JP2001073056A - Aluminum alloy cast material excellent in impact fracture strength and its production - Google Patents
Aluminum alloy cast material excellent in impact fracture strength and its productionInfo
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車のサスペン
ション部品などの輸送機の構造材用に好適な、衝撃破壊
強度に優れたアルミニウム合金鋳造材、更にアルミニウ
ム合金鋳造材の製造方法 (以下、アルミニウムを単にAl
と言う) に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing an aluminum alloy cast material having excellent impact fracture strength, which is suitable for a structural material of a transportation machine such as a suspension part of an automobile, and a method of manufacturing an aluminum alloy cast material (hereinafter, referred to as aluminum). Simply Al
).
【０００２】[0002]
【従来の技術】周知の通り、建築物や構造物、或いは鉄
道車両、航空機、船舶、自動車、自動二輪、自転車等の
輸送機等の構造部材や構造部品 (これらを総称して構造
材と言う) に、例えば、自動車などの輸送機材の構造材
あるいはナックル、ロアアーム、アッパーアームなどの
サスペンション部品用として、軽量化を目的として、鋼
材に代わり、Al合金材が使用され始めている。2. Description of the Related Art As is well known, structural members and structural parts of buildings and structures, or transport vehicles such as railway vehicles, aircraft, ships, automobiles, motorcycles, bicycles, and the like (these are collectively referred to as structural materials). For example, Al alloy materials have begun to be used instead of steel materials for the purpose of weight reduction, for example, for structural materials of transportation equipment such as automobiles or suspension parts such as knuckles, lower arms, and upper arms.
【０００３】これらAl合金構造材の製造方法としては、
製造コストの低減や、複雑形状部品への加工の点から、
一般的に鋳造法や鍛造法などが用いられる。特に、Al合
金鋳造材で、高強度で高靱性などの機械的性質を有し、
構造材として重要な破壊に対して信頼の高い構造材がで
きれば、鍛造や圧延などの塑性加工工程が省略できる
等、製造コスト的に最も有利となる。[0003] As a method of producing these Al alloy structural materials,
From the viewpoint of reduction of manufacturing cost and processing of complex shaped parts,
Generally, a casting method or a forging method is used. In particular, Al alloy cast material, having mechanical properties such as high strength and high toughness,
If a structural material having high reliability against destruction, which is important as a structural material, can be obtained, it is most advantageous in terms of manufacturing cost, for example, a plastic working process such as forging or rolling can be omitted.
【０００４】従来のAl合金鋳造材は、ダイカスト法、砂
型鋳造法、金型鋳造法、高圧鋳造法(溶湯鍛造法) など
の種々の鋳造方法によって鋳込まれたAl合金材をT6など
の溶体化処理後焼き入れを行い、人工時効硬化処理を施
して製造される。[0004] Conventional Al alloy casting materials include Al alloy materials cast by various casting methods such as a die casting method, a sand casting method, a die casting method, a high pressure casting method (a molten metal forging method), and the like. It is manufactured by quenching after chemical treatment and by artificial age hardening.
【０００５】これら鋳造法の内、特に、高圧鋳造法 (溶
湯鍛造法) は、前記他の鋳造法に比して、構造材として
重要な破壊に対して信頼の高い構造材ができ、Al合金構
造材の製造方法として主流となっている。[0005] Among these casting methods, the high-pressure casting method (melt forging method), in particular, can produce a structural material having high reliability against destruction, which is important as a structural material, as compared with the other casting methods. It has become mainstream as a method of manufacturing structural materials.
【０００６】この高圧鋳造法は、高圧下で溶湯を凝固さ
せる (溶湯の凝固過程を制御するために加圧する) 鋳造
法であって、この点、溶湯を鋳型キャビティに注入させ
るために加圧するダイカスト法とは区別される (また、
ダイカスト法は肉厚の異なる部位を有するサスペンショ
ン部品など本発明が対象とする構造材の製造には不適で
ある) 。そして、より具体的には、溶解炉から横型乃至
縦型のスリーブ内に、Al合金溶湯を給湯管などを介して
流し込み、その後スリーブ内のAl合金溶湯をピストンに
より加圧して、Al合金溶湯をスリーブ内の金型に接触さ
せて冷却する方式である。This high-pressure casting method is a casting method in which a molten metal is solidified under high pressure (pressing to control the solidification process of the molten metal). In this regard, die casting in which the molten metal is pressurized to be injected into a mold cavity is used. Distinct from the law (and
The die casting method is unsuitable for manufacturing a structural material targeted by the present invention, such as a suspension part having portions having different thicknesses). More specifically, the Al alloy melt is poured from a melting furnace into a horizontal or vertical sleeve through a hot water supply pipe or the like, and then the Al alloy melt in the sleeve is pressurized by a piston to remove the Al alloy melt. This is a method of cooling by contacting the mold inside the sleeve.
【０００７】そして、この高圧鋳造法は、スリーブ内に
Al合金溶湯を流し込む際の、空気の巻き込みを防止で
き、スリーブ内のAl合金溶湯の空気との接触面積を少な
くすることができるため、空気や酸化物の巻き込みが少
ない。更に、溶湯を加圧して冷却するために、引け巣等
の鋳造欠陥が抑制され、また、冷却速度を早めることが
できるため、凝固結晶粒やデンドライト二次アーム間隔
(DAS) を細かくすることが可能となる。この結果、前記
他の鋳造方法に比較して、Al合金鋳造材の鋳造欠陥を抑
制し、より高強度で高靱性化することが可能となる。ま
た、鋳造ロット毎の品質の安定性や量産性にも優れてい
る。したがって、特に素材の耐破壊性などの信頼性が要
求される、構造材用のAl合金鋳造材の製造方法として、
高圧鋳造法は適している。[0007] This high-pressure casting method is used in a sleeve.
Entrapment of air when pouring the Al alloy melt can be prevented, and the contact area of the Al alloy melt with air in the sleeve can be reduced, so that air and oxides are less involved. Further, since the molten metal is pressurized and cooled, casting defects such as shrinkage cavities are suppressed, and the cooling rate can be increased.
(DAS) can be made finer. As a result, as compared with the other casting methods, it is possible to suppress casting defects of the Al alloy casting material and to achieve higher strength and higher toughness. It is also excellent in quality stability and mass productivity for each casting lot. Therefore, as a method of manufacturing aluminum alloy castings for structural materials, especially where reliability such as the fracture resistance of the material is required,
High pressure casting is suitable.
【０００８】この高圧鋳造法を用いて、構造材用のAl合
金鋳造材を製造しようとする場合、Al合金としては、鋳
造性と機械的性質が優れており、Siを6.5 〜7.5% (質量
% 、以下同じ) 含む、Al-Si-Mg系のJIS AC4CH 等の Al
鋳造用合金が用いられている。そして、鋳造材の高強度
化乃至高靱性化のために、前記他の鋳造法と同じく、Al
合金材のSiやMgなどの合金元素を固溶させる溶体化処理
後に焼入れし、その後、前記合金元素を化合物として析
出させる高温での人工時効硬化処理を行う。When an Al alloy cast material for a structural material is to be manufactured by using this high-pressure casting method, the Al alloy is excellent in castability and mechanical properties, and has an Si content of 6.5 to 7.5% (mass
%, The same shall apply hereinafter) including Al-Si-Mg-based JIS AC4CH etc.
Casting alloys are used. Then, in order to increase the strength or toughness of the cast material, as in the other casting methods, Al
After a solution treatment for forming a solid solution of an alloy element such as Si or Mg of the alloy material, the alloy material is quenched, and then an artificial age hardening treatment at a high temperature is performed to precipitate the alloy element as a compound.
【０００９】しかし、近年、前記自動車などのサスペン
ション部品などのAl合金構造材自体は軽量化のために、
より薄肉化される傾向にあり、構造材用Al合金鋳造材
も、薄肉化された状態で、より優れた耐破壊性、即ちよ
り優れた衝撃破壊強度を発揮することが要求されてい
る。However, in recent years, Al alloy structural materials such as the above-mentioned suspension parts for automobiles have been used to reduce the weight.
There is a tendency that the thickness of the cast Al alloy for structural materials is further reduced, and it is required that the cast Al alloy material for a structural material exhibit superior fracture resistance, that is, superior impact fracture strength in a thinned state.
【００１０】この要求に対し、現状の高圧鋳造法を用い
た、構造材用のAl合金鋳造材では、必ずしも期待通りに
衝撃破壊強度が高くならず、この種用途に要求される耐
衝撃破壊性を満足できないという問題があった。[0010] In response to this requirement, the Al alloy cast material for structural materials using the current high pressure casting method does not always have high impact fracture strength as expected, and the impact fracture resistance required for this type of application is not always achieved. Was not satisfied.
