JPS63145741A - Al-cu-mg high tensile aluminum alloy for casting and its production - Google Patents
Al-cu-mg high tensile aluminum alloy for casting and its productionInfo
- Publication number
- JPS63145741A JPS63145741A JP29261486A JP29261486A JPS63145741A JP S63145741 A JPS63145741 A JP S63145741A JP 29261486 A JP29261486 A JP 29261486A JP 29261486 A JP29261486 A JP 29261486A JP S63145741 A JPS63145741 A JP S63145741A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- casting
- alloy
- strength
- small amount
- 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 62
- 238000005266 casting Methods 0.000 title claims abstract description 32
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 229910017818 Cu—Mg Inorganic materials 0.000 claims abstract description 31
- 238000011282 treatment Methods 0.000 claims abstract description 18
- 230000032683 aging Effects 0.000 claims abstract description 7
- 238000002844 melting Methods 0.000 claims abstract description 4
- 230000008018 melting Effects 0.000 claims abstract description 4
- 238000010791 quenching Methods 0.000 claims abstract description 4
- 230000000171 quenching effect Effects 0.000 claims abstract description 3
- 238000005496 tempering Methods 0.000 claims abstract 2
- 229910018182 Al—Cu Inorganic materials 0.000 claims 2
- 229910045601 alloy Inorganic materials 0.000 abstract description 16
- 239000000956 alloy Substances 0.000 abstract description 16
- 229910052720 vanadium Inorganic materials 0.000 abstract description 11
- 229910052721 tungsten Inorganic materials 0.000 abstract description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 abstract description 2
- 230000002929 anti-fatigue Effects 0.000 abstract 1
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 16
- 239000007789 gas Substances 0.000 description 10
- 229910052786 argon Inorganic materials 0.000 description 8
- 238000007664 blowing Methods 0.000 description 8
- 238000007872 degassing Methods 0.000 description 7
- 238000010276 construction Methods 0.000 description 5
- 239000000243 solution Substances 0.000 description 5
- 238000009849 vacuum degassing Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 238000005452 bending Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 229910000737 Duralumin Inorganic materials 0.000 description 1
- 241000257465 Echinoidea Species 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000007667 floating Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
Landscapes
- Continuous Casting (AREA)
- Forging (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は車両、船舶、陸上機械分野で用いられるｖＩ造
用ＡＮ−Ｃｕ−Ｍｇ系高力アルミニウム合金及びその製
造方法に関するしのである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to an AN-Cu-Mg-based high-strength aluminum alloy for VII construction used in the fields of vehicles, ships, and land machinery, and a method for producing the same.
［従来の技術］
一般にｆ）造品とＫ ７ｊ４品とでは、礪械的性質につ
いて鍛造品が優れていることは周知の如くである。[Prior Art] It is generally known that forged products are superior in terms of mechanical properties between f) forged products and K7J4 products.
黙しながら、鋳造でなければ！Ｆ！！造できない形状の
部品もあり、近年車両、船舶、陸上機械分野においては
疲労強度に優れ、耐熱性を有する！８Ｔｌ川高力アルミ
ニウム合金が求められている。Silently, if it's not a casting! F! ! There are some parts with shapes that cannot be manufactured, and in recent years, it has excellent fatigue strength and heat resistance in the fields of vehicles, ships, and land machinery! 8Tl high strength aluminum alloy is desired.
従来、鋳造用高力アルミニウム合金としては、例えばジ
ュラルミンに代表される。ｌｌ−Ｃｕ−Ｍｏ系アルミニ
ウム合金がある。このＡｆ−Ｃｕ−Ｍｇ系を基本組成と
した合金としては、スミカＯイＨ−１３（日本） 、Ｘ
１４９（米国） 、ＫＯ−１（米国）等の合金が開
発されている。なかでも、スミカロイｌ−１−１３（特
公昭５２−２１４４８号）は重量百分率でＣＩＩ ：
４．２〜５．２％、Ｍｇ： ０，２〜０．４％。Conventionally, a high-strength aluminum alloy for casting is typified by, for example, duralumin. There is an ll-Cu-Mo aluminum alloy. As alloys whose basic composition is this Af-Cu-Mg system, Sumika Oi H-13 (Japan), X
Alloys such as 149 (USA) and KO-1 (USA) have been developed. Among them, Sumikaloy 1-1-13 (Special Publication No. 52-21448) has a weight percentage of CII:
4.2-5.2%, Mg: 0.2-0.4%.
