JPH0941064A - Production of aluminum alloy for casting and aluminum alloy casting material - Google Patents
Production of aluminum alloy for casting and aluminum alloy casting materialInfo
- Publication number
- JPH0941064A JPH0941064A JP21253295A JP21253295A JPH0941064A JP H0941064 A JPH0941064 A JP H0941064A JP 21253295 A JP21253295 A JP 21253295A JP 21253295 A JP21253295 A JP 21253295A JP H0941064 A JPH0941064 A JP H0941064A
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- casting
- aluminum alloy
- strength
- alloy
- elongation
- Prior art date
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、機械的性質および
耐食性に優れた鋳造用アルミニウム合金およびその合金
を用いた鋳造材の製造方法に関するものであり、詳しく
は簡易な熱処理によって高い強度（特に耐力）と良好な
伸びが得られるＡｌ−Ｍｇ−Ｚｎ−Ｓｉ系の鋳造用アル
ミニウム合金および該合金を用いた鋳造材の製造法に関
するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy for casting which is excellent in mechanical properties and corrosion resistance, and a method for producing a cast material using the alloy. ) And an Al-Mg-Zn-Si-based aluminum alloy for casting that provides good elongation, and a method for producing a cast material using the alloy.
【０００２】[0002]
【従来の技術】最近、自動車軽量化の観点から自動車部
品のアルミ化が進められているが、Ａｌ合金鋳物を自動
車部品として用いるためには、優れた強度と伸びを兼ね
備え、また耐食性にも優れていることが要求される。従
来、上記用途における代表的な鋳造用Ａｌ合金として
は、ＪＩＳ ＡＣ４ＣＨに代表される鋳造性に優れたＡ
ｌ−Ｓｉ系合金が用いられている。この系合金は、所定
の強度と伸びを得るために、高温で長時間加熱する溶体
化処理を行った後、低温で加熱する時効処理を行ってお
り、この溶体化処理と時効処理とを行わなければ所望の
機械的性質を得ることができない。2. Description of the Related Art Recently, in order to reduce the weight of automobiles, automobile parts are being made of aluminum. However, in order to use an Al alloy casting as automobile parts, it has both excellent strength and elongation and excellent corrosion resistance. Is required. Conventionally, as a typical casting Al alloy for the above-mentioned applications, A having excellent castability represented by JIS AC4CH is used.
An l-Si alloy is used. In order to obtain a predetermined strength and elongation, this system alloy is subjected to a solution treatment of heating at high temperature for a long time, and then an aging treatment of heating at a low temperature, and the solution treatment and the aging treatment are performed. Without it, the desired mechanical properties cannot be obtained.
【０００３】[0003]
【発明が解決しようとする課題】しかし、自動車部品等
に対しては、機械的性質に加えてコスト低減の要求も強
く、部品材料として使用されるＡｌ合金鋳物の材料費低
減が望まれている。ところで、前述したＡｌ−Ｓｉ系合
金では、必要な性質を得るために溶体化処理を経た時効
処理が必要であるが、この溶体化処理は高温長時間で行
われるために、作業時間および加熱エネルギの点からコ
ストを増大させる要因になっている。このため、溶体化
処理を要することなく所望の機械的性質が得られる材料
の開発が望まれている。However, for automobile parts and the like, there is a strong demand for cost reduction in addition to mechanical properties, and it is desired to reduce the material cost of Al alloy castings used as part materials. . By the way, in the above-mentioned Al-Si alloy, an aging treatment after a solution treatment is necessary in order to obtain necessary properties, but since this solution treatment is performed at a high temperature for a long time, the working time and the heating energy are increased. Therefore, it is a factor that increases the cost. Therefore, it is desired to develop a material that can obtain desired mechanical properties without requiring solution treatment.
【０００４】また、耐食性の良好な非熱処理型のＡｌ−
Ｍｇ系合金に着目して、Ｚｎなどを添加することにより
強度や鋳造性を改善したＡｌ合金が提案されている（特
公平６−４７７０４号）。しかし、この合金の耐力は高
々１５ｋｇ／ｍｍ2程度であり、自動車部品等に適用す
るには強度が不十分である。Further, a non-heat treatment type Al- which has good corrosion resistance
Focusing on Mg alloys, Al alloys having improved strength and castability by adding Zn and the like have been proposed (Japanese Patent Publication No. 6-47704). However, the yield strength of this alloy is at most about 15 kg / mm 2 , and its strength is insufficient for application to automobile parts and the like.
