JPH0327883A - Manufacture of aluminum alloy clad plate with crystal assembly azimuth controlled - Google Patents
Manufacture of aluminum alloy clad plate with crystal assembly azimuth controlledInfo
- Publication number
- JPH0327883A JPH0327883A JP16129189A JP16129189A JPH0327883A JP H0327883 A JPH0327883 A JP H0327883A JP 16129189 A JP16129189 A JP 16129189A JP 16129189 A JP16129189 A JP 16129189A JP H0327883 A JPH0327883 A JP H0327883A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- clad plate
- rolling
- alloy
- less
- 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.)
- Granted
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 31
- 239000013078 crystal Substances 0.000 title claims abstract description 28
- 238000004519 manufacturing process Methods 0.000 title claims description 12
- 238000005096 rolling process Methods 0.000 claims abstract description 29
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 16
- 239000000956 alloy Substances 0.000 claims abstract description 16
- 238000001953 recrystallisation Methods 0.000 claims abstract description 16
- 238000000034 method Methods 0.000 claims abstract description 12
- 239000002245 particle Substances 0.000 claims abstract description 8
- 239000006104 solid solution Substances 0.000 claims abstract 2
- 239000002244 precipitate Substances 0.000 claims description 13
- 239000000126 substance Substances 0.000 claims description 10
- 238000005275 alloying Methods 0.000 claims description 9
- 239000000654 additive Substances 0.000 claims description 5
- 230000000996 additive effect Effects 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims 2
- 238000001816 cooling Methods 0.000 abstract description 5
- 238000010791 quenching Methods 0.000 abstract description 4
- 230000000171 quenching effect Effects 0.000 abstract description 4
- 230000032683 aging Effects 0.000 abstract description 3
- 238000007711 solidification Methods 0.000 abstract description 2
- 230000008023 solidification Effects 0.000 abstract description 2
- 238000002425 crystallisation Methods 0.000 abstract 2
- 230000008025 crystallization Effects 0.000 abstract 2
- 230000003247 decreasing effect Effects 0.000 abstract 1
- 229910052782 aluminium Inorganic materials 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 6
- 238000005259 measurement Methods 0.000 description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000002791 soaking Methods 0.000 description 3
- 238000004544 sputter deposition Methods 0.000 description 3
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical compound F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 description 2
- 238000004220 aggregation Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 238000012937 correction Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000005477 sputtering target Methods 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
- 230000002747 voluntary effect Effects 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、異なった結晶集合方位をもつ板を重ね合せた
構造を有するアルミニウム合金クラッド板の製造方法に
関するものであり、スパッタリング用ターゲットに用い
ることができる。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a method for manufacturing an aluminum alloy clad plate having a structure in which plates having different crystal orientations are stacked, and is used as a sputtering target. be able to.
電子産業の発展とともに、ＩＣやＬＳＩの需要が増加し
ている。これ等の素子に用いられる配線は、高純度アル
ミニウムまたはその合金をターゲットとして、スパッタ
リングにより薄膜化して用いられるのが主である。With the development of the electronics industry, demand for ICs and LSIs is increasing. The wiring used in these devices is mainly made into a thin film by sputtering using high-purity aluminum or an alloy thereof as a target.
溶融金属の蒸発による蒸着注とは異なり、スパッタ法で
はターゲットの表面および内部の結晶構造がターゲット
からの原子の放出特性に大きな影響を与えることが知ら
れている。Unlike vapor deposition by evaporating molten metal, it is known that in the sputtering method, the surface and internal crystal structure of the target has a large effect on the characteristics of emitting atoms from the target.
そこで、高純度アルミニウムまたはその合金のターゲッ
トは、結晶方位の影響を避けるため微細でしかも結晶方
位がランダムになるように製造されてきた。しかしなが
ら、スパッタリングによりターゲットが消耗し、その形
状が変化して放出特性が変化するが、このような放出特
性の変化を避けるためには、結晶方位がランダムである
よりは特定の分布を持った集合方位であることが好まし
い場合もあるということが判明した。Therefore, targets of high-purity aluminum or its alloys have been manufactured to be fine and have random crystal orientations in order to avoid the influence of crystal orientation. However, sputtering wears out the target, changing its shape and changing its emission characteristics.In order to avoid such changes in emission characteristics, it is better to use a set of crystals with a specific distribution rather than a random crystal orientation. It has been found that in some cases it is preferable to be azimuth.