Ｓｔ ： ０，１５〜０．３％、 Ｆｅ ：
０，１以下、Ｍｎ：０．１〜０．５％、７ｉ：０，１
〜０．３％、３：０，０１〜０．１％から成るアルミニ
ウム合金であり、その機械的性質は引張強さ４８ｋｇ／
ａ＋ｍ２のとき０．２％耐力４３ｋｇ／ｍｍ２ 、伸び
６％を示す優れた合金である。St: 0.15~0.3%, Fe:
0.1 or less, Mn: 0.1 to 0.5%, 7i: 0.1
It is an aluminum alloy consisting of ~0.3% and 3:0.01~0.1%, and its mechanical properties are tensile strength of 48 kg/
It is an excellent alloy that exhibits a 0.2% yield strength of 43 kg/mm2 and an elongation of 6% at a+m2.
［発明が解決しようとする問題点］
ところで、このスミ力ロイト１−１３にあっては次のご
とき問題点があった。[Problems to be Solved by the Invention] By the way, this Sumiyuki Reuto 1-13 had the following problems.
１０７ サイクルにおける疲労強度は９に！；ｌ ／１
１１１２であり、この値は他の一般的鋳造用合金、例え
ばＡ３５６等と比較して劣っているという問題があった
。Fatigue strength in 107 cycles is 9! ;l/1
1112, and there was a problem in that this value was inferior to that of other general casting alloys, such as A356.
またｔ！ｒＴｉ割れが発生し易＜ 、ｕ ３１性の面に
おいても劣っているという問題があった。T again! There were problems in that rTi cracking was likely to occur and the U31 properties were also poor.
上述のごとき問題点に鑑みて本発明は疲労強度及び鋳造
性を向上させると共に、耐熱性を向上させて鍛造品に匹
敵する鋳造用Ａｊ！−Ｃｕ−Ｍｇ系高力アルミニウム合
金を１に供することを目的とするものである。In view of the above-mentioned problems, the present invention improves fatigue strength and castability, as well as improves heat resistance, making it comparable to forged products. -Cu-Mg based high-strength aluminum alloy.
［問題点を解決するための手段］
従来技術における問題点を解決するために第１の発明の
鋳造用Ａ ｌｌ−Ｃｕ−Ｍｇ系高力アルミニウム合金は
Ａｊ！−Ｃｕ−Ｍｇ系アルミニウム合金に少量のＶと少
量のＷとを添加したものである。[Means for Solving the Problems] In order to solve the problems in the prior art, an All-Cu-Mg based high-strength aluminum alloy for casting according to the first invention is developed. -Cu-Mg-based aluminum alloy with a small amount of V and a small amount of W added.
また、第２の発明の鋳造用ＡＩｌ−Ｃｕ−Ｍｇ系高力ア
ルミニウム合金の製造方法は少量のＶと少δのＷとを添
加したＡｆ−Ｃｕ−Ｍ（ｌ系ア□ルミニウム合金を真空
雰囲気中で２２１製してｗＩ造し、５２０℃付近で溶体
化処理した後、焼゛入れし、１６０℃付近で焼もどして
人工時効処理するものである。In addition, the method for producing the Al-Cu-Mg-based high-strength aluminum alloy for casting according to the second invention involves producing an Af-Cu-M (l-based aluminum alloy with a small amount of V and a small amount of W) in a vacuum atmosphere. It is made by manufacturing 221 in a wafer, solution-treated at around 520°C, quenched, tempered at around 160°C, and subjected to artificial aging treatment.
［作 用］
第゛１の発明の如く構成され、上記へβ−Ｃｕ −Ｍｏ
系アルミニウム合金に上記少量のＶを添加したことによ
り、Ａｆ−Ｃｕ−Ｍｏ系アルミニウム合金の結晶粒が微
細化されて疲労強度が増大されると共に、Ｂ温じん性が
高められ、焼？１れが防止されてＨ’；ａ ＦＪれが防
止されるものである。且つ、上記少量のＷ＠添加したこ
とにより、耐熱性が向上されるものである。[Function] Constructed as in the first invention, β-Cu-Mo
By adding the above-mentioned small amount of V to the Af-Cu-Mo-based aluminum alloy, the grains of the Af-Cu-Mo-based aluminum alloy are made finer and the fatigue strength is increased. 1 is prevented, and H';a FJ is prevented. Moreover, by adding the above-mentioned small amount of W@, heat resistance is improved.
