JPH06330202A - Method for manufacturing high strength / high toughness aluminum alloy member and casting aluminum alloy - Google Patents
Method for manufacturing high strength / high toughness aluminum alloy member and casting aluminum alloyInfo
- Publication number
- JPH06330202A JPH06330202A JP13946993A JP13946993A JPH06330202A JP H06330202 A JPH06330202 A JP H06330202A JP 13946993 A JP13946993 A JP 13946993A JP 13946993 A JP13946993 A JP 13946993A JP H06330202 A JPH06330202 A JP H06330202A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- strength
- toughness
- casting
- weight
- 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.)
- Pending
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 74
- 238000005266 casting Methods 0.000 title claims abstract description 39
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 25
- 238000000034 method Methods 0.000 title abstract description 12
- 238000001816 cooling Methods 0.000 claims abstract description 37
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 36
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 28
- 229910052796 boron Inorganic materials 0.000 claims abstract description 26
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 25
- 229910052797 bismuth Inorganic materials 0.000 claims abstract description 24
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 22
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 21
- 239000002994 raw material Substances 0.000 claims abstract description 18
- 229910052751 metal Inorganic materials 0.000 claims abstract description 13
- 239000002184 metal Substances 0.000 claims abstract description 13
- 230000008018 melting Effects 0.000 claims abstract description 8
- 238000002844 melting Methods 0.000 claims abstract description 8
- 229910052725 zinc Inorganic materials 0.000 claims description 17
- 239000012535 impurity Substances 0.000 claims description 8
- 239000000203 mixture Substances 0.000 abstract description 15
- 238000007711 solidification Methods 0.000 abstract description 12
- 230000008023 solidification Effects 0.000 abstract description 12
- 230000008859 change Effects 0.000 abstract description 8
- 239000011572 manganese Substances 0.000 description 64
- 239000011777 magnesium Substances 0.000 description 32
- 230000000694 effects Effects 0.000 description 29
- 239000010936 titanium Substances 0.000 description 29
- 239000011701 zinc Substances 0.000 description 19
- 150000001875 compounds Chemical class 0.000 description 18
- 239000000956 alloy Substances 0.000 description 15
- 229910045601 alloy Inorganic materials 0.000 description 14
- 239000006104 solid solution Substances 0.000 description 14
- 238000005728 strengthening Methods 0.000 description 14
- 239000013078 crystal Substances 0.000 description 13
- 229910052787 antimony Inorganic materials 0.000 description 12
- 229910052719 titanium Inorganic materials 0.000 description 10
- 238000010438 heat treatment Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 9
- 230000009471 action Effects 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 238000002425 crystallisation Methods 0.000 description 6
- 230000008025 crystallization Effects 0.000 description 6
- 230000007423 decrease Effects 0.000 description 5
- 239000010419 fine particle Substances 0.000 description 5
- 239000000470 constituent Substances 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 230000002411 adverse Effects 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 238000004512 die casting Methods 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 230000009897 systematic effect Effects 0.000 description 2
- 229910018134 Al-Mg Inorganic materials 0.000 description 1
- 229910018467 Al—Mg Inorganic materials 0.000 description 1
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 description 1
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- VSZWPYCFIRKVQL-UHFFFAOYSA-N selanylidenegallium;selenium Chemical compound [Se].[Se]=[Ga].[Se]=[Ga] VSZWPYCFIRKVQL-UHFFFAOYSA-N 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Continuous Casting (AREA)
Abstract
(57)【要約】
【目的】 凝固時の冷却速度および組成の両方の広い範
囲にわたって性質変化が小さく、熱処理をしない鋳造の
ままでも高い強度と靭性を兼備した高強度・高靭性アル
ミニウム合金部材を製造できる方法および該製造方法に
用いる鋳造用アルミニウム合金を提供する。
【構成】 重量％で、Ｍｎ：0.５〜2.５％、Ｍｇ：2.５
〜７％と、少なくともＴｉ：0.15〜0.５％、Ｚｒ：0.15
〜0.５％、Ｂ：0.01〜0.１％のうちの一種、および少な
くともＳｂ：0.01〜0.５％、Ｂｉ：0.01〜0.５％のうち
の一種を含み、残部が実質的にアルミニウムとなるよう
に原料を溶解し、前記原料の溶湯を0.５℃／秒以上の冷
却速度で凝固させることを特徴とする高強度・高靭性ア
ルミニウム合金部材の製造方法、およびこれに用いる鋳
造用アルミニウム合金。(57) [Summary] [Purpose] A high-strength / high-toughness aluminum alloy member that has little change in properties over a wide range of both cooling rate during solidification and composition and has high strength and toughness even in the as-cast state without casting. Provided are a method that can be manufactured and an aluminum alloy for casting used in the manufacturing method. [Constitution] Weight%, Mn: 0.5-2.5%, Mg: 2.5
~ 7%, at least Ti: 0.15 to 0.5%, Zr: 0.15
To 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi: 0.01 to 0.5%, and the balance substantially. A method for producing a high-strength / high-toughness aluminum alloy member, which comprises melting a raw material so as to become aluminum and solidifying the molten metal of the raw material at a cooling rate of 0.5 ° C./second or more, and casting used for the same Aluminum alloy for.
Description
【０００１】[0001]
【産業上の利用分野】本発明は、高強度・高靭性アルミ
ニウム合金部材の製造方法および高強度で靭性に優れた
非熱処理型の鋳造用アルミニウム合金に関し、さらに詳
しくは、熱処理をしない鋳放しのままで使用できるＡｌ
−Ｍｎ−Ｍｇ−Ｔｉ−Ｓｂ系またはＡｌ−Ｍｎ−Ｍｇ−
Ｚｎ−Ｔｉ−Ｓｂ系からなる鋳造用アルミニム合金、お
よびこの合金を用いて高強度・高靭性のアルミニウム合
金部材を製造する方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a high strength / high toughness aluminum alloy member and a non-heat treatment type casting aluminum alloy having high strength and excellent toughness. Al that can be used up to
-Mn-Mg-Ti-Sb system or Al-Mn-Mg-
The present invention relates to an aluminum alloy for casting, which is made of a Zn-Ti-Sb system, and a method for producing an aluminum alloy member having high strength and high toughness using this alloy.
【０００２】[0002]
【従来の技術】構造用として用いられるアルミニウム合
金部材、殊にアルミニウム合金の鋳造材は、軽量化や製
品の性能向上のために高品質化が望まれている。特に、
自動車の足廻り部品などの重要保安部品にアルミニウム
合金を使用するには、引張強さと伸びを兼備した、すな
わち高強度で高靭性な材料であることが要求される。ま
た、これらの部品は過酷な腐食環境下にさらされること
から、耐食性や耐応力腐食割れ性にも優れる必要があ
る。また、生産性を高めるとともに、コストを低く抑え
るため、長時間を要する熱処理を施さなくてもよい材料
であることが望ましい。さらに、自動車用の鋳物は、肉
厚不同が大きいことや、大量に生産されることなどか
ら、鋳造や凝固の条件が多少変動しても高い品質が安定
して得られる材料が望まれる。2. Description of the Related Art Aluminum alloy members used for structural purposes, particularly cast aluminum alloy materials, are required to have higher quality in order to reduce weight and improve product performance. In particular,
In order to use an aluminum alloy for important safety parts such as undercarriage parts of automobiles, it is required that the material has both tensile strength and elongation, that is, high strength and high toughness. Further, since these parts are exposed to a severe corrosive environment, it is necessary to have excellent corrosion resistance and stress corrosion cracking resistance. Further, in order to improve the productivity and keep the cost low, it is desirable that the material does not need a heat treatment that requires a long time. Further, since castings for automobiles have a large wall thickness variation and are produced in large quantities, it is desired to have a material that can stably obtain high quality even if the casting and solidification conditions slightly change.
【０００３】従来、鋳造用に用いられるアルミニウム合
金は、鋳造性のよいアルミニウム−珪素（Ａｌ−Ｓｉ）
系が大半を占めていたが、脆弱な共晶珪素が多量に晶出
するため、強度、特に靭性が低く、高品質化の要望に沿
うには限界があった。一方、ＪＩＳに定められるＡＣ７
Ａ及びＡＣ７ＢのようなＡｌ−Ｍｇ系の合金では、靭性
は高いものの、鋳造性が悪く、強度も十分ではないとい
う欠点があった。このように、従来の鋳造用に用いられ
るアルミニウム合金には、熱処理をしない鋳造のまま
で、十分な強度と靭性を兼ね備えているだけでなく、さ
らに耐食性や応力腐食割れ性の良好な合金およびその製
造方法は未だ見出されていないのが現状である。Conventionally, an aluminum alloy used for casting is aluminum-silicon (Al-Si) having good castability.