板の厚さ方向に結晶集合方位が異なるアルミニウム合金
板を得る為には異なった結晶方位を有する単結晶板や特
定集合方位を有する板を重ね合わせてクラッド圧延によ
る方法が用いられるが、単結晶板や特定集合方位の板を
得ることは容易ではなく、またクラッド圧延時の塑性加
工や加熱により、もとの結晶組織が変化してしまい、こ
れまでは充分満足できるものを得ることができなかった
。In order to obtain an aluminum alloy plate with different crystal orientations in the thickness direction of the plate, a method is used in which single crystal plates with different crystal orientations or plates with a specific aggregate orientation are stacked and clad rolled. It is not easy to obtain a plate or a plate with a specific collective orientation, and the original crystal structure changes due to plastic processing and heating during clad rolling, so it has not been possible to obtain a plate that is fully satisfactory until now. Ta.
かかる事情に鑑み、本発明者らは結晶集合方位の異なる
板が重なり合った構造の合金板の製造方法について鋭意
検討を行った結果、アルミニウムに添加した合金元素の
晶出物や析出物の寸法を変えたアルミニウム合金板を重
ね合せて、特定の圧下率と圧延温度でクラッド圧延し、
あるいは圧延後に熱処理を施すことにより、異なった結
晶集合方位が重なり合った構造をもつアルミニウム合金
板が容易に得られる事を見出した。In view of these circumstances, the inventors of the present invention have conducted intensive studies on a method for producing an alloy plate having a structure in which plates with different crystal orientations overlap. The different aluminum alloy plates are stacked together and clad rolled at a specific rolling reduction rate and rolling temperature.
Alternatively, it has been found that an aluminum alloy plate having a structure in which different crystal orientations overlap can be easily obtained by heat-treating after rolling.
すなわち、本発明は同一組威で、添加合金元素の晶出物
や析出物の寸法が異なる２枚以上のアルミニウム合金板
を重ね合せる圧延において、圧延時の塑性加工量および
温度を制御することにより、添加合金元素の晶出物や析
出物の寸法が大きい合金板においては不連続再結晶が生
じ、添加合金元素の晶出物や析出物の寸法が小さい合金
板においては不連続再結晶が生じないか、あるいは生じ
ても部分的か、または連続再結晶させることを特徴とす
るアルミニウム合金クラッド板の製造方ｌ去に関するも
のであり、添加合金元素の晶出物あるいは析出物の寸法
を変えることにより、アルミニウム合金の再結晶挙動を
変え、板の厚さ方向で異なった結晶集合方位を有するア
ルミニウム合金板を得るものである。That is, the present invention has the advantage of controlling the plastic working amount and temperature during rolling in rolling of two or more aluminum alloy plates of the same assembly but having different sizes of crystallized substances or precipitates of added alloying elements. Discontinuous recrystallization occurs in alloy plates with large crystallized or precipitated additive alloying elements, and discontinuous recrystallization occurs in alloy plates with small crystallized or precipitated additive alloying elements. This relates to a method for producing an aluminum alloy clad plate characterized by no recrystallization, or partial or continuous recrystallization, and changing the dimensions of crystallized or precipitated substances of added alloying elements. By changing the recrystallization behavior of the aluminum alloy, an aluminum alloy plate having different crystal aggregation orientations in the thickness direction of the plate can be obtained.
以下本発明を詳細に説明する。The present invention will be explained in detail below.
アルミニウムに添加する合金元素としては、アルミニウ
ムとの固溶範囲を有することが必要であり、たとえばＳ
ｉ， Ｃｕ． Ｔｉ． Ｃｒ， Ｗ， Ｍｏ， Ｍｇ等
を単独に添加したり、あるいはこれらのいくつかを複数
添加したものが用いられる。The alloying element added to aluminum must have a solid solubility range with aluminum; for example, S
i, Cu. Ti. Cr, W, Mo, Mg, etc. may be added singly or a plurality of these may be added.
