JP3802796B2

JP3802796B2 - Method for producing semi-melt molded billet of aluminum alloy for transportation equipment

Info

Publication number: JP3802796B2
Application number: JP2001337404A
Authority: JP
Inventors: 滋三久保; 政文溝内; 康幸村山; 綱樹岩下; 達雄里
Original assignee: Kyushu Mitsui Aluminum Industries Inc
Current assignee: Kyushu Mitsui Aluminum Industries Inc
Priority date: 2001-11-02
Filing date: 2001-11-02
Publication date: 2006-07-26
Anticipated expiration: 2021-11-02
Also published as: JP2003147497A

Description

【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】
半溶融成型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。これに使用するビレットの鋳造方法としては、ペネシー・アルマックス方式として知られているビレット段階での初晶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、Ｃｕ０．２０ｗｔ％以下、Ｓｉ０．５０ｗｔ％以下、Ｍｇ２．０〜６．０ｗｔ％、Ｚｎ０．３５ｗｔ％以下、Ｆｅ０．５０ｗｔ％以下と、Ｔｉ０．００１〜０．５ｗｔ％及びＢ０．０００１〜０．５ｗｔ％の少なくとも１種以上と、Ｍｎ０．０５〜１．５ｗｔ％、Ｚｒ０．０３〜０．３５ｗｔ％及びＣｒ０．０３〜０．４０ｗｔ％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、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、その後固相線温度以上に昇温し、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】
【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。
【０００９】
Ｃｕ成分は、０．２０ｗｔ％を超えると、耐食性が悪くなるので０．２０ｗｔ％以下とした。
【００１０】
Ｓｉ成分は、その量が０．５ｗｔ％を超えると伸び・靭性が劣化し冷間鍛造加工性が悪くなるので０．５ｗｔ％以下とした。
【００１１】
Ｍｇ成分は、固溶体強化として機械的性質の向上に寄与し、また切削性の向上や耐食性の向上に寄与するが、２．０ｗｔ％未満ではその効果が小さく、一方６．０ｗｔ％を超えると溶湯の酸化が促進され、鋳造が難しくなるので２．０〜６．０ｗｔ％とした。
【００１２】
Ｚｎ成分は、耐食性を劣化させるため０．３５ｗｔ％を上限とした。
【００１３】
Ｆｅ成分は、Ａｌ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、０．５０ｗｔ％以下とした。
【００１４】
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、０．００１ｗｔ％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。
【００１５】
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、０．５ｗｔ％を超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。
【００１６】
Ｍｎ、Ｃｒ、Ｚｒ成分は、再結晶粒の微細化あるいは再結晶を抑制し、強度・伸び・靭性を向上させる。また、耐食性、成型加工性、溶接性の向上に寄与するが、Ｍｎ０．０５ｗｔ％未満、Ｃｒ０．０３ｗｔ％未満、Ｚｒ０．０３ｗｔ％未満ではその効果が小さく、Ｍｎ１．５ｗｔ％、Ｃｒ０．４０ｗｔ％、Ｚｒ０．３５ｗｔ％をそれぞれ越えると鍛造時にＭｎＡｌ_６、ＣｒＡｌ_７、ＺｒＡｌ_３の粗大金属間化合物が晶出し、延性や加工性に悪影響を及ぼすのでＭｎ０．０５〜１．５ｗｔ％、Ｃｒ０．０３〜０．４ｗｔ％及びＺｒ０．０３〜０．３５ｗｔ％とした。
【００１７】
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、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。
【００１８】
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_２Ｃｕ、Ｍｇ_２Ｓｉ等の晶出物がマトリックスに固溶する。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、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なう。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見られず、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。
【００１９】
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、なおかつ鋳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。
【００２０】
加工導入速度は、ビレット鋳塊の結晶粒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、再結晶温度以上になると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。
【００２１】
その後、ビレットを固相線温度以上に昇温し、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、半溶融成型するが、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、固相線温度以上の半溶融温度域での液相率は２０〜８０％とした。
【００２２】
【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。
【００２３】
Ｃｕ、Ｓｉ、Ｍｇ、Ｚｎ、Ｆｅ、Ｔｉ、Ｂ、Ｍｎ、Ｃｒ及びＺｒ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。
【００２４】
【表１】

