JPS6143422B2 - - Google Patents
Info
- Publication number
- JPS6143422B2 JPS6143422B2 JP55167794A JP16779480A JPS6143422B2 JP S6143422 B2 JPS6143422 B2 JP S6143422B2 JP 55167794 A JP55167794 A JP 55167794A JP 16779480 A JP16779480 A JP 16779480A JP S6143422 B2 JPS6143422 B2 JP S6143422B2
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- strength
- content
- brightness
- present
- 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
Links
- 239000000956 alloy Substances 0.000 claims description 27
- 229910045601 alloy Inorganic materials 0.000 claims description 27
- 238000004519 manufacturing process Methods 0.000 claims description 22
- 238000010438 heat treatment Methods 0.000 claims description 11
- 238000001816 cooling Methods 0.000 claims description 8
- 239000002244 precipitate Substances 0.000 description 10
- 239000006104 solid solution Substances 0.000 description 8
- 238000000137 annealing Methods 0.000 description 7
- 239000013078 crystal Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 238000000034 method Methods 0.000 description 5
- 238000005498 polishing Methods 0.000 description 5
- 239000000047 product Substances 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 238000005097 cold rolling Methods 0.000 description 4
- 238000000265 homogenisation Methods 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000000465 moulding Methods 0.000 description 3
- 239000005022 packaging material Substances 0.000 description 3
- 238000004806 packaging method and process Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 239000004615 ingredient Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910002551 Fe-Mn Inorganic materials 0.000 description 1
- 238000007743 anodising Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 239000002537 cosmetic Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000004577 ear development Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000002932 luster Substances 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
Description
本発明は光輝性及び強度に優れたＡ合金の製
造法に関する。
一般に、光輝性を有するＡ合金の用途とし
て、光輝性包装用品、例えば、化粧品キヤツプ、
パネルのツマミ及びケツトル、鍋等がある。これ
は通常Ａ合金を成形加工後、電解研磨、或い
は、化学研磨を行ない、アルマイト処理を施して
製品とする。そして、このような光輝性包装用材
料のＡ合金として要求される特性は次に示すも
のである。
即ち、
(1)成形割れを生じないこと。
(2)光輝性に優れていること。（反射率が高く、か
つ圧延模様を生じないこと。）
(3)絞り耳が低いこと。（歩留りが良いこと。）
(4)肌荒れを起さないこと。（結晶粒度が細かいこ
と。）
(5)強度が高いこと。（変形しないこと。）
の５項目が挙げられる。この各項目毎に組成及び
製造条件を選択することによつて満足するものが
得られる。即ち、成形性については伸びを高める
こと（軟質化）、光輝性についてはＡの純度を
上げること、また、強度についてはＡの純度を
下げること等である。しかし、これらの条件は互
に矛盾しているため光輝性包装用材料としてのＡ
合金に要求される特性を全べて満足させること
は非常に困難なことである。従つて、現在、光輝
性包装用材料としてのＡ合金には、99.85％の
高純度Ａを使用し、かつ、強度を必要とするも