添加元素量は、アルミニウムと添加元素との平衡状態図
からその範囲が決められるが、現実には添加元素は必ず
しも平衡的に存在するとは限らず好ましい成分範囲はも
う少し広くなる。たとえば、Ｓｉでは０．２〜２．０重
量％、Ｃｕは０．２〜６．０重量％の範囲が好ましく、
それぞれ単独に、または両者を同時に添加すことができ
る。The range of the amount of added elements is determined based on the equilibrium phase diagram between aluminum and the added elements, but in reality, the added elements do not necessarily exist in equilibrium, and the preferable range of components is a little wider. For example, Si is preferably in a range of 0.2 to 2.0% by weight, and Cu is preferably in a range of 0.2 to 6.0% by weight.
Each can be added individually or both can be added at the same time.
添加元素の晶出物あるいは析出物の寸ｌ去を変える方広
は、通常の方法を用いることができ、たとえば晶出物の
寸法はアルミニウム合金の凝固時の冷却速度を遅くする
と大きくなり、冷却速度を早くすると小さくなる、とい
う方法が適用できる。To change the size of crystallized substances or precipitates of added elements, a conventional method can be used.For example, the size of crystallized substances increases by slowing the cooling rate during solidification of an aluminum alloy, A method can be applied in which increasing the speed reduces the size.
析出物の寸法は、焼入れおよび人工時効処理により数μ
ｍ以上の粒径から完全な固冶状態まで変化させることが
できる。The size of the precipitates is reduced to several micrometers by quenching and artificial aging treatment.
It is possible to change the particle size from m or more to a completely solidified state.
晶出物または析出物の寸法がｌμｍ以上の大きなものが
存在するアルミニウム合金板と、ｌμｍ未満の小さなも
のが存在するアルミニウム合金板とを重ね合わせるクラ
ッド圧延は通常の方ｌ去が用いられる。晶出物または析
出物の寸法が異なるアルミニウム合金板を重ね合せてク
ラッド圧延をおこなうとき、全て同一組織となってしま
わないために以下の条件で圧延をおこなう必要がある。A conventional method is used for clad rolling in which an aluminum alloy plate in which large crystallized substances or precipitates of 1 μm or more are present and an aluminum alloy plate in which small crystallized substances or precipitates of less than 1 μm are present are superimposed. When clad rolling is performed by stacking aluminum alloy plates having different sizes of crystallized substances or precipitates, it is necessary to carry out rolling under the following conditions in order to prevent them from forming the same structure.
つまり、クラッド圧延において圧下率は好ましくは１５
％以上７５％以下であり、圧延温度は２５０℃以上４２
５℃以下が好ましい。In other words, the rolling reduction ratio in clad rolling is preferably 15
% or more and 75% or less, and the rolling temperature is 250°C or more and 42
The temperature is preferably 5°C or lower.
２５０℃以下でクラッド圧延をおこなった後２ ５ ０
℃以上４２５℃以下で熱処理をおこなうことも有効で
ある。After clad rolling at 250℃ or less 250
It is also effective to perform heat treatment at a temperature of 425°C or higher.
このような処理により同一合金板内で異なった結晶集合
方位が得られる。またアルミニウム合金の再結晶特性は
、添加合金元素の量や晶出物または析出物の寸法、塑性
加工量、加熱温度等により下記のようになる事が知られ
ている。Through such treatment, different crystal aggregation orientations can be obtained within the same alloy plate. It is also known that the recrystallization characteristics of aluminum alloys vary as shown below depending on the amount of added alloying elements, the dimensions of crystallized substances or precipitates, the amount of plastic working, the heating temperature, etc.
（イ）不連続再結晶゜゜“゜・再結晶集合組織（口）連
続再結晶 ・゛゛加工集合類似組織（ハ）未再結晶
゛゜゛ 加工集合組織（“アルミニウム材料の基礎と
工業技術”軽金属協会編 ｐ ． １１３（１９８５）
）このような現象の臨界寸法として粒径ｌμｍ以上であ
れば（イ）が、未満であれば（口）や（ハ）が生じるも
のと考えられる。(a) Discontinuous recrystallization゜゜“゜・Recrystallization texture (mouth) Continuous recrystallization ・゛゛Working texture similar texture (c) Unrecrystallized
゛゜゛ Processed Texture (“Basics and Industrial Technology of Aluminum Materials” edited by the Light Metals Association, p. 113 (1985)
) If the grain size is 1 μm or more as the critical dimension for such a phenomenon, then (a) will occur, and if it is less than that, (c) or (c) will occur.
