JP2006274435A - Aluminum alloy shaping material and its production method - Google Patents
Aluminum alloy shaping material and its production method Download PDFInfo
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本発明は、アルミニウム合金成形材及びその製造方法に関する。 The present invention relates to an aluminum alloy molded material and a method for producing the same.
航空機材料、自動車部品材料、精密機械部品材料、電子材料、バネ材料、ネジ材料等においては、軽量化の要求から高強度のアルミニウム合金成形材が広く用いられるようになっている。しかし、強度の点では鉄鋼材料と比較すると未だ十分でないことから、種々の高強度合金が検討されている。 In aircraft materials, automobile parts materials, precision machine parts materials, electronic materials, spring materials, screw materials, etc., high-strength aluminum alloy moldings are widely used because of the demand for weight reduction. However, since it is still not sufficient in terms of strength compared to steel materials, various high strength alloys have been studied.
特許文献１には、Ｃｏ、Ｎｉ、Ｃｕ、Ｚｎ、Ａｇ、Ｌｉ、Ｍｇ、Ｓｉ、Ｃａ、Ｔｉ、Ｚｒ、Ｃｒ、Ｍｎ又はＦｅ等を含む、高力、耐熱性アルミニウム合金が開示されている。 Patent Document 1 discloses a high-strength, heat-resistant aluminum alloy containing Co, Ni, Cu, Zn, Ag, Li, Mg, Si, Ca, Ti, Zr, Cr, Mn, Fe, or the like.
特許文献２には、Ｚｎ５〜１１重量％、Ｍｇ２〜４．５重量％、Ｃｕ０．５〜２重量％及びＡｇ０．０１〜０．５重量％含むアルミニウム合金急冷凝固粉末、及び当該アルミニウム合金急冷凝固粉末を空気中、真空中又は不活性ガス雰囲気中で熱間固化成形した後、得られた成形体を時効処理して強度を高めることを特徴とするアルミニウム合金成形材の製造方法が開示されている。
しかしながら、アルミニウムは延性の高い金属であるため、単に引張強度が高いだけでは高荷重負荷時に合金成形材が変形するおそれがある。 However, since aluminum is a highly ductile metal, there is a risk that the alloy molded material may be deformed when a high load is applied only by having a high tensile strength.
したがって、本発明は、高い引張強度及び高い耐力を兼ね備えたアルミニウム合金成形材及びその製造方法を提供することを目的とする。 Therefore, an object of the present invention is to provide an aluminum alloy molded material having a high tensile strength and a high yield strength and a method for producing the same.
本発明者は、従来技術の問題に鑑みて鋭意研究を重ねた結果、特定組成のアルミニウムを一定の条件下で製造することにより、上記目的を達成できることを見出し、本発明を完成するに至った。 As a result of intensive studies in view of the problems of the prior art, the present inventors have found that the above object can be achieved by producing aluminum having a specific composition under a certain condition, and have completed the present invention. .
すなわち、本発明は、下記のアルミニウム合金成形材及びその製造方法に係る。
１． アルミニウム合金成形材を製造する方法であって、
（１）Ｚｎ５〜１１重量％、Ｍｇ２〜４．５重量％、Ｃｕ０．５〜２重量％、Ｍｎ２〜６重量％及びＡｇ０．０１〜０．５重量％含み、残部が実質的にＡｌからなるＡｌ合金急冷凝固粉末を予備成形する第１工程、
（２）前記予備成形体１００ｇに対する不活性ガス流量が１リットル／分〜１００リットル／分である不活性ガス雰囲気中で温度４５０℃〜５５０℃及び押し出し比２０〜１００の範囲で前記予備成形体を熱間固化成形する第２工程、及び
（３）前記成形体を時効処理する第３工程
を含むことを特徴とするアルミニウム合金成形材の製造方法。
２． Ａｌ合金急冷凝固粉末がＺｒ０．０１〜２．０重量％をさらに含有する、前記項１に記載の製造方法。
３． Ａｌ合金急冷凝固粉末がＦｅ０．０１〜０．２重量％及びＳｉ０．０１〜０．２重量％をさらに含有する、前記項１又は２に記載のアルミニウム合金成形材の製造方法。
４． Ａｌ合金急冷凝固粉末の平均粒径が７５μｍ未満である、前記項１〜３のいずれかに記載の製造方法。
５． 前記項１〜４のいずれかに記載の製造方法により得られる、耐力８５ｋｇ／ｍｍ２以上のアルミニウム合金成形材。
That is, the present invention relates to the following aluminum alloy formed material and a method for producing the same.
