JP7073068B2 - Al-Cu-Mg-based aluminum alloy and Al-Cu-Mg-based aluminum alloy material - Google Patents
Al-Cu-Mg-based aluminum alloy and Al-Cu-Mg-based aluminum alloy material Download PDFInfo
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Description
本発明は、焼き入れ性に優れたAl-Cu-Mg系アルミニウム合金及びAl-Cu-Mg系アルミニウム合金材料に関する。 The present invention relates to an Al—Cu—Mg-based aluminum alloy and an Al—Cu—Mg-based aluminum alloy material having excellent hardenability.
2000系や7000系等の熱処理型合金は、溶体化処理後に急冷され、その後人工時効処理を施されて、高い強度を得ている。ただし、これらの合金は、焼入れ感受性が高く、空冷や放冷等の冷却速度が小さい手法では、冷却中に固溶元素の析出が進行して、時効硬化能が低下してしまうため、水冷等の冷却速度の大きな手法を用いる必要があり、製造上の制限があった。 Heat-treated alloys such as 2000 series and 7000 series are rapidly cooled after solution treatment and then subjected to artificial aging treatment to obtain high strength. However, these alloys have high quenching sensitivity, and in methods such as air cooling and cooling with a low cooling rate, precipitation of solid-dissolved elements progresses during cooling and the age hardening ability decreases, so water cooling, etc. It was necessary to use a method with a large cooling rate, and there was a manufacturing limitation.
従来、2000系合金で焼入れ性を改善する手法としては、例えば、特許文献1、特許文献2のように、Liを含有させて、溶体化処理後の冷却時に固溶元素の析出を抑制することが挙げられる。しかし、Liの添加は、製造条件の制約が多く、製造の難易度が高いため、工業的な量産には向かないという難点があった。 Conventionally, as a method for improving hardenability with a 2000 series alloy, for example, as in Patent Document 1 and Patent Document 2, Li is contained to suppress precipitation of solid solution elements during cooling after solution treatment. Can be mentioned. However, the addition of Li has a drawback that it is not suitable for industrial mass production because there are many restrictions on the manufacturing conditions and the manufacturing difficulty is high.
また、特許文献3のように、溶体化処理後の冷却手法を工夫し、固溶元素の析出を抑制する方法もあるが、工程がやや煩雑になるという懸念があった。 Further, as in Patent Document 3, there is a method of suppressing the precipitation of solid solution elements by devising a cooling method after the solution treatment, but there is a concern that the process becomes a little complicated.
6000系合金のうち、6063合金は、熱処理型合金の中でも焼入れ感受性が低いために、製造上の制限が少なく、溶体化処理後あるいは熱間押出後に空冷程度の冷却速度でも添加元素の固溶状態を保持することができ、人工時効処理により強度を向上することができる。しかし、6063合金は、熱処理型合金の中では強度が低いため、使用用途の制限がある。 Of the 6000 series alloys, the 6063 alloy has low quenching sensitivity among heat-treated alloys, so there are few restrictions on manufacturing, and the solid-dissolved state of the added element even at a cooling rate of air cooling after solution treatment or hot extrusion. Can be retained, and the strength can be improved by artificial aging treatment. However, since the 6063 alloy has a low strength among the heat-treated alloys, there are restrictions on its intended use.
一方、6061合金等の中強度合金は、2000系、7000系合金と同様に焼入れ感受性が高いため、水冷等が必要となる。 On the other hand, medium-strength alloys such as 6061 alloys have high quenching sensitivity like 2000 series and 7000 series alloys, and therefore require water cooling or the like.
従って、本発明の目的は、中~高強度を有する熱処理型のAl-Cu-Mg系アルミニウム合金であって、焼き入れ性に優れたアルミニウム合金及びアルミニウム合金材料を提供することにある。 Therefore, an object of the present invention is to provide a heat-treated Al—Cu—Mg-based aluminum alloy having medium to high strength, and an aluminum alloy and an aluminum alloy material having excellent hardenability.