【０００５】本発明は、上記事情を背景としてなされた
ものであり、溶体化処理を経ずに時効処理だけで、十分
な強度（引張強さと耐力）と伸びが得られ、さらに耐食
性や鋳造性が良好で、自動車部品等に好適な鋳造用アル
ミニウム合金およびその製造法を提供するものである。The present invention has been made in view of the above circumstances. Sufficient strength (tensile strength and yield strength) and elongation can be obtained only by aging treatment without solution treatment, and further corrosion resistance and castability can be obtained. And an aluminum alloy for casting suitable for automobile parts and the like and a method for producing the same.
【０００６】[0006]
【課題を解決するための手段】本発明者らは、上述の従
来技術の問題に対し、鋭意検討を重ねた結果、引張強
さ、耐食性および鋳造性に優れたＡｌ−Ｍｇ−Ｚｎ系に
着目し、この系において人工時効による析出によって強
化する作用のあるＳｉを添加し、さらに冷却速度の速い
鋳造法を用いることによって、これらの元素を過飽和に
強制固溶させることにより、所期の目的が達成されるこ
とを見い出した。DISCLOSURE OF THE INVENTION As a result of intensive studies on the above-mentioned problems of the prior art, the present inventors have focused on an Al--Mg--Zn system having excellent tensile strength, corrosion resistance and castability. However, by adding Si, which has the effect of strengthening by precipitation by artificial aging in this system, and by using a casting method with a faster cooling rate, these elements are forced to form a solid solution in supersaturation, thereby achieving the intended purpose. I have found that it can be achieved.
【０００７】すなわち、本発明のうち第１の発明の鋳造
用アルミニウム合金は、重量％で、Ｍｇ：２．５〜５．
５％、Ｚｎ：１〜３％、Ｓｉ：０．２％越え〜０．６
％、Ｍｎ：０．１〜２％を含み、残部がＡｌと不可避不
純物からなる組成を有することを特徴とする。第２の発
明の鋳造用アルミニウム合金は、第１の発明の成分に加
え、重量％で、Ｔｉ：０．００５〜０．１０％未満また
は前記ＴｉとＢ：０．０００１〜０．００４％の２種を
含有することを特徴とする。第３の発明の鋳造用アルミ
ニウム合金は、第１または第２の発明の成分に加え、重
量％で、Ｂｅ：０．０００１〜０．０１％を含有するこ
とを特徴とする。That is, the aluminum alloy for casting according to the first aspect of the present invention is Mg: 2.5-5.
5%, Zn: 1-3%, Si: 0.2% over-0.6
%, Mn: 0.1 to 2%, with the balance being Al and inevitable impurities. The aluminum alloy for casting of the second invention, in addition to the components of the first invention, has a weight% of Ti: 0.005 to less than 0.10% or Ti and B: 0.0001 to 0.004%. It is characterized by containing two kinds. The casting aluminum alloy of the third invention is characterized in that, in addition to the components of the first or second invention, it contains Be: 0.0001 to 0.01% by weight.
【０００８】第４の発明のアルミニウム合金鋳造材の製
造方法は、第１〜第３の発明のいずれかに記載の組成を
有する合金溶湯を、５０℃／ｍｉｎ以上の冷却速度で凝
固させ、その後、１５０〜２２０℃の温度範囲で０．５
〜１６時間加熱することを特徴とする。A method for manufacturing an aluminum alloy cast material according to a fourth aspect of the present invention is to solidify an alloy melt having a composition according to any one of the first to third aspects of the invention at a cooling rate of 50 ° C./min or more, and thereafter. 0.5 in the temperature range of 150 to 220 ° C
It is characterized by heating for ~ 16 hours.