1. A method for producing an aluminum alloy molded material,
(1) Zn 5 to 11 wt%, Mg 2 to 4.5 wt%, Cu 0.5 to 2 wt%, Mn 2 to 6 wt% and Ag 0.01 to 0.5 wt%, the balance being substantially made of Al A first step of preforming an Al alloy rapidly solidified powder;
(2) The preform in the range of a temperature of 450 ° C. to 550 ° C. and an extrusion ratio of 20 to 100 in an inert gas atmosphere having an inert gas flow rate of 1 liter / min to 100 liter / min with respect to 100 g of the preform. A method for producing an aluminum alloy molded material, comprising: a second step of hot solidifying and forming; and (3) a third step of aging treatment of the compact.
2. Item 2. The method according to Item 1, wherein the Al alloy rapidly solidified powder further contains 0.01 to 2.0% by weight of Zr.
3. Item 3. The method for producing an aluminum alloy molded material according to Item 1 or 2, wherein the Al alloy rapidly solidified powder further contains 0.01 to 0.2 wt% Fe and 0.01 to 0.2 wt% Si.
4). Item 4. The production method according to any one of Items 1 to 3, wherein the Al alloy rapidly solidified powder has an average particle size of less than 75 µm.
5. An aluminum alloy molded material having a yield strength of 85 kg / mm 2 or more, obtained by the production method according to any one of Items 1 to 4.
本発明の製造方法によれば、特定の雰囲気下でＡｌ合金急冷凝固粉末の圧粉体を熱処理することから、より高い引張強度及び耐力を有する材料を提供することができる。 According to the production method of the present invention, since the green compact of the Al alloy rapidly solidified powder is heat-treated in a specific atmosphere, a material having higher tensile strength and proof stress can be provided.
本発明の製造方法により得られるアルミニウム合金成形材は、例えば航空機材料、自動車部品材料、精密機械部品材料、電子材料、バネ材料、ネジ材料等として好適に用いることができる。特に軽量化及び精密化の要請が高い自動車部品等の材料としても最適である。 The aluminum alloy molded material obtained by the production method of the present invention can be suitably used as, for example, aircraft materials, automobile component materials, precision machine component materials, electronic materials, spring materials, screw materials, and the like. In particular, it is optimal as a material for automobile parts and the like that are highly demanded for weight reduction and precision.
本発明のアルミニウム合金成形材の製造方法は、アルミニウム合金成形材を製造する方法であって、
（１）Ｚｎ５〜１１重量％、Ｍｇ２〜４．５重量％、Ｃｕ０．５〜２重量％、Ｍｎ２〜６重量％及びＡｇ０．０１〜０．５重量％含み、残部が実質的にＡｌからなるＡｌ合金急冷凝固粉末を予備成形する第１工程、
（２）前記予備成形体１００ｇに対する不活性ガス流量が１リットル／分〜１００リットル／分である不活性ガス雰囲気中で温度４５０℃〜５５０℃及び押し出し比２０〜１００の範囲で前記予備成形体を熱間固化成形する第２工程、及び
（３）前記成形体を時効処理する第３工程
を含むことを特徴とする。
＜第１工程＞
第１工程では、Ｚｎ５〜１１重量％、Ｍｇ２〜４．５重量％、Ｃｕ０．５〜２重量％、Ｍｎ２〜６重量％及びＡｇ０．０１〜０．５重量％含み、残部が実質的にＡｌからなるＡｌ合金急冷凝固粉末を予備成形する。
The method for producing an aluminum alloy molded material of the present invention is a method for producing an aluminum alloy molded material,
(1) Zn 5 to 11 wt%, Mg 2 to 4.5 wt%, Cu 0.5 to 2 wt%, Mn 2 to 6 wt% and Ag 0.01 to 0.5 wt%, the balance being substantially made of Al A first step of preforming an Al alloy rapidly solidified powder;
(2) The preform in the range of a temperature of 450 ° C. to 550 ° C. and an extrusion ratio of 20 to 100 in an inert gas atmosphere having an inert gas flow rate of 1 liter / min to 100 liter / min with respect to 100 g of the preform. And (3) a third step of aging treatment of the molded body.