Although the majority of the systems occupy a large amount of brittle eutectic silicon, the strength, particularly toughness, is low, and there is a limit to meeting the demand for higher quality. On the other hand, AC7 specified in JIS
Although Al-Mg alloys such as A and AC7B have high toughness, they have the drawbacks of poor castability and insufficient strength. Thus, the aluminum alloy used for conventional casting, as-cast without heat treatment, not only has sufficient strength and toughness, but also has good corrosion resistance and stress corrosion cracking alloy and its At present, the manufacturing method has not been found yet.
【０００４】そこで、本発明者らは、これら問題を解決
するために、ＡｌとＭｎとからなる化合物を細かく分散
させ、さらにＭｇやＺｎを添加して強化した高靱性アル
ミニウム合金を提案した（特開平３−２０２４３６号公
報、特開平５−９６３８号公報）。すなわち、特開平３
−２０２４３６号に提案されたアルミニウム合金は、重
量％でＭｎ：0.９〜２.0％、Ｔｉ：0.15〜0.６％、Ｍ
ｇ：４〜８％を含み、残部がＡｌと不可避物質とからな
る高靱性アルミニウム合金である。この合金は、引張強
さが３０kgf/mm2 以上、伸びが２０％以上と極めて高い
延性と中程度の強度を有した合金である。In order to solve these problems, the present inventors have proposed a high toughness aluminum alloy in which a compound consisting of Al and Mn is finely dispersed and further strengthened by adding Mg or Zn (special feature: (Kaihei 3-202436, JP-A-5-9638). That is, JP-A-3
The aluminum alloy proposed in No. 202436 has a weight percentage of Mn: 0.9 to 2.0%, Ti: 0.15 to 0.6%, M.
g: A high toughness aluminum alloy containing 4 to 8% with the balance being Al and an unavoidable substance. This alloy has a tensile strength of 30 kgf / mm 2 or more and an elongation of 20% or more and has extremely high ductility and medium strength.
【０００５】また、特開平５−９６３８号に提案された
アルミニウム合金は、重量％でＭｎ：0.９〜２％、Ｍ
ｇ：２.5〜７％、Ｚｎ：１〜５％と、少なくともＴｉ：
0.15〜0.５％、Ｚｒ：0.15〜0.５％、Ｂ：0.01〜0.1 ％
のうちの一種を含み、残部がＡｌと不可避物質とからな
る高強度、高靱性アルミニウム合金、および上記原料を
溶解し原料の溶湯を１℃／秒以上の冷却速度で凝固させ
ることを特徴とする高強度、高靱性アルミニウム合金の
製造方法である。この合金は、引張強さが３５kgf/mm2
以上、伸びが１０％以上を示す合金を実現している。ま
た、該合金は凝固時の冷却速度が１℃／秒以上の時には
上述したような、優れた性質を示すとしている。The aluminum alloy proposed in Japanese Unexamined Patent Publication No. 9638/1993 has a Mn of 0.9 to 2% by weight and M
g: 2.5 to 7%, Zn: 1 to 5%, and at least Ti:
0.15 to 0.5%, Zr: 0.15 to 0.5%, B: 0.01 to 0.1%
A high-strength, high-toughness aluminum alloy having the balance consisting of Al and an unavoidable substance, and melting the raw material to solidify the molten metal at a cooling rate of 1 ° C./second or more. This is a method for producing a high strength, high toughness aluminum alloy. This alloy has a tensile strength of 35 kgf / mm 2
As described above, an alloy having an elongation of 10% or more is realized. The alloy is said to exhibit the above-mentioned excellent properties when the cooling rate during solidification is 1 ° C./sec or more.
【０００６】[0006]
【発明が解決しようとする課題】しかしながら、特開平
３−２０２４３６号公報に提案された高靱性アルミニウ
ム合金では、厚肉の高圧鋳造部材などのように冷却速度
の小さい場合や含有量の上限のＭｎ量の２％を超えた場
合には、初晶Ａｌ6 Ｍｎが晶出して引張特性が低下して
しまうという問題を有している。However, in the high-toughness aluminum alloy proposed in Japanese Patent Laid-Open No. 3-202436, when the cooling rate is small as in a thick high-pressure cast member or the upper limit of the Mn content is Mn. If it exceeds 2% of the amount, there is a problem that the primary crystal Al 6 Mn is crystallized and the tensile properties are deteriorated.
【０００７】また、特開平５−９６３８号公報に提案さ
れた高強度、高靱性アルミニウム合金およびその製造方
法では、冷却速度が１℃／秒を下回ると、粗い角板状の
初晶Ａｌ6 Ｍｎが晶出して、引張特性が著しく低下す
る。このため、厚肉部を有する鋳物や冷却速度の小さい
鋳造法に該合金を適用するには制約があった。また、金
型や注湯温度が変動して冷却速度が小さくなった時に、
引張特性が低下して不良を生じる虞があるという問題を
有している。さらに、該合金の引張強さはＭｎが多いほ
ど高くなるが、含有量の上限のＭｎ量である２％をこえ
ると、初晶Ａｌ6Ｍｎが晶出して引張特性が急激に低下
するという問題を有している。従って、高い引張強さが
要求されてＭｎ量を高くしたい場合でも、組成の変動に
よって引張特性が著しく低下してしまう危険性をはらん
でいるので、安全をみて低めに設定せざるを得ないとい
うことになる。Further, in the high-strength, high-toughness aluminum alloy and the method for producing the same proposed in Japanese Patent Laid-Open No. 9638/1993, when the cooling rate is lower than 1 ° C./sec, a rough rectangular plate-shaped primary crystal Al 6 Mn is used. Are crystallized, and the tensile properties are significantly reduced. Therefore, there is a limitation in applying the alloy to a casting having a thick portion or a casting method having a low cooling rate. In addition, when the mold or pouring temperature fluctuates and the cooling rate decreases,
There is a problem that the tensile properties may be deteriorated to cause a defect. Further, the tensile strength of the alloy increases as the content of Mn increases, but if the content exceeds the upper limit of the content of Mn, which is 2%, primary Al 6 Mn is crystallized and the tensile properties deteriorate sharply. have. Therefore, even if high tensile strength is required and the amount of Mn is desired to be high, there is a risk that the tensile properties will be significantly deteriorated due to compositional changes. It turns out that.
【０００８】このような状況から、溶解・鋳造や凝固な
どのプロセスの条件あるいは組成等が変動しても、安定
して高い性質を示す合金の開発が嘱望されていた。そこ
で、本発明者らは、上述の如き従来技術の問題点を解決
すべく鋭意研究し、各種の系統的実験を重ねた結果、本
発明を成すに至ったものである。Under these circumstances, there has been a strong demand for the development of an alloy which exhibits stable and high properties even if the conditions of the process such as melting / casting or solidification or the composition thereof change. Therefore, the inventors of the present invention have earnestly studied in order to solve the above-mentioned problems of the prior art, and as a result of various systematic experiments, the present invention has been accomplished.
【０００９】（発明の目的）本発明の目的は、凝固時の
冷却速度および組成の両方の広い範囲にわたって性質変
化が小さく、熱処理をしない鋳造のままでも高い強度と
靭性を兼備した高強度・高靭性アルミニウム合金部材を
製造できる方法および該製造方法に用いる鋳造用アルミ
ニウム合金を提供することにある。(Purpose of the Invention) The object of the present invention is that the change in properties is small over a wide range of both the cooling rate during solidification and the composition, and high strength and high toughness with high strength and toughness are obtained even in the as-cast state without heat treatment. It is an object to provide a method capable of manufacturing a tough aluminum alloy member and an aluminum alloy for casting used in the manufacturing method.