【００２５】
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。
【００２６】
【表２】

【００２７】
表２に示した加工歪導入時の成型性は、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の良好なものを○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。
【００２８】
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。
【００２９】
【発明の効果】
以上述べて来た如く、本発明方法によれば、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-melt molded billet has recently been attracting attention because it has advantages such as less 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 of performing electromagnetic and mechanical stirring in the semi-melting temperature range in order to spheroidize the primary crystal α (Al) phase in the billet stage, known as the Pennecy Almax system. (Method A) or a method of adding a larger amount of Al-Ti-B than the amount normally added at the time of casting, raising the temperature to the latter half melting temperature region (method) (scheme) B). 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 aluminum alloy for transportation equipment of the present application is Cu 0.20 wt% or less, Si 0.50 wt% or less, Mg 2.0 to 6.0 wt%, Zn 0.35 wt% or less. Fe 0.50 wt% or less, Ti 0.001 to 0.5 wt% and at least one of B 0.0001 to 0.5 wt%, Mn 0.05 to 1.5 wt%, Zr 0.03 to 0.35 wt% and An aluminum alloy containing at least one of Cr 0.03 to 0.40 wt%, the balance being substantially composed of Al, and having a dendrite branch interval (DAS) of 200 μm or less, and then producing a strain rate of 5 -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 solidus temperature or higher and maintained at a temperature at which the liquid phase ratio becomes 20 to 80%. It is a method of melt processing.
[0007]
In this case, for homogenization of component segregation and release of casting stress, it is preferable to perform a homogenization treatment at a temperature of 450 to 550 ° C. for 1 to 10 hours before introducing processing strain.
[0008]
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.
[0009]
If the Cu component exceeds 0.20 wt%, the corrosion resistance deteriorates, so the content was set to 0.20 wt% or less.
[0010]
If the amount of the Si component exceeds 0.5 wt%, the elongation and toughness deteriorate and the cold forging workability deteriorates.
[0011]
The Mg component contributes to improvement of mechanical properties as solid solution strengthening, and also contributes to improvement of machinability and corrosion resistance. However, the effect is small at less than 2.0 wt%, whereas the molten metal exceeds 6.0 wt%. The oxidation was promoted and casting became difficult, so the content was made 2.0 to 6.0 wt%.
[0012]
The Zn component has an upper limit of 0.35 wt% in order to deteriorate the corrosion resistance.
[0013]
The Fe component produces an intermetallic compound with Al, and if it is contained in a large amount, it becomes an Al—Fe—Si compound and adversely affects elongation, toughness, and corrosion resistance.
[0014]
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 0.001 wt%, while the giant crystallized TiAl ₃ is present if it exceeds 0.5 wt%. Of 0.005 to 0.5 wt% because it promotes the generation of cracks and leads to cracks during cold forging and deterioration of mechanical properties of transport equipment parts.
[0015]
The B component also refines the ingot structure 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%, and cracking during cold forging if it exceeds 0.5 wt%. In addition, since the mechanical properties of transport equipment parts are lowered, the content is set to 0.0001 to 0.5 wt%.
[0016]
Mn, Cr, and Zr components suppress recrystallization grain refinement or recrystallization, and improve strength, elongation, and toughness. Moreover, it contributes to the improvement of corrosion resistance, molding processability, and weldability, but the effect is small when Mn is less than 0.05 wt%, Cr is less than 0.03 wt%, and Zr is less than 0.03 wt%, Mn1.5 wt%, Cr0.40 wt%, If Zr 0.35 wt% is exceeded, coarse intermetallic compounds of MnAl ₆ , CrAl ₇ , ZrAl ₃ crystallize during forging, which adversely affects ductility and workability, so Mn 0.05 to 1.5 wt%, Cr 0.03 to 0 .4 wt% and Zr 0.03 to 0.35 wt%.
[0017]
Billets with a dendrite branch spacing (DAS) of 200 μm or less are cast. When the dendrite branch spacing (DAS) exceeds 200 μm, the primary α (Al) phase becomes uniform and fine spheroidized when heated to the semi-melting temperature range. When the homogenization process is performed, it takes time for the homogenization process, so the dendrite branch interval (DAS) is set to 200 μm or less.
[0018]
By homogenizing the billet obtained by casting, crystallized substances such as Al ₂ Cu and Mg ₂ Si crystallized at the crystal grain boundaries during casting are dissolved in the matrix. When the homogenization temperature is less than 450 ° C. or when the heating time does not reach 1 hour, sufficient solid solution cannot be obtained and casting distortion is not sufficiently removed. However, at a processing temperature exceeding 550 ° C., eutectic melting occurs and the workability during forging is impaired. On the other hand, when the heating time exceeds 10 hours, no increase in homogenization effect corresponding to the long heating time is observed, 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.
[0019]
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 to the entire billet for casting. 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. Not only the change in the α (Al) phase size is observed, but also cracking occurs during cold forging. The distortion rate here is (L ₁ −L ₂ ) / L ₁ × 100 (%), where L ₁ is the original length of the forging billet and L ₂ is the length of the billet after forging. Defined.
[0020]
The processing introduction speed can be greatly increased by adding grain refinement and homogenization treatment of the billet ingot. 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. In addition, 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 the primary α (Al) phase is granular even when the temperature is raised to the semi-melting temperature. Since it does not become a structure, it was set below the recrystallization temperature.
[0021]
Thereafter, the billet is heated to a temperature equal to or higher than the solidus temperature and held at a temperature at which the liquid phase ratio becomes 20 to 80%, and semi-molten molding is performed, but if the liquid phase ratio is less than 20%, the primary α (Al) phase The uniform spheroidization cannot be achieved and semi-molten molding is performed, but the deformation resistance of the semi-molten molding is large, and pressure molding becomes 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 rate in the semi-melting temperature range above the solidus temperature was set to 20 to 80%.
[0022]
【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.
[0023]
A molten metal was prepared so that Cu, Si, Mg, Zn, Fe, Ti, B, Mn, Cr, and Zr each had a composition as shown in Table 1 below, and an aluminum alloy billet was cast by continuous casting.
[0024]
[Table 1]

