, a water-cooled continuous casting method, a twin roll type continuous casting method, a belt type continuous casting method, a block type continuous casting method, etc. can be adopted, but the transition time from the continuous casting to the hot rolling step It is preferable to adjust the timing after the inside of the slab has fallen below the solidus temperature and has completely solidified. 2. The starting temperature of hot rolling performed after continuous casting is 35
The range of 0-550 degreeC is preferable. 3. In continuous casting, a plate-shaped slab with a wall thickness of about 4 to 30 mm is usually continuously produced, and 1 to 1 is obtained by hot rolling.
After rolling to about 5 mm, 0.1 to 1 by cold rolling
It is rolled into an Al alloy plate having a thickness of about mm. 4. INDUSTRIAL APPLICABILITY The present invention is applied to a method in which hot rolling is performed immediately after continuous casting, and subsequently or once wound, and then sent to a cold rolling step. Then, it can be applied to a method in which hot rolling is performed after adjusting the hot rolling temperature or higher, and then sent to the cold rolling step. 5. INDUSTRIAL APPLICABILITY The present invention is advantageous in a so-called continuous casting / direct feed rolling method in which the temperature of a moving strip obtained by continuous casting is maintained and immediately hot-rolled, and subsequently or once wound and then sent to a cold rolling step. Other than the above, the method may be applied to a method in which after continuous casting, the temperature is once held, sent to hot rolling before the slab temperature is substantially lowered, and further cold rolled.
【００１０】[0010]
【作用】上記の様に本発明では、使用するＡｌ合金の成
分組成を規定すると共に、連続鋳造を行なう時の冷却速
度を規定すると共に、その後直ちに、あるいは一旦保持
し鋳片温度が実質的に降下しないうちに熱間圧延を行な
ってから所定の速度で冷却し、次いで冷間圧延、適正な
温度条件での連続中間焼鈍、更に冷間圧延を行なうこと
により、過飽和固溶元素の析出を抑制し、たとえ析出し
たとしても微細均一に析出させることによって、冷間圧
延製品の高強度化を達成すると共に、その後に行なわれ
る焼き付け塗装熱処理後の耐力を高め、更には深絞り成
形性等においても一段と優れたＡｌ合金板を得ることに
成功したものである。以下、本発明で定めるＡｌ合金の
成分組成および冷間圧延工程で行なわれる中間焼鈍条件
などを含めた製造条件について詳細に説明する。まず、
本発明で使用するＡｌ合金の成分組成を定めた理由を説
明する。As described above, in the present invention, the component composition of the Al alloy to be used is defined and the cooling rate at the time of continuous casting is defined. Suppress precipitation of supersaturated solid solution elements by performing hot rolling before lowering, cooling at a specified rate, then cold rolling, continuous intermediate annealing under appropriate temperature conditions, and cold rolling However, even if it precipitates, it is possible to increase the strength of the cold-rolled product by finely and uniformly precipitating it, enhance the proof stress after the subsequent baking coating heat treatment, and further in terms of deep drawing formability, etc. This succeeded in obtaining a more excellent Al alloy plate. Hereinafter, the compositional composition of the Al alloy defined in the present invention and the manufacturing conditions including the intermediate annealing conditions performed in the cold rolling process will be described in detail. First,
The reason for defining the component composition of the Al alloy used in the present invention will be described.
【００１１】Ｍｎ：０．４〜１．５％ Ｍｎは固溶強化元素としてＡｌ合金板の強度を高めるの
に欠くことのできない元素であるばかりでなく、Ａｌ−
Ｍｎ系もしくはＡｌ−Ｆｅ−Ｍｎ系晶出物の生成によっ
てしごき加工性を高める作用も有しており、これらの作
用を有効に発揮させるには少なくとも０．４％以上含有
させなければならない。しかしながら多くなり過ぎる
と、固溶しきれないＭｎ量の増大により成形性（絞り、
しごき、張り出し性、フランジ性等）を却って悪化させ
る傾向が現れてくるので、１．５％以下に抑えなければ
ならない。Ｍｎ含有率の好ましい下限値は０．８％、よ
り好ましくは１．１％、好ましい上限値は１．４％であ
る。Mn: 0.4-1.5% Mn is not only an element which is indispensable for enhancing the strength of the Al alloy plate as a solid solution strengthening element, but also Al-
It also has the effect of enhancing the ironing workability by forming Mn-based or Al-Fe-Mn-based crystallized substances, and at least 0.4% or more must be contained in order to exert these effects effectively. However, if the amount is too large, the formability (drawing, drawing,
Since ironing, overhanging property, flangeability, etc.) tend to worsen, it must be kept below 1.5%. The preferable lower limit of the Mn content is 0.8%, more preferably 1.1%, and the preferable upper limit is 1.4%.