<First step>
In the first step, Zn is 5 to 11% by weight, Mg is 2 to 4.5% by weight, Cu is 0.5 to 2% by weight, Mn is 2 to 6% by weight, and Ag is 0.01 to 0.5% by weight, and the balance is substantially Al. An Al alloy rapidly solidified powder made of is preformed.
Ａｌ合金急冷凝固粉末
本発明においては、出発原料としてＺｎ５〜１１重量％、Ｍｇ２〜４．５重量％、Ｃｕ０．５〜２重量％、Ｍｎ２〜６重量％及びＡｇ０．０１〜０．５重量％含み、残部が実質的にＡｌからなるＡｌ合金急冷凝固粉末を用いる。
Al alloy rapidly solidified powder In the present invention, Zn as a starting material 5-11 wt%, Mg2-4.5 wt%, Cu0.5-2 wt%, Mn2-6 wt% and Ag0.01-0.5 wt% An Al alloy rapidly solidified powder is used, the balance being substantially made of Al.
このような粉末は、公知の製法により作製することができる。例えば、Ｚｎ５〜１１重量％、Ｍｇ２〜４．５重量％、Ｃｕ０．５〜２重量％、Ｍｎ２〜６重量％及びＡｇ０．０１〜０．５重量％を含み、残余が実質的にＡｌからなる組成のＡｌ基合金の溶湯をアトマイズすることにより得ることができる。このようなＡｌ基合金は、通常のＡｌ合金が含有する程度の量の不可避的不純物（Ｆｅ、Ｓｉ等）を含んでいても良い。 Such a powder can be produced by a known production method. For example, Zn 5 to 11% by weight, Mg 2 to 4.5% by weight, Cu 0.5 to 2% by weight, Mn 2 to 6% by weight and Ag 0.01 to 0.5% by weight, with the balance being substantially Al. It can be obtained by atomizing a molten Al-based alloy having a composition. Such an Al-based alloy may contain inevitable impurities (Fe, Si, etc.) in an amount that a normal Al alloy contains.
Ｚｎ、Ｍｎ、Ｃｕに関し、これらの添加元素量が多すぎる場合には、急冷凝固を経たとしても、これらの添加元素は、Ａｌ中に固溶できないため、粗大な晶出物を形成し、Ａｌ合金の引張強度低下の原因となるため好ましくない。一方、これら添加元素量が少なすぎる場合には、ＧＰゾーン等の微細析出相の体積分率が減少するため、分散析出によるＡｌ合金の引張強度改善への寄与が薄れる。従って、本発明においては、Ａｌ合金中の添加量をＺｎ５〜１１重量％、Ｍｇ２〜４．５重量％及びＣｕ０．５〜２重量％とする。 With respect to Zn, Mn, and Cu, if the amount of these additive elements is too large, even after rapid solidification, these additive elements cannot be dissolved in Al, so that coarse crystallized substances are formed. This is not preferable because it causes a decrease in the tensile strength of the alloy. On the other hand, when the amount of these additive elements is too small, the volume fraction of the finely precipitated phase such as the GP zone decreases, and the contribution to the improvement of the tensile strength of the Al alloy due to the dispersion precipitation is reduced. Therefore, in this invention, the addition amount in Al alloy shall be Zn 5-11 weight%, Mg2-4.5 weight%, and Cu0.5-2 weight%.