【００１１】この耐衝撃破壊性の問題を、より具体的に
説明すると、自動車などのサスペンション部品として
の、図1 に示すような形状の、アーム類などの輸送機用
の構造材では、軽量化のための薄肉化が前提となってい
る。また、他の構造材との関連や全体形状の制約から
も、構造材の靱性や伸びを高めるためには、建築物など
のような構造材と違い、構造材自体を大きく乃至厚肉化
することができない。したがって、輸送機用の構造材で
は、比較的小型乃至薄肉化された部材として、前記高い
耐衝撃破壊性を有する必要があるという、他の構造材用
途には無い、課題を有する。[0011] The problem of the impact destruction resistance will be described more specifically. In the case of a structural material for a transport machine such as an arm having a shape as shown in FIG. It is assumed that the thickness is reduced for the purpose. In addition, in order to increase the toughness and elongation of the structural material due to the relationship with other structural materials and restrictions on the overall shape, the structural material itself is made larger or thicker, unlike structural materials such as buildings. Can not do. Therefore, a structural material for a transport machine has a problem that it is necessary to have the high impact fracture resistance as a relatively small-sized or thinned member, which is not found in other structural material applications.
【００１２】また、特に、前記アーム類などでは、図1
に示すように、アーム1 の取り付け部2 における可動代
を確保するために、取り付け部 (突起部) の付け根部
T2、T3、T4では、設計上、特に細径化された形状を有す
る。この細径化部分は、細径化されているがゆえに、ア
ームの他の部分よりも、衝撃などの外力によって破壊し
やすくなる。また、この他、アームの中央部T1も、常
時、かつ種々の方向からの応力や衝撃などの負荷が集中
するために、破壊しやすくなる。Particularly, in the case of the above-mentioned arms, etc., FIG.
As shown in the figure, to secure the movable allowance at the mounting part 2 of the arm 1, the base of the mounting part (projection)
T 2 , T 3 , and T 4 have a particularly reduced shape in design. The reduced diameter portion is more easily broken by an external force such as an impact than the other portions of the arm because of the reduced diameter. In addition to this, the central portion T 1 of the arm is also always and to load such stresses and shocks from various directions are concentrated, tends to break.
【００１３】したがって、重要保安部品と呼ばれる、こ
れら輸送機用の構造材では、軽量化のために、構造材の
厚みを、部位によっては、15mm以下の薄肉とすることを
前提に、前記アームの細径化部分や中央部など、形状や
構造上、より破壊しやすくなっている部位の耐衝撃破壊
性を向上させる必要があるという困難性がある。[0013] Therefore, in these transport structural materials, which are called important security parts, in order to reduce the weight, the thickness of the structural material may be reduced to 15 mm or less depending on the part, so that the weight of the arm may be reduced. There is a difficulty that it is necessary to improve the impact fracture resistance of a portion that is more easily broken in terms of shape and structure, such as a reduced diameter portion and a central portion.
【００１４】従来から、構造材用のAl合金鋳造材の、構
造材としての高強度化や高靱性化のための改善は種々提
案されている。例えば、「Al基合金の強度と破壊特性」
(軽金属学会、平成9 年9 月1 日発行) では、Al鋳造用
合金の破壊特性に及ぼす、種々の要因について解明が行
われている。この中でも、特に、AC4CH など、Al-Si
系、Al-Si-Mg系のAl鋳造用合金について、12頁〜19頁に
は、Al鋳造用合金の破壊特性に悪影響を及ぼす要因とし
て、非金属介在物、デンドライトの粗密度 (広間隔) 、
ガス成分、Fe等の不純物等が挙げられている。Hitherto, various proposals have been made for improving the strength and toughness of a cast aluminum alloy material for a structural material. For example, "Strength and fracture characteristics of Al-based alloy"
The Japan Institute of Light Metals (September 1, 1997) has elucidated various factors affecting the fracture characteristics of Al casting alloys. Among them, especially, Al-Si such as AC4CH
Alloys, Al-Si-Mg alloys for Al casting, page 12 to 19, non-metallic inclusions, coarse density of dendrite (wide spacing) ,
Examples include gas components and impurities such as Fe.
【００１５】そして、これら非金属介在物、ガス成分、
Fe等の不純物等の低減等が、破壊強度を高める手段とし
て提案されている。また、鋳造の際に生成する共晶Siの
粗大化や針状化も破壊の起点となり、破壊強度を高める
ためには、共晶Siを微細化および形態を粒状化させる必
要があることが開示されている。[0015] These non-metallic inclusions, gas components,
Reduction of impurities such as Fe has been proposed as a means for increasing the breaking strength. In addition, coarsening and needle formation of eutectic Si generated during casting also become the starting point of fracture, and it is necessary to refine eutectic Si and granulate morphology in order to increase fracture strength Have been.
【００１６】また、共晶Siの微細化および形態の粒状化
のために、合金元素として、Na、Sr、Sb、或いはLi等を
添加して、靱性を強化する方法も開示されている。Also disclosed is a method of adding Na, Sr, Sb, Li, or the like as an alloying element to enhance the toughness in order to refine eutectic Si and granulate the form.
【００１７】[0017]
【発明が解決しようとする課題】しかし、前記非金属介
在物、ガス成分、Fe等の不純物等は、鋳物の溶解原料か
ら必然的に混入し、これらを低減するためには、溶解原
料にリサイクル材ではなく、新しい地金が必要になり、
溶解鋳造工程でも、これら不純物低減のための工程付加
やや設備等が必要になる。このため、破壊強度の向上を
不純物の低減のみに依存する方法では、どうしてもAl合
金鋳造材のコストアップに繋がる。また、前記Na、Sr、
Sb、或いはLi等の合金元素の添加も、添加量が多けれ
ば、却って共晶Siの粗大化 (靱性低下) を招くことにな
り、添加量に限界があり、効果の点でも限界があるとと
もに、Al合金鋳造材のコストアップに繋がる。However, the non-metallic inclusions, gas components, impurities such as Fe and the like are inevitably mixed from the raw material of the casting, and in order to reduce them, the non-metallic inclusions and the gas components must be recycled to the molten raw material. Instead of wood, we need new bullion,
In the melting and casting process, it is necessary to add a process for reducing these impurities and to use some equipment. For this reason, a method that depends only on the reduction of impurities for improving the fracture strength necessarily leads to an increase in the cost of the Al alloy casting material. Further, the Na, Sr,
Addition of alloying elements such as Sb or Li also leads to coarsening of eutectic Si (decrease in toughness) if the amount of addition is large, which limits the amount of addition and limits the effect. This leads to an increase in the cost of the Al alloy cast material.
【００１８】また、破壊強度の向上を目的として、デン
ドライトの密度を緻密化するためには、鋳造時の冷却速
度を大きくする必要がある。しかし、冷却速度が大きく
なると、逆に、前記ガスの巻き込み量も大きくなって、
却って、破壊強度を低下させてしまうことにも繋がる。In order to increase the dendrite density for the purpose of improving the breaking strength, it is necessary to increase the cooling rate during casting. However, when the cooling rate increases, conversely, the amount of entrainment of the gas also increases,
On the contrary, it also leads to lowering the breaking strength.
【００１９】したがって、現状の高圧鋳造法を用いたAl
合金鋳造材では、要求される耐衝撃破壊性を満足するも
のはなく、特に、前記重要保安部品などの構造材へのAl
合金鋳造材の適用が妨げられていたのが実情である。Therefore, Al using the current high pressure casting method
There is no alloy cast material that satisfies the required impact fracture resistance.
The fact is that the application of alloy castings has been hindered.
【００２０】本発明はこの様な事情に着目してなされた
ものであって、その目的は、特に、前記重要保安部品な
どの構造材で、しかも15mm以下の薄肉部位を有する構造
材に好適な、耐衝撃破壊性 (衝撃破壊強度) に優れた、
高圧鋳造法によるAl合金鋳造材およびその製造方法を提
供しようとするものである。The present invention has been made in view of such circumstances, and is particularly suitable for a structural material such as the above-mentioned important security parts and having a thin portion of 15 mm or less. , With excellent impact fracture resistance (impact fracture strength)
An object of the present invention is to provide an Al alloy cast material by a high-pressure casting method and a method for producing the same.