【０００９】[0009]
【発明の実施の形態】本発明のアルミニウム合金は公知
の製造方法によって製造することができ、望ましくは鋳
造時の冷却速度を５０℃／ｍｉｎ以上とする。これによ
り、Ａｌ中に強化元素のＳｉ、Ｍｇ、Ｚｎ、Ｍｎを過飽
和に強制固溶させることができる。５０℃／ｍｉｎ未満
では特にＳｉの過飽和固溶量が不十分となり、後の時効
処理（溶体化処理を含まない、以下同じ）において十分
な時効硬化が得られない。さらに、５０℃／ｍｉｎ未満
の冷却速度では、Ｍｇ、Ｚｎ、Ｍｎの固溶量が低下し、
強度が低下すると同時に、粗大な晶出物量が増加し、伸
びが著しく低下する。凝固時に５０℃／ｍｉｎ以上の冷
却速度を実現するための鋳造法としては、Ｄ．Ｃ．鋳造
法、ダイカスト法、高圧鋳造法などがあるが、高品質の
複雑形状の鋳物を製造するには高圧鋳造法が望ましい。BEST MODE FOR CARRYING OUT THE INVENTION The aluminum alloy of the present invention can be manufactured by a known manufacturing method, and the cooling rate during casting is preferably 50 ° C./min or more. As a result, the strengthening elements Si, Mg, Zn, and Mn can be forced into a supersaturated solid solution in Al. If it is less than 50 ° C./min, the supersaturated solid solution amount of Si becomes particularly insufficient, and sufficient age hardening cannot be obtained in the subsequent aging treatment (excluding solution treatment, the same applies hereinafter). Furthermore, when the cooling rate is less than 50 ° C./min, the solid solution amounts of Mg, Zn, and Mn decrease,
At the same time as the strength decreases, the amount of coarse crystallized substances increases and the elongation remarkably decreases. As a casting method for achieving a cooling rate of 50 ° C./min or more during solidification, D. C. There are casting method, die casting method, high pressure casting method and the like, but the high pressure casting method is preferable for producing a high quality casting having a complicated shape.
【００１０】溶製されたアルミニウム合金鋳造材には、
溶体化処理を経ることなく、１５０〜２２０℃の温度範
囲で０．５〜１６時間加熱する、いわゆるＴ５処理を施
すことによって時効硬化が起こる。この処理により、溶
体化処理を経ないでも微細なＭｇ2Ｓｉ化合物が析出
し、強度が向上する。なお、時効温度が１５０℃未満で
は所期の強度を得るためには時効時間が長時間となり不
経済であり、一方、時効温度が２２０℃超あるいは時効
時間が３０分未満では所期の強度が得られない。得られ
たアルミニウム鋳造材は、高い強度（特に耐力）と伸び
を有し、さらに優れた耐食性を有しており、前述したよ
うに足回り部品、エンジン回り部品等の自動車部品とし
て用いることができる。また、その他には機械部品、電
気機器部品等への適用も考えられるが、本発明の用途
が、これら例示したものに限定されるものではない。The molten aluminum alloy cast material includes
Age hardening occurs by performing a so-called T5 treatment of heating in a temperature range of 150 to 220 ° C. for 0.5 to 16 hours without performing solution treatment. By this treatment, a fine Mg 2 Si compound is deposited without the solution treatment and the strength is improved. If the aging temperature is less than 150 ° C, it is uneconomical because the aging time becomes long to obtain the desired strength, while if the aging temperature exceeds 220 ° C or the aging time is less than 30 minutes, the desired strength is not obtained. I can't get it. The obtained aluminum cast material has high strength (especially yield strength) and elongation, and further has excellent corrosion resistance, and as described above, it can be used as an automobile part such as an undercarriage part and an engine part. . Further, other applications such as mechanical parts and electric equipment parts are also conceivable, but the use of the present invention is not limited to those exemplified above.