【００１０】本発明者らは、上述の従来技術の問題に関
し、以下のことに着眼した。すなわち、ＳｂやＢｉの添
加により初晶Ａｌ6 Ｍｎの晶出が抑制される効果がある
ことを見出し、各種の系統的実験を重ねて検討した結
果、上記Ａｌ−Ｍｎ−Ｍｇ−Ｔｉ系アルミニウム合金ま
たはＡｌ−Ｍｎ−Ｍｇ−Ｚｎ−Ｔｉ系アルミニウム合金
にＳｂまたはＢｉを添加することによって、これまでよ
りも高いＭｎ量まで、あるいは広い冷却速度の範囲まで
安定して高い性質を具備できる高強度・高靱性アルミニ
ウム合金を実現するに至った。The present inventors have focused on the following points regarding the above-mentioned problems of the prior art. That is, it was found that the addition of Sb and Bi has the effect of suppressing the crystallization of primary Al 6 Mn, and after various systematic experiments were repeated and examined, the results were the above Al—Mn—Mg—Ti based aluminum alloys. Alternatively, by adding Sb or Bi to the Al-Mn-Mg-Zn-Ti-based aluminum alloy, high strength and stable properties can be provided up to a higher Mn content or a wider cooling rate range. We have come to realize a high toughness aluminum alloy.
【００１１】[0011]
（第１発明の構成）本第１発明の高強度・高靭性アルミ
ニウム合金部材の製造方法は、重量％で、Ｍｎ：0.５〜
2.５％、Ｍｇ：2.５〜７％と、少なくともＴｉ：0.15〜
0.５％、Ｚｒ：0.15〜0.５％、Ｂ：0.01〜0.１％のうち
の一種、および少なくともＳｂ：0.01〜0.５％、Ｂｉ：
0.01〜0.５％のうちの一種を含み、残部が実質的にアル
ミニウムとなるように原料を溶解し、前記原料の溶湯を
0.５℃／秒以上の冷却速度で凝固させることを特徴とす
る。(Structure of First Invention) The method for manufacturing a high-strength / high-toughness aluminum alloy member according to the first invention is such that Mn is 0.5 to 0.5% by weight.
2.5%, Mg: 2.5 to 7% and at least Ti: 0.15 to
0.5%, Zr: 0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi:
0.01 to 0.5% of one kind is melted, the raw material is melted so that the balance is substantially aluminum, and the molten metal of the raw material is added.
It is characterized by solidifying at a cooling rate of 0.5 ° C./second or more.
【００１２】（第２発明の構成）本第２発明の高強度・
高靭性アルミニウム合金部材の製造方法は、重量％で、
Ｍｎ：0.５〜2.５％、Ｍｇ：2.５〜７％、Ｚｎ：１〜５
％と、少なくともＴｉ：0.15〜0.５％、Ｚｒ：0.15〜0.
５％、Ｂ：0.01〜0.１％のうちの一種、および少なくと
もＳｂ：0.01〜0.５％、Ｂｉ：0.01〜0.５％のうちの一
種を含み、残部が実質的にアルミニウムとなるように原
料を溶解し、前記原料の溶湯を0.５℃／秒以上の冷却速
度で凝固させることを特徴とする。(Structure of Second Invention) High strength of the second invention
The manufacturing method of the high toughness aluminum alloy member is, in weight%,
Mn: 0.5-2.5%, Mg: 2.5-7%, Zn: 1-5
%, At least Ti: 0.15 to 0.5%, Zr: 0.15 to 0.
5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi: 0.01 to 0.5%, and the balance is substantially aluminum. Thus, the raw material is melted, and the molten metal of the raw material is solidified at a cooling rate of 0.5 ° C./second or more.
【００１３】（第３発明の構成）本第３発明の鋳造用ア
ルミニウム合金は、重量％で、Ｍｎ：0.５〜２.5％、Ｍ
ｇ：２.5〜７％と、少なくともＴｉ：0.15〜0.５％、Ｚ
ｒ：0.15〜0.５％、Ｂ：0.01〜0.１％のうちの一種、お
よび少なくともＳｂ：0.01〜0.５％、Ｂｉ：0.01〜0.５
％のうちの一種を含み、残部がアルミニウム及び不可避
不純物からなることを特徴とする。(Structure of the Third Invention) The aluminum alloy for casting according to the third invention is, by weight%, Mn: 0.5 to 2.5%, M
g: 2.5-7% and at least Ti: 0.15-0.5%, Z
r: 0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi: 0.01 to 0.5%
%, And the balance consists of aluminum and unavoidable impurities.
【００１４】（第４発明の構成）本第４発明の鋳造用ア
ルミニウム合金は、重量％で、Ｍｎ：0.５〜2.５％、Ｍ
ｇ：2.５〜７％、Ｚｎ：１〜５％と、少なくともＴｉ：
0.15〜0.５％、Ｚｒ：0.15〜0.５％、Ｂ：0.01〜0.１％
のうちの一種、および少なくともＳｂ：0.01〜0.5 ％、
Ｂｉ：0.01〜0.５％のうちの一種を含み、残部がアルミ
ニウム及び不可避不純物からなることを特徴とする。(Constitution of Fourth Invention) The aluminum alloy for casting according to the fourth invention is, by weight%, Mn: 0.5 to 2.5%, M
g: 2.5 to 7%, Zn: 1 to 5%, and at least Ti:
0.15 to 0.5%, Zr: 0.15 to 0.5%, B: 0.01 to 0.1%
One of these, and at least Sb: 0.01-0.5%,
Bi: 0.01 to 0.5% of one kind is contained, and the balance is made of aluminum and unavoidable impurities.
【００１５】[0015]
【作用】本第１発明および第２発明の高強度・高靭性ア
ルミニウム合金部材の製造方法、および本第３発明およ
び第４発明の鋳造用アルミニウム合金が、優れた効果を
発揮するメカニズムについては、未だ必ずしも明らかで
はないが、次のように考えられる。With respect to the mechanism by which the method for producing a high-strength / high-toughness aluminum alloy member of the first and second inventions and the casting aluminum alloys of the third and fourth inventions exhibit excellent effects, Although not clear yet, it can be considered as follows.
【００１６】（第１発明の作用）本第１発明の高強度・
高靭性アルミニウム合金部材の製造方法では、先ず、重
量％で、Ｍｎ：0.５〜2.５％、Ｍｇ：2.５〜７％と、少
なくともＴｉ：0.15〜0.５％、Ｚｒ：0.15〜0.５％、
Ｂ：0.01〜0.１％のうちの一種、および少なくともＳ
ｂ：0.01〜0.５％、Ｂｉ：0.01〜0.５％のうちの一種を
含み、残部が実質的にアルミニウムとなるように原料を
溶解し、次いで、所定の冷却速度で凝固させてなる。(Operation of First Invention) High strength of the first invention
In the method of manufacturing a high toughness aluminum alloy member, first, in weight%, Mn: 0.5 to 2.5%, Mg: 2.5 to 7%, and at least Ti: 0.15 to 0.5% and Zr: 0.15. ~ 0.5%,
B: 0.01 to 0.1%, and at least S
b: 0.01 to 0.5%, Bi: 0.01 to 0.5%, and the raw material is melted so that the balance is substantially aluminum, and then solidified at a predetermined cooling rate. .
【００１７】ここで、原料中のマンガン（Ｍｎ）の含有
量は、0.５〜2.５重量％である。Ｍｎは、Ａｌ中に固溶
して強化するとともに、ＡｌとＡｌ6 Ｍｎとからなる化
合物を形成して、アルミニウム合金母材を強化する。ま
た、アルミニウム合金母材の耐食性を向上させる効果を
有する。このＭｎの含有量が0.５重量％未満の場合、十
分な強度が得られない。また、該含有量が2.５重量％を
超える場合は、初晶として粗大なＡｌ6 ＭｎやＡｌ4 Ｍ
ｎが晶出し、著しく強度が低下するので適当ではない。Here, the content of manganese (Mn) in the raw material is 0.5 to 2.5% by weight. Mn forms a solid solution in Al and strengthens it, and at the same time forms a compound consisting of Al and Al 6 Mn to strengthen the aluminum alloy base material. It also has the effect of improving the corrosion resistance of the aluminum alloy base material. If the Mn content is less than 0.5% by weight, sufficient strength cannot be obtained. When the content exceeds 2.5% by weight, coarse Al 6 Mn or Al 4 M as primary crystals is used.
n is crystallized and the strength is remarkably reduced, which is not suitable.