のはCu、或いは、Mgを含有させることによつて
対応しているが、未だ不充分であつて研究が行な
われている。
また、現在使用されている光輝性包装用Ａ合
金について説明すると、上記説明の通り光輝性を
付与するために高純度Ａを使用しているが、こ
れは、凝固時に生じる晶出物及び均質化処理、焼
鈍等により生じる析出物の生成を抑制するためで
ある。この晶出物や析出物は電解研磨、化学研磨
により溶出してＡ素地表面を粗面化し、これに
アルマイトを行なうとアルマイト皮膜のムラ、及
びアルマイト皮膜に歪を生じて光輝性を低下させ
るのである。
また、強度を上げるために、Mg或いはCuを含
有させるが、この２つの元素は他の元素よりＡ
に固溶し易く析出物を生成させないとともに固溶
強化も高いためである。さらに、光輝性について
も、Mgはアルマイト性に優れ、Cuは均一に固溶
するため反射率向上に効果がある。
次に、99.85％というような高純度Ａを使用
せずに、99.50％Ａ、或いは、99.0％Ａのよ
うな普通純度のＡを使用することにより光輝性
包装用Ａ合金を製造できることが望ましい。
本発明は、上記に説明した技術的問題点、又
は、技術的背景に鑑み、(1)光輝性に優れた組成及
び製造工程、(2)光輝性を損なわずに強度を上げる
組成及び製造工程、(3)普通純度のＡを使用でき
る製造工程について研究の結果完成された光輝性
及び強度に優れたＡ合金の製造法である。
本発明に係る光輝性及び強度に優れたＡ合金
の特徴とするところは、Cu0.05〜0.5％、Mg0.1
〜0.5％、Si0.01〜0.4％を含み、Fe含有量を0.6％
まで許容したＡ合金に対して、加熱速度100
℃／分以上で昇温して450℃以上の高温に10分以
下保持し、その後100℃／時間以上の冷却速度で
冷却する高温短時間熱処理を施すことにある。
また、本発明に係る光輝性及び強度に優れたＡ
合金の製造法において使用するＡ合金には、
Ti0.01〜0.3％、B0.001〜0.05％の１種以上を含
有することがある。
本発明に係る光輝性及び強度に優れたＡ合金
の製造法（以下本発明に係る製造法ということも
ある。）について詳細に説明する。
先づ、本発明に係る製造法において使用するＡ
合金について、含有成分及び成分割合について
説明する。
Cuは光輝性を損なわずに強度を付与する元素
であるが、含有量が0.5％を越えると耐食性が低
下し、また、0.05％末満では固溶強化が得られ
ず、電解研磨、化学研磨による光沢性を向上させ
ることが難かしくなる。よつて、Cu含有量は
0.05〜0.5％とする。
MgはCuと同様な効果を付与する元素であり、
含有量が0.5％を越えると強度が高くなり過ぎて
程度の高い成形の際割れを発生するようになり、
更にMgは表面に拡散して酸化し易く、多くなる
と色調が黒くなるという問題がある。また、0.1
％末満では固溶強化を得ることができない。よつ
て、Mg含有量は0.1〜0.5％とする。
Siは絞り加工時に発生する耳を抑制する効果が
あり、そして、Feが含有されることによつて増
加する45゜方向耳（圧延方向に対し）を低くする
ものであつて、含有量が0.4％を越えると陽極酸
化時に着色し易くなり、かつ、成形性を阻害し、
また、0.01％未満では耳の発生を抑制する効果が
なくなる。よつて、Si含有量は0.01〜0.4％とす
る。
Feは通常不純物として或る程度含まれるもの
で強度を付与するが、Cu、Mgに比し固溶量が低
く通常晶出物、及び、析出物（Ａ3Fe）を生じ
光輝性を損なう。しかし、光輝性を損なわずに
Fe含有量を増加するも可能であるが、含有量が
0.6％を越えると晶出物、及び、析出物が多量に
生成し、光輝性を損なう。よつて、Fe含有量は
0.6％未満とする。しかし、このFeが含有される
ことによつて99.85％の高純度Ａを使用しない
で、普通純度のＡを使用することが可能とな
る。
Ti、Ｂは単独、或いは、同時に含有されるこ
とにより鋳造時の組織を微細均一にする元素であ
り、含有量がTi0.3％、B0.05％を越えると組織を
微細均一にする効果がなく、巨大初晶化合物の発
生を起し易く成形性を阻害し、また、Ti0.01％、
B0.001％未満では組織を微細均一にする効果はな
くなる。よつて、Ti含有量は0.01〜0.3％、Ｂ含
有量は0.001〜0.05％とする。
この外にMn、Zn、Crは通常Ａ、或いは、Ａ
合金に不純物として含有されている範囲であれ
ば、本発明に係る製造法の作用及び／又は効果を
阻害することはない。そして、Mnについては、
この含有量が増加してくるとＡ―Fe―Mnの巨
大化合物、及び、Ａ6Mnの析出物が生成する
が、Mn含有量が0.1％以下であればこれら巨大化
合物や析出物を抑制することができる。
次に、本発明に係る製造法における熱処理につ
いて説明する。
上記した含有成分、成分割合のＡ合金を、通
常行なわれている450゜〜600℃×数時間の均質化
処理をしてＡ鋳塊内の偏析をなくし、熱間圧
延、及び、必要に応じて冷間圧延を行なつた後焼
鈍をするのである。
この場合の焼鈍が本発明に係る製造法であり、
一般に、通常の焼鈍においては昇温速度、冷却速
度が遅く（50℃／時間以下）、かつ、到達温度も
低いのであるが（400℃以下、数時間保持）、本発
明に係る製造法においては、450℃以上の高温に
100℃／分以上の昇温速度で急速加熱して10分間
以下保持し、次に100℃／時間以上の冷却速度で
急速冷却を行なうものである。必要に応じて冷間
圧延、及び、熱処理（非完全焼鈍）を行なつても
よい。
このように、通常の焼鈍は到達温度が低いこと
からそれ以前に生成した析出物の再固溶量は少な
く、かつ、昇温速度、及び、冷却速度が遅いこと
から到達温度までの各温度で各種析出物が生成す
る時間を有する結果、光輝性は劣化し、添加元素
の過飽和による固溶体硬化も得られないばかりか
再結晶粒の成長を促進し肌荒れの原因となる。
しかして、本発明に係る製造法は到達温度が高
く、かつ、昇温速度、及び、冷却速度が速いこと
