JP3840400B2 - Method for producing semi-melt molded billet of aluminum alloy for transportation equipment - Google Patents
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【０００１】
【発明の属する技術分野】
本発明は、輸送機器用として用いるアルミニウム合金の半溶融成型ビレットの製造方法に関するものである。
【０００２】
【従来の技術】
半溶融ビレットを用いるチクソキャスト法は、従来の金型鋳造法と比較し鋳造偏析・欠陥が少なく、金型寿命が長いなどの利点があり最近注目されている技術である。これに用いるビレットの鋳造方法としては、ペシネー・アルマックス方式として知られているビレット段階で初晶α（Ａｌ）相を球状化するため、半溶融温度域で電磁・機械撹拌を行う方法（方式Ａ）や、鋳造時に通常添加されている量よりも多量のＡｌ−Ｔｉ−Ｂを添加し、その後半溶融温度域まで昇温し初晶α（Ａｌ）相を球状化させる方法（方式Ｂ）がある。また、押出・圧延にて歪みを導入後、方式Ｂのように昇温し球状化させる方法（方式Ｃ）が広く知られている。
【０００３】
【発明が解決しようとする課題】
従来の半溶融製造法の場合、方式Ａでは工程が非常に煩雑で、製造コストが高くつく不具合があった。
また、方式Ｂでは、多量のＡｌ−Ｔｉ−Ｂを添加するため溶融炉内でのＴｉＢ ２ 沈降による品質不安定が発生し、更に方式Ｃの圧延により歪みを導入する方法は均一な歪みの導入が難しく、また押出では常温押出により作業工程が煩雑で、しかも均一な歪み導入が難しいし、両歪み導入法とも加工後の製品加工が必要となり、量産化や低コスト化が図れないという問題があった。
【０００４】
特許第２９７６０７３号には、改良された方法が開示されている。即ち、そこには第１項中に「完全に固化した金属または金属合金材料をその再結晶温度未満の温度で変形する工程、該材料の微小構造の再結晶を起こさせるために変形材料を加熱する工程、および該材料の温度をその固相線温度を上回る温度に上昇させることによりチキソトロピック的な挙動を呈する液状マトリックス中に独立した粒子を形成させるために、再結晶構造を部分的に融解させる工程を備えた方法」である。
この方法は、該材料の微小構造の再結晶を起こさせるために変形材料を加熱する工程、および該材料の温度をその固相線温度を上回る温度に上昇させるといういわば２段階加熱とも言うべき加熱が行われる。このような方法は、従来の技術に比べれば、改善された技術と言えるが、やはり２段階の加熱を必要とし、工程が複雑で加熱制御が難しいという問題があった。
【０００５】
本発明は、上記従来技術の欠点を解消し、工程が簡素で低コスト化を促進でき、得られる製品が均質な輸送機器用アルミニウム合金の半溶融成型ビレットの製造方法を提供することを目的とするものである。
【０００６】
【課題を解決するための手段】
上記目的を達成するため、本願の輸送機器用アルミニウム合金の半溶融成型ビレットの製造方法は、Ｃｕ０．４０〜５．５ｗｔ％、Ｓｉ１１．０〜１５．０ｗｔ％、Ｚｎ１．０ｗｔ％以下、Ｆｅ１．５ｗｔ％以下、Ｍｎ０．６５ｗｔ％以下と、Ｔｉ０．００５〜０．５ｗｔ％及びＢ０．０００１〜０．５ｗｔ％の少なくとも１種以上と、Ｍｇ０．４０〜１．８ｗｔ％及びＮｉ０．０５〜１．７ｗｔ％の少なくとも１種以上を含み、残部が実質的にＡｌの組成から成り、共晶Ｓｉの平均粒径が２００μｍ以下で、しかもデンドライト枝間隔（ＤＡＳ）が２００μｍ以下であるアルミニウム合金を製造し、次いで歪み率５〜５０％、加工導入速度５０ｍｍ／ｓｅｃ．以下で再結晶温度未満の温度で、冷間型枠鍛造にて加工歪みを導入し、その後共晶温度以上に昇温し、液相率が２０〜８０％となる温度で保持して半溶融加工する方法である。
【０００７】
この場合に、成分偏析の均質化、共晶Ｓｉの分断球状化及び鋳造応力の解放のために、加工歪みを導入する前に、４５０〜５５０℃の温度で１〜１０時間の均質化処理を行うと好ましい。
【０００８】
また、上記目的を達成するため、本願の輸送機器用アルミニウム合金の半溶融成型ビレットの製造方法は、Ｃｕ０．４０〜５．５ｗｔ％、Ｓｉ１１．０〜１５．０ｗｔ％、Ｚｎ１．０ｗｔ％以下、Ｆｅ１．５ｗｔ％以下、Ｍｎ０．６５ｗｔ％以下と、Ｔｉ０．００５〜０．５ｗｔ％及びＢ０．０００１〜０．５ｗｔ％の少なくとも１種以上と、Ｍｇ０．４０〜１．８ｗｔ％及びＮｉ０．０５〜１．７ｗｔ％の少なくとも１種以上と、Ｓｒ０．００１〜０．１０ｗｔ％、Ｎａ０．０３〜０．０１ｗｔ％及びＳｂ０．０５〜０．２ｗｔ％の中の少なくとも１種以上を含み、残部が実質的にＡｌの組成から成り、共晶Ｓｉの平均粒径が２００μｍ以下で、しかもデンドライト枝（ＤＡＳ）が２００μｍ以下であるアルミニウム合金を製造し、次いで歪み率５〜５０％、加工導入速度５０ｍｍ／ｓｅｃ．以下で再結晶温度未満の温度で、冷間型枠鍛造にて加工歪みを導入し、その後共晶温度以上に昇温し、液相率が２０〜８０％となる温度で保持して半溶融加工する方法である。