上記課題は、以下の本発明により解決される。
すなわち、本発明(1)は、熱処理型のAl-Cu-Mg系アルミニウム合金であって、
0.5~2.5質量%のCu、0.2~1.3質量%のMg、及び0.4~1.5質量%のMnを含有し、Siの含有量が0.25質量%以下、Feの含有量が0.25質量%以下、Crの含有量が0.10質量%以下、Znの含有量が0.10質量%以下、Tiの含有量が0.05質量%以下であり、残部Al及び不可避的不純物からなるアルミニウム合金であり、
CuとMgの含有量の合計(Cu+Mg)が1.1~3.1質量%であり、
下記式:
((Ts(水冷)-Ts(空冷))/Ts(水冷))×100
(式中、Ts(水冷)は、500℃で1時間溶体化処理後に30℃/秒の冷却速度で水冷されてから190℃で8時間時効処理された場合の引張強さを示し、Ts(空冷)は、500℃で1時間溶体化処理後に1℃/秒の冷却速度で空冷されてから190℃で8時間時効処理された場合の引張強さを示す。)
で求められる強度低下率(%)が10%未満であり、
Ts(空冷)が140MPa以上であること、
を特徴とするAl-Cu-Mg系アルミニウム合金を提供するものである。
The above problem is solved by the following invention.
That is, the present invention (1) is a heat treatment type Al—Cu—Mg-based aluminum alloy.
It contains 0.5 to 2.5% by mass of Cu, 0.2 to 1.3% by mass of Mg, and 0.4 to 1.5% by mass of Mn, and has a Si content of 0.25% by mass. Hereinafter, when the Fe content is 0.25% by mass or less, the Cr content is 0.10% by mass or less, the Zn content is 0.10% by mass or less, and the Ti content is 0.05% by mass or less. Yes, it is an aluminum alloy consisting of the balance Al and unavoidable impurities.
The total content of Cu and Mg (Cu + Mg) is 1.1 to 3.1% by mass.
The following formula:
((Ts (water cooling) -Ts (air cooling)) / Ts (water cooling)) x 100
(In the formula, Ts (water cooling) indicates the tensile strength when water-cooled at 500 ° C. for 1 hour , then water-cooled at a cooling rate of 30 ° C./sec, and then aged at 190 ° C. for 8 hours . (Air cooling) indicates the tensile strength when air-cooled at a cooling rate of 1 ° C./sec after solution treatment at 500 ° C. for 1 hour and then aged at 190 ° C. for 8 hours .)
The strength reduction rate (%) required in is less than 10%,
Ts (air cooling) is 140 MPa or more,
The present invention provides an Al—Cu—Mg-based aluminum alloy characterized by the above.
また、本発明(2)は、熱処理型のAl-Cu-Mg系アルミニウム合金であって、
0.5~2.5質量%のCu、0.2~1.3質量%のMg、及び0.4~1.5質量%のMnを含有し、Siの含有量が0.25質量%以下、Feの含有量が0.25質量%以下、Crの含有量が0.10質量%以下、Znの含有量が0.10質量%以下、Tiの含有量が0.05質量%以下であり、残部Al及び不可避的不純物からなるアルミニウム合金であり、CuとMgの含有量の合計(Cu+Mg)が1.1~3.1質量%であり、下記式:
((Ts(水冷)-Ts(空冷))/Ts(水冷))×100
(式中、Ts(水冷)は、500℃で1時間溶体化処理後に30℃/秒の冷却速度で水冷されてから190℃で8時間時効処理された場合の引張強さを示し、Ts(空冷)は、500℃で1時間溶体化処理後に1℃/秒の冷却速度で空冷されてから190℃で8時間時効処理された場合の引張強さを示す。)
で求められる強度低下率(%)が10%未満であり、Ts(空冷)が140MPa以上であるAl-Cu-Mg系アルミニウム合金で構成されていることを特徴とするAl-Cu-Mg系アルミニウム合金材料を提供するものである。
Further, the present invention (2) is a heat treatment type Al—Cu—Mg-based aluminum alloy.