【００１１】なお、本発明のアルミニウム合金における
各成分が果たす作用およびその限定の理由を以下に説明
する。 （ａ）Ｍｇ：２．５〜５．５％ ＭｇはＡｌ中に固溶してベース強度を上げるとともに、
一部が時効処理によりＳｉと共に析出して強度を向上さ
せる。但し、２．５％未満では、その効果が少なく所望
の高強度を確保できない。一方、５．５％を越えるとＡ
ｌ−Ｍｇ系の晶出物の量が増えて伸びが低下するだけで
なく、鋳造性も低下し、また、応力腐食割れ性を助長す
るので、Ｍｇ含有量を上記範囲に定めた。なお、上記と
同様の理由で下限を２．５％、上限を４．５％未満とす
るのが望ましく、さらに、上限を４．０％以下とするの
が一層望ましい。The action of each component in the aluminum alloy of the present invention and the reason for its limitation will be described below. (A) Mg: 2.5 to 5.5% Mg forms a solid solution in Al to increase the base strength, and
A part of it precipitates together with Si by the aging treatment and improves the strength. However, if it is less than 2.5%, its effect is small and desired high strength cannot be secured. On the other hand, if it exceeds 5.5%, A
Not only does the amount of l-Mg-based crystallized material increase and the elongation decreases, but also the castability decreases, and the stress corrosion cracking property is promoted. Therefore, the Mg content is set within the above range. For the same reason as above, the lower limit is preferably 2.5% and the upper limit is less than 4.5%, and more preferably the upper limit is 4.0% or less.
【００１２】（ｂ）Ｚｎ：１〜３％ Ｚｎは鋳造性向上させ、またＭｇ2Ｓｉの析出硬化を促
進して機械的性質を向上させる。但し、１％未満では、
その効果が少なく、一方、３％を越えるとＭｇＺｎ2化
合物が多量に晶出し伸びが低下するだけでなく、耐食性
も劣化するので、Ｚｎ含有量を上記範囲に定めた。(B) Zn: 1-3% Zn improves castability and promotes precipitation hardening of Mg 2 Si to improve mechanical properties. However, if less than 1%,
The effect is small, while if it exceeds 3%, not only a large amount of MgZn 2 compound is crystallized but the elongation is lowered, but also the corrosion resistance is deteriorated. Therefore, the Zn content is set within the above range.
【００１３】（ｃ）Ｓｉ：０．２％越え〜０．６％ Ｓｉは時効処理によりＭｇと結合して微細なＭｇ2Ｓｉ
化合物として析出して強度を向上させる。但し、０．２
％以下では、その効果がなく、一方０．６％を越えると
凝固時およびその後の冷却中に粗大なＭｇ2Ｓｉ化合物
を生成し伸びが低下する。また、Ｓｉは焼入れ感受性を
阻害する元素であり、０．６％を越える過量の添加は避
ける必要があるので、Ｓｉ含有量を上記範囲に定めた。
なお、同様の理由で下限を０．３％、上限を０．５％と
するのが望ましい。(C) Si: over 0.2% to 0.6% Si is combined with Mg by aging treatment to form fine Mg 2 Si.
Precipitates as a compound to improve strength. However, 0.2
%, The effect is not obtained. On the other hand, if it exceeds 0.6%, a coarse Mg 2 Si compound is formed during solidification and cooling thereafter, and elongation is reduced. Further, Si is an element that inhibits quenching sensitivity, and it is necessary to avoid adding an excessive amount exceeding 0.6%. Therefore, the Si content is set within the above range.
For the same reason, it is desirable to set the lower limit to 0.3% and the upper limit to 0.5%.
【００１４】（ｄ）Ｍｎ：０．１〜２．０％ Ｍｎは鋳造性、耐食性を向上させ、さらに靭性、伸び等
の機械的性質を向上させる。また、Ｍｇと化合しないで
残存したＳｉと化合し、Ｓｉによる焼入れ感受性の低下
を防止する。但し、０．１％未満では、これらの効果が
なく、一方、２．０％を越えると粗大なＡｌ6Ｍｎ化合
物が晶出し、機械的性質が著しく低下する。なお、同様
の理由で下限を０．８％、上限を１．５％に限定するの
が望ましい。(D) Mn: 0.1 to 2.0% Mn improves castability and corrosion resistance, and further improves mechanical properties such as toughness and elongation. Further, it combines with the remaining Si without combining with Mg, and prevents deterioration of quenching sensitivity due to Si. However, if it is less than 0.1%, these effects are not exhibited, while if it exceeds 2.0%, a coarse Al 6 Mn compound is crystallized and the mechanical properties are remarkably deteriorated. For the same reason, it is desirable to limit the lower limit to 0.8% and the upper limit to 1.5%.