また、第２の発明の如くなされ、上記少量の■と上記少
量のＷとが添加されて真空雰囲気中で溶製され、大気中
または真空雰囲気中で鋳造されたＡｆ−Ｃｕ−Ｍｇ系ア
ルミニウム合金に５２０℃付近で溶体化ｆｆ１ｌ！Ｉ！
が施された後、焼入れされ、１６０℃付近で焼もどして
人工時効処理すると、ガス成分、フｒｔＬ属介在物がき
わめて少量なために固溶したＣＬＩＡｊ！ｚが結晶粒内
及び粒界に均一に析出する過程で機械的性質が向上し、
疲労強度が増大するものである。Further, an Af-Cu-Mg-based aluminum alloy made as in the second invention, which is melted in a vacuum atmosphere with the addition of the above small amount (1) and the above small amount W, and is cast in the air or a vacuum atmosphere Solution solution ff1l at around 520℃! I!
After being quenched and then tempered at around 160°C and subjected to artificial aging treatment, CLIAj! gas components and inclusions of the rtL group were dissolved in solid solution due to extremely small amounts. The mechanical properties are improved through the process of uniformly precipitating z within the grains and at the grain boundaries.
This increases fatigue strength.
［実施例］
以下に本発明の！８造用Ａｉ’−ＧＯ−Ｍｏ系高力アル
ミニウム合金及びその製造方法の実施例及びその特性を
添付図面に従って詳述する。[Example] Below are examples of the present invention! Examples of Ai'-GO-Mo-based high-strength aluminum alloys for 8-car construction and methods for producing the same and their characteristics will be described in detail with reference to the accompanying drawings.
ここで、以下に示す第１〜第４の実施例における鋳造用
へで−Ｃｕ−Ｍｇ系高力アルミニウム合金は５２５℃ｘ
１４ｈｒの溶体化処理を行な９た箋、９０℃以上の温
水中にて焼入れ、１６５℃Ｘ ２０ｈｒの焼もどしをし
て人工時効処理を施すというｆｆＪ ｎ方法を採用した
。Here, the -Cu-Mg-based high-strength aluminum alloy for casting in the first to fourth examples shown below was heated at 525°C x
The ffJn method was adopted, in which solution treatment was performed for 14 hours, quenched in hot water at 90°C or higher, tempered at 165°C for 20 hours, and artificial aging treatment was performed.
第１の実施例の鋳造用ＡＩｌ−Ｃｕ−Ｍ！］系＾力アル
ミニウム合金は１１百分率でＣｕ ： ４．７％。First example of casting AIl-Cu-M! ] series aluminum alloy is 11% Cu: 4.7%.
Ｍｇ ： ０，３５％を含有したＡｌ１−ＣＩｌ−Ｍ
ｇ系アルミニウム合金にｉ！重量百分率でＶ：０，１８
％、Ｗ：０．１７％を含有させたものである。第１の実
施例にあっては大気中でアルゴンガスを吹き込む方法に
より脱ガス、なしながら溶製し、大気中で鋳造を行なっ
た。そして、この第１の実施例の鋳造用Ａｉ’−Ｃｕ−
Ｍｇ系高力アルミニウム合金における疲労強度を確認す
べく上記■及びＷを添加しない八で−ＣＬＩＴＭｇ系ア
ルミニウニアルミニウム合金転曲げ試験を常温にて行な
った。Mg: Al1-CIl-M containing 0.35%
i! for g-based aluminum alloys! V in weight percentage: 0,18
%, W: 0.17%. In the first example, the melt was produced while degassing by blowing argon gas in the atmosphere, and casting was performed in the atmosphere. Then, Ai'-Cu- for casting of this first embodiment
In order to confirm the fatigue strength of Mg-based high-strength aluminum alloys, rolling bending tests were conducted on the above-mentioned (1) and -CLIT Mg-based aluminum sea urchin aluminum alloys at room temperature.
第１図は試験結果により１！７られた疲労特性を示すも
のである。図中、■はｆｆ重量百分率でＶ：０．１８％
、 Ｗ： ０．１７％を含有させた場合の疲労特性を
示ずものであり、■は■及びＷを含有しない場合の疲労
特性を示すものである。図示するように、第１の実施例
のｖｉ造用Ａｌ−Ｃｕ−Ｍｇ系高力アルミニウム合金は
Ｖ及びＷの添加により疲労強度が増大していることがＫ
ｌ ｖｔされた。この疲労強度の増加率は１０６サイク
ル強さで１５％、１０７サイクル強さで１Ｇ％を示して
いるが、この値は八で−Ｃｕ−Ｍｇ系アルミニウム合金
に添加するＶ及びＷの添加ｍによって変化するものであ
る。FIG. 1 shows the fatigue properties that were evaluated by 1!7 based on the test results. In the figure, ■ is ff weight percentage, V: 0.18%
, W: 0.17% is not shown, and ■ indicates the fatigue properties when neither ■ nor W is contained. As shown in the figure, the fatigue strength of the Al-Cu-Mg-based high-strength aluminum alloy for VI construction of the first example is increased by the addition of V and W.
l vt was done. The rate of increase in fatigue strength is 15% at the 106th cycle strength and 1G% at the 107th cycle strength, but this value is changed by the addition of V and W added to the -Cu-Mg-based aluminum alloy at 8. It changes.