【００２１】[0021]
【課題を解決するための手段】この目的を達成するため
に、本発明衝撃破壊強度に優れたAl合金鋳造材の要旨
は、Siを2.0% (質量% 、以下同じ) 以上含み、高圧鋳造
法により鋳込まれ、溶体化処理および人工時効硬化処理
が施されたAl合金鋳造材であって、溶体化処理後の組織
中の共晶Siの最大径 (円相当径) が3.5 μm 以下および
アスペクト比が1.4 以下であり、人工時効硬化処理後の
鋳造材の耐力 (σ0.2)が230N/mm2以上、シャルピー衝撃
値が12J/cm2 以上、および伸びが17% 以上であることと
する。In order to achieve this object, the gist of the Al alloy casting material excellent in impact fracture strength according to the present invention is that a high-pressure casting method containing at least 2.0% (mass%, the same applies hereinafter) of Si. An Al alloy casting material that has been cast and subjected to solution treatment and artificial age hardening treatment.The maximum diameter (equivalent circle diameter) of eutectic Si in the structure after solution treatment is 3.5 μm or less and the aspect ratio The ratio is 1.4 or less, the proof stress (σ 0.2 ) of the cast material after the artificial age hardening treatment is 230 N / mm 2 or more, the Charpy impact value is 12 J / cm 2 or more, and the elongation is 17% or more.
【００２２】この内、Al合金鋳造材の製造上、衝撃破壊
強度を確実に向上させるためには、好ましくは、前記溶
体化処理を鋳造時の組織中の共晶Siの最大径が粗大化し
ないような時間で行う (請求項2 に対応) 。Of these, in order to reliably improve the impact fracture strength in the production of an Al alloy cast material, preferably, the solution treatment is performed so that the maximum diameter of eutectic Si in the structure at the time of casting does not become coarse. It is performed in such a time (corresponding to claim 2).
【００２３】また、Al合金鋳造材の成分組成上、衝撃破
壊強度を確実に向上させるために、好ましくは、Al合金
鋳造材に含まれるFeを0.2%以下に規制する (請求項3 に
対応) 。Further, in order to reliably improve the impact fracture strength, the content of Fe contained in the Al alloy casting material is preferably restricted to 0.2% or less in view of the component composition of the Al alloy casting material (corresponding to claim 3). .
【００２４】そして、Al合金鋳造材のより高強度化のた
めに、好ましくは、Al合金鋳造材に更にMgを0.2 〜1.6%
含ませる (請求項4 に対応) か、または、Al合金鋳造材
に含まれるSi量を6.5 〜7.5%とする (請求項5 に対応)
。In order to further increase the strength of the cast Al alloy material, it is preferable to further add 0.2 to 1.6% of Mg to the cast Al alloy material.
Included (corresponding to claim 4) or the amount of Si contained in the Al alloy cast material is 6.5-7.5% (corresponding to claim 5)
.
【００２５】更に、本発明Al合金鋳造材の最も好適な用
途としては、輸送機の構造材用であり (請求項6 に対
応) 、厚みが15mm以下の部位を有する輸送機の構造材用
である(請求項7 に対応) 。Further, the most preferable use of the cast aluminum alloy material of the present invention is for a structural material of a transport machine (corresponding to claim 6), and for a structural material of a transport machine having a portion having a thickness of 15 mm or less. (Corresponding to claim 7).
【００２６】また、本発明のAl合金鋳造材の製造方法の
要旨は、前記衝撃破壊強度に優れたAl合金鋳造材を得る
ために、Siを2.0%以上含むアルミニウム合金溶湯を高圧
鋳造法により鋳込んだ後、鋳造材の溶体化処理を、500
〜580 ℃の温度で2.0 時間以下行い、更に、人工時効硬
化処理を行うことである (請求項8 に対応) 。The gist of the method for producing an Al alloy cast material of the present invention is to cast an aluminum alloy melt containing 2.0% or more of Si by high pressure casting in order to obtain an Al alloy cast material having excellent impact fracture strength. After casting, solution treatment of casting material
This is performed at a temperature of about 580 ° C. for 2.0 hours or less, and is further subjected to an artificial age hardening treatment (corresponding to claim 8).
【００２７】本発明者らは、鋳造により晶出する晶出物
と、鋳造および熱処理されたAl合金組織の特性との関係
について検討した結果、鋳造により晶出する共晶Siが、
前記衝撃破壊強度と深く関わっていることを知見した。The present inventors have studied the relationship between the crystallized material crystallized by casting and the properties of the Al alloy structure that has been cast and heat treated.
It has been found that it is closely related to the impact fracture strength.
【００２８】即ち、Siを2.0%以上含むAl合金において
は、鋳造により、必然的に共晶SiがAl合金組織中に晶出
する。この共晶Siは、構造材に衝撃等の応力が負荷され
た場合に、破壊の起点 (ディンプルの起点）となりやす
い。そして、Al合金組織中に存在する共晶Siの粒径が大
きく、かつ長い形状を有している場合には、重要保安部
品である前記輸送機用の構造材では、前記アームの細径
化部分や中央部等、形状や構造上、比較的小型乃至薄肉
化された、より破壊しやすくなっている部位で、特に破
壊の起点となりやすく、衝撃破壊強度を低下させる。That is, in an Al alloy containing 2.0% or more of Si, eutectic Si is inevitably crystallized in the Al alloy structure by casting. This eutectic Si tends to be a starting point of fracture (a starting point of dimple) when a stress such as an impact is applied to the structural material. When the grain size of the eutectic Si present in the Al alloy structure is large and has a long shape, in the structural material for the transport machine, which is an important security part, the diameter of the arm is reduced. A part which is relatively small or thin in shape or structure, such as a part or a center part, and which is more easily broken, particularly easily becomes a starting point of destruction and lowers impact fracture strength.
【００２９】Al合金鋳造材の分野において、従来から
も、Al合金組織中に存在する共晶Siが靱性を阻害するこ
とは、前記した通り、一般的に公知である。しかし、高
圧鋳造法により鋳込まれるAl合金鋳造材の分野におい
て、溶体化処理を受けた組織中の共晶Siの形態と、構造
材としての衝撃破壊強度との関係は必ずしも明確ではな
かった。In the field of Al alloy castings, it has been generally known that eutectic Si present in the Al alloy structure impairs toughness as described above. However, in the field of Al alloy castings cast by high pressure casting, the relationship between the form of eutectic Si in the solution-treated structure and the impact fracture strength as a structural material was not always clear.
【００３０】例えば、従来の砂型鋳造法、金型鋳造法を
含め、高圧鋳造法により鋳込まれたAl合金鋳造材でも、
通常、500 〜580 ℃×5 〜12時間の溶体化処理を施す。
そして、砂型鋳造法、金型鋳造法などにおけるAl合金鋳
造材の組織中に存在する共晶Siは、前記通常の溶体化処
理前後で、長細い形状から丸い形状に形態は変化するも
のの、その大きさ (最大径) は殆ど変化しない。For example, even in the case of an Al alloy casting material cast by a high-pressure casting method, including a conventional sand casting method and a mold casting method,
Usually, a solution treatment is performed at 500 to 580 ° C for 5 to 12 hours.
Then, eutectic Si present in the structure of the Al alloy casting material in sand casting, mold casting, etc., before and after the normal solution treatment, although the form changes from a long and thin shape to a round shape, The size (maximum diameter) hardly changes.
【００３１】しかし、一方、高圧鋳造法により鋳込まれ
たAl合金鋳造材では、前記通常の溶体化処理を施した場
合、Al合金組織中に存在する共晶Siの形態も、長細い形
状から丸い形状に変化するとともに、その大きさ (最大
径) も変化し、しかも溶体化処理時間によって著しく粗
大化する事実を本発明者らは知見した。On the other hand, in the case of the Al alloy cast material cast by the high-pressure casting method, when the above-mentioned ordinary solution treatment is performed, the form of eutectic Si present in the Al alloy structure also changes from a long and thin shape. The present inventors have found that the shape (maximum diameter) changes as the shape changes to a round shape, and that the shape is remarkably coarsened by the solution treatment time.
【００３２】言い換えると、従来の砂型鋳造法、金型鋳
造法などによって鋳込まれたAl合金鋳造材では、前記比
較的長時間の溶体化処理を施すことによって、SiやMgの
固溶(溶体化) が進む一方で、共晶Siの大きさは変わら
ず、形態のみが丸い形状に変化するため、構造材として
の衝撃破壊強度にとって好ましい形態となる。In other words, in the Al alloy cast material cast by the conventional sand casting method, mold casting method, or the like, the solution treatment of Si or Mg is carried out by performing the solution treatment for a relatively long time. While the size of the eutectic Si does not change and only the form changes to a round shape, which is a preferable form for impact fracture strength as a structural material.
【００３３】これに対し、高圧鋳造法により鋳込まれた
Al合金鋳造材では、通常の、前記比較的長時間の溶体化
処理を施すことによって、SiやMgの固溶 (溶体化) が進
み、共晶Siの形態も丸い形状に変化する点は他の鋳造材
と同じであるものの、共晶Siの最大径が粗大化するた
め、構造材としての衝撃破壊強度は著しく低下するとい
う逆の減少が生じることになる。On the other hand, it was cast by a high pressure casting method.