【００１８】マグネシウム（Ｍｇ）の含有量は、2.５〜
７重量％である。Ｍｇは、Ａｌ中に固溶するとともに、
一部がＡｌ、Ｚｎとともに析出して、強度を向上させ
る。このＭｇの含有量が2.５重量％未満の場合、十分な
強度が得られない。また、該含有量が７重量％を超える
場合は、化合物相が晶出し脆化してしまう。The content of magnesium (Mg) is 2.5 to
It is 7% by weight. Mg is a solid solution in Al,
A part is precipitated together with Al and Zn to improve the strength. If the Mg content is less than 2.5% by weight, sufficient strength cannot be obtained. If the content exceeds 7% by weight, the compound phase will crystallize and become brittle.
【００１９】チタン（Ｔｉ）の含有量は、0.15〜0.５重
量％である。Ｔｉは、結晶粒を微細化するだけでなく、
Ａｌ6 Ｍｎ化合物を細かく丸い形状で、かつ均一に晶出
させ、強度および靭性を向上させる。このＴｉの含有量
が0.15重量％未満の場合、強度および靱性向上の効果が
得られないばかりか、逆に悪影響が出てしまう。また、
該含有量が0.５重量％を超える場合は、溶解・鋳造温度
を1000℃まで高めても、初晶として粗大な針状のＡｌ3
Ｔｉが晶出して、著しく強度が低下する。The content of titanium (Ti) is 0.15 to 0.5% by weight. Ti not only makes the crystal grains finer, but also
The Al 6 Mn compound has a fine and round shape and is uniformly crystallized to improve strength and toughness. If the content of Ti is less than 0.15% by weight, not only the effect of improving strength and toughness cannot be obtained but, conversely, adverse effects occur. Also,
If the content exceeds 0.5% by weight, even if the melting / casting temperature is increased to 1000 ° C, coarse needle-like Al 3 as primary crystals is formed.
Ti crystallizes out and the strength is significantly reduced.
【００２０】ジルコニウム（Ｚｒ）の含有量は、0.15〜
0.５重量％である。Ｚｒは、前述のＴｉと同様の作用を
奏する。このＺｒの含有量が0.15重量％未満の場合、強
度および靱性向上の効果が得られないばかりか、逆に悪
影響が出てしまう。また、該含有量が0.５重量％を超え
る場合は、溶解・鋳造温度を1000℃まで高めても、初晶
として粗大な針状のＡｌ3 Ｚｒが晶出して、強度および
靱性が著しく低下する。The content of zirconium (Zr) is 0.15 to
It is 0.5% by weight. Zr has the same effect as Ti described above. When the content of Zr is less than 0.15% by weight, not only the effect of improving strength and toughness cannot be obtained but, on the contrary, adverse effects occur. When the content exceeds 0.5% by weight, coarse needle-like Al 3 Zr as primary crystals crystallizes even if the melting / casting temperature is increased to 1000 ° C, resulting in a marked decrease in strength and toughness. To do.
【００２１】硼素（Ｂ）の含有量は、0.01〜0.１重量％
である。Ｂは、前述のＴｉと同様の作用を奏する。この
Ｂの含有量が0.01重量％未満の場合、強度および靱性向
上の効果が得られないばかりか、逆に悪影響が出てしま
う。また、該含有量が0.１重量％を超える場合は、溶解
・鋳造温度を1000℃まで高めても、初晶として粗大な針
状のＡｌＢ2 が晶出して、強度および靱性が著しく低下
する。The content of boron (B) is 0.01 to 0.1% by weight.
Is. B has the same effect as Ti described above. When the content of B is less than 0.01% by weight, not only the effect of improving strength and toughness cannot be obtained but, conversely, adverse effects are produced. On the other hand, when the content exceeds 0.1% by weight, coarse needle-like AlB 2 as a primary crystal is crystallized even if the melting / casting temperature is raised to 1000 ° C, and the strength and toughness are significantly reduced. .
【００２２】アンチモン（Ｓｂ）の含有量は、0.01〜0.
５重量％である。Ｓｂは、初晶Ａｌ6 Ｍｎの晶出を抑え
る効果を有するので、Ｍｎ量の高い合金を用いる場合も
しくは凝固時の冷却速度がある程度小さい場合でも、Ｍ
ｎを強制的に固溶させることができる。即ち、肉厚不同
が大きく、部位ごとによって冷却速度の著しく異なった
鋳物においても、全部位にわたってほぼ同等の高い機械
的性質を保持させることができる。このＳｂの含有量が
0.01重量％未満の場合、十分な上記効果が得られない。
また、該含有量が0.５重量％を超える場合は、ＳｂとＭ
ｇとがＭｇ3 Ｓｂ2 なる化合物を生成して応力集中源と
なってしまうことと、強化に寄与するＭｇ量が減少する
ために、かえって強度を低下させてしまう。The content of antimony (Sb) is 0.01 to 0.
It is 5% by weight. Since Sb has an effect of suppressing crystallization of primary crystal Al 6 Mn, even if an alloy having a high Mn content is used or the cooling rate during solidification is small to some extent, M
n can be forced to form a solid solution. That is, even in a casting having a large thickness variation and a cooling rate remarkably different depending on each part, it is possible to maintain substantially the same high mechanical properties over all parts. The content of this Sb is
If it is less than 0.01% by weight, the above-mentioned effects cannot be sufficiently obtained.
When the content exceeds 0.5% by weight, Sb and M
Since g and Mg form a compound of Mg 3 Sb 2 and serve as a stress concentration source, and the amount of Mg contributing to strengthening decreases, the strength rather decreases.
【００２３】ビスマス（Ｂｉ）の含有量は、0.01〜0.５
重量％である。Ｂｉは、前述のＳｂと同様の作用を奏す
る。このＢｉの含有量が0.01重量％未満の場合、十分な
上記効果が得られない。また、該含有量が0.５重量％を
超える場合は、ＢｉとＭｇとがＭｇ3 Ｂｉ2 なる化合物
を生成して応力集中源となってしまうことと、強化に寄
与するＭｇ量が減少するために、かえって強度を低下さ
せてしまう。The content of bismuth (Bi) is 0.01 to 0.5.
% By weight. Bi has the same effect as Sb described above. If the content of Bi is less than 0.01% by weight, the above effect cannot be sufficiently obtained. When the content exceeds 0.5% by weight, Bi and Mg form a compound of Mg 3 Bi 2 to serve as a stress concentration source, and the amount of Mg contributing to strengthening decreases. Therefore, the strength is rather reduced.
【００２４】次に、溶解した前記所定組成の原料からな
る溶湯を凝固させるときの冷却速度は、0.５℃／秒以上
の冷却速度である。これにより、アルミニウム中へ強化
元素のＭｎ、Ｍｇ等を過飽和に強制固溶させることがで
きる。従って、鋳放しのままで高強度・高靱性のアルミ
ニウム合金部材を得ることができる。例えば、Ｍｎで
は、ＭｇやＺｎと共存したときの平衡固溶量は１重量％
未満であるが、本発明のような冷却速度の得られる鋳造
法によれば１％以上強制固溶させることが可能であり、
強度の向上に寄与する。また、Ｍｎを２.5重量％まで含
有させることができるので、引張強さ等の強度をより向
上させることが可能となる。Next, the cooling rate at the time of solidifying the melt made of the melted raw material having the above-mentioned predetermined composition is 0.5 ° C./sec or more. As a result, the strengthening elements Mn, Mg, and the like can be forced into solid solution in the aluminum in a supersaturated manner. Therefore, it is possible to obtain an aluminum alloy member having high strength and high toughness as it is as cast. For example, in Mn, the equilibrium solid solution amount when coexisting with Mg or Zn is 1% by weight.
Although it is less than 1, it is possible to forcibly form a solid solution by 1% or more according to the casting method capable of obtaining a cooling rate as in the present invention.
It contributes to the improvement of strength. Further, since Mn can be contained up to 2.5% by weight, the strength such as tensile strength can be further improved.