It contains 0.5 to 2.5% by mass of Cu, 0.2 to 1.3% by mass of Mg, and 0.4 to 1.5% by mass of Mn, and has a Si content of 0.25% by mass. Hereinafter, when the Fe content is 0.25% by mass or less, the Cr content is 0.10% by mass or less, the Zn content is 0.10% by mass or less, and the Ti content is 0.05% by mass or less. It is an aluminum alloy consisting of the balance Al and unavoidable impurities, and the total content of Cu and Mg (Cu + Mg) is 1.1 to 3.1% by mass, and the following formula:
((Ts (water cooling) -Ts (air cooling)) / Ts (water cooling)) x 100
(In the formula, Ts (water cooling) indicates the tensile strength when water-cooled at 500 ° C. for 1 hour , then water-cooled at a cooling rate of 30 ° C./sec, and then aged at 190 ° C. for 8 hours . (Air cooling) indicates the tensile strength when air-cooled at a cooling rate of 1 ° C./sec after solution treatment at 500 ° C. for 1 hour and then aged at 190 ° C. for 8 hours .)
Al—Cu—Mg-based aluminum, which is composed of an Al—Cu—Mg-based aluminum alloy having a strength reduction rate (%) obtained in 1) of less than 10% and a Ts (air cooling) of 140 MPa or more. It provides an alloy material.
本発明によれば、中~高強度を有する熱処理型のAl-Cu-Mg系アルミニウム合金であって、焼き入れ性に優れたアルミニウム合金及びアルミニウム合金材料を提供することができる。 According to the present invention, it is possible to provide a heat-treated type Al—Cu—Mg-based aluminum alloy having medium to high strength, and an aluminum alloy and an aluminum alloy material having excellent hardenability.
本発明のAl-Cu-Mg系アルミニウム合金は、0.5~2.5質量%のCu、0.2~1.3質量%のMg、及び0.4~1.5質量%のMnを含有し、残部Al及び不可避的不純物からなるアルミニウム合金であり、CuとMgの含有量の合計(Cu+Mg)が1.1~3.1質量%であることを特徴とするAl-Cu-Mg系アルミニウム合金である。 The Al—Cu—Mg-based aluminum alloy of the present invention contains 0.5 to 2.5% by mass of Cu, 0.2 to 1.3% by mass of Mg, and 0.4 to 1.5% by mass of Mn. It is an aluminum alloy containing Al and an unavoidable impurity, and is characterized in that the total content of Cu and Mg (Cu + Mg) is 1.1 to 3.1% by mass. It is an aluminum alloy.
本発明のAl-Cu-Mg系アルミニウム合金は、Cu、Mg及びMnを必須の元素として含有し、残部Al及び不可避的不純物からなるアルミニウム合金である。 The Al—Cu—Mg-based aluminum alloy of the present invention is an aluminum alloy containing Cu, Mg and Mn as essential elements, and is composed of the balance Al and unavoidable impurities.
Cuは強度を向上させる元素として機能する。本発明のAl-Cu-Mg系アルミニウム合金中のCu含有量は、0.5~2.5質量%、好ましくは0.8~2.0質量%である。アルミニウム合金中のCu含有量が、上記範囲であることにより、中~高強度の熱処理型アルミニウム合金として必要な強度を達成でき、且つ、優れた焼き入れ性を有するアルミニウム合金となる。一方、アルミニウム合金中のCu含有量が、上記範囲未満だと、1000系合金と同程度の強度となり、熱処理型合金に要求される強度を達成することができず、また、上記範囲を超えると、焼き入れ性が低くなってしてしまう。 Cu functions as an element that improves strength. The Cu content in the Al—Cu—Mg-based aluminum alloy of the present invention is 0.5 to 2.5% by mass, preferably 0.8 to 2.0% by mass. When the Cu content in the aluminum alloy is in the above range, the aluminum alloy can achieve the strength required for a medium to high strength heat treatment type aluminum alloy and has excellent hardenability. On the other hand, if the Cu content in the aluminum alloy is less than the above range, the strength becomes about the same as that of the 1000 series alloy, and the strength required for the heat treatment type alloy cannot be achieved, and if it exceeds the above range. , The hardenability becomes low.