In the case of Al alloy castings, the usual solution treatment for a relatively long time promotes solid solution (solution solution) of Si and Mg and changes the eutectic Si form into a round shape. However, since the maximum diameter of the eutectic Si is coarsened, the impact fracture strength as a structural material is remarkably reduced.
【００３４】更に、本発明者らが知見したところによれ
ば、高圧鋳造法により鋳込まれたAl合金鋳造材は、温度
条件にもよるが、概ね2 時間を越える溶体化処理では、
前記共晶Siの最大径の粗大化が生じ、概ね1 時間程度の
溶体化処理では、共晶Siの形状は、長細い形状から丸い
形状に変化するものの、その大きさ (最大径) は殆ど変
化しなくなる。Further, according to the findings of the present inventors, the Al alloy cast material cast by the high-pressure casting method, although depending on the temperature conditions, is subjected to a solution treatment generally exceeding 2 hours.
The maximum diameter of the eutectic Si is coarsened, and in the solution treatment for about 1 hour, the shape of the eutectic Si changes from a long thin shape to a round shape, but the size (maximum diameter) is almost zero. Will not change.
【００３５】したがって、高圧鋳造法により鋳込まれた
Al合金鋳造材に対し、SiやMgを十分固溶 (溶体化) させ
る従来の溶体化処理の観点から、他の鋳造材と同じく、
比較的長時間の溶体化処理を施した場合には、必然的に
共晶Siの粗大化が生じ、衝撃破壊強度が低くならざるを
得なかったものである。Therefore, it was cast by the high pressure casting method.
From the viewpoint of the conventional solution treatment in which Si and Mg are sufficiently solid-dissolved (solution solution) in the Al alloy cast material, like other cast materials,
When the solution treatment was performed for a relatively long time, the eutectic Si was inevitably coarsened, and the impact fracture strength had to be reduced.
【００３６】この鋳造方法の違いによる、溶体化処理に
おける共晶Siの挙動の違いの理由は定かではないが、高
圧鋳造法により鋳込まれたAl合金鋳造材の場合、溶体化
処理前の共晶Siのサイズが、他の鋳造法に比較して、よ
り細かいことによるものと考えられる。The reason for the difference in the behavior of eutectic Si in the solution treatment due to the difference in the casting method is not clear, but in the case of the Al alloy cast material cast by the high pressure casting method, the It is considered that the size of the crystalline Si is finer than other casting methods.
【００３７】[0037]
【発明の実施の形態】(溶体化処理後の共晶Si)本発明で
規定する溶体化処理後の共晶Siの最大径 (円相当径) と
アスペクト比について、以下に説明する。BEST MODE FOR CARRYING OUT THE INVENTION (Eutectoid Si after solution treatment) The maximum diameter (equivalent circle diameter) and aspect ratio of eutectic Si after solution treatment specified in the present invention will be described below.
【００３８】本発明で言う共晶Siの最大径 (円相当径)
とは、400 倍の光学顕微鏡若しくは走査型電子顕微鏡(S
EM) による鋳造材組織の観察において、視野内で観察さ
れる最も大きな共晶Si粒子の最大の長さを長径とし、こ
れに直交する長さを短径とする楕円の面積に等しい円の
面積の直径である。そして、測定結果に再現性をもたせ
るために、共晶Siの最大径の測定 (前記鋳造材の組織観
察) は、図1 のT1〜T3などの所定部位において、10〜20
視野数行い、その平均を求め、本発明ではこの平均値を
3.5 μm 以下と規定する。Maximum diameter (equivalent circle diameter) of eutectic Si referred to in the present invention
A 400x optical microscope or scanning electron microscope (S
In the observation of the structure of the cast material by EM), the maximum length of the largest eutectic Si particle observed in the visual field is defined as the major axis, and the area of a circle equal to the area of the ellipse whose minor axis is the length orthogonal to this. Is the diameter of Then, in order to give reproducibility to the measurement results, measurement of the maximum diameter of eutectic Si (observation of the structure of the cast material) is performed at a predetermined site such as T1 to T3 in FIG.
The number of fields of view is calculated and the average is obtained.
It is specified to be 3.5 μm or less.
【００３９】また、本発明で言う共晶Siのアスペクト比
とは、前記最も大きな共晶Si粒子の最大の長さ (長径)
と、これに直交する長さ (短径) との比 (長径/ 短径)
である。そして、共晶Siの最大径と同様に、測定は10〜
20視野数行い、その平均を求め、本発明ではこの平均値
を1.4 以下と規定する。The aspect ratio of eutectic Si referred to in the present invention means the maximum length (major axis) of the largest eutectic Si particles.
And the length (minor axis) perpendicular to this (major axis / minor axis)
It is. And, like the maximum diameter of eutectic Si, the measurement is 10 ~
The number of fields of view is calculated for 20 fields, and the average is determined.
【００４０】溶体化処理後の共晶Siの前記最大径が3.5
μm を越える、およびアスペクト比が1.4 を越える場
合、前記自動車のサスペンション部品などの重要保安部
品用の構造材として要求される、人工時効硬化処理後の
耐力 (σ0.2)が230N/mm2以上、シャルピー衝撃値が12/c
m2以上、および伸びが17% 以上の、強度、靱性や伸びが
達成できず、衝撃破壊強度を満足できない。The maximum diameter of the eutectic Si after solution treatment is 3.5
If it exceeds μm and the aspect ratio exceeds 1.4, the proof stress after artificial age hardening (σ 0.2 ) required as a structural material for important safety parts such as the suspension parts of the automobile is 230 N / mm 2 or more, Charpy impact value of 12 / c
The strength, toughness and elongation of m 2 or more and elongation of 17% or more cannot be achieved, and the impact fracture strength cannot be satisfied.
【００４１】本発明で規定するこれら機械的な特性は、
構造材としての各部位の平均ではなく、これら機械的な
特性が最も低くなる部位、或いは最も衝撃破壊しやすい
部位の最低値の規定、即ち構造材としての下限の規定で
ある。特に、これら機械的な特性が最も低くなる部位と
しては、前記アーム類の取り付け部 (突起部) の付け根
部などの、薄肉化および細径化された部分がある。ま
た、最も衝撃破壊しやすい部位としては、常時かつ種々
の方向からの応力や衝撃などの負荷が集中するアームの
中央部などである。これら、特に衝撃破壊しやすい部分
の、衝撃破壊強度を満足できない。These mechanical properties defined in the present invention are:
It is not the average of each part as a structural material, but the minimum value of those parts having the lowest mechanical properties or the parts that are most likely to be impact-broken, that is, the lower limit of the structural material. In particular, the parts having the lowest mechanical properties include thinned and thinned parts such as the base of the mounting part (projection) of the arms. In addition, the most susceptible to impact destruction is the central portion of the arm where loads such as stresses and impacts are constantly concentrated from various directions. In particular, the impact fracture strength of these parts that are easily damaged by impact cannot be satisfied.
【００４２】なお、溶体化処理後の共晶Siの最大径およ
びアスペクト比は、人工時効処理等によっても、殆ど変
化しないので、人工時効処理後に共晶Siの最大径および
アスペクト比を測定しても良い。共晶Siの最大径および
アスペクト比の測定は、400倍程度の光学顕微鏡若しく
は走査型電子顕微鏡(SEM) の目視観察乃至画像解析観察
による行うことができる。Since the maximum diameter and the aspect ratio of the eutectic Si after the solution treatment hardly change even by the artificial aging treatment, the maximum diameter and the aspect ratio of the eutectic Si are measured after the artificial aging treatment. Is also good. The measurement of the maximum diameter and the aspect ratio of eutectic Si can be performed by visual observation or image analysis observation with an optical microscope or a scanning electron microscope (SEM) of about 400 times.
【００４３】(Al合金の化学成分組成)次に、本発明Al合
金鋳造材における、化学成分組成について説明する。本
発明のAl合金は、人工時効硬化処理後の耐力 (σ0.2)が
230N/mm2以上、シャルピー衝撃値が12/cm2以上、および
伸びが18% 以上確保できるものであれば、或いはこれら
機械的特性の他、好ましい特性として、耐蝕性を有して
いるものであれば、高強度化のために必要なSiを2.0%以
上含む、JIS に規格されている重力鋳造用Al合金が適宜
使用可能である。より具体的には、Al-Cu-Si系のAC2A、
AC2B、Al-Si 系のAC3A、Al-Si-Mg系のAC4A、AC4C、AC4C
H 、Al-Si-Cu系のAC4B、Al-Si-Cu-Mg 系のAC4D、Al-Si-
Ni-Cu-Mg系のAC8A、AC8B、AC8C等のAl合金が使用可能で
ある。(Chemical Composition of Al Alloy) Next, the chemical composition of the cast aluminum alloy material of the present invention will be described. The Al alloy of the present invention has a proof stress (σ 0.2 ) after artificial age hardening.