【００１２】Ｍｇ：０．８〜２．５％以下 Ｍｇも、固溶強化元素として作用すると共に、Ａｌ−Ｍ
ｇ系もしくはＡｌ−Ｍｇ−Ｃｕ系晶出物の生成によって
強度を高める作用を有しており、本発明で意図するレベ
ルの強度を確保するには０．８％以上含有させなければ
ならない。しかしながら含有量が多過ぎると、Ｍｎの場
合と同様に固溶しきれないＭｇ量の増大によって成形性
を悪化させるので、２．５％以下に抑えなければならな
い。Ｍｇ含有率の好ましい下限値は１．３％、より好ま
しくは１．６％、好ましい上限値は２．４％である。Mg: 0.8 to 2.5% or less Mg also acts as a solid solution strengthening element, and Al-M
It has the effect of increasing the strength by forming g-type or Al-Mg-Cu-type crystallized substances, and must be contained in an amount of 0.8% or more in order to secure the level of strength intended in the present invention. However, if the content is too large, the formability deteriorates due to an increase in the amount of Mg that is not completely dissolved, as in the case of Mn, so it must be suppressed to 2.5% or less. The preferable lower limit of the Mg content is 1.3%, more preferably 1.6%, and the preferable upper limit thereof is 2.4%.
【００１３】Ｃｕ：０．２５％以下 Ｃｕは必ずしも必須というわけではないが、Ａｌ−Ｍｇ
−Ｃｕ系晶出物の生成によって強度を高める作用を有し
ているので、強度に対する要求度が高い場合には積極的
に含有させることが望ましい。しかし、多過ぎると成形
性に悪影響が現れてくるので０．２５％以下に抑えなけ
ればならない。強度と成形性のバランスを考えてより好
ましいＣｕの含有率は０．１５〜０．２０％の範囲であ
る。Cu: 0.25% or less Cu is not always essential, but Al-Mg
Since it has the effect of increasing the strength by the formation of the Cu-based crystallized substance, it is desirable to positively add it when the demand for the strength is high. However, if it is too large, the formability is adversely affected, so it must be suppressed to 0.25% or less. Considering the balance between strength and formability, a more preferable Cu content is in the range of 0.15 to 0.20%.
【００１４】Ｚｎ：０．２５％以下 Ｚｎも必須の成分ではないが、適量含有させることによ
って絞りやしごき等の成形性を高める作用を有してお
り、特に過酷な成形条件が加えられる用途に使用する場
合は少量含有させることが好ましい。しかし、多過ぎる
と成形性が悪くなる傾向が現れてくるばかりでなくコス
ト的にも不利であるので、含有させる場合でも０．２５
％以下に抑えなければならない。Ｚｎのより好ましい含
有率は０．１６〜０．２２％の範囲である。Zn: 0.25% or less Zn is not an essential component, but it has an effect of enhancing the formability such as drawing and ironing by containing an appropriate amount, and is particularly suitable for applications where severe molding conditions are added. When used, it is preferably contained in a small amount. However, if the amount is too large, not only the moldability tends to deteriorate, but it is also disadvantageous in terms of cost.
% Must be kept below. The more preferable content rate of Zn is 0.16 to 0.22%.
【００１５】Ｆｅ：０．１〜１．０％、Ｓｉ：０．１〜
１．０％ これらの元素は成形性や強度を一段と高める元素として
有効である。即ちＦｅは、Ａｌ−Ｍｎ−Ｆｅ系晶出物を
生成して成形時の肌荒れ防止作用を発揮すると共にしご
き加工性を高める作用があり、０．１％以上含有させる
必要がある。しかし多過ぎると、鋳造時に粗大晶出物が
生成して成形性を悪化させるので１．０％を上限とす
る。またＳｉは、Ｍｇ2 Ｓｉ系の微細な析出物を生成し
て高強度化に寄与するもので、少なくとも０．１％以上
含有させなければならないが、多過ぎると、Ｓｉが単体
として析出して成形性に悪影響が現れてくるので１．０
％を上限とする。これらの利害得失を考慮して、Ｆｅの
より好ましい含有率は０．１〜０．８％、Ｓｉのより好
ましい含有率は０．１〜０．６％の範囲である。Fe: 0.1 to 1.0%, Si: 0.1
1.0% These elements are effective as elements that further improve the formability and strength. That is, Fe has an effect of forming an Al—Mn—Fe-based crystallized substance to prevent rough skin during molding and also has an effect of enhancing ironing workability, and it is necessary to contain 0.1% or more. However, if it is too large, coarse crystallized substances are formed during casting to deteriorate the formability, so 1.0% is made the upper limit. Further, Si forms fine Mg 2 Si-based precipitates and contributes to strengthening, and it must be contained at least 0.1% or more, but if it is too much, Si precipitates as a simple substance. 1.0 because the formability is adversely affected
% Is the upper limit. Considering these advantages and disadvantages, the more preferable Fe content is 0.1 to 0.8%, and the more preferable Si content is 0.1 to 0.6%.