以下本発明を実施例により説明するが、本発明はこれ等
に限定されるものではない。The present invention will be explained below with reference to Examples, but the present invention is not limited thereto.
実施例ｌ
Ｓｉを０．８％、Ｃｕを２．０％含有した純度９９．
９９％のアルミニウム合金板（ ５０ｘ ２００ｘ ２
００ｍｍ） ２枚を５２０℃でｌＯＨｒ均熱処理後、直
ちに水冷した。水冷後２枚のうち１枚を４００℃で５Ｈ
ｒ人工時効処理をおこない、ＳｉとＡＩ．Ｃｕの析出物
を有する合金板を得た。Example 1 Purity 99. containing 0.8% Si and 2.0% Cu.
99% aluminum alloy plate (50x 200x 2
00 mm) The two sheets were soaked in lOHr at 520° C. and immediately cooled with water. After cooling with water, one of the two sheets was heated to 400℃ for 5 hours.
rArtificial aging treatment is performed, and Si and AI. An alloy plate having Cu precipitates was obtained.
析出物の寸法は、試料の一部を切り取り研磨後フッ酸に
より軽くエッチングして析出物を顕出し、金属顕微鏡に
より測定した結果、平均３μｍであった。それぞれの板
の重ね合わせる面をワイヤーブラシで粗面化し、３５０
℃の温度で圧下率６０％でクラッド圧延をおこなった。The size of the precipitates was determined by cutting out a part of the sample, polishing it, lightly etching it with hydrofluoric acid to reveal the precipitates, and measuring the size using a metallurgical microscope. The average size was 3 μm. Roughen the overlapping surfaces of each board with a wire brush, and
Cladding rolling was performed at a temperature of 0.degree. C. and a reduction ratio of 60%.
得られたクラッド板から結晶方位測定用のサンプルを切
出し、両面の結晶方位を極点図から求めた結果、均熱処
理後水冷し、その後人工時効処理を施した板の表面側は
（１００１を中心とする再結晶の集合組織であり、均熱
処理後水冷のままの板の表面側はｉｌｌＯ ）を中心と
する熱間圧延の集合組織であった。A sample for crystal orientation measurement was cut out from the obtained clad plate, and the crystal orientation on both sides was determined from the pole figure. As a result, the surface side of the plate, which was soaked, water-cooled, and then artificially aged, was (centered on 1001). The surface side of the plate that had been water-cooled after the soaking treatment had a hot rolling texture centered on illO2.
実施例２
Ｓｉを０．８％、Ｃｕを１．０％含有した純度９９．
９９％のアルミニウム合金板（ １０ Ｘ ２００ ｘ
２００ ｍｍ）を２枚鋳造した。鋳造組織を実施例１
と同様にして金属顕微鏡により測定した結果、析出物の
平均粒径は１０μｍであった。該鋳造板のうち１枚を５
２５℃でｌＯｈ『の均熱処理後水焼入れをおこなった。Example 2 Purity 99.0 containing 0.8% Si and 1.0% Cu.
99% aluminum alloy plate (10 x 200 x
200 mm) were cast. Example 1 of casting structure
As a result of measurement using a metallurgical microscope in the same manner as above, the average particle size of the precipitates was 10 μm. One of the cast plates is 5
Water quenching was performed after soaking at 25°C for lOh.
これを金属顕微鏡観察したところ１００倍では晶析物や
析出物は観察されなかった。When this was observed under a metallurgical microscope, no crystallized substances or precipitates were observed under 100x magnification.
これら２枚の板の重ね合わせる面を旋盤にて而削した後
、ワイヤーブラシで粗面化しクラッド圧延した。圧延温
度は３００℃で圧下率は６０％であった。The overlapping surfaces of these two plates were ground with a lathe, roughened with a wire brush, and clad rolled. The rolling temperature was 300°C and the reduction ratio was 60%.
得られたクラッド板から結晶方位測定用のサンプルを切
出し、両面の結晶方位を極点図から求めた結果、鋳造の
ままの板では表面が［１００１ に平行な再結晶の集合
方位で鋳造後均熱処理をして水焼入れをおこなった板の
表面は＋１１０１ に平行な圧延の集合方位を示し、板
の厚さ方向に重なった集合方位を有しているのが認めら
れた。A sample for crystal orientation measurement was cut from the obtained clad plate, and the crystal orientation on both sides was determined from the pole figure. As a result, the surface of the as-cast plate had a recrystallization collection orientation parallel to [1001] and was soaked after casting. It was observed that the surface of the plate subjected to water quenching in the same manner as shown in FIG.