【００２５】以上のように、所定組成の原料を溶解し、
該所定組成の溶湯を所定速度で凝固させることにより、
凝固時の冷却速度および組成の両方の広い範囲にわたっ
て性質変化が小さく、熱処理をしない鋳造のままで、高
い強度と靭性を兼備した高強度・高靭性アルミニウム合
金部材を製造することができるものと考えられる。As described above, the raw material having the predetermined composition is melted,
By solidifying the molten metal of the predetermined composition at a predetermined speed,
We believe that it is possible to manufacture high-strength and high-toughness aluminum alloy members that have both high strength and toughness in the as-cast state without any heat treatment, since the property changes are small over a wide range of both the cooling rate and composition during solidification. To be
【００２６】（第２発明の作用）本第２発明の高強度・
高靭性アルミニウム合金部材の製造方法では、先ず、重
量％で、Ｍｎ：0.５〜2.５％、Ｍｇ：2.５〜７％、Ｚ
ｎ：１〜５％と、少なくともＴｉ：0.15〜0.５％、Ｚ
ｒ：0.15〜0.５％、Ｂ：0.01〜0.１％のうちの一種、お
よび少なくともＳｂ：0.01〜0.５％、Ｂｉ：0.01〜0.５
％のうちの一種を含み、残部が実質的にアルミニウムと
なるように原料を溶解し、次いで、所定の冷却速度で凝
固させてなる。(Operation of Second Invention) High strength of the second invention
In the method of manufacturing a high toughness aluminum alloy member, first, in% by weight, Mn: 0.5 to 2.5%, Mg: 2.5 to 7%, Z
n: 1 to 5% and at least Ti: 0.15 to 0.5%, Z
r: 0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi: 0.01 to 0.5%
%, The raw material is melted so that the balance is substantially aluminum, and then solidified at a predetermined cooling rate.
【００２７】ここで、本第２発明の作用は、Ｚｎの作用
を除いて上述の第１発明の作用と同様であるので、Ｚｎ
の作用を中心に説明する。すなわち、亜鉛（Ｚｎ）の含
有量は、１〜５重量％である。Ｚｎは、Ａｌ中に固溶す
るとともに、一部がＡｌ、Ｍｇとともに析出して、強度
を上昇させる。このＺｎの含有量が１重量％未満の場
合、十分な強度が得られない。また、該含有量が５重量
％を超える場合は、化合物相が晶出して脆化するだけで
なく、耐食性や耐応力腐食割れ性が低下する。次いで、
溶解した前記所定組成の原料からなる溶湯を凝固させる
ときの冷却速度は、0.５℃／秒以上の冷却速度である
が、これにより、ＳｂやＢｉが添加されているため初晶
Ａｌ6 Ｍｎの晶出を抑制することができ、アルミニウム
中へ強化元素であるＭｎ、Ｍｇ、Ｚｎ等を過飽和に強制
固溶させることができる。Here, the function of the second invention is the same as the function of the first invention except for the function of Zn.
The operation will be mainly described. That is, the content of zinc (Zn) is 1 to 5% by weight. Zn forms a solid solution in Al, and partly precipitates together with Al and Mg to increase the strength. If the Zn content is less than 1% by weight, sufficient strength cannot be obtained. If the content exceeds 5% by weight, not only the compound phase crystallizes and becomes brittle, but also the corrosion resistance and the stress corrosion cracking resistance are deteriorated. Then
The cooling rate at the time of solidifying the molten metal having the above-mentioned predetermined composition is 0.5 ° C./sec or more, but since Sb and Bi are added, the primary crystal Al 6 Mn is added. Can be suppressed and the strengthening elements Mn, Mg, Zn, etc. can be forced into solid solution into aluminum.
【００２８】（第３発明の作用）本第３発明の鋳造用ア
ルミニウム合金は、重量％で、Ｍｎ：0.５〜２.5％、Ｍ
ｇ：２.5〜７％と、少なくともＴｉ：0.15〜0.５％、Ｚ
ｒ：0.15〜0.５％、Ｂ：0.01〜0.１％のうちの一種、お
よび少なくともＳｂ：0.01〜0.５％、Ｂｉ：0.01〜0.５
％のうちの一種を含み、残部がアルミニウム及び不可避
不純物からなる。本発明の鋳造用アルミニウム合金の構
成元素であるＭｎ、Ｍｇ、Ｔｉ、Ｚｒ、Ｂ、Ｓｂ、Ｂｉ
の作用は、前述の第１発明の高強度・高靭性アルミニウ
ム合金部材の製造方法の作用において説明したＭｎ、Ｍ
ｇ、Ｔｉ、Ｚｒ、Ｂ、Ｓｂ、Ｂｉの作用と同様である。(Operation of Third Invention) The aluminum alloy for casting according to the third invention of the present invention is, by weight%, Mn: 0.5 to 2.5%, M
g: 2.5-7% and at least Ti: 0.15-0.5%, Z
r: 0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi: 0.01 to 0.5%
%, With the balance being aluminum and inevitable impurities. Mn, Mg, Ti, Zr, B, Sb, Bi which are the constituent elements of the aluminum alloy for casting of the present invention
The action of Mn, M explained in the action of the method for producing a high-strength / high-toughness aluminum alloy member of the first invention described above.
The action is the same as that of g, Ti, Zr, B, Sb, and Bi.
【００２９】本第３発明の鋳造用アルミニウム合金は、
前記所定含有量の元素を構成元素としてなる。このよう
にすることにより、原料として少なくともＴｉ、Ｚｒ、
Ｂの一種とＭｎとを共存させたので、Ｍｎ化合物を丸い
形状様の微細な粒子としてアルミニウム母材中に均一に
分散させることができ、さらにアルミニウムに良く固溶
するＭｇを含有させることにより、靭性を損なわずに強
度を向上させることができる。さらに、初晶Ａｌ6 Ｍｎ
の晶出を抑えるＳｂ又はＢｉを添加したので、広い冷却
速度の範囲で凝固した場合でも、高強度で高靭性のアル
ミニウム合金部材を得ることができるものと思われる。
また、これら組成の原料からなる溶湯を、0.５℃／秒以
上の冷却速度で凝固させることにより、アルミニウム中
へ強化元素のＭｎ、Ｍｇ等を過飽和に強制固溶させるこ
とができる。The aluminum alloy for casting of the third invention is
The predetermined content of the element is used as a constituent element. By doing so, at least Ti, Zr,
Since one type of B and Mn are allowed to coexist, the Mn compound can be uniformly dispersed in the aluminum base material as fine particles having a round shape, and by containing Mg that is well solid-dissolved in aluminum, Strength can be improved without impairing toughness. Furthermore, primary crystal Al 6 Mn
Since Sb or Bi that suppresses the crystallization is added, it is considered that an aluminum alloy member having high strength and high toughness can be obtained even when solidified in a wide cooling rate range.
Further, by solidifying the molten metal composed of the raw materials having these compositions at a cooling rate of 0.5 ° C./sec or more, the strengthening elements Mn, Mg, etc. can be forced into solid solution into aluminum to form a solid solution.
【００３０】（第４発明の作用）本第４発明の鋳造用ア
ルミニウム合金は、重量％で、Ｍｎ：0.５〜２.5％、Ｍ
ｇ：２.5〜７％、Ｚｎ：１〜５％と、少なくともＴｉ：
0.15〜0.５％、Ｚｒ：0.15〜0.５％、Ｂ：0.01〜0.１％
のうちの一種、および少なくともＳｂ：0.01〜0.５％、
Ｂｉ：0.01〜0.５％のうちの一種を含み、残部がアルミ
ニウム及び不可避不純物からなる。本発明の鋳造用アル
ミニウム合金の構成元素であるＭｎ、Ｍｇ、Ｚｎ、Ｔ
ｉ、Ｚｒ、Ｂ、Ｓｂ、Ｂｉの作用は、前述の第２発明の
高強度・高靭性アルミニウム合金部材の製造方法の作用
において説明したＭｎ、Ｍｇ、Ｚｎ、Ｔｉ、Ｚｒ、Ｂ、
Ｓｂ、Ｂｉの作用と同様である。(Operation of Fourth Invention) The aluminum alloy for casting according to the fourth invention is, by weight%, Mn: 0.5 to 2.5%, M
g: 2.5 to 7%, Zn: 1 to 5%, and at least Ti:
0.15 to 0.5%, Zr: 0.15 to 0.5%, B: 0.01 to 0.1%
One of the above, and at least Sb: 0.01 to 0.5%,
Bi: 0.01 to 0.5% of one type, with the balance being aluminum and unavoidable impurities. Mn, Mg, Zn, T which are the constituent elements of the aluminum alloy for casting of the present invention
The actions of i, Zr, B, Sb, and Bi are Mn, Mg, Zn, Ti, Zr, B, which are explained in the action of the method for producing a high-strength / high-toughness aluminum alloy member of the second invention.