【０００９】
この場合に、成分偏析の均質化、共晶Ｓｉの分断球状化及び鋳造応力の解放のために、加工歪みを導入する前に、４５０〜５５０℃の温度で１〜１０時間の均質化処理を行うと好ましい。
【００１０】
【発明の実施の形態】
以下本発明で用いるアルミニウム合金成分量の数値限定等種々の数値限定理由について詳述する。
【００１１】
Ｃｕ成分は、機械的性質の向上のみならず、硬度・切削性・鋳造性を良くするが、０．４０ｗｔ％未満ではその効果は小さく、一方５．５ｗｔ％を越えると耐食性の低下をまねくので０．４０〜５．５ｗｔ％とした。
【００１２】
Ｓｉ成分は、鋳造性を良くする効果があるが、その量が１１．０ｗｔ％未満ではその効果は小さく、一方１５．０ｗｔ％を越えると伸び・靭性が劣化し冷間鍛造加工性が悪くなるので、１１．０〜１５．０ｗｔ％とした。
【００１３】
Ｍｇ成分は、Ｍｇ ２ Ｓｉを析出し機械的性質の向上に寄与するが、０．４０ｗｔ％未満ではその効果は小さく、一方１．８ｗｔ％を超えると冷間鍛造加工性が悪くなるため、０．４０〜１．８ｗｔ％とした。
【００１４】
Ｆｅ成分は、Ａｌ成分と金属間化合物をつくり、多く含有されるとＡｌ−Ｆｅ−Ｓｉ系化合物となり伸び・靭性・耐食性に悪影響を及ぼすため、１．５ｗｔ％以下とした。
【００１５】
Ｔｉ成分は、鋳塊の組織を微細化し、鋳塊割れの発生を防止するが、０．００５ｗｔ％未満ではその効果が小さく、一方０．５ｗｔ％を超えるとＴｉＡｌ ３ の巨大な晶出物の発生を促進させ、冷間鍛造加工時の割れや輸送機器部品の機械的性質の低下をまねくので０．００５〜０．５ｗｔ％とした。
【００１６】
Ｂ成分もまたＴｉ成分と共に鋳塊の組織を微細化し、鋳塊割れの発生を防止するが、０．０００１ｗｔ％未満ではその効果は小さく、一方０．５ｗｔ％を越えると冷間鍛造加工時の割れや輸送機器部品の機械的性質の低下をまねくので、０．０００１〜０．５ｗｔ％とした。
【００１７】
Ｚｎ成分は、鋳造性を改善するが、耐食性を劣化させるため、１．０ｗｔ％以下とした。
【００１８】
Ｍｎ成分は、粗大金属間化合物の生成による靭性低下を起こすことから０．６５ｗｔ％以下とした。
【００１９】
Ｎｉ成分は、高温強度の向上に寄与するが、０．０５ｗｔ％未満ではその効果は小さく、一方１．７ｗｔ％を超えると耐食性を劣化させるため、０．０５〜１．７ｗｔ％とした。
【００２０】
Ｓｒ、Ｎａ、Ｓｂ成分は、共晶Ｓｉを微細化し機械的性質の向上に寄与するが、Ｓｒ０．００１ｗｔ％、Ｎａ０．００３ｗｔ％、Ｓｂ０．０５ｗｔ％未満ではその効果は小さく、一方Ｓｒ０．１０ｗｔ％、Ｎａ０．０１ｗｔ％を越えると鋳造時の溶湯の流動性が低下し、Ｓｂ０．２ｗｔ％を越えると溶体化処理時に灰黒色に着色し外観を害するため、Ｓｒ０．００１〜０．１０ｗｔ％、Ｎａ０．００３〜０．０１ｗｔ％、Ｓｂ０．０５〜０．２ｗｔ％とした。
【００２１】
共晶Ｓｉの平均粒径が２００μｍ以下で、しかもデンドライト枝間隔（ＤＡＳ）が２００μｍ以下であるビレットを鋳造するが、共晶Ｓｉの平均粒径が２００μｍを越え、しかもデンドライト枝間隔（ＤＡＳ）が２００μｍを越えると半溶融温度域に加熱した際に初晶α（Ａｌ）相の均一微細球状化が難しくなるし、また均質化処理を行う場合には均質化処理に時間を要するので、デンドライト枝間隔（ＤＡＳ）を２００μｍ以下とした。
【００２２】
鋳造で得られたビレットを均質化処理することにより、鋳造時に結晶粒界に晶出したＡｌ ２ Ｃｕの晶出物がマトリックスに固溶する。また、均質化処理によって共晶Ｓｉを球状化し冷間鍛造加工時の変形抵抗を小さくする。均質化処理温度が４５０℃未満や１時間に達しない加熱時間では、固溶化が充分得られず、また共晶Ｓｉの球状化や鋳造歪の除去も不充分である。しかし５５０℃を越える処理温度では、共晶融解が発生し鍛造時の加工性を損う。また、１０時間を越える加熱時間では、加熱時間の長時間に見合った均質化の効果上昇が得られず、加熱エネルギーの損失となる。このため、均質化処理条件は４５０〜５５０℃の温度で１〜１０時間加熱とした。
【００２３】
次に加工歪みの導入は、工程が簡素化でき、かつ少ない加工率で歪みが有効に導入されるように冷間鍛造で行い、なおかつ鍛造用ビレットの全体に均一に歪みが導入されるように型枠鍛造とする。歪み率は、５％未満の場合には歪み導入が少ないため半溶融温度域まで昇温しても初晶α（Ａｌ）相の均一な球状化は図れず、一方５０％を越えると初晶α（Ａｌ）相サイズに変化は見られないのみならず冷間鍛造時に割れが発生するため、５〜５０％とした。ここでの歪み率は、鍛造用ビレットの元の長さをＬ １ とし、鍛造後のビレットの長さをＬ ２ とした時、（Ｌ １ −Ｌ ２ ）／Ｌ １ ×１００（％）で定義した。