次に第２の実施例の鋳造用ＡＮ−ＣＩ−Ｍｇ系高力アル
ミニウム合金は重量百分率でＣＩｌ ： ４．６％、
Ｍｇ： ０，３７％を含有した／ｌ！−Ｃｕ−Ｍｃ＋
系アルミニウム合金に重量百分率でＶ：０．１５％。Next, the AN-CI-Mg-based high-strength aluminum alloy for casting of the second example has a weight percentage of CIl: 4.6%,
Mg: Contains 0.37%/l! -Cu-Mc+
V: 0.15% by weight percentage in the aluminum alloy.
Ｗ：０，２５％を含有させたものである。It contains W: 0.25%.
溶製中の溶湯の脱ガス法は第１の実ｆＩＩ！！例と同様
に大気中でアルゴンガスを吹き込む方法により行なった
。そして、第２の実施例の鋳造用Ａｌ−ＣＩＪ−Ｍｇ系
高力アルミニウム合全高力アルミニウム合金すべく上記
Ｖ及びＷを添加しないへ２−Ｃｕ−ＭｒＪ系アルミニウ
ム合金と比較してクリープ試験を２００℃にて行なった
。The degassing method of molten metal during melting is the first practical fII! ! This was carried out by blowing argon gas into the atmosphere in the same manner as in the example. In order to obtain a total high-strength aluminum alloy for casting using Al-CIJ-Mg-based high-strength aluminum of the second embodiment, a creep test of 200 It was carried out at ℃.
第２図は試験結果により得られたクリープ破断特性を示
すものである。図中■は重量百分率でＶ：０．１５％、
Ｗ：０．２５％を含有させた場合のクリープ破断特性を
示すものであり、ＯはＶ及びＷを含有しない場合のクリ
ープ破断特性を示すものである。図示するように、第２
の実施例の鋳ｊ′ｌｉ用ＡＮ−ＣＯ−Ｍｇ系高力アルミ
ニウム合金はＶ及びＷの添加によりクリープ破断強さが
増大していることが確認された。このクリープ破断強度
の増加は０．６ｋｇ／ ｍｍ２程度と小さいが、町らか
に増加傾向を示している。FIG. 2 shows the creep rupture properties obtained from the test results. ■ in the figure is the weight percentage, V: 0.15%,
This shows the creep rupture properties when 0.25% of W is contained, and O shows the creep rupture properties when neither V nor W is contained. As shown, the second
It was confirmed that the creep rupture strength of the AN-CO-Mg-based high-strength aluminum alloy for casting according to Example 1 was increased by the addition of V and W. Although this increase in creep rupture strength is small at about 0.6 kg/mm2, it shows a gradual increasing trend.
また、第２の実施例のｔ２ｆ造用ＡクーＣｌ１−Ｍ０系
高力アルミニウム合金の２００℃におけるクリ−プ破断
強さはｆＩ造用アルミニウム合金の中でも浸れた耐熱性
を示す２６１８合金のクリープ破断強さに匹敵する。更
に、第２の実施例の１８造用Ａｌ−ＣＬＩ−Ｍｇ系高力
アルミニウム合金に重量百分率で０．０５〜０．２％ま
でのＡＱを添加すると、耐熱性がより増大することがｒ
１１認された。In addition, the creep rupture strength at 200°C of the Aku Cl1-M0 series high-strength aluminum alloy for T2F construction in the second example is comparable to the creep rupture strength of the 2618 alloy, which exhibits the highest heat resistance among the aluminum alloys for fI construction. comparable in strength. Furthermore, when AQ is added in an amount of 0.05 to 0.2% by weight to the 18-frame Al-CLI-Mg high-strength aluminum alloy of the second example, the heat resistance is further increased.
11 approved.