Mgは、Cuと同様に強度を向上させる元素として機能する。本発明のAl-Cu-Mg系アルミニウム合金中のMg含有量は、0.2~1.3質量%、好ましくは0.25~1.0質量%である。アルミニウム合金中のMg含有量が、上記範囲であることにより、中~高強度の熱処理型アルミニウム合金として必要な強度を達成でき、且つ、優れた焼き入れ性を有するアルミニウム合金となる。一方、アルミニウム合金中のMg含有量が、上記範囲未満だと、1000系合金と同程度の強度となり、熱処理型合金に要求される強度を達成することができず、また、上記範囲を超えると、焼き入れ性が低くなってしてしまう。 Mg functions as an element for improving strength like Cu. The Mg content in the Al—Cu—Mg-based aluminum alloy of the present invention is 0.2 to 1.3% by mass, preferably 0.25 to 1.0% by mass. When the Mg content in the aluminum alloy is in the above range, the aluminum alloy can achieve the strength required for a medium to high strength heat treatment type aluminum alloy and has excellent hardenability. On the other hand, if the Mg content in the aluminum alloy is less than the above range, the strength becomes about the same as that of the 1000 series alloy, and the strength required for the heat treatment type alloy cannot be achieved, and if it exceeds the above range. , The hardenability becomes low.
本発明のAl-Cu-Mg系アルミニウム合金中、CuとMgの含有量の合計(Cu+Mg)は、1.1~3.1質量%である。アルミニウム合金中のCuとMgの含有量の合計が、上記範囲にあることにより、中~高強度の熱処理型アルミニウム合金として必要な強度を達成でき、且つ、優れた焼き入れ性を有するアルミニウム合金となる。一方、アルミニウム合金中のCuとMgの含有量の合計が、上記範囲未満だと、1000系や3000系等の低強度の非熱処理型合金と同程度の強度となり、熱処理型合金に要求される強度を達成することができず、また、上記範囲を超えると、溶体化処理後の冷却時に固溶元素の析出が進行し易くなるため、従来の2000系合金と同様に水冷等の冷却速度の大きな手法で冷却する必要がある。 In the Al—Cu—Mg-based aluminum alloy of the present invention, the total content of Cu and Mg (Cu + Mg) is 1.1 to 3.1% by mass. When the total content of Cu and Mg in the aluminum alloy is within the above range, the strength required for a medium to high strength heat treatment type aluminum alloy can be achieved, and the aluminum alloy has excellent hardenability. Become. On the other hand, if the total content of Cu and Mg in the aluminum alloy is less than the above range, the strength is about the same as that of low-strength non-heat-treated alloys such as 1000 series and 3000 series, which is required for heat-treated alloys. If the strength cannot be achieved and the above range is exceeded, precipitation of solid-dissolved elements tends to proceed during cooling after the solution heat treatment. Therefore, the cooling rate such as water cooling is similar to that of the conventional 2000 series alloy. It needs to be cooled by a large method.
Mnは、強度を向上させるために添加される。本発明のAl-Cu-Mg系アルミニウム合金中のMn含有量は、0.4~1.5質量%、好ましくは0.45~1.0質量%である。アルミニウム合金中のMn含有量が、上記範囲であることにより、中~高強度の熱処理型アルミニウム合金として必要な強度を達成できるアルミニウム合金となる。一方、アルミニウム合金中のMn含有量が、上記範囲未満だと、Mn添加による強度向上の効果が得られず、また、上記範囲を超えると、熱間の変形抵抗が上昇するため、圧延や押出等での製造が困難となる。 Mn is added to improve the strength. The Mn content in the Al—Cu—Mg-based aluminum alloy of the present invention is 0.4 to 1.5% by mass, preferably 0.45 to 1.0% by mass. When the Mn content in the aluminum alloy is within the above range, the aluminum alloy can achieve the strength required for a medium to high strength heat-treated aluminum alloy. On the other hand, if the Mn content in the aluminum alloy is less than the above range, the effect of improving the strength by adding Mn cannot be obtained, and if it exceeds the above range, the deformation resistance between heats increases, so that rolling or extrusion is performed. It becomes difficult to manufacture in such cases.