から、それ以前に生成した析出物が一部再固溶
し、かつ、到達温度までの各温度で析出する余裕
を与えず、その結果、光輝性が優れ、含有元素の
過飽和による固溶体硬化を得ることができる。そ
して、短時間焼鈍であるため結晶粒の成長が起こ
らずに微細な再結晶粒が得られる。このことによ
つて更に強度が高くなる。
この場合において、昇温速度を100℃／分以上
にするのは、昇温速度が100℃／分未満では再結
晶粒の成長を抑制することができないからであ
り、450℃以上に10分以下保持するのは、保持時
間をこれ以上長くしても効果はなく、逆に再結晶
粒の成長を促進するからである。又工業上も長時
間保持は不利である。
次に本発明に係る光輝性及び強度に優れたＡ
合金の製造法についての実施例を説明する。
実施例 １
The present invention relates to a method for producing alloy A having excellent brightness and strength. In general, A-alloy with glitter is used for glitter packaging products, such as cosmetic caps,
There are panel knobs, kettles, pots, etc. This is usually done by molding the A alloy, then electrolytically polishing or chemically polishing it, and then anodizing it to produce a product. The characteristics required of the A alloy for such a glitter packaging material are as follows. That is, (1) Molding cracks should not occur. (2) Excellent brightness. (High reflectance and no rolling pattern.) (3) Low aperture selvedge. (It should have a good yield.) (4) It should not cause rough skin. (Fine crystal grain size.) (5) High strength. (Do not deform.) There are five items. By selecting the composition and manufacturing conditions for each item, a satisfactory product can be obtained. That is, for moldability, it is necessary to increase the elongation (softening), for brightness, it is necessary to increase the purity of A, and for strength, it is necessary to decrease the purity of A. However, these conditions are mutually contradictory, so A as a glitter packaging material cannot be used.
It is extremely difficult to satisfy all the properties required of an alloy. Therefore, currently, high-purity A of 99.85% is used for the A-alloy used as a glitter packaging material, and if strength is required, Cu or Mg is added to the A-alloy. However, it is still insufficient and research is still being conducted. In addition, to explain the glitter A alloy currently used for packaging, as explained above, high purity A is used to impart glitter, but this is due to the crystallization and homogenization that occur during solidification. This is to suppress the formation of precipitates caused by processing, annealing, etc. These crystallized substances and precipitates are eluted by electropolishing and chemical polishing and roughen the surface of the A substrate, and when alumite is applied to this, it causes unevenness and distortion of the alumite film, reducing the brightness. be. Also, in order to increase the strength, Mg or Cu is included, but these two elements have a higher A content than other elements.