また、第３の実施例の鋳造用△６−Ｃｕ −Ｍｇ系高力
アルミニウム合金は重量百分率でＣｕ ：５．３％、
Ｍｇ ： ０，３２％を含有したＡｌ−Ｃｕ−Ｍｇ系
アルミニウム合金に重り百分率でＶ：０．１９％、Ｗ：
０．０９％を含有させたものである。Further, the △6-Cu-Mg-based high-strength aluminum alloy for casting of the third embodiment has a weight percentage of Cu: 5.3%,
Al-Cu-Mg based aluminum alloy containing Mg: 0.32%, V: 0.19%, W:
It contains 0.09%.
特に第３の実施例にあっては７１０℃で３０分間ロータ
リポンプにて排気して真空脱ガス処理を施しながら溶製
し、大気中で鋳造したものである。そして、この第３の
実施例の鋳造用ＡＪ２−Ｃｕ −Ｍｇ系高力アルミニウ
ム合金における疲労強度をＷ１認すべく上記■及びＷを
添加せず、旦つ大気中でアルゴンガス吹き込み脱ガスを
行なったΔＲ−Ｃｕ−Ｍｇ系アルミニウム含アルミニウ
ム合金にて回転曲げ試験を行なった。In particular, in the third embodiment, the melt was produced at 710° C. for 30 minutes using a rotary pump to perform vacuum degassing treatment, and then cast in the atmosphere. In order to confirm the fatigue strength of the AJ2-Cu-Mg-based high-strength aluminum alloy for casting of this third example as W1, the above-mentioned (2) and W were not added, and degassing was performed by blowing argon gas in the atmosphere. A rotating bending test was conducted on the ΔR-Cu-Mg-based aluminum-containing alloy.
第３図は試験結果により得られた疲労特性を示すもので
ある。図中、［相］は凱厨百分率でＶ：０．１９％、Ｗ
：０．０９％を含有させ真空脱ガス処理した場合の疲労
特性を示すものであり、［相］はＶ及びＷを含有せず大
気中でアルゴンガス吹き込み脱ガスを行なった場合の疲
労特性を示すものである。図示するように、第３の実施
例の鋳造用Ａｌ７Ｃｕ−Ｍｇ系高力アルミニウム合金は
真空脱ガス処理を施すことにより■及びＷの添加の効果
は著しく増大しているのが確認された。FIG. 3 shows the fatigue properties obtained from the test results. In the figure, [phase] is expressed as a percentage of V: 0.19%, W
:0.09% and vacuum degassing treatment, [phase] shows the fatigue characteristics when degassing is performed by blowing argon gas in the atmosphere without containing V or W. It shows. As shown in the figure, it was confirmed that the effect of addition of (1) and W was significantly increased by vacuum degassing treatment of the Al7Cu-Mg high-strength aluminum alloy for casting of the third example.
この疲労強度の増加率は１０ サイクル強さで１３ｋ
ｇ、、’ｍｎ＋２以上であり、これはＶ及びＷを含有せ
ず大気中でアルゴンガス吹き込み脱ガスを行なった合金
と比較して４０％以上もの著しい増加を示した。The rate of increase in fatigue strength is 13k at 10 cycle strength.
g,,'mn+2 or more, which was a remarkable increase of more than 40% compared to an alloy that did not contain V or W and was degassed by blowing argon gas in the atmosphere.
これは真空脱ガス処理を施すことにより１１２等のガス
成分の著しい低減、Ｊｔ合金１ｒｉ介在物生成防止およ
び脱ガスに伴なう非金属介在物の浮上分離ににって合金
の清浄化、析出相の均一化が実現されろためである。This is achieved by performing vacuum degassing treatment, which significantly reduces gas components such as 112, prevents the formation of Jt alloy 1ri inclusions, and cleans the alloy by floating and separating nonmetallic inclusions due to degassing. This is because the phase should be made uniform.
上記第３の実施例の鋳造用へり−ＣＩｌ−Ｍ（ｌ系高力
アルミニウム合金の常温における疲労強度は７０７５鍛
造材の疲労強度よりも若干劣るが、本発明の合金は第２
の実施例に示した如（耐熱性にも優れていることから、
１００℃以上の温度で使用する場合には鍛造材の代苔と
充分なり（りる。The fatigue strength of the casting edge of the third embodiment -CIl-M (I-based high-strength aluminum alloy at room temperature is slightly inferior to that of 7075 forged material, but the alloy of the present invention is second
As shown in the example (because of its excellent heat resistance,
When used at temperatures above 100°C, it is sufficient as a substitute for forged materials.