本発明においては、さらにＭｎ２〜６重量％（好ましくは３〜５重量％）を配合することを必須とする。このＭｇの配合により、結晶粒径の微細化、金属間化合物Ａｌ６Ｍｎの形成に起因する転位密度の増大による加工硬化等の効果が達成され、成形材の引張強度が改善される。また、この金属間化合物は、押し出し方向に沿って、細長い板状に形成されていることが確認されており、これは繊維状の補強材的にも働いている。Ｍｎ含有量が２重量％未満である場合には、結晶粒微細化の効果が十分でなくなる。一方、Ｍｎ含有量が６重量％を上回る場合には、Ａｌ6Ｍｎの粗大な析出物が形成されるため、好ましくない。 In the present invention, it is essential to further contain 2 to 6% by weight (preferably 3 to 5% by weight) of Mn. By blending this Mg, effects such as work hardening by increasing the dislocation density due to the refinement of the crystal grain size and the formation of the intermetallic compound Al 6 Mn are achieved, and the tensile strength of the molding material is improved. Moreover, it has been confirmed that this intermetallic compound is formed in an elongated plate shape along the extrusion direction, and this also works as a fibrous reinforcing material. When the Mn content is less than 2% by weight, the effect of crystal grain refinement is not sufficient. On the other hand, when the Mn content exceeds 6% by weight, a coarse precipitate of Al 6 Mn is formed, which is not preferable.
本発明においては、さらにＡｇ０．０１〜０．５重量％（好ましくは、０．０１〜０．１重量％）を配合することを必須とする。このＡｇの配合により、Ａｌ合金急冷凝固粉末を成形した材料の時効処理後の引張強度が著しく改善される。 In the present invention, it is essential to further contain 0.01 to 0.5% by weight of Ag (preferably 0.01 to 0.1% by weight). By adding this Ag, the tensile strength after aging treatment of the material formed from the Al alloy rapidly solidified powder is remarkably improved.
本発明では、必要に応じてＺｒを０．０１〜２重量％の範囲で添加することにより、アルミニウム合金成形材の引張強度及び耐力をさらに向上させることができる。Ｚｒの添加量が、０．０１重量％未満の場合には、添加による効果の改善が十分でないのに対し、２重量％を上回る場合には、粗大析出物の形成により、むしろ引張強度低下の原因となることがある。 In the present invention, the tensile strength and proof stress of the aluminum alloy molded material can be further improved by adding Zr in the range of 0.01 to 2% by weight as necessary. When the amount of Zr added is less than 0.01% by weight, the effect of the addition is not sufficiently improved. On the other hand, when the amount exceeds 2% by weight, the formation of coarse precipitates causes a decrease in tensile strength. It can be a cause.
また、不可避的不純物であるＦｅ及びＳｉをそれぞれ０．２重量％以下とすることにより、Ａｌ−Ｆｅ−Ｓｉ系の粗大な晶出物の形成を抑制し、さらに引張強度を改善することができる。Ｆｅ及びＳｉ含有量の下限値は特に限定されないが、工業的にはそれぞれ０．０１重量％程度である。 In addition, by making Fe and Si, which are inevitable impurities, 0.2% by weight or less, the formation of Al-Fe-Si coarse crystals can be suppressed, and the tensile strength can be further improved. . Although the lower limit of Fe and Si content is not specifically limited, Industrially, it is about 0.01 weight%, respectively.
アトマイズは、空気アトマイズ法、Ａｒ、Ｈｅ等を用いる不活性ガスアトマイズ法、Ｎ２ガスアトマイズ法等の任意の方式を採用することができる。アトマイズに際しては、Ａｌ基合金溶湯を１０２Ｋ／秒以上の冷却速度で凝固させる。 For the atomization, an arbitrary method such as an air atomization method, an inert gas atomization method using Ar, He, or the like, an N 2 gas atomization method, or the like can be adopted. At the time of atomization, the Al-based alloy molten metal is solidified at a cooling rate of 10 2 K / second or more.
上記のＡｌ合金急冷凝固粉末の平均粒径は７５μｍ以下、好ましくは５０μｍ以下である。平均粒径下限は製造可能であれば特に限定されないが、通常は１μｍ以上である。粉末粒径が７５μｍを超えると、比表面積が減少して、引張強度及び耐力の増大に寄与する表面酸化皮膜量が減少するおそれがある。 The average particle diameter of the Al alloy rapidly solidified powder is 75 μm or less, preferably 50 μm or less. The lower limit of the average particle diameter is not particularly limited as long as it can be produced, but is usually 1 μm or more. When the powder particle size exceeds 75 μm, the specific surface area decreases, and the amount of the surface oxide film that contributes to the increase in tensile strength and proof stress may decrease.