【００２４】
加工導入速度は、ビレット鋳塊の結晶粒微細化や共晶Ｓｉの微細化と均質化処理を加えることにより大幅にアップできる。生産性から言えば加工導入速度はできるだけ早い方が好ましい。しかしながら、５０ｍｍ／ｓｅｃ．を越えると鍛造時に割れが生じたり、鍛造デッドゾーンが発生し、歪みが均一に導入されないため５０ｍｍ／ｓｅｃ．以下とした。また冷間型枠鍛造の際のビレット温度は、再結晶温度以上では所定の加工率に対する歪み導入が不充分となり、半溶融温度に昇温しても初晶α（Ａｌ）相が粒状組織とならないため再結晶温度未満とした。
【００２５】
その後、ビレットを共晶温度以上に昇温し、液相率が２０〜８０％となる温度で保持して半溶融成型するが、液相率が２０％未満では初晶α（Ａｌ）相の均一な球状化は図れず、半溶融成型の変形抵抗が大きく加圧成型が困難となる。また、８０％を越えると均一な組織を有する成型品が得られない。このため共晶温度以上の半溶融温度域での液相率は２０〜８０％とした。
【００２６】
【実施例】
以下本発明の具体的な実施例を示す。
図１は本発明方法で用いる冷間型枠鍛造の模式図であり、図中符号１は鍛造用金型、２は鍛造用金型ポンチ、３はアルミニウム合金ビレットを示す。
【００２７】
Ｃｕ、Ｓｉ、Ｍｇ、Ｚｎ、Ｆｅ、Ｔｉ、Ｂ、Ｎｉ、Ｓｒ及びＳｂをそれぞれ下記表１に示すような組成となるように溶湯を調製し、連続鋳造にてアルミニウム合金ビレットを鋳造した。
【００２８】
【表１】
上記表１に示すアルミニウム合金ビレットを、表２に示す条件で処理し、半溶融成型の成型性、半溶融成型後の初晶α（Ａｌ）相の形状を評価した結果も表２に併記した。
【００３０】
【表２】
表２に示した加工歪み導入時の成型性は、表２で示す成型条件で成型した際に割れが発生せず成型性が良好なものを○とし、割れが見られるものを×で判定した。半溶融成型の成型性は、良好なものを○とし、成型性の悪いものを×と判定した。半溶融成型後の初晶α（Ａｌ）相の形状は、球状化が認められるものを○とし、球状化が不充分であるものを×と判定した。半溶融成型後の初晶α（Ａｌ）相の微細均一化では初晶α（Ａｌ）相のサイズが１００μｍ以下を○とし、１００μｍを越えるサイズのものを×と判定した。
【００３２】
図２は、初晶α（Ａｌ）相の微細均一化が○評価の代表例写真を示す。
【００３３】
【発明の効果】
以上述べて来た如く、本発明によれば、従来の半溶融ビレットよりも工程が簡素化され低コスト化が図れる。また、得られる組織も初晶α（Ａｌ）相サイズが平均１００μｍ以下で、かつ初晶α（Ａｌ）相の面積率５０％の均一球状化組織となっており、自動車部材等の輸送機器用として使用が可能である。
【図面の簡単な説明】
【図１】冷間型枠鍛造の模式図である。
【図２】初晶α（Ａｌ）相の微細均一化が○評価の代表例の顕微鏡組織写真であり、倍率は５０倍である。
【符号の説明】
１ 鍛造用金型
２ 鍛造用金型ポンチ
３ アルミニウム合金ビレット[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a method for producing a semi-melt molded billet of an aluminum alloy used for transportation equipment.
[0002]
[Prior art]
The thixocast method using a semi-molten billet is a technology that has recently been attracting attention because it has advantages such as fewer casting segregation and defects and a longer die life compared to conventional die casting methods. The billet casting method used for this is a method (method) in which electromagnetic and mechanical stirring is performed in the semi-melting temperature range in order to spheroidize the primary crystal α (Al) phase at the billet stage known as the Pesine Almax method. A) or a method of adding a larger amount of Al-Ti-B than the amount normally added at the time of casting, and raising the temperature to the latter half melting temperature range to spheroidize the primary crystal α (Al) phase (Method B) There is. Further, a method (method C) in which strain is introduced by extrusion / rolling and then heated and spheroidized as in method B is widely known.