230N / mm 2 or more, Charpy impact value of 12 / cm 2 or more, and elongation of 18% or more can be secured, or, in addition to these mechanical properties, those having corrosion resistance as a preferable property If so, an aluminum alloy for gravitational casting specified in JIS and containing 2.0% or more of Si necessary for high strength can be appropriately used. More specifically, Al-Cu-Si based AC2A,
AC2B, AC3A of Al-Si system, AC4A, AC4C, AC4C of Al-Si-Mg system
H, AC4B of Al-Si-Cu system, AC4D of Al-Si-Cu-Mg system, Al-Si-
Al alloys such as Ni-Cu-Mg-based AC8A, AC8B, AC8C can be used.
【００４４】しかし、前記JIS 各成分規格通りにならず
とも、前記基本的な特性を有してさえいれば、更なる特
性の向上や他の特性を付加するための、適宜成分組成の
変更は許容される。この点、上記元素の成分範囲の変更
や、より具体的な用途および要求特性に応じて、他の元
素を適宜含むことは許容される。また、H2やO2などのガ
ス成分や溶解原料スクラップなどから必然的に混入され
る不純物も、本発明鍛造材の品質を阻害しない範囲で許
容される。However, even if it does not conform to the above-mentioned JIS component standards, as long as it has the basic characteristics, it is not possible to appropriately change the component composition in order to further improve the characteristics or add other characteristics. Permissible. In this regard, it is permissible to change the component range of the above-mentioned elements and appropriately include other elements according to more specific applications and required characteristics. Further, impurities which are inevitably mixed from gas components such as H 2 and O 2, scrap from dissolved raw material, and the like are also allowed as long as the quality of the forged material of the present invention is not impaired.
【００４５】(本発明Al合金の元素量) 次に、本発明Al
合金材の各元素の含有量について、臨界的意義や好まし
い範囲について説明する。(Elemental Content of Al Alloy of the Present Invention)
Regarding the content of each element in the alloy material, critical significance and preferred ranges will be described.
【００４６】Si:2.0〜12% 、好ましくは6.5 〜7.5%。 SiもMgとともに、人工時効処理により、化合物として析
出して、最終製品使用時の高強度 (耐力) を付与するた
めに必須の元素である。Siの2.0%未満の含有、好ましく
は6.5%未満の含有では、人工時効でも耐力で230N/mm2以
上の高い強度が得られない。一方、12% を越えて含有さ
れると、好ましくは7.5%を越えて含有されると、鋳造時
および焼き入れ時に粗大な単体Si粒子として析出して、
前記した靱性を低下させるので、12J/cm2 以上の高靱性
を得ることができない。更に伸びが低くなるなどの問題
も生じる。したがって、Siの含有量は2.0 〜12% 、好ま
しくは、6.5 〜7.5%の範囲とする。Si: 2.0 to 12%, preferably 6.5 to 7.5%. Si is also an element that, together with Mg, precipitates as a compound by artificial aging treatment and imparts high strength (proof stress) when the final product is used. If the content of Si is less than 2.0%, preferably less than 6.5%, a high strength of 230 N / mm 2 or more cannot be obtained even with artificial aging. On the other hand, if it is contained in excess of 12%, preferably if it is contained in excess of 7.5%, it will precipitate as coarse single Si particles during casting and quenching,
Since the toughness is reduced, high toughness of 12 J / cm 2 or more cannot be obtained. Further, problems such as low elongation also occur. Therefore, the content of Si should be in the range of 2.0 to 12%, preferably 6.5 to 7.5%.
【００４７】Mg:0.2〜1.6%。 Mgは高温の人工時効により、Siとともに化合物として析
出して、また、Cu含有組成では、更にCu、Alと化合物相
を形成して、最終製品使用時の高強度 (耐力)を向上さ
せる。従って、Mgはこの目的乃至必要性のために選択的
に含有する。Mgの0.2%未満の含有では人工時効でも耐力
で230N/mm2以上の高い強度が得られない。一方、1.6%を
越えて含有されると、強度 (耐力) が高くなりすぎ、靱
性が低くなり、シャルピー衝撃値で12J/cm2 以上の高靱
性を得ることができない。したがって、含有させる場合
のMgの量は0.2 〜1.6%の範囲とする。Mg: 0.2-1.6%. Mg precipitates as a compound together with Si by artificial aging at high temperature, and in a Cu-containing composition, further forms a compound phase with Cu and Al to improve the high strength (proof stress) when the final product is used. Therefore, Mg is selectively contained for this purpose or necessity. If the content of Mg is less than 0.2%, a high strength of 230 N / mm 2 or more cannot be obtained even with artificial aging. On the other hand, if the content exceeds 1.6%, the strength (proof stress) becomes too high, the toughness becomes low, and high toughness of 12 J / cm 2 or more in Charpy impact value cannot be obtained. Therefore, the content of Mg when contained is in the range of 0.2 to 1.6%.
【００４８】Cu:0.1〜5.0%。 Cuは、Mg、Alと化合物相を形成して析出し、マトリック
ス強度の向上に寄与する他、人工時効処理に際して、他
の合金元素の析出に対する核の作用を生じ、析出物を微
細に均一分散させ、最終製品の時効硬化を著しく促進す
る効果を有する。従って、Cuはこの目的乃至必要性のた
めに選択的に含有する。Cuの含有量が0.1%未満では、こ
れらの効果が無く、1.0%を越えると効果が飽和する。ま
た、Cuの含有量が1.0%を越えると、却って靱性乃至熱間
鍛造性を低下させる。したがって、含有させる場合のCu
の量は0.1 〜1.0%とする。Cu: 0.1-5.0%. Cu forms a compound phase with Mg and Al and precipitates, contributing to the improvement of the matrix strength.In addition, during artificial aging treatment, it acts as a nucleus for the precipitation of other alloying elements and finely disperses the precipitate finely. Has the effect of remarkably accelerating the age hardening of the final product. Therefore, Cu is selectively contained for this purpose or necessity. When the content of Cu is less than 0.1%, these effects are not obtained, and when the content exceeds 1.0%, the effects are saturated. On the other hand, if the Cu content exceeds 1.0%, the toughness or hot forgeability is rather lowered. Therefore, when containing Cu
Is 0.1 to 1.0%.
【００４９】Mn:0.1〜0.6%。 Mnは、溶解、鋳造時に生成するAl-Fe-Si-(Mn、Cr、Zr)
系の金属間化合物や晶出物の形態を、針状からスケルト
ン (網目) 状に制御して、前記金属間化合物や晶出物が
破壊の起点となり、鋳造材の破壊靱性を低下させること
を抑制する効果がある。従って、Mnはこの目的乃至必要
性のために選択的に含有する。Mn:0.1%未満では、この
効果が得られず、一方0.6%を越えて含有すると、却って
鋳造材の破壊靱性を低下させる。したがって、含有させ
る場合のMnの量は0.1 〜0.6%とする。Mn: 0.1-0.6%. Mn is Al-Fe-Si- (Mn, Cr, Zr) generated during melting and casting
By controlling the form of the intermetallic compound or crystallized material from a needle shape to a skeleton (mesh) shape, the intermetallic compound or crystallized material serves as a starting point of fracture, thereby reducing the fracture toughness of the cast material. It has the effect of suppressing. Therefore, Mn is selectively contained for this purpose or necessity. If Mn is less than 0.1%, this effect cannot be obtained, while if it exceeds 0.6%, the fracture toughness of the cast material is rather lowered. Therefore, when Mn is contained, the amount of Mn is set to 0.1 to 0.6%.
【００５０】Ti:0.001〜0.1%。 Tiは鋳塊の結晶粒を微細化させる。従って、Tiはこの目
的乃至必要性のために選択的に含有する。しかし、Tiの
0.001%未満の含有では、この効果が得られず、一方、Ti
を0.1%を越えて含有すると、粗大な晶出物を形成し、靱
性を低下させる。したがって、含有させる場合のTiの量
は0.001 〜0.1%の範囲とすることが好ましい。Ti: 0.001 to 0.1%. Ti refines the crystal grains of the ingot. Therefore, Ti is selectively contained for this purpose or necessity. But Ti
If the content is less than 0.001%, this effect cannot be obtained.
If it exceeds 0.1%, coarse crystals are formed and the toughness is reduced. Therefore, the content of Ti when it is contained is preferably in the range of 0.001 to 0.1%.