【００１６】本発明におけるＡｌ合金の残部成分はＡｌ
と不可避不純物からなるものであり、不可避不純物とし
てはＮｉ，Ｃｒ，Ｖ，Ｔｉ，Ｚｒ，Ｌｉ等が例示される
が、それらは不可避不純物量である限り、本発明で意図
する性能を確保する上で格別の障害になることはない。
次に、上記Ａｌ合金を用いた連続鋳造、熱間圧延、冷間
圧延などの各条件について説明する。The balance component of the Al alloy in the present invention is Al
And unavoidable impurities such as Ni, Cr, V, Ti, Zr, Li, etc., but as long as the amount is an unavoidable impurity, it is necessary to ensure the performance intended in the present invention. It doesn't hinder you.
Next, each condition such as continuous casting using the above Al alloy, hot rolling, cold rolling will be described.
【００１７】本発明では、上記成分組成の要件を満足す
るＡｌ合金を使用し、凝固時の冷却速度が下記（１），
（２）式 Ｒ≧７．５（［Ｆｅ］＋［Ｓｉ］）＋２……（１） Ｒ≧５……（２） 但し、Ｒ：凝固時の冷却速度（℃／ｓｅｃ） ［Ｆｅ］，［Ｓｉ］：Ａｌ合金中のＦｅ、Ｓｉの含有率
（％） を同時に満足する条件で連続鋳造した後、該鋳片を熱間
圧延温度以上に保持された状態で直ちに、あるいは熱間
圧延温度以上に調整してから熱間圧延し、熱間圧延後１
００℃／分以上の速度で冷却し、次いで冷間圧延と５０
０℃〜固相線温度での連続中間焼鈍を行ない、更に冷間
圧延するところに製法として最大の特徴を有している。In the present invention, an Al alloy satisfying the above-mentioned compositional requirements is used, and the cooling rate at the time of solidification is (1)
(2) Formula R ≧ 7.5 ([Fe] + [Si]) + 2 (1) R ≧ 5 (2) where R: cooling rate during solidification (° C./sec) [Fe], [Si]: After continuous casting under the condition that the content ratios (%) of Fe and Si in the Al alloy are simultaneously satisfied, immediately or in a state in which the slab is kept at a hot rolling temperature or higher, or a hot rolling temperature. After the above adjustment, hot rolling is performed, and after hot rolling, 1
Cool at a rate of 00 ° C / min or more, then cold-roll and 50
The greatest characteristic of the manufacturing method is that continuous intermediate annealing is performed at 0 ° C to the solidus temperature and further cold rolling is performed.
【００１８】即ち従来例では、先に記載した様に熱間圧
延後の冷間圧延工程で、加工性を高めるため通常５００
℃未満の比較的低温で短時間の中間焼鈍を行なっている
が、この方法では、連続鋳造および熱間圧延後の冷却過
程や中間焼鈍工程で過飽和固溶元素の析出が起こり、固
溶強化効果が不十分になって最終製品の高強度化が阻害
されると共に、絞り成形性にも悪影響を及ぼす。ところ
が、上記の様に連続鋳造時の冷却速度および熱間圧延後
の冷却速度を規定すると共に、冷間圧延工程中に５００
〜固相線温度の範囲で連続中間焼鈍を行なってやれば、
鋳造時および中間焼鈍時における過飽和固溶元素の析出
が抑制され、固溶強化効果が有効に発揮されて高強度化
が達成されると共に、固溶元素の増大によって焼き付け
塗装硬化性も高められる。更には立方体方位も増加する
ため、最終冷間圧延製品の成形性が向上し、特に耳率を
著しく低減することが可能となる。That is, in the conventional example, in order to improve the workability in the cold rolling step after the hot rolling as described above, it is usually 500.
Although intermediate annealing is performed for a short time at a relatively low temperature of less than ℃, in this method, precipitation of supersaturated solid solution elements occurs in the cooling process and intermediate annealing process after continuous casting and hot rolling, and the solid solution strengthening effect Becomes insufficient, which hinders the increase in strength of the final product, and adversely affects the drawability. However, as described above, the cooling rate during the continuous casting and the cooling rate after the hot rolling are specified, and the cooling rate during the cold rolling process is 500%.
~ If you perform continuous intermediate annealing in the range of solidus temperature,
Precipitation of a supersaturated solid solution element during casting and during intermediate annealing is suppressed, the solid solution strengthening effect is effectively exhibited, and high strength is achieved, and the increase in the solid solution element also enhances the baking coating curability. Furthermore, since the cubic orientation also increases, the formability of the final cold-rolled product is improved, and the ear ratio can be significantly reduced.