It is similar to the action of Sb and Bi.
【００３１】本第４発明の鋳造用アルミニウム合金は、
前記所定含有量の元素を構成元素としてなる。このよう
にすることにより、原料として少なくともＴｉ、Ｚｒ、
Ｂの一種とＭｎとを共存させたので、Ｍｎ化合物を丸い
形状様の微細な粒子としてアルミニウム母材中に均一に
分散させることができ、さらにアルミニウムに良く固溶
するＭｇ、Ｚｎを含有させることにより、靭性を損なわ
ずに強度を向上させることができる。さらに、初晶Ａｌ
6 Ｍｎの晶出を抑えるＳｂ又はＢｉを添加したので、広
い冷却速度の範囲で凝固した場合でも、高強度で高靭性
のアルミニウム合金部材を得ることができるものと思わ
れる。また、これら組成の原料からなる溶湯を、0.５℃
／秒以上の冷却速度で凝固させることにより、アルミニ
ウム中へ強化元素のＭｎ、Ｍｇ等を過飽和に強制固溶さ
せることができる。The casting aluminum alloy of the fourth invention is
The predetermined content of the element is used as a constituent element. By doing so, at least Ti, Zr,
Since one type of B and Mn are allowed to coexist, the Mn compound can be uniformly dispersed in the aluminum base material as fine particles having a round shape, and further, Mg and Zn which are well solid-dissolved in aluminum should be contained. Thereby, the strength can be improved without impairing the toughness. Furthermore, primary crystal Al
Since Sb or Bi that suppresses crystallization of 6 Mn was added, it is considered that an aluminum alloy member having high strength and high toughness can be obtained even when solidified in a wide cooling rate range. In addition, the molten metal consisting of the raw materials of these compositions is
By solidifying at a cooling rate of not less than / sec, the strengthening elements Mn, Mg, etc. can be forced into solid solution in aluminum.
【００３２】[0032]
（第１発明の効果）本第１発明の高強度・高靭性アルミ
ニウム合金部材の製造方法により、凝固時の冷却速度お
よび組成の両方の広い範囲にわたって性質変化が小さ
く、熱処理をしない鋳造のままで高い強度と靭性を兼備
したアルミニウム合金部材を製造することができる。(Effect of the first invention) By the method for producing a high-strength / high-toughness aluminum alloy member of the first invention, the property change is small over a wide range of both the cooling rate during solidification and the composition, and as-cast without heat treatment. An aluminum alloy member having both high strength and toughness can be manufactured.
【００３３】（第２発明の効果）本第２発明の高強度・
高靭性アルミニウム合金部材の製造方法により、凝固時
の冷却速度および組成の両方の広い範囲にわたって性質
変化が小さく、熱処理をしない鋳造のままで高い強度と
靭性を兼備したアルミニウム合金部材を製造することが
できる。(Effect of Second Invention) High strength of the second invention
According to the method for producing a high toughness aluminum alloy member, it is possible to produce an aluminum alloy member that has high strength and toughness as cast without heat treatment, with little property change over a wide range of both cooling rate and composition during solidification. it can.
【００３４】（第３発明の効果）本第３発明の鋳造用ア
ルミニウム合金を用いることににより、凝固時の冷却速
度および組成の両方の広い範囲にわたって性質変化が小
さく、熱処理をしない鋳造のままで高い強度と靭性を兼
備したアルミニウム合金部材を製造することができる。(Effect of the third invention) By using the aluminum alloy for casting according to the third invention, the property change is small over a wide range of both the cooling rate during solidification and the composition, and as-cast without heat treatment. An aluminum alloy member having both high strength and toughness can be manufactured.
【００３５】（第４発明の効果）本第４発明の鋳造用ア
ルミニウム合金を用いることににより、凝固時の冷却速
度および組成の両方の広い範囲にわたって性質変化が小
さく、熱処理をしない鋳造のままで高い強度と靭性を兼
備したアルミニウム合金部材を製造することができる。(Effect of Fourth Invention) By using the aluminum alloy for casting according to the fourth invention, the property change is small over a wide range of both the cooling rate during solidification and the composition, and as-cast without heat treatment. An aluminum alloy member having both high strength and toughness can be manufactured.
【００３６】[0036]
（第１発明〜第４発明の具体例）以下に、前記第１発明
〜第４発明をさらに具体的にした具体例について説明す
る。(Specific Examples of First to Fourth Inventions) Specific examples of the first to fourth inventions will be described below.
【００３７】本第１発明および第２発明のアルミニウム
合金部材の製造方法により、ＴｉとＭｎとを共存させた
ので、Ｍｎ化合物を丸い形状の20μｍ以下の微細な粒子
としてアルミニウム母材中に均一に分散させることがで
きるので、化合物による切欠き効果を極力抑えて脆弱的
に破断するのを防ぎ、複合強化あるいは分散強化効果を
有効に作用させることができる。Since Ti and Mn were allowed to coexist by the method for producing an aluminum alloy member according to the first and second aspects of the invention, the Mn compound was uniformly formed in the aluminum base material as round fine particles of 20 μm or less. Since the compound can be dispersed, it is possible to suppress the notch effect of the compound as much as possible, to prevent brittle fracture, and to effectively exert the composite strengthening or dispersion strengthening effect.
【００３８】本第１発明ないし第４発明において、Ｍｎ
の含有量は、１.0〜２.2重量％が好適である。このよう
にすることにより、引張強さが３０kgf/mm2 以上、0.２
％耐力が１５kgf/mm2 以上、伸びが２０％以上とより高
強度で高靭性のアルミニウム合金部材を得ることができ
る。In the first to fourth inventions, Mn
The content of is preferably 1.0 to 2.2% by weight. By doing so, the tensile strength is 30 kgf / mm 2 or more, 0.2
With a% proof stress of 15 kgf / mm 2 or more and an elongation of 20% or more, an aluminum alloy member having higher strength and high toughness can be obtained.
【００３９】本第１発明および第２発明において、凝固
時の0.５℃／秒以上の冷却速度を実現するための鋳造法
としては、高圧鋳造法を用いることが好ましい。すなわ
ち、溶解炉で溶解したアルミニウム合金を金型内の製品
部分に充填後、直ちに、該溶湯表面にパンチ等の加圧媒
体によって２００〜２０００kgf/cm2 の圧力を加えなが
ら凝固させる。これより、溶湯が温度の低い金型表面に
直接接するために、急冷凝固される効果とともに、その
際に溶湯に加えられる圧力の効果によって、強化元素の
Ｍｎ、Ｍｇ、Ｚｎをアルミニウム中に過飽和に強制固溶
させることができる。また、Ｄirect Ｃhill（Ｄ．
Ｃ．）鋳造法、ダイカスト法を用いても良く、金型鋳造
法も一部適用できる。In the first and second aspects of the present invention, it is preferable to use a high pressure casting method as a casting method for achieving a cooling rate of 0.5 ° C./sec or more during solidification. That is, immediately after the aluminum alloy melted in the melting furnace is filled in the product portion in the mold, it is solidified while applying a pressure of 200 to 2000 kgf / cm 2 to the surface of the molten metal with a pressure medium such as a punch. As a result, since the molten metal is in direct contact with the mold surface having a low temperature, it is rapidly solidified, and due to the effect of the pressure applied to the molten metal at that time, the strengthening elements Mn, Mg and Zn are supersaturated in aluminum. It can be forced to form a solid solution. In addition, Direct Chill (D.