実施例３
実施例ｌにおいて、圧延温度を１５０゜Ｃとし、圧下率
を５５．％に変えた以外はすべて同様にしてクラッド板
を得た。得られたクラッド板を３５０℃でｌＯ分間熱処
理後、結晶方位測定用のサンプルを切出し、両面の結晶
方位を極点図から求めた結果、均熱処理後水冷し、その
後人工時効処理を施した板の表面は＋１００ １ を中
心とする再結晶の集合組織であり、均熱処理後水冷まで
の板の表面は［１１０１を中心とする熱間圧延の集合組
織であった。Example 3 In Example 1, the rolling temperature was 150°C and the rolling reduction was 55. A clad plate was obtained in the same manner except that the percentage was changed. After heat-treating the obtained clad plate at 350°C for 10 minutes, a sample for crystal orientation measurement was cut out, and the crystal orientation on both sides was determined from the pole figure. The surface had a recrystallized texture centered on +100 1 , and the surface of the plate after soaking until water cooling had a hot rolled texture centered on [1101].
比較例１
実施例ｌにおいて、圧下率を８０％に変えた以外はすべ
て同様にした結果、両面ともｔｔｏｏ ＋ を中心とす
る再結晶の集合組織であった。Comparative Example 1 The same procedure as in Example 1 was carried out except that the rolling reduction was changed to 80%. As a result, both surfaces had a recrystallized texture centered on ttoo + .
比較例２
実施例ｌにおいて、圧延温度を４５０℃に変えた以外は
すべて同様にした結果、両面ともｔ１００１を中心とす
る再結晶の集合組織であった。Comparative Example 2 The same procedure as in Example 1 was repeated except that the rolling temperature was changed to 450° C. As a result, both surfaces had a recrystallized texture centered on t1001.
比較例３
実施例３において、圧延温度を２００℃に変えた以外は
すべて同様にしてクラッド板を得た。得られたクラッド
板を熱処理せず、結晶方位測定用のサンプルを切出し、
両面の結晶方位を極点図から求めた結果、両面とも（１
１０１を中心とする熱間圧延の集合組織であった。Comparative Example 3 A clad plate was obtained in the same manner as in Example 3 except that the rolling temperature was changed to 200°C. The obtained clad plate was not heat-treated, and samples for crystal orientation measurement were cut out.
As a result of finding the crystal orientation of both sides from the pole figure, both sides are (1
It had a hot-rolled texture centered around 101.
本発明によれば厚さ方向で集合結晶方位の異なる結晶方
位制御クラッド板を通常の圧延方法にて容易に得ること
ができる。According to the present invention, a crystal orientation controlled clad plate having different collective crystal orientations in the thickness direction can be easily obtained by a normal rolling method.
手続補正冑（自発）Procedure correction helmet (voluntary)
Claims (6)
法が異なる２枚以上のアルミニウム合金板を重ね合せる
圧延において、圧延時の塑性加工量および温度を制御す
ることにより、添加合金元素の晶出物や析出物の寸法が
大きい合金板においては不連続再結晶が生じ、添加合金
元素の晶出物や析出物の寸法が小さい合金板においては
不連続再結晶が生じないか、あるいは生じても部分的か
、または連続再結晶させることを特徴とするアルミニウ
ム合金クラッド板の製造方法。(1) When rolling two or more aluminum alloy plates of the same composition but with different sizes of crystallized or precipitated additive alloy elements, the additive alloy Does discontinuous recrystallization occur in alloy plates with large crystallized or precipitated elements, and does discontinuous recrystallization occur in alloy plates with small crystallized or precipitated elements of added alloying elements? Alternatively, a method for producing an aluminum alloy clad plate, characterized in that recrystallization is carried out partially or continuously even if it occurs.