なお、本発明の平均粒径は、レーザー回折式粒度分布測定法による値を示す。粉末形状も限定されず、例えば涙滴状、真球状、回転楕円体状、フレーク状、不定形状等いずれであっても良い。 In addition, the average particle diameter of this invention shows the value by the laser diffraction type particle size distribution measuring method. The powder shape is not limited, and may be any of, for example, a teardrop shape, a true spherical shape, a spheroid shape, a flake shape, and an indefinite shape.
予備成形
Ａｌ合金急冷凝固粉末の予備成形は、冷間静水圧あるいは一軸のプレス加工により冷間圧縮成形すれば良い。圧縮成形時の圧力は、得られた予備成形材が次工程まで工業的に取り扱える範囲とすれば良い。
＜第２工程＞
第２工程では、前記予備成形体１００ｇに対する不活性ガス流量が１リットル／分〜１００リットル／分である不活性ガス雰囲気中で温度４５０℃〜５５０℃及び押し出し比２０〜１００の範囲で前記予備成形体を熱間固化成形する。
The preformed Al alloy rapidly solidified powder may be preformed by cold compression molding by cold isostatic pressing or uniaxial pressing. The pressure at the time of compression molding may be set within a range in which the obtained preform can be handled industrially until the next step.
<Second step>
In the second step, the preliminary gas flow in an inert gas atmosphere having an inert gas flow rate of 1 liter / minute to 100 liter / minute with respect to the preform 100g is set at a temperature of 450 ° C. to 550 ° C. and an extrusion ratio of 20 to 100. The compact is hot solidified.
Ａｌ合金急冷凝固粉末表面には、表面酸化皮膜とともに多くの水分が吸着している。特に、Ｚｎ及びＭｇを含む合金は水分を吸着しやすい。また、予備成形時には、これらの水分が除去される機会はない。水分が多く残存していると、容体化処理時に水素ガスとなり成型材中にボイドを形成し、引張強度及び耐力を低下させるおそれがある。 A lot of moisture is adsorbed on the surface of the Al alloy rapidly solidified powder together with the surface oxide film. In particular, an alloy containing Zn and Mg tends to adsorb moisture. In addition, there is no opportunity to remove these moisture during preforming. If a large amount of moisture remains, it becomes hydrogen gas during the volumeification treatment, and voids are formed in the molding material, which may reduce the tensile strength and proof stress.
予備成形体１００ｇに対する不活性ガス流量が１リットル／分〜１００リットル／分とし、好ましくは５リットル／分〜６０リットル／分とする。前記不活性ガス流量が１リットル／分未満では、水分が十分除去されない。不活性ガス流量の上限値は特に限定されないが、１００リットル／分程度でその効果は飽和する。雰囲気の不活性ガスは特に限定されず、窒素、アルゴン等の露点の低いガスが好適に使用される。 The inert gas flow rate with respect to 100 g of the preform is 1 liter / minute to 100 liter / minute, preferably 5 liter / minute to 60 liter / minute. When the flow rate of the inert gas is less than 1 liter / minute, the water is not sufficiently removed. The upper limit of the inert gas flow rate is not particularly limited, but the effect is saturated at about 100 liters / minute. The inert gas in the atmosphere is not particularly limited, and a gas having a low dew point such as nitrogen or argon is preferably used.
不活性ガス流量時間は、予備成形体の大きさ等な応じて適宜設定することができるが、一般的には１０分〜１０時間程度とすることが好ましい。 The inert gas flow time can be appropriately set according to the size of the preform, and is generally preferably about 10 minutes to 10 hours.
固化成形温度は、４５０〜５５０℃、好ましくは４６０〜５２０℃である。固化成形温度が５５０℃を超えると粉末が溶融し始めるため好ましくない。また、４６０未満になると固化時に成型圧力が高くなるおそれがある。 The solidification molding temperature is 450 to 550 ° C, preferably 460 to 520 ° C. If the solidification molding temperature exceeds 550 ° C., the powder starts to melt, which is not preferable. On the other hand, if it is less than 460, the molding pressure may increase during solidification.