This is because it easily dissolves in solid solution, does not generate precipitates, and has high solid solution strengthening. Furthermore, in terms of brightness, Mg has excellent alumite properties, and Cu is uniformly dissolved in solid solution, which is effective in improving reflectance. Next, it would be desirable to be able to produce bright packaging A alloy by using A of normal purity, such as 99.50% A or 99.0% A, without using high purity A such as 99.85%. In view of the technical problems or technical background explained above, the present invention provides (1) a composition and manufacturing process with excellent glitter, (2) a composition and manufacturing process that increases strength without impairing glitter. , (3) This is a method for producing A alloy with excellent brightness and strength, which was completed as a result of research on a production process that can use A of ordinary purity. The characteristics of the A alloy with excellent brightness and strength according to the present invention are Cu0.05-0.5%, Mg0.1
~0.5%, Si0.01~0.4%, Fe content 0.6%
Heating rate 100 for alloy A, which was allowed up to
The purpose is to perform a high-temperature, short-time heat treatment in which the temperature is raised at a rate of 450°C or higher for 10 minutes or less, and then cooled at a cooling rate of 100°C/hour or higher. In addition, A with excellent glitter and strength according to the present invention
The A alloy used in the alloy manufacturing method includes:
It may contain one or more of Ti0.01-0.3% and B0.001-0.05%. The method for manufacturing alloy A having excellent brightness and strength according to the present invention (hereinafter also referred to as the manufacturing method according to the present invention) will be explained in detail. First, A used in the production method according to the present invention
Regarding the alloy, the contained components and component ratios will be explained. Cu is an element that imparts strength without impairing brightness, but if the content exceeds 0.5%, corrosion resistance decreases, and if the content is less than 0.05%, solid solution strengthening cannot be obtained, and electrolytic polishing, chemical polishing It becomes difficult to improve the glossiness due to Therefore, the Cu content is
Set to 0.05-0.5%. Mg is an element that provides the same effect as Cu,
If the content exceeds 0.5%, the strength will be too high and cracks will occur during severe molding.
Furthermore, Mg is easily diffused onto the surface and oxidized, and when the amount increases, there is a problem that the color tone becomes black. Also, 0.1
%, solid solution strengthening cannot be obtained. Therefore, the Mg content is set to 0.1 to 0.5%. Si has the effect of suppressing the sag that occurs during drawing, and also reduces the 45° sag (with respect to the rolling direction) that increases due to the inclusion of Fe, and the content is 0.4 If it exceeds %, it becomes easy to color during anodic oxidation and inhibits moldability.
Furthermore, if it is less than 0.01%, it will not be effective in suppressing ear development. Therefore, the Si content is set to 0.01 to 0.4%. Fe is usually included as an impurity to some extent and imparts strength, but its solid solution content is lower than that of Cu and Mg, and it usually forms crystallized substances and precipitates (A 3 Fe), impairing brightness. However, without losing the brightness
Although it is possible to increase the Fe content,
If it exceeds 0.6%, a large amount of crystallized substances and precipitates will be formed, impairing the brightness. Therefore, the Fe content is
Less than 0.6%. However, the inclusion of Fe makes it possible to use ordinary purity A without using 99.85% high purity A. Ti and B are elements that make the structure fine and uniform during casting when contained alone or at the same time, and when the content exceeds 0.3% Ti and 0.05% B, it has the effect of making the structure fine and uniform. Ti0.01%, Ti0.01%,
If B is less than 0.001%, the effect of making the structure fine and uniform is lost. Therefore, the Ti content is 0.01 to 0.3%, and the B content is 0.001 to 0.05%. In addition to this, Mn, Zn, and Cr are usually A or A
As long as it is contained as an impurity in the alloy, it will not impede the operation and/or effect of the manufacturing method according to the present invention. And for Mn,