【００５１】B:1 〜300ppm。 B はTiと同様、鋳塊の結晶粒を微細化させる。従って、
B はこの目的乃至必要性のために選択的に含有する。し
かし、B の1ppm未満の含有では、この効果が得られず、
一方、300ppmを越えて含有されると、やはり粗大な晶出
物を形成し、靱性を低下させる。したがって、含有させ
る場合のB の量は1 〜300ppmの範囲とすることが好まし
い。B: 1 to 300 ppm. B refines the crystal grains of the ingot similarly to Ti. Therefore,
B is selectively contained for this purpose or need. However, if the content of B is less than 1 ppm, this effect cannot be obtained.
On the other hand, if the content exceeds 300 ppm, a coarse crystallized product is also formed and the toughness is reduced. Therefore, when B is contained, the amount of B is preferably in the range of 1 to 300 ppm.
【００５２】その他の不純物元素についても以下に説明
しておく。Al合金に不純物として含まれやすいFeは、Al
7Cu2Fe、Al12(Fe,Mn)3Cu2 、(Fe,Mn)Al6、Al3Fe 、或い
は本発明で問題とする粗大なAl-Fe-Si-(Mn、Cr、Zr) 系
の晶出物を生成する。これらの晶出物は、前記した通
り、破壊靱性および疲労特性などを劣化させる。特に、
Feの含有量が0.2%を越えると、自動車用のサスペンショ
ン部品などに要求される、より高強度で高靱性、より具
体的には、σ0.2 で230N/mm2以上の高強度を有する場合
の、シャルピー衝撃値が12J/cm2 以上の高靱性を得るこ
とができない。したがって、Feの含有量は0.2%以下とす
ることが好ましい。Other impurity elements will be described below. Fe, which is easily contained as an impurity in Al alloys, is Al
7 Cu 2 Fe, Al 12 (Fe, Mn) 3 Cu 2 , (Fe, Mn) Al 6 , Al 3 Fe, or coarse Al-Fe-Si- (Mn, Cr, Zr) which is a problem in the present invention Produces system crystallization. As described above, these crystals degrade the fracture toughness and the fatigue properties. In particular,
When the Fe content exceeds 0.2%, high strength and high toughness required for automotive suspension parts, etc., more specifically, when having a high strength of 230 N / mm 2 or more at σ 0.2 However, high toughness having a Charpy impact value of 12 J / cm 2 or more cannot be obtained. Therefore, the content of Fe is preferably set to 0.2% or less.
【００５３】Cr、Zrは、Al-Fe-Si-(Mn、Cr、Zr) 系の金
属間化合物や晶出物を、溶解、鋳造時に生成して、破壊
の起点となり、鋳造材の破壊靱性を低下させる。したが
って、できるだけ少ない量に規制することが好ましい
が、鋳造コストの問題もあり、Crは0.2%以下、Zrは0.2%
以下の含有は許容する。Cr and Zr form Al-Fe-Si- (Mn, Cr, Zr) -based intermetallic compounds and crystallized substances at the time of melting and casting, and serve as a starting point of fracture, resulting in fracture toughness of the cast material. Lower. Therefore, it is preferable to regulate the amount as small as possible, but there is also a problem of casting cost, Cr is 0.2% or less, Zr is 0.2%
The following content is acceptable.
【００５４】Znは耐蝕性を劣化させやすい。したがっ
て、できるだけ少ない量に規制することが好ましいが、
鋳造コストの問題もあり、Znは1.0%以下の含有は許容す
る。Zn easily deteriorates the corrosion resistance. Therefore, it is preferable to regulate the amount as small as possible,
There is also the problem of casting cost, and Zn content of 1.0% or less is allowed.
【００５５】V は溶解、鋳造時に粗大なAl-Fe-Si-V系の
金属間化合物や晶出物を生成しやすく、破壊の起点とな
り、靱性を低下させる原因となる。したがって、できる
だけ少ない量に規制することが好ましいが、鋳造コスト
の問題もあり、V は0.2%以下の含有は許容する。V easily forms a coarse Al-Fe-Si-V-based intermetallic compound or crystallized product during melting and casting, becomes a starting point of fracture, and causes a decrease in toughness. Therefore, it is preferable to control the amount to be as small as possible, but there is also a problem of casting cost, so that the content of V of 0.2% or less is allowed.
【００５６】次に、本発明におけるAl合金鋳造材の好ま
しい製造方法について述べる。本発明におけるAl合金鋳
造材の鋳造方法は、前記した通り、ダイカスト法、砂型
鋳造法、金型鋳造法などの他の方法ではなく、高圧鋳造
法 (溶湯鍛造法) により行う。高圧鋳造法以外の鋳造方
法であれば、本発明を採用する意義もなく、前記した、
高圧鋳造法の利点（空気の巻き込み防止、空気や酸化物
の巻き込み少、引け巣等の鋳造欠陥の抑制、凝固結晶粒
やデンドライト二次アーム間隔(DAS) の微細化）が失わ
れ、鋳造欠陥を抑制し、より高強度で高靱性化した、信
頼性の高いAl合金鋳造材を製造することが困難となる。Next, a preferred method for producing an Al alloy casting according to the present invention will be described. As described above, the casting method of the Al alloy cast material in the present invention is performed by a high-pressure casting method (a molten metal forging method) instead of other methods such as a die casting method, a sand casting method, and a die casting method. If it is a casting method other than the high pressure casting method, there is no significance to adopt the present invention, as described above,
The advantages of the high pressure casting method (prevention of air entrapment, reduction of air and oxide entrapment, suppression of casting defects such as shrinkage cavities, miniaturization of solidified crystal grains and dendrite secondary arm spacing (DAS)) are lost and casting defects are lost. It is difficult to produce a highly reliable cast Al alloy material having higher strength and higher toughness.
【００５７】高圧鋳造法自体は、高圧下で溶湯を凝固さ
せ、溶湯の凝固過程を規制でき、ダイカスト法と区別で
きるものであれば、多少の方法や設備の違いは許容され
る。例えば、溶解炉から横型乃至縦型のスリーブ内に、
Al合金溶湯を給湯管などを介して流し込み、その後スリ
ーブ内のAl合金溶湯をピストンにより加圧して、Al合金
溶湯をスリーブ内の金型に接触させて冷却する方式が代
表的な例である。The high-pressure casting method itself allows the molten metal to be solidified under high pressure, regulates the solidification process of the molten metal, and allows some differences in methods and equipment as long as it can be distinguished from the die-casting method. For example, from a melting furnace to a horizontal or vertical sleeve,
A typical example is a method in which the molten Al alloy is poured through a hot water supply pipe or the like, and then the molten Al alloy in the sleeve is pressurized by a piston to bring the molten Al alloy into contact with a mold in the sleeve and cooled.
【００５８】高圧鋳造法により鋳込まれたAl合金材は、
T6などの溶体化処理後焼き入れを行い、人工時効硬化処
理を施して製造される。人工時効硬化処理は、通常通
り、150 〜200 ℃×3 〜10時間で行い、過時効でも、亜
時効でも良い。The Al alloy material cast by the high pressure casting method
It is manufactured by performing quenching after solution treatment such as T6 and performing artificial age hardening treatment. The artificial aging hardening treatment is usually performed at 150 to 200 ° C. for 3 to 10 hours, and may be overaged or subageed.
【００５９】また、溶体化処理の際の温度は、SiやMgの
固溶のための、通常の処理温度500〜580 ℃の範囲で良
い。しかし、溶体化処理の時間（鋳造材が前記処理温度
にある時間）は、前記した共晶Siの粗大化の防止のため
に、特に短時間とする必要がある。より具体的には、鋳
造材の成分組成や溶体化処理の温度によっても異なる
が、Siを6.5 〜7.5%含む、Al-Si-Mg系のJIS AC4CH 等の
Al鋳造用合金において、530 〜540 ℃の溶体化処理温度
を前提とすると、概ね2 時間を越える溶体化処理では、
前記共晶Siの最大径の粗大化が生じ、この粗大化の傾向
は時間とともに大きくなる。そして、構造材としての衝
撃破壊強度は著しく低下し、特に厚みが15mm以下の薄肉
の部位を有する輸送機用構造材には使えなくなる。The temperature for the solution treatment may be in the range of a usual treatment temperature of 500 to 580 ° C. for solid solution of Si or Mg. However, the solution treatment time (time during which the casting material is at the treatment temperature) needs to be particularly short in order to prevent the eutectic Si from being coarsened. More specifically, it varies depending on the component composition of the casting material and the temperature of the solution treatment, but contains 6.5 to 7.5% of Si, such as JIS AC4CH of Al-Si-Mg system.
Assuming a solution heat treatment temperature of 530 to 540 ° C for Al casting alloys, a solution heat treatment generally exceeding 2 hours
The maximum diameter of the eutectic Si is coarsened, and the tendency of the coarsening increases with time. And the impact fracture strength as a structural material is remarkably reduced, and it cannot be used especially for a transport structural material having a thin portion having a thickness of 15 mm or less.