押出比は、２０以上１００以下、好ましくは３０以上６０以下である。押出比が２０より小さいとＡｌ合金急冷凝固粉末の表面酸化皮膜が十分に破壊されず、Ａｌ合金急冷凝固粉末の新生面が不足して固化成形体内の結合力が低下して高い引張強度及び耐力が得られなくなるおそれがある。また、押出比が１００を超えると設備の負荷が増大するので好ましくない。
＜第３工程＞
第３工程では、前記成形体を時効処理する。時効処理に先立って溶体化処理することもできる。溶体化処理を行う場合、容体化処理温度は４５０℃〜５１０℃、容体化処理時間は１〜１０時間程度とすれば良い。また、時効処理温度及び時間は、縦軸に温度、横軸に時間をとったグラフにおいて、１００℃・４０時間、１００度・１００時間、１４０℃・１時間及び１４０℃・４時間の４点で囲まれる範囲内に設定することが好ましい。
The extrusion ratio is 20 or more and 100 or less, preferably 30 or more and 60 or less. When the extrusion ratio is less than 20, the surface oxide film of the Al alloy rapidly solidified powder is not sufficiently destroyed, the new surface of the Al alloy rapidly solidified powder is insufficient, the bonding strength in the solidified molded body is reduced, and high tensile strength and yield strength are obtained. There is a risk that it will not be obtained. Moreover, since the load of an installation will increase when extrusion ratio exceeds 100, it is unpreferable.
<Third step>
In the third step, the molded body is subjected to an aging treatment. A solution treatment can also be performed prior to the aging treatment. When solution treatment is performed, the solution treatment temperature may be 450 to 510 ° C., and the solution treatment time may be about 1 to 10 hours. The aging treatment temperature and time are 4 points of 100 ° C./40 hours, 100 ° C./100 hours, 140 ° C./1 hour and 140 ° C./4 hours in the graph with temperature on the vertical axis and time on the horizontal axis. It is preferable to set within the range surrounded by.
以下に実施例及び比較例を示し、本発明の特徴とするところをより一層明らかにする。ただし、本発明は、実施例に限定されない。 Examples and comparative examples are shown below to further clarify the features of the present invention. However, the present invention is not limited to the examples.
実施例１〜１５及び比較例１〜１４
表１に示す合金組成を有するＡｌ地金を調製し、アトマイズ機に付属する高周波熔解炉により融解し、空気アトマイズ法により急冷凝固粉末とした。得られたＡｌ合金急冷凝固粉末を１５０μｍ以下、７５μｍ以下又は４４μｍ以下に分級し、１．５ｔｏｎ／ｃｍ２の冷間静水圧で直径３０ｍｍ、長さ７０ｍｍの丸棒型予備成型材を作製した。
Examples 1-15 and Comparative Examples 1-14
An Al metal having an alloy composition shown in Table 1 was prepared, melted by a high-frequency melting furnace attached to an atomizer, and rapidly solidified powder by an air atomization method. The obtained Al alloy rapidly solidified solid powder was classified into 150 μm or less, 75 μm or less, or 44 μm or less, and a round bar-shaped preform with a diameter of 30 mm and a length of 70 mm was prepared with a cold isostatic pressure of 1.5 ton / cm 2 .
得られた予備成型材を、表２に示す条件でアルゴンガス中にて熱間固化成形した。次いで、熱間固化成形から試験片を切り出し、４９０℃で溶体化処処理後焼き入れし、１２０℃２４時間の時効処理を行い、アルミニウム合金成形材を得た。 The obtained preform was hot solidified and molded in argon gas under the conditions shown in Table 2. Next, a test piece was cut out from the hot solidification molding, quenched after solution treatment at 490 ° C., and subjected to aging treatment at 120 ° C. for 24 hours to obtain an aluminum alloy molded material.
表３に各アルミニウム合金成形材の合金番号、製造工程、引張強度及び耐力を示す。また、表３には従来例として、市販の７０７５合金を調整し、同様に作製、評価した。 Table 3 shows the alloy number, manufacturing process, tensile strength, and yield strength of each aluminum alloy molded material. In Table 3, as a conventional example, a commercially available 7075 alloy was prepared, and similarly produced and evaluated.