【００１５】（ｅ）Ｔｉ：０．００５〜０．１０％未
満、Ｂ：０．０００１〜０．００４％ Ｔｉは、鋳造組織を微細化すると共に、鋳造割れを防止
する為に添加される。このためには０．００５％以上の
含有が必要であり、一方、過度に含有させると、粗大な
Ｔｉ化合物を生成して伸びを低下させるので上限を０．
１０％未満とする。なお、同様の理由で上限を０．０５
％以下とするのが望ましい。また、Ｂは、Ｔｉとの複合
添加により上記作用を増大させる。そのためには０．０
００１％以上の含有が必要であり、一方、０．００４％
を越えて含有させても効果は飽和するので、Ｂ含有量を
上記範囲に定めた。 （ｆ）Ｂｅ：０．０００１〜０．０１％ Ｂｅは溶解時のＭｇの酸化を防止し、鋳造性を向上する
働きがある。この作用を得るためには０．０００１％以
上の含有が必要であり、一方、０．０１％を越えて含有
させても、その効果は飽和するのでＢｅ含有量を上記範
囲とした。(E) Ti: 0.005 to less than 0.10%, B: 0.0001 to 0.004% Ti is added in order to refine the cast structure and prevent casting cracks. For this purpose, the content of 0.005% or more is required. On the other hand, if it is excessively contained, a coarse Ti compound is formed and the elongation is lowered, so the upper limit is set to 0.
It is less than 10%. The upper limit is 0.05 for the same reason.
% Is desirable. Further, B increases the above-mentioned action by the combined addition of Ti. For that, 0.0
001% or more is required, while 0.004%
If the content exceeds B, the effect is saturated, so the B content is set within the above range. (F) Be: 0.0001 to 0.01% Be has a function of preventing oxidation of Mg during melting and improving castability. In order to obtain this effect, it is necessary to contain 0.0001% or more. On the other hand, if the content exceeds 0.01%, the effect is saturated, so the Be content is set to the above range.
【００１６】[0016]
【実施例】自動車用のエンジンブラケットを想定して、
Ａｌ鋳造材の目標値を耐力で２００ＭＰａ以上、伸びを
８％とし、以下の実験を行った。すなわち表１に示すＡ
ｌ合金（発明合金および比較合金）を溶解した後、Ｄ．
Ｃ．鋳造または金型鋳造により、４５×１８０×２５０
ｍｍ3の鋳塊を作成した。なお、Ｄ．Ｃ鋳造では、６０
０℃／ｍｉｎの凝固速度が得られ、金型鋳造では３０℃
／ｍｉｎの凝固速度が得られた。得られた鋳塊からＪＩ
Ｓ４号引張試験片を切り出し、１８０℃で８時間の時効
処理を施した後、引張試験を行い、その結果を表２に示
した。なお、各鋳造材に使用されているアルミニウム合
金は、鋳造材Ｎｏ．と同一Ｎｏ．のものである。[Example] Assuming an engine bracket for an automobile,
The following experiments were conducted with the target values of the Al cast material being 200 MPa or more in yield strength and 8% elongation. That is, A shown in Table 1
After melting the alloys (invention alloy and comparative alloy), D.I.
C. 45 x 180 x 250 by casting or die casting
An ingot of mm 3 was prepared. In addition, D. 60 in C casting
A solidification rate of 0 ° C / min is obtained, and 30 ° C in die casting.
A coagulation rate of / min was obtained. From the obtained ingot, JI
A No. S4 tensile test piece was cut out, subjected to an aging treatment at 180 ° C. for 8 hours, and then subjected to a tensile test. The results are shown in Table 2. The aluminum alloy used for each cast material is the cast material No. Same as No. belongs to.