[0003]
[Problems to be solved by the invention]
In the case of the conventional semi-molten production method, the method A has a problem that the process is very complicated and the production cost is high.
Moreover, in method B, since a large amount of Al—Ti—B is added, quality instability occurs due to TiB 2 sedimentation in the melting furnace, and the method of introducing strain by rolling in method C introduces uniform strain. In addition, the extrusion process is cumbersome due to room temperature extrusion, and it is difficult to introduce uniform strain, and both strain introduction methods require product processing after processing, and mass production and cost reduction cannot be achieved. there were.
[0004]
Japanese Patent No. 2976073 discloses an improved method. That is, in the first item, there is described in “the step of deforming a fully solidified metal or metal alloy material at a temperature below its recrystallization temperature, heating the deformable material to cause recrystallization of the microstructure of the material. And partially melting the recrystallized structure to form independent particles in a liquid matrix that exhibits thixotropic behavior by raising the temperature of the material above its solidus temperature. It is a method including the step of
In this method, the deformation material is heated to cause recrystallization of the microstructure of the material, and heating that is called so-called two-step heating in which the temperature of the material is raised to a temperature above the solidus temperature. Is done. Such a method can be said to be an improved technique as compared with the conventional technique, but it still requires two-stage heating, and has a problem that the process is complicated and heating control is difficult.