【００１９】まず本発明者等が確認したところによる
と、最終圧延製品の強度や絞り加工性は、Ａｌ合金中に
含まれるＦｅおよびＳｉの含有率をパラメータとして連
続鋳造時の冷却速度をうまくコントロールすることによ
って著しく高められ、該凝固時の冷却速度が前記（１）
式と（２）式を同時に満たす様に設定することが重要で
あることを知った。しかして最終圧延製品の前記特性に
は、連続鋳造工程とその後の圧延並びに中間焼鈍条件が
影響するが、特にＡｌ合金中のＦｅおよびＳｉは連続鋳
造時に粗大晶出物を生じる原因となり、それらは最終圧
延製品の前述の様な特性に悪影響を及ぼす。ところが、
連続鋳造時の冷却速度を前記（１）式と（２）式の条件
を満たす様に設定してやれば、ＦｅやＳｉに由来する粗
大晶出物の生成が阻止され、その後の圧延時の連続中間
焼鈍条件の設定とも相まって、最終圧延製品の前記特性
を著しく高めることができるのである。First, the inventors of the present invention have confirmed that the strength and drawability of the final rolled product are well controlled by controlling the cooling rate during continuous casting with the content ratios of Fe and Si contained in the Al alloy as parameters. The cooling rate during solidification is significantly increased by the above (1)
I learned that it is important to set so that the formula and the formula (2) are satisfied at the same time. However, the above properties of the final rolled product are affected by the continuous casting step and the subsequent rolling and intermediate annealing conditions. Especially, Fe and Si in the Al alloy cause coarse crystallized substances during continuous casting, and they are The above-mentioned properties of the final rolled product are adversely affected. However,
If the cooling rate during continuous casting is set so as to satisfy the conditions of the above formulas (1) and (2), the formation of coarse crystallized substances derived from Fe and Si is prevented, and the continuous intermediate during rolling thereafter. Together with the setting of annealing conditions, the above-mentioned characteristics of the final rolled product can be remarkably enhanced.
【００２０】尚、上記条件式（１），（２）で示される
推奨範囲は、図１に示される如く、［Ｆｅ］＋［Ｓｉ］
の値が０．４％超のときは式（１）によって、また［Ｆ
ｅ］＋［Ｓｉ］の値が０．４％以下のときは式（２）に
よって規定されることを意味する。ちなみに、凝固時の
冷却速度が前記要件を外れる場合は、連続鋳造組織中に
ＦｅやＳｉに由来する粗大な晶出物が生成し、それらが
その後の圧延および連続中間焼鈍工程でも残存して強度
や加工性に悪影響を及ぼすことになる。The recommended range represented by the conditional expressions (1) and (2) is [Fe] + [Si] as shown in FIG.
When the value of is more than 0.4%, it is calculated by the formula (1), and [F
When the value of e] + [Si] is 0.4% or less, it means that it is defined by the equation (2). By the way, if the cooling rate during solidification deviates from the above requirements, coarse crystallized substances derived from Fe and Si are generated in the continuous casting structure, and they remain in the subsequent rolling and continuous intermediate annealing steps to improve the strength. And workability will be adversely affected.
【００２１】また、上記連続鋳造の後は直ちに、或は鋳
片温度が実質的に降下しないうちに熱間圧延を行ない、
この熱間圧延後は１００℃／分以上の速度で冷却するこ
とが必要となる。しかして、該冷却速度が１００℃／分
未満の低速になると、熱間圧延後の冷却過程で過飽和固
溶体の析出が起こり、固溶強化による高強度化の目的が
達成できなくなるからである。Further, hot rolling is carried out immediately after the above continuous casting or before the slab temperature substantially drops.
After this hot rolling, it is necessary to cool at a rate of 100 ° C./min or more. However, if the cooling rate becomes lower than 100 ° C./min, precipitation of a supersaturated solid solution occurs in the cooling process after hot rolling, and the purpose of strengthening by solid solution strengthening cannot be achieved.
【００２２】更に、その後の冷間圧延時に行なわれる連
続中間焼鈍温度を５００℃〜固相線温度の範囲と定めた
のは、５００℃未満の低温では、飽和固溶元素の析出を
十分に防止できなくなって高強度化が達成されなくなる
ばかりでなく、焼き付け塗装硬化性や成形性も十分に上
がらなくなるからである。尚、この連続中間焼鈍後は、
１００℃／分以上の冷却速度で５０〜１００℃程度まで
冷却することが好ましい。Furthermore, the reason why the continuous intermediate annealing temperature performed during the subsequent cold rolling is set in the range of 500 ° C. to the solidus temperature is that the precipitation of the saturated solid solution element is sufficiently prevented at a low temperature of less than 500 ° C. This is because not only cannot it be achieved but high strength cannot be achieved, but also the curing property for baking coating and the moldability cannot be sufficiently improved. After this continuous intermediate annealing,
It is preferable to cool to about 50 to 100 ° C. at a cooling rate of 100 ° C./minute or more.