【００６０】一方、2 時間以下、好ましくは1.5 時間以
下の溶体化処理では、共晶Siの形状は、長細い形状から
丸い形状に変化するものの、その大きさ (最大径) は殆
ど変化しなくなる。したがって、溶体化処理時間は、通
常の (従来の) 溶体化処理時5 〜6 時間に対し、2 時間
以下、好ましくは1.5 時間以下の短時間とするのが必要
となる。なお、溶体化処理の最低時間は、SiやMgの固溶
を固溶させるために最低必要時間となる。なお、Siを6.
5 〜7.5%含む、Al-Si-Mg系のJIS AC4CH 等のAl鋳造用合
金 (高圧鋳造法による) では、溶体化処理を2 時間以下
の1 時間程度の短時間としても、SiやMgの固溶が充分図
られており、この点も、高圧鋳造法による鋳造材の、従
来の技術常識を覆す特異性である。したがって、鋳造材
の溶体化処理は500 〜580 ℃の温度×2.0 時間以下で行
う。On the other hand, in the solution treatment for 2 hours or less, preferably 1.5 hours or less, the shape of eutectic Si changes from a long and thin shape to a round shape, but its size (maximum diameter) hardly changes. . Therefore, the solution treatment time needs to be as short as 2 hours or less, preferably 1.5 hours or less, compared to 5 to 6 hours during the usual (conventional) solution treatment. Note that the minimum time of the solution treatment is a minimum time required for solid solution of Si and Mg. In addition, Si is 6.
For Al casting alloys (by high pressure casting) such as JIS AC4CH of Al-Si-Mg system containing 5 to 7.5%, even if the solution treatment is as short as 2 hours or less, about 1 hour, Si or Mg The solid solution is sufficiently achieved, and this point is also a peculiarity of the cast material by the high-pressure casting method, which reverses the conventional technical knowledge. Therefore, the solution treatment of the cast material is performed at a temperature of 500 to 580 ° C. × 2.0 hours or less.
【００６１】[0061]
【実施例】次に、本発明の実施例を説明する。表1 に示
す成分組成のAl合金鋳塊を、いずれも図1 のアーム1 の
形状 (ニアネットシェイプ、平均肉厚10mm) を、表2 に
示す通り、高圧鋳造法、コールドチャンバー式および可
動型のダイキャビティのダイカスト鋳造法、金型鋳造法
により溶製した。高圧鋳造法は、溶解炉から縦型のスリ
ーブ内に、Al合金溶湯を給湯管を介して流し込み、その
後スリーブ内のAl合金溶湯をピストンにより加圧して、
Al合金溶湯をスリーブ内の金型に接触させて冷却した。Next, embodiments of the present invention will be described. For the Al alloy ingots with the component compositions shown in Table 1, the shape of the arm 1 (near net shape, average thickness 10 mm) in Fig. 1 was changed to the high pressure casting method, cold chamber type, and movable type as shown in Table 2. Was melted by die casting and die casting. In the high-pressure casting method, an Al alloy melt is poured from a melting furnace into a vertical sleeve through a hot water supply pipe, and then the Al alloy melt in the sleeve is pressurized by a piston.
The molten Al alloy was cooled by contacting the mold in the sleeve.
【００６２】その後、鋳塊を表2 、3 に示す温度と時間
で溶体化処理を施した後、共通して65℃の水に浸漬して
焼入れを行い(T6 処理) 、更に共通して160 ℃×5 時間
の人工時効処理 (亜時効処理) を行った。Thereafter, the ingot was subjected to a solution treatment at the temperature and time shown in Tables 2 and 3, and then immersed and quenched in water at 65 ° C. (T6 treatment). An artificial aging treatment (sub-aging treatment) was performed at 5 ° C for 5 hours.
【００６３】これらの熱処理を行ったアーム1 の取り付
け部2(突起部) の付け根部T3およびアームの中央部T1か
ら試験片を採取し、厚み方向の断面の組織を、400 倍の
倍率の走査型電子顕微鏡(SEM) により、観察および画像
解析を行い、組織中の共晶Siの最大径 (μm)とアスペク
ト比を測定した。これらの結果を表2 、3 に示す。Test pieces were taken from the base T3 of the mounting portion 2 (projection) of the heat-treated arm 1 and the center T1 of the arm, and the cross-sectional structure in the thickness direction was scanned at a magnification of 400 times. Observation and image analysis were performed with a scanning electron microscope (SEM) to measure the maximum diameter (μm) and aspect ratio of eutectic Si in the structure. The results are shown in Tables 2 and 3.
【００６４】組織中の共晶Siの最大径 (μm)とアスペク
ト比の測定結果は、測定部位によるバラツキを考慮する
ため、試験片の任意の測定箇所20視野の目視観察結果の
平均によって行った。The measurement results of the maximum diameter (μm) and aspect ratio of the eutectic Si in the structure were determined by averaging the visual observation results of 20 visual fields at arbitrary measurement points on the test piece in order to take into account the variation depending on the measurement site. .
【００６５】なお、共晶Siの最大径とアスペクト比は、
溶体化処理とは異なり、比較的低温の人工時効処理によ
っても変化しないので、これらの測定は、溶体化処理後
であれば、溶体化処理および焼入れ後( 人工時効処理
前) であっても、人工時効処理後であっても良いので、
本実施例では、人工時効処理後のもので測定した。The maximum diameter and aspect ratio of eutectic Si are as follows:
Unlike solution treatment, it does not change even by artificial aging treatment at relatively low temperature, so these measurements are performed after solution treatment, even after solution treatment and quenching (before artificial aging treatment), Because it may be after artificial aging treatment,
In this example, the measurement was performed after the artificial aging treatment.
【００６６】更に、アーム1 のアームの中央部T1および
付け根部 T2 の試験片 (JIS Z 2201に基づく 4号引張試
験片) の引張強度 (σB 、N/mm2)、耐力 (σ0.2 、N/mm
2)、伸び (δ、%)の機械的特性を、JIS Z 2241等に基づ
き測定した。また、同じく試験片 (JIS Z 2202に基づく
3号衝撃試験片) の靱性= シャルピー衝撃値(J/cm2)
を、JIS Z 2242等に基づき測定した。更に、アーム1 の
耐衝撃破壊強度を直接的に測定するため、鋳造した各ア
ーム1 の衝撃試験を行った。これらの結果を表4、5 に
示す。なお、アーム1 の衝撃試験は、JASO (日本自動車
技術会) で規定している落錘試験機を用いたホイールの
衝撃試験に準じて行い、固定したアーム1の付け根部 T
2 部位の55mm上方から重量 1トンの錘をT2部位に向けて
落下、衝突させ、T2部位に細かい亀裂および変形は生じ
たが圧壊しなかったものを○、大きな亀裂および変形が
生じたが圧壊しなかったものを△、飛散状態で圧壊した
ものを×として評価した。Further, the tensile strength (σ B , N / mm 2 ), proof stress (σ) of the test piece (No. 4 tensile test piece based on JIS Z 2201) of the central part T 1 and the base T 2 of the arm 1 0.2 , N / mm
2 ) The mechanical properties of elongation (δ,%) were measured based on JIS Z 2241 and the like. Also, the test piece (based on JIS Z 2202)
No. 3 impact test piece) toughness = Charpy impact value (J / cm 2 )
Was measured based on JIS Z 2242 and the like. Further, in order to directly measure the impact fracture strength of the arm 1, an impact test of each cast arm 1 was performed. Tables 4 and 5 show these results. The impact test of Arm 1 is performed in accordance with the wheel impact test using a falling weight tester specified by JASO (Japan Automotive Engineers Association).
Dropped from 55mm above the 2 sites toward the weight of weight 1 ton to T 2 site, collide, ○ those yielded the fine cracks and deformation T 2 sites that did not collapse, large cracks and deformation occurred Was not crushed, and △ was crushed in a scattered state.
【００６７】表2 、4 から明らかな通り、溶体化処理時
間が1.5 時間以内と短い、発明例No.1〜5 は、溶体化処
理後の組織中の共晶Siの最大径が3.5 μm 以下およびア
スペクト比が1.4 以下である。この結果、10mm厚みと薄
肉化されたアーム類であっても、そして、図1 に示した
アームの中央部T1や、特に細径化された付け根部T2にお
いても、表4 に示す通り、人工時効硬化処理後の鋳造材
の耐力 (σ0.2)が230N/mm2以上、シャルピー衝撃値が12
J/cm2 以上、および伸びが17% 以上であり、衝撃試験に
よる衝撃破壊強度に優れている。As is clear from Tables 2 and 4, the solution treatment time was as short as 1.5 hours or less, and in Invention Examples No. 1 to 5, the maximum diameter of eutectic Si in the structure after the solution treatment was 3.5 μm or less. And the aspect ratio is 1.4 or less. As a result, even 10mm thick and thinned arm such, and, and the central portion T 1 of the arm shown in FIG. 1, in the base portion T 2 which is particularly smaller diameter, as shown in Table 4 The proof stress (σ 0.2 ) of the cast material after artificial age hardening is 230 N / mm 2 or more, and the Charpy impact value is 12
It has a J / cm 2 or more and an elongation of 17% or more, and is excellent in impact breaking strength by an impact test.