[0005]
An object of the present invention is to provide a method for producing a semi-molten molded billet of an aluminum alloy for transportation equipment in which the disadvantages of the above prior art are eliminated, the process is simple and cost reduction can be promoted, and the resulting product is homogeneous. To do.
[0006]
[Means for Solving the Problems]
In order to achieve the above object, the manufacturing method of the semi-molten molded billet of the aluminum alloy for transportation equipment of the present application is Cu 0.40 to 5.5 wt%, Si 11.0 to 15.0 wt%, Zn 1.0 wt% or less, Fe1. 5 wt% or less, Mn 0.65 wt% or less, Ti 0.005 to 0.5 wt% and at least one of B 0.0001 to 0.5 wt%, Mg 0.40 to 1.8 wt% and Ni 0.05 to 1. An aluminum alloy containing at least one or more of 7 wt%, the balance being substantially composed of Al, the eutectic Si having an average particle diameter of 200 μm or less, and a dendrite branch interval (DAS) of 200 μm or less is manufactured. Then, the strain rate is 5 to 50%, and the processing introduction speed is 50 mm / sec. In the following, processing strain is introduced by cold mold forging at a temperature lower than the recrystallization temperature, and then the temperature is raised to the eutectic temperature or higher, and the liquid phase ratio is maintained at a temperature of 20 to 80% and semi-molten. It is a method of processing.
[0007]
In this case, homogenization for 1 to 10 hours at a temperature of 450 to 550 ° C. is performed before processing strain is introduced in order to homogenize component segregation, spheroidization of eutectic Si and release of casting stress. Preferably it is done.
[0008]
Moreover, in order to achieve the said objective, the manufacturing method of the semi-molten shaping | molding billet of the aluminum alloy for transportation apparatuses of this application is Cu0.40-5.5 wt%, Si11.0-15.0 wt%, Zn1.0 wt% or less, Fe 1.5 wt% or less, Mn 0.65 wt% or less, Ti 0.005 to 0.5 wt% and at least one of B 0.0001 to 0.5 wt%, Mg 0.40 to 1.8 wt% and Ni 0.05 to At least one or more of 1.7 wt% and at least one of Sr 0.001 to 0.10 wt%, Na 0.03 to 0.01 wt% and Sb 0.05 to 0.2 wt%, with the balance being substantially In particular, an aluminum alloy having an Al composition and an eutectic Si average particle size of 200 μm or less and a dendrite branch (DAS) of 200 μm or less is manufactured, and then strain is produced. 5% to 50%, processing introduction speed 50 mm / sec. In the following, processing strain is introduced by cold mold forging at a temperature lower than the recrystallization temperature, and then the temperature is raised to the eutectic temperature or higher, and the liquid phase ratio is maintained at a temperature of 20 to 80% and semi-molten. It is a method of processing.
[0009]
In this case, homogenization for 1 to 10 hours at a temperature of 450 to 550 ° C. is performed before processing strain is introduced in order to homogenize component segregation, spheroidization of eutectic Si and release of casting stress. Preferably it is done.
[0010]
DETAILED DESCRIPTION OF THE INVENTION
Hereinafter, various numerical limitation reasons such as numerical limitation of the amount of aluminum alloy components used in the present invention will be described in detail.
[0011]
The Cu component improves not only mechanical properties but also hardness, machinability, and castability. However, the effect is small if it is less than 0.40 wt%, while corrosion resistance decreases if it exceeds 5.5 wt%. It was set to 0.40 to 5.5 wt%.
[0012]
The Si component has an effect of improving the castability, but if the amount is less than 11.0 wt%, the effect is small. On the other hand, if it exceeds 15.0 wt%, the elongation / toughness deteriorates and the cold forgeability deteriorates. Therefore, it was 11.0-15.0 wt%.
[0013]
The Mg component precipitates Mg 2 Si and contributes to the improvement of mechanical properties. However, if the content is less than 0.40 wt%, the effect is small. On the other hand, if it exceeds 1.8 wt%, the cold forging workability deteriorates. 40-1.8 wt%.
[0014]
The Fe component produces an Al component and an intermetallic compound, and if it is contained in a large amount, it becomes an Al—Fe—Si compound and adversely affects elongation, toughness, and corrosion resistance.