【００２３】本発明では、上記の様に連続鋳造時および
熱間圧延後の冷却速度を規定すると共に、熱間圧延後に
行なわれる冷間圧延時における連続中間焼鈍温度を高め
に設定したところに最大の特徴を有するものであり、そ
の他の条件には格別の制限はないが、その他の好ましい
条件等について説明すると下記の通りである。In the present invention, the cooling rate during continuous casting and after hot rolling is specified as described above, and the maximum value is set when the continuous intermediate annealing temperature during cold rolling performed after hot rolling is set higher. Other conditions are not particularly limited, but other preferable conditions and the like will be described below.
【００２４】本発明は、連続鋳造の後移動帯板の温度を
熱間圧延温度以上に保持した状態で直ちに熱間圧延し、
あるいは該連鋳片を熱間圧延温度以上に調整してから熱
間圧延し、引き続いて、若しくは一旦巻き取ってから冷
間圧延工程へ送る方法（連鋳・直送圧延法）に適用され
るものであり、それにより、連続鋳造後一旦巻き取り、
冷却してから熱間圧延を行なう方法に比べて熱ロスが少
なく、且つ生産性を高める上でも効果的である。尚、こ
こで採用される連続鋳造法としては、前記した様な水冷
式連続鋳造法、双ロール式連続鋳造法、ベルト式連続鋳
造法、ブロック式連続鋳造法などを適宜選択して採用す
ることができる。According to the present invention, after continuous casting, hot rolling is performed immediately while maintaining the temperature of the moving strip at a temperature equal to or higher than the hot rolling temperature.
Alternatively, it is applied to a method (continuous casting / direct feed rolling method) in which the continuous cast slab is adjusted to a hot rolling temperature or higher and then hot rolled, and subsequently or once wound and then sent to a cold rolling step. Therefore, after continuous casting, once wound up,
Compared with the method of performing hot rolling after cooling, it has less heat loss, and is also effective in increasing productivity. As the continuous casting method adopted here, a water-cooled continuous casting method, a twin roll continuous casting method, a belt continuous casting method, a block continuous casting method or the like as described above may be appropriately selected and used. You can
【００２５】連続鋳造後に行なわれる熱間圧延の開始温
度は３５０〜５５０℃、より好ましくは４００〜５００
℃の範囲であり、また熱間圧延終了温度は１５０〜２８
０℃、より好ましくは２１０〜２６０℃の範囲である。
また本発明を実施するに当たっては、連続鋳造によって
通常４〜３０ｍｍ程度の肉厚の板状鋳片を連続的に製造
し、これを直ちに熱間圧延することにより肉厚を１〜５
ｍｍとし、更に冷間圧延することによって０．１〜１ｍ
ｍ程度の肉厚のＡｌ合金製品板が製造される。The starting temperature of hot rolling performed after continuous casting is 350 to 550 ° C., more preferably 400 to 500.
And the hot rolling finish temperature is 150 to 28
It is 0 ° C., and more preferably 210 to 260 ° C.
Further, in carrying out the present invention, a plate-shaped slab having a wall thickness of about 4 to 30 mm is usually continuously produced by continuous casting, and immediately hot-rolled to obtain a wall thickness of 1 to 5
mm to 0.1 to 1 m by cold rolling.
An Al alloy product plate having a wall thickness of about m is manufactured.
【００２６】上記の様に本発明では、連続鋳造時および
熱間圧延後の冷却速度を規定すると共に、熱間圧延後に
行なわれる冷間圧延時に適正な温度条件で連続中間焼鈍
を行なうところに製法としての最大の特徴を有するもの
であり、その特徴は、殊に中間焼鈍温度を高めに設定す
ることによる飽和固溶元素の析出防止効果は、前記従来
技術の項でも詳述した様に連鋳・直送圧延法を適用した
ときにより効果的に発揮されるが、この方法の他にも、
連続鋳造の後、一旦保持し該鋳片温度が実質的に降下し
ないうちに熱間圧延および冷間圧延工程へ送る方法に適
用した場合においても享受できる。As described above, in the present invention, the cooling rate during continuous casting and after hot rolling is regulated, and continuous intermediate annealing is performed under appropriate temperature conditions during cold rolling performed after hot rolling. It has the greatest feature as, that is, the effect of preventing the precipitation of the saturated solid solution element by setting the intermediate annealing temperature to a high value is continuous casting as described in detail in the section of the prior art.・ It is more effective when the direct rolling method is applied.
It can also be enjoyed when applied to a method in which after continuous casting, the temperature is once held and sent to the hot rolling and cold rolling steps before the slab temperature substantially drops.
【００２７】[0027]
【実施例】次に本発明の実施例を示すが、本発明はもと
より下記実施例によって制限を受けるものではなく、前
後記の趣旨に適合し得る範囲で適当に変更を加えて実施
することも勿論可能であり、それらはいずれも本発明の
技術的範囲に含まれる。EXAMPLES Next, examples of the present invention will be shown, but the present invention is not limited by the following examples, and may be carried out with appropriate modifications within a range compatible with the gist of the preceding and following description. Of course, it is possible, and all of them are included in the technical scope of the present invention.