【００６８】これに対し、溶体化処理時間が2.0 時間と
比較的長い発明例No.6は、共晶Siの最大径が比較的大き
く、人工時効硬化処理後の鋳造材の耐力、シャルピー衝
撃値、および伸び、更には衝撃破壊強度が発明例No.1〜
5 に比して劣っている。On the other hand, in Invention Example No. 6 in which the solution treatment time was relatively long at 2.0 hours, the maximum diameter of the eutectic Si was relatively large, and the yield strength and Charpy impact value of the cast material after the artificial age hardening treatment , And elongation, and also the impact fracture strength of Invention Example No. 1 ~
Inferior to 5.
【００６９】更に、表3 から明らかな通り、溶体化処理
時間が2.0 時間を越える、通常の溶体化処理時間とし
た、比較例No.7〜10は、溶体化処理後の組織中の共晶Si
の最大径が3.5 μm を越えるか、および/ または、アス
ペクト比が1.4 を越えている。この結果、10mm厚みと薄
肉化されたアーム類にあっては、アームの中央部T1や、
特に細径化された付け根部T3において、人工時効硬化処
理後の鋳造材の耐力 (σ 0.2)が230N/mm2未満か、シャル
ピー衝撃値が12J/cm2 未満か、伸びが17% 未満であり、
しかも共通して衝撃破壊強度が劣っている。このため、
特に、15mm以下の厚みの部位を有する薄肉化された重要
保安部品となる構造材には使用できないことが分かる。Further, as is clear from Table 3, the solution treatment
Time exceeds 2.0 hours, and
Comparative Examples Nos. 7 to 10 were eutectic Si in the structure after solution treatment.
The maximum diameter exceeds 3.5 μm and / or
The pect ratio exceeds 1.4. As a result, 10mm thickness and thin
In the case of fleshed arms, the central part T of the arm1And
Especially thinned base TThreeIn the artificial age hardening
Strength of cast material after processing (σ 0.2) Is 230N / mmTwoLess than or char
P impact value is 12J / cmTwo Or less than 17% elongation,
Moreover, the impact fracture strength is generally inferior. For this reason,
In particular, it is important to have a thinner part with a thickness of 15 mm or less.
It can be seen that it cannot be used as a structural material for security parts.
【００７０】そして、以上の結果から、本発明における
共晶Siの形状と大きさ、或いは溶体化処理時間の、15mm
以下の厚みの部位を有する薄肉化された構造材における
要求特性からの、臨界的な意義が分かる。From the above results, the shape and size of the eutectic Si in the present invention or the solution treatment time of 15 mm
Critical significance can be seen from the required characteristics of the thinned structural material having the following thickness portions.
【００７１】[0071]
【表１】 [Table 1]
【００７２】[0072]
【表２】 [Table 2]
【００７３】[0073]
【表３】 [Table 3]
【００７４】[0074]
【表４】 [Table 4]
【００７５】[0075]
【表５】 [Table 5]
【００７６】[0076]
【発明の効果】本発明によれば、重要保安部品などの構
造材で、しかも15mm以下の薄肉の部位を有する構造材に
好適な、耐衝撃破壊性に優れた、高圧鋳造法によるAl合
金鋳造材およびその製造方法を提供することができる。
したがって、Al合金鋳造材の自動車、車両、船舶などの
輸送機材用などの構造材への用途の拡大を図ることがで
きる点で、多大な工業的な価値を有するものである。According to the present invention, Al alloy casting by high-pressure casting, which is excellent in impact fracture resistance, is suitable for structural materials such as important security parts and has a thin portion of 15 mm or less. A material and a method for manufacturing the same can be provided.
Therefore, the use of the cast Al alloy in structural materials such as transportation equipment such as automobiles, vehicles and ships is of great industrial value.
【図１】本発明の用途のサスペンション部品用アームの
一例を示す説明図である。FIG. 1 is an explanatory view showing an example of a suspension component arm for use in the present invention.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｆ 1/043 Ｃ２２Ｆ 1/043 // Ｂ６０Ｇ 7/00 Ｂ６０Ｇ 7/00 Ｃ２２Ｆ 1/00 ６０１ Ｃ２２Ｆ 1/00 ６０１ ６３０ ６３０Ｂ ６８２ ６８２ ６９１ ６９１Ｂ ６９１Ｃ ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (Reference) C22F 1/043 C22F 1/043 // B60G 7/00 B60G 7/00 C22F 1/00 601 C22F 1/00 601 630 630B 682 682 691 691B 691C
Claims (8)
み、高圧鋳造法により鋳込まれ、溶体化処理および人工
時効硬化処理が施されたアルミニウム合金鋳造材であっ
て、溶体化処理後の組織中の共晶Siの最大径 (円相当
径) が3.5 μm 以下およびアスペクト比が1.4 以下であ
り、人工時効硬化処理後の鋳造材の耐力 (σ0.2)が230N
/mm2以上、シャルピー衝撃値が12J/cm2 以上、および伸
びが17% 以上であることを特徴とする衝撃破壊強度に優
れたアルミニウム合金鋳造材。1. An aluminum alloy cast material containing at least 2.0% (mass%, the same applies hereinafter) of Si, cast by a high-pressure casting method, and subjected to a solution treatment and an artificial age hardening treatment. The maximum diameter (equivalent circle diameter) of eutectic Si in the structure after formation is 3.5 μm or less and the aspect ratio is 1.4 or less, and the proof stress (σ 0.2 ) of the cast material after artificial age hardening is 230 N
/ mm 2 or more, Charpy impact value 12 J / cm 2 or more, and the casted aluminum alloy excellent in impact fracture strength, wherein the elongation of 17% or more.
Siの最大径が粗大化しないような時間で行う請求項１に
記載の衝撃破壊強度に優れたアルミニウム合金鋳造材。2. The eutectic in the structure at the time of casting the solution treatment.
The cast aluminum alloy material having excellent impact fracture strength according to claim 1, wherein the casting is performed for a time such that the maximum diameter of Si does not become coarse.
Feを0.2%以下に規制した請求項１または２に記載の衝撃
破壊強度に優れたアルミニウム合金鋳造材。3. Included in the cast aluminum alloy material
3. The cast aluminum alloy material according to claim 1, wherein Fe is controlled to 0.2% or less.
を0.2 〜1.6%含む請求項１乃至３の何れか１項に記載の
衝撃破壊強度に優れたアルミニウム合金鋳造材。4. The aluminum alloy cast material further comprises Mg
The aluminum alloy cast material having excellent impact fracture strength according to any one of claims 1 to 3, comprising 0.2 to 1.6%.
5 〜7.5%含む請求項１乃至４の何れか１項に記載の衝撃
破壊強度に優れたアルミニウム合金鋳造材。5. The aluminum alloy casting material according to claim 6, wherein Si is 6.
The cast aluminum alloy material having excellent impact fracture strength according to any one of claims 1 to 4, comprising 5 to 7.5%.
構造材用である請求項１乃至５の何れか１項に記載の衝
撃破壊強度に優れたアルミニウム合金鋳造材。6. The aluminum alloy casting excellent in impact fracture strength according to claim 1, wherein the aluminum alloy casting is used for a structural material of a transport machine.
部位を有する請求項６に記載の衝撃破壊強度に優れたア
ルミニウム合金鋳造材。7. The cast aluminum alloy material having excellent impact fracture strength according to claim 6, wherein the structural material of the transporter has a portion having a thickness of 15 mm or less.
ム合金鋳造材の製造方法であって、アルミニウム合金溶
湯を高圧鋳造法により鋳込んだ後、鋳造材の溶体化処理
を、500 〜580 ℃の温度で2.0 時間以下行い、更に、人
工時効硬化処理を行うことを特徴とする衝撃破壊強度に
優れたアルミニウム合金鋳造材の製造方法。8. The method for producing an aluminum alloy casting according to claim 1, wherein after the molten aluminum alloy is cast by a high-pressure casting method, a solution treatment of the casting is performed at 500 to 580 ° C. A method for producing an aluminum alloy cast material having excellent impact fracture strength, which is performed at a temperature of 2.0 hours or less and further subjected to an artificial age hardening treatment.
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