As this content increases, giant compounds of A-Fe-Mn and precipitates of A 6 Mn are formed, but if the Mn content is 0.1% or less, these giant compounds and precipitates are suppressed. be able to. Next, heat treatment in the manufacturing method according to the present invention will be explained. Alloy A with the above-mentioned components and ratios is subjected to the usual homogenization treatment at 450° to 600°C for several hours to eliminate segregation in the A ingot, hot rolled, and as necessary. After cold rolling, annealing is performed. Annealing in this case is the manufacturing method according to the present invention,
Generally, in normal annealing, the heating rate and cooling rate are slow (below 50°C/hour), and the temperature reached is also low (below 400°C, held for several hours), but in the manufacturing method according to the present invention, , at high temperatures over 450℃
Rapid heating is performed at a temperature increase rate of 100°C/min or more, held for 10 minutes or less, and then rapid cooling is performed at a cooling rate of 100°C/hour or more. Cold rolling and heat treatment (non-complete annealing) may be performed as necessary. In this way, in normal annealing, the reached temperature is low, so the amount of precipitates that were formed before is re-dissolved into solid form is small, and the heating rate and cooling rate are slow, so at each temperature up to the reached temperature, As a result of having time for various precipitates to form, the luster deteriorates, solid solution hardening due to supersaturation of added elements is not achieved, and the growth of recrystallized grains is promoted, causing rough skin. However, since the production method according to the present invention has a high attained temperature and a fast heating rate and cooling rate, some of the precipitates generated before that time are re-dissolved, and until the attained temperature As a result, it is possible to obtain excellent brightness and solid solution hardening due to supersaturation of the contained elements. Further, since the annealing is performed for a short time, fine recrystallized grains can be obtained without crystal grain growth. This further increases the strength. In this case, the temperature increase rate is set to 100℃/min or more because the growth of recrystallized grains cannot be suppressed if the temperature increase rate is less than 100℃/min. The reason for holding is that extending the holding time any longer has no effect, and on the contrary promotes the growth of recrystallized grains. Also, from an industrial perspective, holding for a long time is disadvantageous. Next, A with excellent brightness and strength according to the present invention
An example of an alloy manufacturing method will be described. Example 1
【表】
第１表に示す含有成分、及び、成分割合となる
ように溶製によりＡ合金を製造した後鋳造す
る。この鋳塊を通常の均質化処理、熱間圧延、及
び、冷間圧延を行なつて0.8mmｔの板を得た。
この板に対して焼鈍を行なつた。
その結果を第２表、及び結晶粒度を顕微写真の
第１図に示す。
第１図ａは本発明に係る製造法により作られた
ものの顕微鏡写真で結晶粒が微細均一化されてい
るが、第１図ｂは現行方法で作られたものの顕微
鏡写真で結晶粒は大きくかつ不揃いである。[Table] Alloy A is produced by melting so as to have the ingredients and proportions shown in Table 1, and then cast. This ingot was subjected to conventional homogenization treatment, hot rolling, and cold rolling to obtain a plate of 0.8 mmt. This plate was annealed. The results are shown in Table 2, and the crystal grain size is shown in FIG. 1, which is a micrograph. Figure 1a is a photomicrograph of a product made using the manufacturing method of the present invention, and the crystal grains are fine and uniform, while Figure 1b is a photomicrograph of a product made using the current method, and the crystal grains are large and uniform. It is irregular.
【表】
従つて、本発明に係る製造法では、上記の通
り、強度は高く、光輝性の優れたもので、結晶粒
度も微細均一で肌荒れを生じることがなく、か
つ、成形性も良好である。
実施例 ２[Table] Therefore, as mentioned above, the production method according to the present invention has high strength and excellent brightness, has a fine and uniform crystal grain size, does not cause rough skin, and has good moldability. be. Example 2
【表】
第３表に示す含有成分、及び、成分割合となる
ように溶製によりＡ合金を製造し、鋳造した。
この鋳塊を通常の均質化処理、熱間圧延、及び、
冷間圧延を行なつて1.2mmｔの板を作つた。
この板に対して焼鈍を行なつた。
次いで、0.8mmｔまで冷間圧延し硬質材を得
た。その材料特性を第４表に示す。[Table] Alloy A was produced by melting so as to have the ingredients and proportions shown in Table 3, and was cast.
This ingot is subjected to normal homogenization treatment, hot rolling, and
A plate of 1.2 mmt was made by cold rolling. This plate was annealed. Next, the material was cold rolled to a thickness of 0.8 mm to obtain a hard material. The material properties are shown in Table 4.