法が異なる２枚以上のアルミニウム合金板を重ね合せる
合金クラッド板の製造方法において、各アルミニウム合
金板が共に不連続再結晶を生じない塑性加工量および温
度にてクラッド圧延後、添加合金元素の晶出物や析出物
の寸法の大きい合金板でのみ不連続再結晶が生じる温度
で熱処理することを特徴とするアルミニウム合金クラッ
ド板の製造方法。(2) In a method for producing an alloy clad plate in which two or more aluminum alloy plates of the same composition but with different sizes of crystallized substances or precipitates of added alloying elements are stacked together, each aluminum alloy plate undergoes discontinuous recrystallization. An aluminum alloy clad plate characterized in that after clad rolling at a temperature and amount of plastic deformation that does not occur, heat treatment is performed at a temperature that causes discontinuous recrystallization only in alloy plates with large crystallized or precipitated crystals of added alloying elements. manufacturing method.
ラッド板の製造方法において、圧下率が１５％以上７５
％以下で、クラッド圧延温度が２５０℃以上４２５℃以
下であることを特徴とするアルミニウム合金クラッド板
の製造方法。(3) In the method for manufacturing an aluminum alloy clad plate according to claim 1, the rolling reduction is 15% or more.
% or less, and the clad rolling temperature is 250°C or more and 425°C or less.
ラッド板の製造方法において、圧下率が１５％以上７５
％以下で、クラッド圧延温度が２５０℃未満であり、圧
延後の熱処理温度が２５０℃以上４２５℃以下であるこ
とを特徴とするアルミニウム合金クラッド板の製造方法
。(4) In the method for manufacturing an aluminum alloy clad plate according to claim 2, the rolling reduction is 15% or more.
% or less, the clad rolling temperature is less than 250°C, and the heat treatment temperature after rolling is 250°C or more and 425°C or less.
ニウム合金クラッド板の製造方法において、添加合金の
晶出物や析出物の寸法の大きいものが粒径１μｍ以上で
あり、小さいものが粒径１μｍ未満または固溶状態であ
ることを特徴とするアルミニウム合金クラッド板の製造
方法。(5) In the method for manufacturing an aluminum alloy clad plate according to claims 1 and 2, the large crystallized or precipitated particles of the additive alloy have a particle size of 1 μm or more, and the small ones have a particle size of 1 μm or more. A method for producing an aluminum alloy clad plate, characterized in that the particles have a particle size of less than 1 μm or are in a solid solution state.
ニウム合金クラッド板の製造方法において、添加成分元
素が０．２〜２．０％のＳｉか、０．２〜６．０％のＣ
ｕか、または０．２〜２．０％のＳｉと０．２〜６．０
％のＣｕであることを特徴とするアルミニウム合金クラ
ッド板の製造方法。(6) In the method for manufacturing an aluminum alloy clad plate according to claims 1 and 2, the additional component element is 0.2 to 2.0% Si or 0.2 to 6.0% Si. C
u or 0.2-2.0% Si and 0.2-6.0
% of Cu.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1161291A JP2687597B2 (en) | 1989-06-23 | 1989-06-23 | Method for producing aluminum alloy clad plate with controlled crystal aggregation direction |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1161291A JP2687597B2 (en) | 1989-06-23 | 1989-06-23 | Method for producing aluminum alloy clad plate with controlled crystal aggregation direction |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0327883A true JPH0327883A (en) | 1991-02-06 |
| JP2687597B2 JP2687597B2 (en) | 1997-12-08 |
Family
ID=15732319
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1161291A Expired - Fee Related JP2687597B2 (en) | 1989-06-23 | 1989-06-23 | Method for producing aluminum alloy clad plate with controlled crystal aggregation direction |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2687597B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002332506A (en) * | 2001-05-07 | 2002-11-22 | Central Res Inst Of Electric Power Ind | Structure material having function of suppressing propagation of cracking |
| CN106583467A (en) * | 2016-12-30 | 2017-04-26 | 西南铝业（集团）有限责任公司 | Hot rolling process method for 2050 alloy cast ingot |
-
1989
- 1989-06-23 JP JP1161291A patent/JP2687597B2/en not_active Expired - Fee Related
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002332506A (en) * | 2001-05-07 | 2002-11-22 | Central Res Inst Of Electric Power Ind | Structure material having function of suppressing propagation of cracking |
| JP4591985B2 (en) * | 2001-05-07 | 2010-12-01 | 財団法人電力中央研究所 | Structural material |
| CN106583467A (en) * | 2016-12-30 | 2017-04-26 | 西南铝业（集团）有限责任公司 | Hot rolling process method for 2050 alloy cast ingot |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2687597B2 (en) | 1997-12-08 |
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