Claims (5)
（１）Ｚｎ５〜１１重量％、Ｍｇ２〜４．５重量％、Ｃｕ０．５〜２重量％、Ｍｎ２〜６重量％及びＡｇ０．０１〜０．５重量％含み、残部が実質的にＡｌからなるＡｌ合金急冷凝固粉末を予備成形する第１工程、
（２）前記予備成形体１００ｇに対する不活性ガス流量が１リットル／分〜１００リットル／分である不活性ガス雰囲気中で温度４５０℃〜５５０℃及び押し出し比２０〜１００の範囲で前記予備成形体を熱間固化成形する第２工程、及び
（３）前記成形体を時効処理する第３工程
を含むことを特徴とするアルミニウム合金成形材の製造方法。 A method for producing an aluminum alloy molded material,
(1) Zn 5 to 11 wt%, Mg 2 to 4.5 wt%, Cu 0.5 to 2 wt%, Mn 2 to 6 wt% and Ag 0.01 to 0.5 wt%, the balance being substantially made of Al A first step of preforming an Al alloy rapidly solidified powder;
(2) The preform in the range of a temperature of 450 ° C. to 550 ° C. and an extrusion ratio of 20 to 100 in an inert gas atmosphere having an inert gas flow rate of 1 liter / min to 100 liter / min with respect to 100 g of the preform. A method for producing an aluminum alloy molded material, comprising: a second step of hot solidifying and forming; and (3) a third step of aging treatment of the compact.
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| JP2008240141A (en) * | 2007-02-28 | 2008-10-09 | Kobe Steel Ltd | HIGH STRENGTH AND HIGH DUCTILITY Al ALLOY, AND METHOD FOR PRODUCING THE SAME |
| CN101899597B (en) * | 2009-05-29 | 2012-07-18 | 爱信轻金属株式会社 | Excellent SCC resistance 7000 series aluminum alloy extrusion material and method for producing the same |
| CN109943791A (en) * | 2019-03-31 | 2019-06-28 | 华南理工大学 | 7075 Aluminium Alloy Extruded Bars of one kind and its manufacturing method |
| JP2020015955A (en) * | 2018-07-26 | 2020-01-30 | 三菱重工業株式会社 | Aluminum alloy material, method for producing aluminum alloy material, cask basket and cask |
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| JPH03243702A (en) * | 1990-02-20 | 1991-10-30 | Riken Corp | Manufacture of high strength aluminum alloy formed body |
| JPH05302104A (en) * | 1992-04-24 | 1993-11-16 | Kobe Steel Ltd | Production of aluminum or aluminum alloy composite material |
| JPH07316601A (en) * | 1994-03-28 | 1995-12-05 | Toyo Alum Kk | Production of rapidly solidified aluminum powder and aluminum alloy compact |
| JPH11302807A (en) * | 1998-04-20 | 1999-11-02 | Sumitomo Light Metal Ind Ltd | Manufacture of aluminum alloy for compressor vane |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JPH03243702A (en) * | 1990-02-20 | 1991-10-30 | Riken Corp | Manufacture of high strength aluminum alloy formed body |
| JPH05302104A (en) * | 1992-04-24 | 1993-11-16 | Kobe Steel Ltd | Production of aluminum or aluminum alloy composite material |
| JPH07316601A (en) * | 1994-03-28 | 1995-12-05 | Toyo Alum Kk | Production of rapidly solidified aluminum powder and aluminum alloy compact |
| JPH11302807A (en) * | 1998-04-20 | 1999-11-02 | Sumitomo Light Metal Ind Ltd | Manufacture of aluminum alloy for compressor vane |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2008240141A (en) * | 2007-02-28 | 2008-10-09 | Kobe Steel Ltd | HIGH STRENGTH AND HIGH DUCTILITY Al ALLOY, AND METHOD FOR PRODUCING THE SAME |
| CN101899597B (en) * | 2009-05-29 | 2012-07-18 | 爱信轻金属株式会社 | Excellent SCC resistance 7000 series aluminum alloy extrusion material and method for producing the same |
| JP2020015955A (en) * | 2018-07-26 | 2020-01-30 | 三菱重工業株式会社 | Aluminum alloy material, method for producing aluminum alloy material, cask basket and cask |
| JP7112275B2 (en) | 2018-07-26 | 2022-08-03 | 三菱重工業株式会社 | Aluminum alloy material, method for producing aluminum alloy material, basket for cask and cask |
| CN109943791A (en) * | 2019-03-31 | 2019-06-28 | 华南理工大学 | 7075 Aluminium Alloy Extruded Bars of one kind and its manufacturing method |
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