更に第４の実施例の鋳造用Ａｌ−へＩｌ−Ｍｇ系高力ア
ルミニウム合金は１ｍｍ分率でＣＬＩ ： ４，７９
６、 Ｍｇ ： ０．２９％を含有したＡｌ−ＣＩｌ
−Ｍｌ）系アルミニウム合金に重量百分率でＶ：０．
１９％、Ｗ：０，１８％を含有させたものである。第４
の実施例にあっては大気中でアルゴンガスを吹き込む方
法により脱ガスをしながら溶興し、大気中で最小羽根厚
０．６ｍｍのターボチャージャーインペラとしてｖＩ造
した。そして、この第４の実施例の鋳造用Ａｆ−Ｃｕ−
Ｍｇ系高力アルミニウム合金製のターボチャージャーイ
ンペラの性能をｌｌ認すべく上記Ｖ及びＷを添加しない
ＡＩｌ−Ｃｕ−Ｍｇ系アルミニウム合金製インペラを製
造して比較を行なった。Furthermore, the Al-Il-Mg based high-strength aluminum alloy for casting in the fourth embodiment has a CLI of 4,79 at a 1 mm fraction.
6. Mg: Al-CIl containing 0.29%
-Ml) based aluminum alloy in terms of weight percentage of V: 0.
19% and W: 0.18%. Fourth
In this example, the material was melted while degassing by blowing argon gas in the atmosphere, and was manufactured as a turbocharger impeller with a minimum blade thickness of 0.6 mm in the atmosphere. Then, the casting Af-Cu-
In order to confirm the performance of a turbocharger impeller made of a Mg-based high-strength aluminum alloy, an impeller made of an Al-Cu-Mg-based aluminum alloy without the addition of V and W was manufactured and compared.
その結果、■及びＷを添加しないＡＩｌ−Ｃｕ−Ｍｇ系
アルミニウム合金にあっては、その約９０％のインペラ
で羽根先端部にクラックの発生が確認された。しかし、
第４の実施例の鋳造用Ａｌ−Ｃ１ｌ−Ｍｇ系高力アルミ
ニウム合金にあってはＶ及びＷの添加によりクラックは
全く発生しなかった、これにより△ｆ−Ｃｕ−ｆｖｌｃ
＋系アルミニウム合金にＶ及びＷを添加することによっ
て鋳造割れが防止され、ｖＩｆＩ性が向上したのがＭ１
＝された。As a result, it was confirmed that cracks were observed at the blade tips of approximately 90% of the impellers of AIl-Cu-Mg-based aluminum alloys without the addition of ■ and W. but,
In the Al-C1l-Mg-based high-strength aluminum alloy for casting of the fourth example, no cracks occurred due to the addition of V and W.
By adding V and W to + series aluminum alloy, casting cracks were prevented and vIfI properties were improved.
= was done.
これは１）に■が焼割れを防止する性質を有するためで
ある。This is because (1) (1) has the property of preventing quench cracking.
尚、以上の第１〜第４の実施例に示した本発明の＄８Ｔ
ｌ用Ａｌ−Ｃｕ−Ｍｇ系高力アルミニウム合金の侵れた
特性はへＪ２−Ｃｕ−Ｍｇ系アルミニウム合金に重量百
分率でＶ：０．１０％以上、Ｗ：０．０５％以上含有さ
せたとぎにＶ＆認され、■＝０．３０％、ｌ／ｌ／：０
．３５％を越えるとそれ以上■及びＷを添加しても変化
しない。Incidentally, the $8T of the present invention shown in the above first to fourth embodiments
The eroded properties of the Al-Cu-Mg-based high-strength aluminum alloy for use in J2-Cu-Mg-based aluminum alloys are shown when V: 0.10% or more and W: 0.05% or more are contained in the weight percentage V& approved, ■=0.30%, l/l/:0
．． When it exceeds 35%, no change occurs even if 2 and W are added further.
［発明の効果゛１
以上型するに本発明によれば次のごとき優れた効果を発
揮する。[Effects of the Invention (1) In summary, the present invention provides the following excellent effects.
＋ｎ Ａｌｌ−Ｃｕ−Ｍｇ系アルミニウム合金に少量
のＶと少量のＷとを添加することににす、耐熱性及び耐
疲労特性を向上させることができる。+n By adding a small amount of V and a small amount of W to an All-Cu-Mg-based aluminum alloy, heat resistance and fatigue resistance can be improved.
（２） 上記少量のＶを添加したことにより、鋳造性
を向上させることができるため、薄肉の回転体に適した
！８通用Ａｉ’−Ｃｕ−Ｍｙ系高力アルミニウム合金を
提供することができる。(2) By adding the above small amount of V, castability can be improved, making it suitable for thin-walled rotating bodies! It is possible to provide a high-strength Ai'-Cu-My system aluminum alloy for general use.