【００１７】表から明らかなように、本発明材Ｎｏ．１
〜８は、引張強さが２９０ＭＰａ以上、耐力が２１０Ｍ
Ｐａ以上、伸びが８％以上と高く、高い強度と伸びを具
備している。但し、発明材のうちで、金型鋳造を採用し
たＮｏ．９は、強度の向上がその他の発明材に比べて低
く、鋳造時に５０℃／ｍｉｎ以上の凝固速度で凝固させ
るのが望ましいことが理解される。これに対し、化学組
成が本発明の範囲から外れている比較材Ｎｏ．１０〜１
８では耐力、伸びのいずれかが劣っており、アルミニウ
ム鋳造材として設定した目標値を満たすことはできなか
った。なお、比較合金Ｎｏ．１８は従来材に相当するＡ
Ｃ４ＣＨ相当材であり、溶体化処理を施さない場合には
強度が低く、使用に耐え得ないものであることが明らか
となっている。As is clear from the table, the material No. 1
Up to 8 has a tensile strength of 290 MPa or more and a proof stress of 210 M
It has a high Pa and a high elongation of 8%, and has high strength and elongation. However, among the invention materials, No. 1 adopting die casting was used. It is understood that in No. 9, the improvement in strength is lower than that of other invention materials, and it is desirable to solidify at a solidification rate of 50 ° C./min or more during casting. On the other hand, Comparative Material No. having a chemical composition outside the range of the present invention. 10-1
In No. 8, either the yield strength or the elongation was inferior, and the target value set as the aluminum casting material could not be satisfied. In addition, comparative alloy No. 18 is A corresponding to the conventional material
It has been clarified that it is a material equivalent to C4CH and has low strength and cannot withstand use when it is not subjected to solution treatment.
【００１８】[0018]
【表１】 [Table 1]
【００１９】[0019]
【表２】 [Table 2]
【００２０】[0020]
【発明の効果】以上説明したように本発明の鋳造用アル
ミニウム合金によれば、溶体化処理を経ない時効処理に
よって所望の機械的性質（特に、耐力、伸び）が得ら
れ、製造工程の簡略化により品質を損なうことなくコス
トを低減することができる。また、本発明のアルミニウ
ム合金鋳造材の製造方法によれば、簡易な時効処理によ
って耐力、伸びに優れた鋳造材を得ることができる。As described above, according to the aluminum alloy for casting of the present invention, desired mechanical properties (in particular, yield strength and elongation) can be obtained by aging treatment without solution treatment, and the manufacturing process can be simplified. The cost can be reduced without compromising the quality. Further, according to the method for producing a cast aluminum alloy material of the present invention, a cast material excellent in yield strength and elongation can be obtained by a simple aging treatment.
Claims (4)
ｎ：１〜３％、Ｓｉ：０．２％越え〜０．６％、Ｍｎ：
０．１〜２％を含み、残部がＡｌと不可避不純物からな
る組成を有することを特徴とする鋳造用アルミニウム合
金1. Mg: 2.5 to 5.5% by weight, Z
n: 1-3%, Si: over 0.2% -0.6%, Mn:
Aluminum alloy for casting, characterized by containing 0.1 to 2% and the balance being Al and unavoidable impurities.
Ｔｉ：０．００５〜０．１０％未満または前記Ｔｉと
Ｂ：０．０００１〜０．００４％の２種を含有すること
を特徴とする鋳造用アルミニウム合金2. In addition to the components of claim 1, in weight percent,
Aluminum alloy for casting, characterized by containing two kinds of Ti: 0.005 to less than 0.10% or Ti and B: 0.0001 to 0.004%.
重量％で、Ｂｅ：０．０００１〜０．０１％を含有する
ことを特徴とする鋳造用アルミニウム合金3. In addition to the component according to claim 1 or 2,
Aluminum alloy for casting, characterized by containing Be: 0.0001 to 0.01% by weight
有する合金溶湯を、５０℃／ｍｉｎ以上の冷却速度で凝
固させ、その後、１５０〜２２０℃の温度範囲で０．５
〜１６時間加熱することを特徴とするアルミニウム合金
鋳造材の製造方法4. A molten alloy having the composition according to any one of claims 1 to 3 is solidified at a cooling rate of 50 ° C./min or more, and then 0.5 in a temperature range of 150 to 220 ° C.