【表】
第４表からも明らかなように、本発明に係る製
造法は強度が高く、使用したＡも99.0％の純度
のものであるが、高純度Ａを使用したと同様な
光輝性を有し、成形性はやや悪いが高強度用であ
れば問題はない。
以上説明したように、本発明に係る光輝性及び
強度に優れたＡ合金の製造法は上記のような構
成を有しているものであるから、光輝性、強度、
及び、肌荒れ性は著しく向上し、成形性、及び方
向性（絞り耳）も良好なものであり、かつ、普通
純度のＡを使用できるという効果を奏するもの
である。[Table] As is clear from Table 4, the production method according to the present invention has high strength, and although the A used has a purity of 99.0%, it has the same brightness as using high purity A. Although the moldability is somewhat poor, there is no problem if it is used for high strength applications. As explained above, since the method for manufacturing Alloy A having excellent glitter and strength according to the present invention has the above-mentioned structure,
Moreover, the rough skin property is significantly improved, the moldability and directionality (squeezing edge) are also good, and A of ordinary purity can be used.
第１図ａ，ｂは本発明に係る光輝性及び強度に
優れたＡ合金の製造法と現行方法とで製造され
たＡ合金の結晶粒度の顕微鏡写真である。
FIGS. 1a and 1b are micrographs of the crystal grain size of alloy A produced by the method of producing alloy A with excellent brightness and strength according to the present invention and the current method.
Claims (1)
％を含み、Fe含有量を0.6％まで許容したＡ合
金に対して、加熱速度100℃／分以上で昇温して
450℃以上の高温に10分以下保持し、その後、100
℃／時間以上の冷却速度で冷却する高温短時間熱
処理を施すことを特徴とする光輝性及び強度に優
れたＡ合金の製造法。 ２ Ａ合金がTi0.01〜0.3％、B0.001〜0.05％
の１種以上を含むことを特徴とする特許請求の範
囲第１項記載の光輝性及び強度に優れたＡ合金
の製造法。[Claims] 1 Cu0.05-0.5%, Mg0.1-0.5%, Si0.01-0.4
%, and the Fe content is allowed up to 0.6%, by heating at a heating rate of 100℃/min or more.
Hold at a high temperature of 450℃ or higher for 10 minutes or less, then 100℃
A method for producing alloy A with excellent brightness and strength, which is characterized by performing a high-temperature, short-time heat treatment by cooling at a cooling rate of ℃/hour or more. 2 A alloy contains Ti0.01~0.3%, B0.001~0.05%
A method for producing alloy A having excellent brightness and strength according to claim 1, characterized in that it contains one or more of the following.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16779480A JPS5792168A (en) | 1980-11-28 | 1980-11-28 | Manufacture of al alloy with superior brightness and strength |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16779480A JPS5792168A (en) | 1980-11-28 | 1980-11-28 | Manufacture of al alloy with superior brightness and strength |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5792168A JPS5792168A (en) | 1982-06-08 |
| JPS6143422B2 true JPS6143422B2 (en) | 1986-09-27 |
Family
ID=15856224
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16779480A Granted JPS5792168A (en) | 1980-11-28 | 1980-11-28 | Manufacture of al alloy with superior brightness and strength |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5792168A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0528228U (en) * | 1991-09-27 | 1993-04-16 | 有限会社オリーブデント | toothbrush |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5640399B2 (en) * | 2010-03-03 | 2014-12-17 | 日本軽金属株式会社 | Aluminum alloy plate with anodized film and method for producing the same |
| CN103614581B (en) * | 2013-12-20 | 2015-09-30 | 西南铝业（集团）有限责任公司 | A kind of production technique of 1 line aluminium alloy cast ingot |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5527497A (en) * | 1978-08-04 | 1980-02-27 | Alusuisse | Preparation of aluminum strip material |
| JPS5579850A (en) * | 1978-12-14 | 1980-06-16 | Furukawa Alum Co Ltd | Sheetlike aluminum alloy with superior strength and formability |
-
1980
- 1980-11-28 JP JP16779480A patent/JPS5792168A/en active Granted
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5527497A (en) * | 1978-08-04 | 1980-02-27 | Alusuisse | Preparation of aluminum strip material |
| JPS5579850A (en) * | 1978-12-14 | 1980-06-16 | Furukawa Alum Co Ltd | Sheetlike aluminum alloy with superior strength and formability |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0528228U (en) * | 1991-09-27 | 1993-04-16 | 有限会社オリーブデント | toothbrush |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5792168A (en) | 1982-06-08 |
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