[0025]
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. .
[0026]
[Table 2]

[0027]
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 had good moldability. . 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 size of the primary crystal α (Al) phase was set to ○ when the size of the primary crystal α (Al) phase was 100 μm or less, and × when the size exceeded 100 μm.
[0028]
FIG. 2 shows a photograph of a representative example in which fine homogenization of the primary crystal α (Al) phase is evaluated as o.
[0029]
【The invention's effect】
As described above, according to the method of 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

Cu 0.20 wt% or less, Si 0.50 wt% or less, Mg 2.0 to 6.0 wt%, Zn 0.35 wt% or less, Fe 0.50 wt% or less, Ti 0.001 to 0.5 wt%, and B 0.0001 to 0.5 wt And at least one of Mn 0.05 to 1.5 wt%, Zr 0.03 to 0.35 wt% and Cr 0.03 to 0.40 wt%, with the balance being inevitable impurities and An aluminum alloy having a composition of Al and having a dendrite branch interval of 200 μm or less is manufactured, and then a strain rate of 5 to 50% and a processing introduction speed of 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 solidus temperature or higher and maintained at a temperature at which the liquid phase ratio becomes 20 to 80%. A method for producing a semi-melt molded billet of an aluminum alloy for transport equipment, characterized by melting.

The semi-molten molding of an aluminum alloy for transportation equipment according to claim 1, wherein the aluminum alloy is manufactured and homogenized for 1 to 10 hours at a temperature of 450 to 550 ° C before introducing processing strain. Billet manufacturing method.