【００２８】実施例 表１に示す化学組成のＡｌ合金を溶解した後、凝固時の
冷却速度が１２℃／ｓｅｃの速度で２０ｍｍの板厚に連
続鋳造して移動帯板とし、その後直ちに圧延開始温度を
４５０℃、終了温度を２６０℃として直送熱間圧延を行
なって３ｍｍ厚の熱延板を作製した。尚、熱間圧延後の
冷却には水ミスト噴霧を採用し、２００℃／分の冷却速
度を確保した。その後、１ｍｍまで冷間圧延し、急速加
熱により５３０℃まで昇温してから１分間の連続中間焼
鈍を行なった後急速冷却し、更に冷間圧延を行なって厚
さ０．３ｍｍのＡｌ冷延板を得た。Example After melting an Al alloy having the chemical composition shown in Table 1, a continuous strip was cast at a plate thickness of 20 mm at a cooling rate of 12 ° C./sec at the time of solidification to form a moving strip, and immediately thereafter, rolling was started. Direct feed hot rolling was performed at a temperature of 450 ° C. and an end temperature of 260 ° C. to produce a hot rolled sheet having a thickness of 3 mm. Incidentally, water mist spraying was adopted for cooling after hot rolling to secure a cooling rate of 200 ° C./min. After that, cold rolling is performed to 1 mm, the temperature is raised to 530 ° C. by rapid heating, 1 minute of continuous intermediate annealing is performed, and then rapid cooling is performed, and further cold rolling is performed to perform cold rolling of 0.3 mm thick Al. I got a plate.
【００２９】得られた各Ａｌ合金冷延板について、深絞
り試験（絞り率：４０％）を行なって耳率を測定した。
また、冷間仕上り材および２００℃×２０分の焼き付け
塗装熱処理材の引張試験を行なった。A deep drawing test (drawing ratio: 40%) was performed on each of the obtained Al alloy cold-rolled sheets to measure the ear ratio.
Further, a tensile test was conducted on the cold finished material and the heat-treated material for baking and coating at 200 ° C. for 20 minutes.
【００３０】耳率：板の異方性のために深絞りの際に対
称に生じる波型の突起の程度をいい ［（山の平均高さ）ー（谷の平均高さ）］／（谷の平均
高さ）×１００％ で表される。圧延方向に対して０〜９０°方向に耳
（山）がある場合は０〜９０°耳、圧延方向に対して４
５°方向に耳（山）がある場合は４５°耳と称される。 ０．２％耐力（Ａｓ耐力及びＡＢ耐力）：ＪＩＳ Ｚ
２２４１に準拠Ear ratio: The degree of corrugated protrusions that are symmetrically produced during deep drawing due to plate anisotropy [(average height of peaks)-(average height of valleys)] / (valleys It is expressed by the average height of 100 × 100%. If there are ears (mountains) in the 0 to 90 ° direction to the rolling direction, 0 to 90 ° ears, 4 to the rolling direction
When there is an ear (mountain) in the 5 ° direction, it is called a 45 ° ear. 0.2% yield strength (As yield strength and AB yield strength): JIS Z
2241 compliant
【００３１】結果は表１に併記する通りであり、Ａｌ合
金の成分組成が本発明の規定要件に合致する実施例（Ｎ
ｏ．１〜３）は、いずれも耳率が小さく且つＡｓ耐力及
びＡＢ耐力のいずれにおいても良好な結果が得られてい
る。これらに対し、連続鋳造時の冷却速度および冷間圧
延工程で行われる連続中間焼鈍は適正であるにもかかわ
らず、Ａｌ合金組成が本発明の規定要件を外れる比較例
（Ｎｏ．４〜８）は、概して４５°耳率が大きく、また
耳率の比較的低いものはＡｓ耐力およびＡＢ耐力が低い
ことが分かる。The results are shown in Table 1 together, and the results are shown in Examples (N) in which the component composition of the Al alloy meets the specified requirements of the present invention.
o. All of 1 to 3) have small ear ratios and good results are obtained in both As proof stress and AB proof stress. On the other hand, although the cooling rate at the time of continuous casting and the continuous intermediate annealing performed in the cold rolling process are proper, the Al alloy composition is out of the prescribed requirements of the present invention (Nos. 4 to 8). It can be seen that generally has a high 45 [deg.] Ear rate, and those with a relatively low ear rate have low As proof stress and AB proof stress.