[0015]
The Ti component refines the structure of the ingot and prevents the occurrence of ingot cracking, but the effect is small if it is less than 0.005 wt%, while the TiAl 3 giant crystallized product is less than 0.5 wt%. Occurrence is promoted and causes cracking during cold forging and deterioration of mechanical properties of transport equipment parts, so 0.005 to 0.5 wt%.
[0016]
The B component also refines the structure of the ingot together with the Ti component to prevent the occurrence of ingot cracking, but the effect is small if it is less than 0.0001 wt%, while it exceeds the 0.5 wt% during cold forging. Since it causes cracks and deterioration of mechanical properties of parts for transportation equipment, the content is set to 0.0001 to 0.5 wt%.
[0017]
The Zn component improves the castability but deteriorates the corrosion resistance.
[0018]
The Mn component is set to 0.65 wt% or less because it causes a decrease in toughness due to the formation of coarse intermetallic compounds.
[0019]
The Ni component contributes to the improvement of the high-temperature strength, but the effect is small when the content is less than 0.05 wt%, whereas the corrosion resistance is deteriorated when the content exceeds 1.7 wt%, so that the Ni content is set to 0.05 to 1.7 wt%.
[0020]
Sr, Na, and Sb components contribute to the improvement of mechanical properties by refining eutectic Si. However, the effect is small when Sr is 0.001 wt%, Na is 0.003 wt%, and Sb is less than 0.05 wt%, while Sr is 0.10 wt%. When Na exceeds 0.01 wt%, the fluidity of the molten metal at the time of casting deteriorates, and when exceeding 0.2 wt%, Sr0.001 to 0.10 wt%, Na0 0.003 to 0.01 wt% and Sb 0.05 to 0.2 wt%.
[0021]
A billet having an average particle size of eutectic Si of 200 μm or less and a dendrite branch interval (DAS) of 200 μm or less is cast, but the average particle size of eutectic Si exceeds 200 μm and the dendrite branch interval (DAS) is If it exceeds 200 μm, it becomes difficult to make the primary α (Al) phase into uniform fine spheroids when heated to the semi-melting temperature range, and it takes time for the homogenization to be performed. The interval (DAS) was set to 200 μm or less.
[0022]
By homogenizing the billet obtained by casting, a crystallized product of Al 2 Cu crystallized at the grain boundary during casting is dissolved in the matrix. Further, the eutectic Si is spheroidized by homogenization treatment to reduce deformation resistance during cold forging. When the homogenization temperature is less than 450 ° C. or when the heating time does not reach 1 hour, sufficient solution cannot be obtained, and eutectic Si spheroidization and removal of casting strain are insufficient. However, if the processing temperature exceeds 550 ° C., eutectic melting occurs and the workability during forging is impaired. On the other hand, when the heating time exceeds 10 hours, the homogenization effect corresponding to the long heating time cannot be obtained, resulting in a loss of heating energy. For this reason, the homogenization treatment conditions were heating at a temperature of 450 to 550 ° C. for 1 to 10 hours.
[0023]
Next, processing strain is introduced by cold forging so that the process can be simplified and strain is effectively introduced at a low processing rate, and strain is uniformly introduced into the entire forging billet. Formwork forging. When the strain rate is less than 5%, the introduction of strain is small, so even if the temperature is raised to the semi-melting temperature range, uniform spheroidization of the primary crystal α (Al) phase cannot be achieved. In addition to no change in the α (Al) phase size, cracks occurred during cold forging, so 5-50%. The distortion rate here is ( L 1 −L 2 ) / L 1 × 100 (%), where L 1 is the original length of the billet for forging and L 2 is the length of the billet after forging. Defined.
[0024]
The processing introduction speed can be greatly increased by adding refinement of crystal grains of billet ingots and refinement and homogenization of eutectic Si. In terms of productivity, it is preferable that the processing introduction speed is as fast as possible. However, 50 mm / sec. Exceeds 50 mm / sec., Because cracking occurs during forging, forging dead zones occur, and strain is not uniformly introduced. It was as follows. Further, when the billet temperature during cold mold forging is higher than the recrystallization temperature, the introduction of strain for the predetermined processing rate is insufficient, and even when the temperature is raised to the semi-melting temperature, the primary α (Al) phase has a granular structure. Therefore, it was set below the recrystallization temperature.