＋３１ 少量のＶと少量のＷとを添加し、溶製及びｖ
ｒ造したＡｌ−Ｃｕ−Ｍｇ系アルミニウム合金を５２０
℃付近で溶体化処理後、焼入れし、１６０℃付近で人工
時効処理することにより、耐疲労特性を向上させること
ができる。特に真空雰囲気中で上記合金の溶製を施した
場合には耐疲労特性を著しく向上させることができる。+31 Add a small amount of V and a small amount of W, melt and v
The manufactured Al-Cu-Mg aluminum alloy is 520
Fatigue resistance properties can be improved by solution treatment at around 160°C, quenching, and artificial aging treatment at around 160°C. In particular, when the above alloy is melted in a vacuum atmosphere, the fatigue resistance can be significantly improved.
（４） そのため鍛造材に匹敵する儂れたａ減的性質
を有する鋳造用へβ−Ｃｕ−Ｍｇ系アルミニウム合金を
得ることができる。(4) Therefore, it is possible to obtain a β-Cu-Mg-based aluminum alloy for casting that has an a-reducing property comparable to that of a forged material.
第１図は本発明の鋳造用Ａｆ−Ｃｕ−Ｍｇ系高力アルミ
ニウム合金を大気中でのアルゴンガス吹き込み脱ガス処
理を施しながら溶製した場合の疲労特性を示すグラフ、
第２図は本発明の鋳造用Ａｌ−Ｃｕ−Ｍ＋系高力アルミ
ニウム合金を大気中でアルゴンガス吹き込み脱がス処理
を施しながら溶製した場合のクリープ破断特性を示すグ
ラフ、第３図は本発明の１３ｉｊ’Ｄ Ａｌ−ＣＩｌ
−Ｍ９系高力アルミニウム合金を真空脱ガス’２！ｌＦ
［！を施しながら溶製した場合の疲労特性を示すグラフ
である。
特許出願人 石川島播磨重工業株式会社代理人弁理士
絹 谷 信 雄第１図
第２図FIG. 1 is a graph showing fatigue characteristics when the Af-Cu-Mg high-strength aluminum alloy for casting of the present invention is melted while being subjected to degassing treatment by blowing argon gas in the atmosphere.
Fig. 2 is a graph showing the creep rupture characteristics of the Al-Cu-M+ based high-strength aluminum alloy for casting according to the present invention, which is melted in the atmosphere while being degassed by blowing argon gas. 13ij'D Al-CIl
-Vacuum degassing of M9 series high strength aluminum alloy '2! lF
[! 2 is a graph showing fatigue characteristics when melting is performed while Patent applicant: Ishikawajima-Harima Heavy Industries Co., Ltd. Representative patent attorney: Nobuo Kinutani Figure 1 Figure 2
Claims (1)
と少量のＷとを添加したことを特徴とする鋳造用Ａｌ−
Ｃｕ−Ｍｇ系高力アルミニウム合金。 （２）上記Ｖが上記Ａｌ−Ｃｕ−Ｍｇ系アルミニウム合
金に対して重量百分率で０．１０〜 ０．３０％、上記Ｗが上記Ａｌ−Ｃｕ−Ｍｇ系アルミニ
ウム合金に対して重量百分率で ０．０５〜０．３５％添加された上記特許請求の範囲第
１項記載の鋳造用Ａｌ−Ｃｕ−Ｍｇ系高力アルミニウム
合金。 （３）少量のＶと少量のＷとを添加したＡｌ−Ｃｕ−Ｍ
ｇ系アルミニウム合金を溶製して鋳造し、５２０℃付近
で溶体化処理した後、焼入れし、１６０℃付近で焼もど
して人工時効処理することを特徴とする鋳造用Ａｌ−Ｃ
ｕ− Ｍｇ系高力アルミニウム合金の製造方法。 （４）上記少量のＶと少量のＷとを添加したＡｌ−Ｃｕ
−Ｍｇ系アルミニウム合金の溶製が真空雰囲気中で施さ
れる上記特許請求の範囲第３項記載の鋳造用Ａｌ−Ｃｕ
−Ｍｇ系高力アルミニウム合金の製造方法。[Claims] (1) A small amount of V in an Al-Cu-Mg aluminum alloy
Casting Al-
Cu-Mg based high strength aluminum alloy. (2) The above-mentioned V is 0.10 to 0.30% by weight with respect to the above-mentioned Al-Cu-Mg-based aluminum alloy, and the above-mentioned W is 0.10-0.30% by weight with respect to the above-mentioned Al-Cu-Mg-based aluminum alloy. The Al-Cu-Mg based high-strength aluminum alloy for casting according to claim 1, wherein the Al-Cu-Mg based high strength aluminum alloy is added in an amount of 0.05 to 0.35%. (3) Al-Cu-M added with a small amount of V and a small amount of W
Al-C for casting, which is characterized by melting and casting g-based aluminum alloy, solution treatment at around 520°C, quenching, and artificial aging treatment by tempering at around 160°C.