【００３２】[0032]
【表１】 [Table 1]
【００３３】次に、表２に示す化学組成のＡｌ合金を溶
解した後、表２に示す凝固時の冷却速度で２０ｍｍの板
厚に連続鋳造して移動帯板とし、これを直ちに熱間圧延
開始温度を４５０℃、終了温度を２６０℃に設定して直
送熱間圧延を行ない、２００℃／分の速度で冷却して３
ｍｍ厚の熱延板を作製した。その後１ｍｍまで冷間圧延
し、急速加熱して５３０℃で１分間保持した後に急冷
し、更に冷間圧延を行なって０．３ｍｍの冷延板を得
た。この板の断面顕微鏡観察によって不溶性化合物の平
均粒子径を測定すると共に、上記と同様にしてＡｓ耐力
を測定し、また応力−歪曲線から引張破断に要する単位
体積当たりの仕事量を求め、靭性の指標とした。結果は
表２に併記する通りであり、本発明の規定要件を満たす
実施例（Ｎｏ．９〜１１）は、いずれも不溶性化合物が
微細であり、Ａｓ耐力および仕事量のいずれにおいても
良好な結果が得られている。これに対し、本発明で定め
る要件のいずれかを欠く比較例（Ｎｏ．１２〜１８）で
は、平均粒径が粗大で仕事量の値が小さく靭性が不良で
あるか、あるいはＡｓ耐力が不十分であることが分か
る。Next, the Al alloy having the chemical composition shown in Table 2 was melted, and then continuously cast at a plate thickness of 20 mm at a cooling rate during solidification shown in Table 2 to obtain a moving strip plate, which was immediately hot rolled. Direct temperature hot rolling was performed by setting the starting temperature to 450 ° C and the ending temperature to 260 ° C, and cooling at a rate of 200 ° C / min.
A hot rolled sheet having a thickness of mm was produced. Then, it was cold-rolled to 1 mm, rapidly heated and held at 530 ° C. for 1 minute, then rapidly cooled, and further cold-rolled to obtain a 0.3 mm cold-rolled sheet. The average particle size of the insoluble compound was measured by observing the plate with a cross-section microscope, the As proof stress was measured in the same manner as above, and the work per unit volume required for tensile rupture was determined from the stress-strain curve to determine the toughness. It was used as an index. The results are shown in Table 2 together. In Examples (Nos. 9 to 11) satisfying the requirements of the invention, the insoluble compound was fine, and good results were obtained in both the As yield strength and the work amount. Has been obtained. On the other hand, in Comparative Examples (No. 12 to 18) lacking any of the requirements defined in the present invention, the average particle size is coarse, the value of the work amount is small, the toughness is poor, or the As proof stress is insufficient. It turns out that
【００３４】[0034]
【表２】 [Table 2]
【００３５】また、表３に示す化学組成のＡｌ合金を溶
解した後、凝固時の冷却速度が１２℃／ｓｅｃの速度で
２０ｍｍの板厚に連続鋳造し、その後直ちに圧延開始温
度を４５０℃、終了温度を２６０℃として直送熱間圧延
を行ない、その後直ちに表３に併記する冷却速度で冷却
して３ｍｍ厚の熱延板を作製した。尚、熱間圧延後の冷
却には水ミスト噴霧を採用した。但し、Ｎｏ．２７につ
いては、連続鋳造の後に一旦冷却して固化し、再加熱し
て５００℃×１２分間保持した後に熱間圧延を行なっ
た。次いで１ｍｍまで冷間圧延し、急速加熱して表３に
示す温度で１分間保持してから急冷し、更に冷間圧延を
行なって厚さ０．３ｍｍのＡｌ合金冷延板を得た。得ら
れた冷延板の耳率、Ａｓ耐力よびＡＢ耐力を上記と同様
にして測定し、表３に併記する結果を得た。After melting the Al alloys having the chemical compositions shown in Table 3, continuous casting was performed to a plate thickness of 20 mm at a cooling rate of 12 ° C./sec at the time of solidification, and immediately thereafter, the rolling start temperature was 450 ° C. Direct-feed hot rolling was performed at an end temperature of 260 ° C., and immediately thereafter, cooling was performed at the cooling rate shown in Table 3 to produce a hot-rolled sheet having a thickness of 3 mm. Water mist spray was used for cooling after hot rolling. However, No. Regarding No. 27, after continuous casting, it was once cooled and solidified, reheated and held at 500 ° C. for 12 minutes, and then hot rolled. Then, it was cold-rolled to 1 mm, rapidly heated, held at the temperature shown in Table 3 for 1 minute, then rapidly cooled, and further cold-rolled to obtain an Al alloy cold-rolled sheet having a thickness of 0.3 mm. The earring rate, As yield strength and AB yield strength of the obtained cold rolled sheet were measured in the same manner as above, and the results shown in Table 3 were obtained together.
【００３６】[0036]
【表３】 [Table 3]
【００３７】表３からも明らかである様に、本発明の規
定要件を全て満足する実施例（Ｎｏ．１９〜２２）は、
Ａｓ耐力、ＡＢ耐力および耳率のいずれにおいても比較
例に比べて良好な結果が得られている。As is clear from Table 3, the examples (Nos. 19 to 22) satisfying all the requirements of the present invention are:
Good results were obtained in all of the As proof stress, AB proof stress, and ear rate as compared with the comparative example.