C. ) A casting method or a die casting method may be used, and a die casting method can be partially applied.
【００４０】本第１発明の高強度・高靭性アルミニウム
合金部材の製造方法により、重量％で、Ｍｎ：0.５〜
２.5％、Ｍｇ：２.5〜７％と、少なくともＴｉ：0.15〜
0.５％、Ｚｒ：0.15〜0.５％、Ｂ：0.01〜0.１％のうち
の一種、および少なくともＳｂ：0.01〜0.５％、Ｂｉ：
0.01〜0.５％のうちの一種を含み、残部がアルミニウム
及び不可避不純物からなり、アルミニウム母材中に２０
μｍ以下のＭｎ化合物が均一に分散してなる高強度で高
靭性のアルミニウム合金部材を得ることができる。すな
わち、少なくともＴｉ、Ｚｒ、Ｂの一種とＭｎを共存さ
せたので、Ｍｎ化合物を丸い形状様の２０μｍ以下の微
細な粒子として分散させることができ、これにより、化
合物による切欠き効果を極力抑えて脆弱的に破断するの
を防ぎ、複合強化あるいは分散強化効果を有効に作用さ
せることができる。また、アルミニウムに良く固溶する
Ｍｇを含有させることにより、固溶強化効果を発揮させ
るとともに、均一な変形組織を生ぜしめて、靱性を損な
わず強度を向上させることができる。さらに、初晶Ａｌ
6 Ｍｎの晶出を抑えるＳｂまたはＢｉを添加することに
より、粗大なＡｌ6 Ｍｎ化合物による切欠き効果によっ
て部材が脆性的に破断するのを防いで、広い冷却速度の
範囲で凝固した場合でも、高強度で高靱性を実現するこ
とができる。By the method for producing a high-strength and high-toughness aluminum alloy member according to the first aspect of the present invention, Mn: 0.5 to 0.5 by weight%
2.5%, Mg: 2.5 to 7%, and at least Ti: 0.15 to
0.5%, Zr: 0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi:
It contains one of 0.01 to 0.5% and the balance is aluminum and unavoidable impurities.
It is possible to obtain a high-strength and high-toughness aluminum alloy member in which a Mn compound having a size of μm or less is uniformly dispersed. That is, since at least one of Ti, Zr and B coexists with Mn, the Mn compound can be dispersed as fine particles having a round shape and having a size of 20 μm or less, thereby suppressing the notch effect of the compound as much as possible. It is possible to prevent fragile breakage and to effectively exert a composite strengthening or dispersion strengthening effect. Further, by containing Mg that is well solid-dissolved in aluminum, it is possible to exert a solid-solution strengthening effect, produce a uniform deformed structure, and improve strength without impairing toughness. Furthermore, primary crystal Al
By adding Sb or Bi that suppresses the crystallization of 6 Mn, the member is prevented from brittle fracture due to the notch effect of the coarse Al 6 Mn compound, and even when solidified in a wide cooling rate range, High strength and high toughness can be realized.
【００４１】本第２発明の高強度・高靭性アルミニウム
合金部材の製造方法により、重量％で、Ｍｎ：0.５〜2.
５％、Ｍｇ：2.５〜７％、Ｚｎ：１〜５％と、少なくと
もＴｉ：0.15〜0.５％、Ｚｒ：0.15〜0.５％、Ｂ：0.01
〜0.１％のうちの一種、および少なくともＳｂ：0.01〜
0.5 ％、Ｂｉ：0.01〜0.５％のうちの一種を含み、残部
がアルミニウム及び不可避不純物からなり、アルミニウ
ム母材中に20μｍ以下のＭｎ化合物が均一に分散してな
る高強度で高靭性のアルミニウム合金部材を得ることが
できる。すなわち、少なくともＴｉ、Ｚｒ、Ｂの一種と
Ｍｎを共存させたので、Ｍｎ化合物を丸い形状様の２０
μｍ以下の微細な粒子として分散させることができる。
また、アルミニウムに良く固溶するＭｇおよびＺｎを含
有させることにより、固溶強化効果を発揮させるととも
に、Ｍｇ，Ｚｎ，Ａｌからなる析出物による強化作用を
発現させて、均一な変形組織を生ぜしめ、靱性低下を極
力抑えて強度を向上させることができる。さらに、初晶
Ａｌ6 Ｍｎの晶出を抑えるＳｂまたはＢｉを添加するこ
とにより、広い冷却速度の範囲で凝固した場合でも、高
強度で高靱性を実現することができた。By the method for producing a high strength / high toughness aluminum alloy member according to the second aspect of the present invention, Mn: 0.5 to 2.
5%, Mg: 2.5-7%, Zn: 1-5% and at least Ti: 0.15-0.5%, Zr: 0.15-0.5%, B: 0.01
~ 0.1%, and at least Sb: 0.01 ~
0.5%, Bi: 0.01 to 0.5%, the balance consisting of aluminum and unavoidable impurities, and a Mn compound of 20 μm or less uniformly dispersed in the aluminum base material. An aluminum alloy member can be obtained. That is, at least one of Ti, Zr, and B coexisted with Mn, so that the Mn compound had a round shape.
It can be dispersed as fine particles having a size of μm or less.
Further, by containing Mg and Zn which are well solid-dissolved in aluminum, the solid solution strengthening effect is exerted, and the strengthening action by the precipitates composed of Mg, Zn, and Al is produced, and a uniform deformed structure is produced. The strength can be improved by suppressing the deterioration of toughness as much as possible. Furthermore, by adding Sb or Bi that suppresses the crystallization of primary crystal Al 6 Mn, it was possible to realize high strength and high toughness even when solidified in a wide cooling rate range.
【００４２】以下に、本発明の実施例を説明する。Examples of the present invention will be described below.
【００４３】第１実施例 第１表に示した鋳造用アルミニウム合金を、高周波誘導
炉を用いて１０００℃で完全に溶解してから、大気中で
８５０℃まで自然冷却した後、２５０℃に予熱したφ９
０×１５０ mm の金型に鋳込み、加圧力９００kgf/cm2
を付加させながら、高圧鋳造しアルミニウム合金部材を
得た。次いで、冷却速度が約５℃／秒となる金型との接
触面から１０mmの部分、および冷却速度が約0.５℃／秒
の鋳物の中心部から、ＪＩＳ４号Ａ引張試験用の試料片
を切り出した。島津製オートグラフを用い、クロスヘッ
ド速度２mm／min で各組成の合金試料片につき４本ずつ
引張試験を行った。以上により得られた結果を、第２表
に示す。 First Example The casting aluminum alloys shown in Table 1 were completely melted at 1000 ° C. in a high frequency induction furnace, then naturally cooled to 850 ° C. in the atmosphere, and then preheated to 250 ° C. Φ9
Cast into a 0 × 150 mm mold and press force 900 kgf / cm 2
Was added to obtain an aluminum alloy member. Then, from the portion 10 mm from the contact surface with the mold where the cooling rate is about 5 ° C / sec, and from the center of the casting with the cooling rate of about 0.5 ° C / sec, the specimen for JIS No. 4A tensile test Cut out. Using an autograph manufactured by Shimadzu, four tensile tests were conducted for each alloy sample piece of each composition at a crosshead speed of 2 mm / min. The results obtained as described above are shown in Table 2.
【００４４】[0044]
【表１】 [Table 1]
【００４５】[0045]
【表２】 [Table 2]
【００４６】本実施例である試料番号１は、冷却速度が
５℃／秒のときには引張強さが３２.6kgf/mm、20.2％耐
力が１６.3kgf/mm2 、伸びが２８.3％であり、0.５℃／
秒のときにはそれぞれ２９.5kgf/mm2 、１５.0kgf/mm2
および１５.0％である。Ｓｂを含まない比較例の試料番
号Ｃ１と比べると、高い引張強さと伸びを示しているこ
とが分かる。試料番号２と試料番号３は、Ｓｂ量を変化
させた例であり、いずれも比較例の試料番号Ｃ１よりも
高い引張強さおよび伸びを有している。試料番号４は、
Ｍｎ量がさらに高い場合の例であり、比較例の試料番号
Ｃ２およびＣ３よりも引張強さと伸びが高い。試料番号
５は、Ｂｉを添加した場合の例であり、Ｓｂと同様な効
果を有することが分かる。さらに、試料番号６は、合金
元素としてＺｎを含んだ場合の例であり、比較例の試料
番号Ｃ４よりも引張強さと伸びが高い。Sample No. 1 of this example has a tensile strength of 32.6 kgf / mm, a 20.2% proof stress of 16.3 kgf / mm 2 , and an elongation of 28.3% when the cooling rate is 5 ° C./sec. Yes, 0.5 ° C /
Each at the time of seconds 29.5kgf / mm 2, 15.0kgf / mm 2
And 15.0%. It can be seen that when compared with the sample number C1 of the comparative example that does not contain Sb, high tensile strength and elongation are exhibited. Sample Nos. 2 and 3 are examples in which the amount of Sb was changed, and both have higher tensile strength and elongation than Sample No. C1 of the comparative example. Sample No. 4 is
This is an example in which the Mn content is higher, and the tensile strength and elongation are higher than those of sample numbers C2 and C3 of the comparative example. Sample No. 5 is an example in which Bi is added, and it can be seen that it has the same effect as Sb. Further, Sample No. 6 is an example in which Zn is contained as an alloy element, and has higher tensile strength and elongation than Sample No. C4 of Comparative Example.