u- Method for producing Mg-based high strength aluminum alloy. (4) Al-Cu added with the above small amount of V and small amount of W
- Al-Cu for casting according to claim 3, wherein the Mg-based aluminum alloy is melted in a vacuum atmosphere.
- A method for producing a Mg-based high-strength aluminum alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61292614A JPH0759731B2 (en) | 1986-12-10 | 1986-12-10 | Casting Al (Cu) -Mg high-strength aluminum alloy and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61292614A JPH0759731B2 (en) | 1986-12-10 | 1986-12-10 | Casting Al (Cu) -Mg high-strength aluminum alloy and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63145741A true JPS63145741A (en) | 1988-06-17 |
| JPH0759731B2 JPH0759731B2 (en) | 1995-06-28 |
Family
ID=17784077
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61292614A Expired - Lifetime JPH0759731B2 (en) | 1986-12-10 | 1986-12-10 | Casting Al (Cu) -Mg high-strength aluminum alloy and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0759731B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5122208A (en) * | 1991-07-22 | 1992-06-16 | General Motors Corporation | Hypo-eutectic aluminum-silicon alloy having tin and bismuth additions |
| US5122207A (en) * | 1991-07-22 | 1992-06-16 | General Motors Corporation | Hypo-eutectic aluminum-silicon-copper alloy having bismuth additions |
| JP2013515169A (en) * | 2009-12-22 | 2013-05-02 | リオ ティント アルカン インターナショナル リミテッド | Cast parts made of copper aluminum alloy with high mechanical strength and high heat-resistant creep resistance |
| CN108080548A (en) * | 2017-12-20 | 2018-05-29 | 西南铝业（集团）有限责任公司 | A kind of processing method of 2024 aluminium alloy open die forgings |
| CN108127344A (en) * | 2017-12-20 | 2018-06-08 | 西南铝业（集团）有限责任公司 | A kind of processing method of 6082 aluminium alloy open die forgings |
| CN114959387A (en) * | 2022-05-13 | 2022-08-30 | 内蒙古工业大学 | High-strength heat-resistant cast aluminum alloy and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5514864A (en) * | 1978-07-19 | 1980-02-01 | Nittetsu Mining Co Ltd | Selecting method for graphite, iron from waste mixture of iron mill containing graphite and iron |
| JPS6152345A (en) * | 1984-08-22 | 1986-03-15 | Mitsubishi Alum Co Ltd | Superplastic al alloy |
-
1986
- 1986-12-10 JP JP61292614A patent/JPH0759731B2/en not_active Expired - Lifetime
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5514864A (en) * | 1978-07-19 | 1980-02-01 | Nittetsu Mining Co Ltd | Selecting method for graphite, iron from waste mixture of iron mill containing graphite and iron |
| JPS6152345A (en) * | 1984-08-22 | 1986-03-15 | Mitsubishi Alum Co Ltd | Superplastic al alloy |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5122208A (en) * | 1991-07-22 | 1992-06-16 | General Motors Corporation | Hypo-eutectic aluminum-silicon alloy having tin and bismuth additions |
| US5122207A (en) * | 1991-07-22 | 1992-06-16 | General Motors Corporation | Hypo-eutectic aluminum-silicon-copper alloy having bismuth additions |
| JP2013515169A (en) * | 2009-12-22 | 2013-05-02 | リオ ティント アルカン インターナショナル リミテッド | Cast parts made of copper aluminum alloy with high mechanical strength and high heat-resistant creep resistance |
| CN108080548A (en) * | 2017-12-20 | 2018-05-29 | 西南铝业（集团）有限责任公司 | A kind of processing method of 2024 aluminium alloy open die forgings |
| CN108127344A (en) * | 2017-12-20 | 2018-06-08 | 西南铝业（集团）有限责任公司 | A kind of processing method of 6082 aluminium alloy open die forgings |
| CN114959387A (en) * | 2022-05-13 | 2022-08-30 | 内蒙古工业大学 | High-strength heat-resistant cast aluminum alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0759731B2 (en) | 1995-06-28 |
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