~ 16 hours heating method for producing aluminum alloy cast material
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21253295A JPH0941064A (en) | 1995-07-28 | 1995-07-28 | Production of aluminum alloy for casting and aluminum alloy casting material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21253295A JPH0941064A (en) | 1995-07-28 | 1995-07-28 | Production of aluminum alloy for casting and aluminum alloy casting material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0941064A true JPH0941064A (en) | 1997-02-10 |
Family
ID=16624239
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21253295A Pending JPH0941064A (en) | 1995-07-28 | 1995-07-28 | Production of aluminum alloy for casting and aluminum alloy casting material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0941064A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1138794A1 (en) * | 2000-03-31 | 2001-10-04 | Corus Aluminium Voerde GmbH | Aliminium die-casting alloy |
| JP2010144253A (en) * | 2010-01-21 | 2010-07-01 | Nippon Light Metal Co Ltd | Method for producing aluminum alloy casting material having excellent thermal conductivity |
| CN103589922A (en) * | 2013-11-29 | 2014-02-19 | 辽宁忠旺集团有限公司 | Technology for producing aluminum alloy section bar for ships |
| CN103602839A (en) * | 2013-10-14 | 2014-02-26 | 广西南南铝加工有限公司 | Processing method for aluminium alloy middle thick plate |
| JP2014136258A (en) * | 2013-01-17 | 2014-07-28 | Kienle & Spiess Gmbh | Method of manufacturing casting metal for used in electric field |
| US8936688B2 (en) | 2004-04-05 | 2015-01-20 | Nippon Light Metal Company, Ltd. | Aluminum alloy casting material for heat treatment excelling in heat conduction and process for producing the same |
| CN105219986A (en) * | 2015-10-31 | 2016-01-06 | 林州市林丰铝电有限责任公司 | A kind of production method of aluminum alloy casting |
| JP2016514209A (en) * | 2013-03-09 | 2016-05-19 | アルコア インコーポレイテッド | Heat-treatable aluminum alloy containing magnesium and zinc and method for producing the same |
-
1995
- 1995-07-28 JP JP21253295A patent/JPH0941064A/en active Pending
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1138794A1 (en) * | 2000-03-31 | 2001-10-04 | Corus Aluminium Voerde GmbH | Aliminium die-casting alloy |
| US6773664B2 (en) | 2000-03-31 | 2004-08-10 | Corus Aluminium Voerde Gmbh | Aluminium die-casting alloy |
| US6929706B2 (en) | 2000-03-31 | 2005-08-16 | Corus Aluminium Voerde Gmbh | Aluminum die-casting alloy |
| US8936688B2 (en) | 2004-04-05 | 2015-01-20 | Nippon Light Metal Company, Ltd. | Aluminum alloy casting material for heat treatment excelling in heat conduction and process for producing the same |
| JP2010144253A (en) * | 2010-01-21 | 2010-07-01 | Nippon Light Metal Co Ltd | Method for producing aluminum alloy casting material having excellent thermal conductivity |
| JP2014136258A (en) * | 2013-01-17 | 2014-07-28 | Kienle & Spiess Gmbh | Method of manufacturing casting metal for used in electric field |
| JP2016514209A (en) * | 2013-03-09 | 2016-05-19 | アルコア インコーポレイテッド | Heat-treatable aluminum alloy containing magnesium and zinc and method for producing the same |
| CN103602839A (en) * | 2013-10-14 | 2014-02-26 | 广西南南铝加工有限公司 | Processing method for aluminium alloy middle thick plate |
| CN103589922A (en) * | 2013-11-29 | 2014-02-19 | 辽宁忠旺集团有限公司 | Technology for producing aluminum alloy section bar for ships |
| CN103589922B (en) * | 2013-11-29 | 2015-09-16 | 辽宁忠旺集团有限公司 | A kind of technique of producing boats and ships aluminium alloy extrusions |
| CN105219986A (en) * | 2015-10-31 | 2016-01-06 | 林州市林丰铝电有限责任公司 | A kind of production method of aluminum alloy casting |
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