【００４７】第２実施例 第３表に示した鋳造用アルミニウム合金を、高周波誘導
炉を用いて１０００℃で完全に溶解してから、大気中で
８５０℃まで自然冷却した後、１５０℃に予熱した３５
×４８×２００mmの金型に鋳込み、圧力９００kgf/cm2
を付加させながら、高圧鋳造してアルミニウム合金部材
を得た。次いで、冷却速度が約15℃／秒となる金型との
接触面から10mmの部分から、第１実施例と同様に、引張
試験のための試料片を切り出して、引張試験を行なっ
た。以上により得られた結果を、第４表に示す。 Second Embodiment The casting aluminum alloys shown in Table 3 were completely melted at 1000 ° C. in a high frequency induction furnace, then naturally cooled to 850 ° C. in the atmosphere, and then preheated to 150 ° C. Done 35
Cast into a mold of × 48 × 200mm, pressure 900kgf / cm 2
Was added to obtain an aluminum alloy member. Then, a sample piece for a tensile test was cut out from a portion 10 mm from the contact surface with the mold where the cooling rate was about 15 ° C./second, and the tensile test was performed. The results obtained as described above are shown in Table 4.
【００４８】[0048]
【表３】 [Table 3]
【００４９】[0049]
【表４】 [Table 4]
【００５０】本実施例である試料番号７〜試料番号１０
と、それぞれに対応したＳｂを含まない比較例の試料番
号Ｃ５〜試料番号Ｃ８とを比較すると、本実施例の場合
はいずれも伸びが高く、試料番号９と試料番号１０とは
引張強さも高くなっていることがわかる。一方、0.２％
耐力は、ほぼ同じであった。このように、Ｓｂを添加し
た本実施例の鋳造用アルミニウム合金は、比較用合金で
は引張特性が低下するＭｎ量の高い範囲まで、高い引張
特性を保持できることが分かる。Sample No. 7 to Sample No. 10 of this Example
And the sample numbers C5 to C8 of the comparative examples that do not include Sb corresponding thereto respectively, the elongation is high in the case of this example, and the tensile strengths of the sample numbers 9 and 10 are also high. You can see that it has become. On the other hand, 0.2%
The yield strength was almost the same. As described above, it is understood that the aluminum alloy for casting of the present example to which Sb is added can maintain high tensile properties up to a range where the amount of Mn in which the tensile properties of the comparative alloy are deteriorated is high.
Claims (4)
2.５〜７％と、少なくともＴｉ：0.15〜0.５％、Ｚｒ：
0.15〜0.５％、Ｂ：0.01〜0.１％のうちの一種、および
少なくともＳｂ：0.01〜0.５％、Ｂｉ：0.01〜0.５％の
うちの一種を含み、残部が実質的にアルミニウムとなる
ように原料を溶解し、前記原料の溶湯を0.５℃／秒以上
の冷却速度で凝固させることを特徴とする高強度・高靭
性アルミニウム合金部材の製造方法。1. Mn: 0.5 to 2.5% by weight, Mg:
2.5 to 7%, at least Ti: 0.15 to 0.5%, Zr:
0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi: 0.01 to 0.5%, and the balance substantially. A method for producing a high-strength / high-toughness aluminum alloy member, characterized in that a raw material is melted to form aluminum and the molten metal of the raw material is solidified at a cooling rate of 0.5 ° C./sec or more.
2.５〜７％、Ｚｎ：１〜５％と、少なくともＴｉ：0.15
〜0.５％、Ｚｒ：0.15〜0.５％、Ｂ：0.01〜0.１％のう
ちの一種、および少なくともＳｂ：0.01〜0.５％、Ｂ
ｉ：0.01〜0.５％のうちの一種を含み、残部が実質的に
アルミニウムとなるように原料を溶解し、前記原料の溶
湯を0.５℃／秒以上の冷却速度で凝固させることを特徴
とする高強度・高靭性アルミニウム合金部材の製造方
法。2. Mn: 0.5 to 2.5% by weight, Mg:
2.5 to 7%, Zn: 1 to 5%, and at least Ti: 0.15
~ 0.5%, Zr: 0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, B
i: containing one of 0.01 to 0.5%, melting the raw material so that the balance is substantially aluminum, and solidifying the molten metal of the raw material at a cooling rate of 0.5 ° C./second or more. A method for producing a high-strength, high-toughness aluminum alloy member characterized.
２.5〜７％と、少なくともＴｉ：0.15〜0.５％、Ｚｒ：
0.15〜0.５％、Ｂ：0.01〜0.１％のうちの一種、および
少なくともＳｂ：0.01〜0.５％、Ｂｉ：0.01〜0.５％の
うちの一種を含み、残部がアルミニウム及び不可避不純
物からなることを特徴とする鋳造用アルミニウム合金。3. By weight%, Mn: 0.5-2.5%, Mg:
2.5 to 7%, at least Ti: 0.15 to 0.5%, Zr:
0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, Bi: 0.01 to 0.5%, the balance being aluminum and An aluminum alloy for casting, which is made of inevitable impurities.
2.５〜７％、Ｚｎ：１〜５％と、少なくともＴｉ：0.15
〜0.５％、Ｚｒ：0.15〜0.５％、Ｂ：0.01〜0.１％のう
ちの一種、および少なくともＳｂ：0.01〜0.5 ％、Ｂ
ｉ：0.01〜0.５％のうちの一種を含み、残部がアルミニ
ウム及び不可避不純物からなることを特徴とする鋳造用
アルミニウム合金。4. By weight%, Mn: 0.5-2.5%, Mg:
2.5 to 7%, Zn: 1 to 5%, and at least Ti: 0.15
To 0.5%, Zr: 0.15 to 0.5%, B: 0.01 to 0.1%, and at least Sb: 0.01 to 0.5%, B
i: An aluminum alloy for casting, containing one of 0.01 to 0.5% and the balance being aluminum and inevitable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13946993A JPH06330202A (en) | 1993-05-17 | 1993-05-17 | Method for manufacturing high strength / high toughness aluminum alloy member and casting aluminum alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13946993A JPH06330202A (en) | 1993-05-17 | 1993-05-17 | Method for manufacturing high strength / high toughness aluminum alloy member and casting aluminum alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH06330202A true JPH06330202A (en) | 1994-11-29 |
Family
ID=15245970
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13946993A Pending JPH06330202A (en) | 1993-05-17 | 1993-05-17 | Method for manufacturing high strength / high toughness aluminum alloy member and casting aluminum alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH06330202A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5925314A (en) * | 1996-03-29 | 1999-07-20 | Mazda Motor Corporation | High ductility aluminum alloy and method for manufacturing the high ductility aluminum alloy |
| JP2003342664A (en) * | 2002-05-30 | 2003-12-03 | Honda Motor Co Ltd | Al-Mg alloy for casting |
| WO2003102257A1 (en) * | 2002-05-30 | 2003-12-11 | Honda Giken Kogyo Kabushiki Kaisha | Die casting having high toughness |
| WO2008138614A1 (en) * | 2007-05-16 | 2008-11-20 | Technische Universität Clausthal | Use of an al-mn alloy for high temperature resistant products |
-
1993
- 1993-05-17 JP JP13946993A patent/JPH06330202A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5925314A (en) * | 1996-03-29 | 1999-07-20 | Mazda Motor Corporation | High ductility aluminum alloy and method for manufacturing the high ductility aluminum alloy |
| JP2003342664A (en) * | 2002-05-30 | 2003-12-03 | Honda Motor Co Ltd | Al-Mg alloy for casting |
| WO2003102257A1 (en) * | 2002-05-30 | 2003-12-11 | Honda Giken Kogyo Kabushiki Kaisha | Die casting having high toughness |
| US7713470B2 (en) | 2002-05-30 | 2010-05-11 | Honda Giken Kogyo Kabushiki Kaisha | Die casting having high toughness |
| WO2008138614A1 (en) * | 2007-05-16 | 2008-11-20 | Technische Universität Clausthal | Use of an al-mn alloy for high temperature resistant products |
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