【００３８】[0038]
【発明の効果】本発明は以上の様に構成されており、成
分組成の特定されたＡｌ合金を連続鋳造した後、該鋳片
を熱間圧延温度以上に保持された状態で直ちに、あるい
は熱間圧延温度に調整してから熱間圧延し、更に冷間圧
延を行なってＡｌ合金板を製造するに際し、特に連続鋳
造時および直送熱間圧延後の冷却速度を規定すると共
に、冷間圧延工程で行なわれる中間焼鈍時における過飽
和固溶元素の析出を可及的に抑制し、最終冷間圧延製品
の強度を高めると共に、焼き付け塗装硬化性や絞り加工
性も改善し、強度と成形性の両特性を満足するＡｌ合金
板を製造し得ることになった。EFFECTS OF THE INVENTION The present invention is configured as described above, and after continuously casting an Al alloy having a specified component composition, the cast slab is immediately or after being hot-rolled at a temperature higher than the hot rolling temperature. When an Al alloy sheet is manufactured by performing hot rolling after adjusting to the hot rolling temperature and then performing cold rolling, the cooling rate is particularly specified during continuous casting and after direct hot rolling, and the cold rolling step is performed. The precipitation of supersaturated solid solution elements during the intermediate annealing carried out in (4) is suppressed as much as possible, the strength of the final cold rolled product is increased, and the baking coating hardenability and drawability are also improved, and both strength and formability are improved. It has become possible to manufacture an Al alloy plate satisfying the characteristics.
【図１】本発明で実施される連続鋳造時の好ましい冷却
速度条件を示すグラフである。FIG. 1 is a graph showing preferable cooling rate conditions during continuous casting carried out in the present invention.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２２Ｃ 21/06 ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification code Internal reference number FI technical display location C22C 21/06
Claims (3)
る、以下同じ） Ｍｇ：０．８〜２．５％ Ｃｕ：０．２５％以下（０％を含む） Ｚｎ：０．２５％以下（０％を含む） Ｆｅ：０．１〜１．０％ Ｓｉ：０．１〜１．０％ の要件を満たすＡｌ合金を、凝固時の冷却速度が Ｒ≧５で、且つＲ≧７．５（［Ｆｅ］＋［Ｓｉ］）＋２ 但し、Ｒ：凝固時の冷却速度（℃／ｓｅｃ） ［Ｆｅ］，［Ｓｉ］：Ａｌ合金中のＦｅ、Ｓｉの含有率
（％） を満足する条件で連続鋳造した後、該鋳片温度を熱間圧
延温度以上に保持して熱間圧延し、熱間圧延後１００℃
／分以上の速度で冷却し、次いで冷間圧延と５００℃〜
固相線温度での連続中間焼鈍を行ない、更に冷間圧延す
ることを特徴とする強度に優れた絞り成形用Ａｌ合金板
の製造方法。1. Mn: 0.4 to 1.5% (meaning weight%; the same applies hereinafter) Mg: 0.8 to 2.5% Cu: 0.25% or less (including 0%) Zn: 0.25% or less (including 0%) Fe: 0.1-1.0% Si: 0.1-1.0% Al alloy satisfying the requirements, the cooling rate during solidification is R ≧ 5, And R ≧ 7.5 ([Fe] + [Si]) + 2, where R: cooling rate during solidification (° C./sec) [Fe], [Si]: Fe and Si content in Al alloy (%) ) Is continuously cast, and the slab temperature is hot-rolled at a temperature not lower than the hot-rolling temperature.
Per minute or more, followed by cold rolling and 500 ° C-
A method for producing an Al alloy sheet for draw forming having excellent strength, which comprises performing continuous intermediate annealing at a solidus temperature and further cold rolling.
延工程へ送る請求項１記載の製造方法。2. The manufacturing method according to claim 1, wherein the continuously cast moving strip is immediately sent to the hot rolling step.
上に調整して熱間圧延工程へ送る請求項１に記載の製造
方法。3. The manufacturing method according to claim 1, wherein the continuously cast slab is adjusted to a hot rolling temperature or higher and sent to a hot rolling step.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4726094A JPH07252615A (en) | 1994-03-17 | 1994-03-17 | Production of aluminum alloy sheet for drawing |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4726094A JPH07252615A (en) | 1994-03-17 | 1994-03-17 | Production of aluminum alloy sheet for drawing |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07252615A true JPH07252615A (en) | 1995-10-03 |
Family
ID=12770323
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4726094A Withdrawn JPH07252615A (en) | 1994-03-17 | 1994-03-17 | Production of aluminum alloy sheet for drawing |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07252615A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2016536465A (en) * | 2013-09-06 | 2016-11-24 | アルコア インコーポレイテッド | Aluminum alloy product and method for producing the product |
-
1994
- 1994-03-17 JP JP4726094A patent/JPH07252615A/en not_active Withdrawn
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2016536465A (en) * | 2013-09-06 | 2016-11-24 | アルコア インコーポレイテッド | Aluminum alloy product and method for producing the product |
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| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 20010605 |