[0025]
Thereafter, the billet is heated to a temperature equal to or higher than the eutectic temperature and held at a temperature at which the liquid phase ratio becomes 20 to 80%, and semi-molten molding is performed. Uniform spheroidization cannot be achieved, and the deformation resistance of semi-molten molding is large, making pressure molding difficult. On the other hand, if it exceeds 80%, a molded product having a uniform structure cannot be obtained. For this reason, the liquid phase ratio in the semi-melting temperature range above the eutectic temperature was set to 20 to 80%.
[0026]
【Example】
Specific examples of the present invention are shown below.
FIG. 1 is a schematic view of cold mold forging used in the method of the present invention, in which 1 is a forging die, 2 is a forging die punch, and 3 is an aluminum alloy billet.
[0027]
A molten metal was prepared so that Cu, Si, Mg, Zn, Fe, Ti, B, Ni, Sr, and Sb each had a composition as shown in Table 1 below, and an aluminum alloy billet was cast by continuous casting.
[0028]
[Table 1]
The aluminum alloy billet shown in Table 1 was processed under the conditions shown in Table 2, and the results of evaluating the moldability of semi-melt molding and the shape of the primary crystal α (Al) phase after semi-melt molding are also shown in Table 2. .
[0030]
[Table 2]
The moldability at the time of introducing the processing strain shown in Table 2 was judged as “Good” when the mold did not generate a crack when molded under the molding conditions shown in Table 2 and the moldability was good. . Regarding the moldability of the semi-melt molding, a good one was evaluated as “good”, and a poor one was determined as “poor”. The shape of the primary crystal α (Al) phase after semi-melt molding was evaluated as “◯” when spheroidization was observed, and “×” when the spheroidization was insufficient. In the fine homogenization of the primary crystal α (Al) phase after semi-melt molding, the primary crystal α (Al) phase size was evaluated as ○ when the size of the primary crystal α (Al) phase was 100 μm or less, and × when the size exceeded 100 μm.
[0032]
FIG. 2 shows a photograph of a representative example in which fine homogenization of the primary crystal α (Al) phase is evaluated as o.
[0033]
【The invention's effect】
As described above, according to the present invention, the process can be simplified and the cost can be reduced as compared with the conventional semi-molten billet. The resulting structure also has a uniform spheroidized structure with an average primary crystal α (Al) phase size of 100 μm or less and an area ratio of primary crystal α (Al) phase of 50%. It can be used as
[Brief description of the drawings]
FIG. 1 is a schematic diagram of cold mold forging.
FIG. 2 is a photomicrograph of a representative example of evaluation of fine homogenization of primary crystal α (Al) phase, with a magnification of 50 times.
[Explanation of symbols]
1 Forging die 2 Forging die punch 3 Aluminum alloy billet
Claims (4)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
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| JP2001342715A JP3840400B2 (en) | 2001-11-08 | 2001-11-08 | Method for producing semi-melt molded billet of aluminum alloy for transportation equipment |
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| JP2001342715A JP3840400B2 (en) | 2001-11-08 | 2001-11-08 | Method for producing semi-melt molded billet of aluminum alloy for transportation equipment |
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| JP2008001954A (en) * | 2006-06-23 | 2008-01-10 | Toyota Central Res & Dev Lab Inc | Aluminum alloy for use in semisolid casting and manufacturing method of aluminum alloy casting |
| DE502007002411D1 (en) * | 2007-05-24 | 2010-02-04 | Rheinfelden Aluminium Gmbh | Heat-resistant aluminum alloy |
| JP5449754B2 (en) * | 2008-12-08 | 2014-03-19 | 宮本工業株式会社 | Forging piston for engine or compressor |
| KR101738038B1 (en) * | 2015-08-13 | 2017-05-19 | 현대자동차주식회사 | Excellent high elasticity and wear resistance hyper-eutectic al-si alloy |
| CN107400792A (en) * | 2017-06-27 | 2017-11-28 | 太仓市雅兴精密冲压件厂 | A kind of preparation method of die casting impact resistance alloy |
| JP7293696B2 (en) * | 2019-02-06 | 2023-06-20 | 株式会社レゾナック | Aluminum alloy casting material and manufacturing method thereof |
| CN113005341A (en) * | 2021-02-23 | 2021-06-22 | 珠海市润星泰电器有限公司 | High-thermal-conductivity aluminum alloy and preparation method thereof |
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