本発明のAl-Cu-Mg系アルミニウム合金は、Cu、Mg及びMn以外に、必要に応じて、Si、Fe、Cr、Zn及びTiのうちの1種又は2種以上を含有することができる。その場合、本発明のAl-Cu-Mg系アルミニウム合金の各元素の含有量は、Siが0.25質量%以下、Feが0.25質量%以下、Crが0.10質量%以下、Znが0.10質量%以下、Tiが0.05質量%以下である。アルミニウム合金中のSi含有量が0.25質量%を超えると、Mg2Si化合物が過剰に形成されて焼き入れ性が低くなる。アルミニウム合金中のFe含有量が0.25質量%を超えると、Al3Fe化合物が過剰に析出して表面欠陥が生じ易くなる。CrはAlとの間に微細なAlCr3化合物を形成し、化合物周囲において固溶元素の析出を促進するため、アルミニウム合金中のCr含有量が0.10質量%を超えると焼き入れ性が低くなる。アルミニウム合金中のZn含有量が0.10質量%を超えると、7000系合金と同様にMgZn2析出物が形成され、焼き入れ性が低くなる。Tiは鋳造組織の微細化など組織微細化剤として添加される。アルミニウム合金中のTiの含有量が0.05質量%を超えると巨大晶出物が生成し表面欠陥を生じ易くなる。 The Al—Cu—Mg-based aluminum alloy of the present invention may contain one or more of Si, Fe, Cr, Zn and Ti, if necessary, in addition to Cu, Mg and Mn. .. In that case, the content of each element of the Al—Cu—Mg-based aluminum alloy of the present invention is 0.25% by mass or less for Si, 0.25% by mass or less for Fe, 0.10% by mass or less for Cr, and Zn. Is 0.10% by mass or less, and Ti is 0.05% by mass or less. When the Si content in the aluminum alloy exceeds 0.25% by mass, the Mg 2 Si compound is excessively formed and the hardenability is lowered. When the Fe content in the aluminum alloy exceeds 0.25% by mass, the Al 3 Fe compound is excessively precipitated and surface defects are likely to occur. Cr forms a fine AlCr 3 compound with Al and promotes the precipitation of solid-dissolving elements around the compound. Therefore, when the Cr content in the aluminum alloy exceeds 0.10% by mass, the hardenability is low. Become. When the Zn content in the aluminum alloy exceeds 0.10% by mass, MgZn 2 precipitates are formed as in the 7000 series alloy, and the hardenability is lowered. Ti is added as a microstructure micronizing agent such as miniaturization of a cast structure. If the Ti content in the aluminum alloy exceeds 0.05% by mass, giant crystallization is generated and surface defects are likely to occur.
なお、本発明のAl-Cu-Mg系アルミニウム合金は、本発明の効果に影響しない範囲で、その他の不純物を含有することは許容される。その場合、アルミニウム合金中のその他の不純物の各々の含有量が0.05質量%以下であり、且つ、その他の不純物の合計含有量が0.15質量%以下であれば許容される。 The Al—Cu—Mg-based aluminum alloy of the present invention is allowed to contain other impurities as long as it does not affect the effect of the present invention. In that case, it is permissible if the content of each of the other impurities in the aluminum alloy is 0.05% by mass or less and the total content of the other impurities is 0.15% by mass or less.
本発明のAl-Cu-Mg系アルミニウム合金は、Cu含有量が、0.5~2.5質量%、好ましくは0.8~2.0質量%であり、Mg含有量が、0.2~1.3質量%、好ましくは0.25~1.0質量%であり、且つ、Mn含有量が、0.4~1.5質量%、好ましくは0.45~1.0質量%であることにより、溶体化処理後に水冷されてから時効処理された場合の引張強さと、溶体化処理後に空冷されてから時効処理された場合の引張強さとの差が小さくなる。そのことを示す指標として、本発明のAl-Cu-Mg系アルミニウム合金は、「溶体化処理後に30℃/秒程度の冷却速度で水冷されてから時効処理された場合の引張強さ(Ts(水冷))」に対する「溶体化処理後に30℃/秒程度の冷却速度で水冷されてから時効処理された場合の引張強さ(Ts(水冷))と溶体化処理後に1℃/秒程度の冷却速度で空冷されてから時効処理された場合の引張強さ(Ts(空冷))との差」の割合(%)、すなわち、「((Ts(水冷)-Ts(空冷))/Ts(水冷))×100」の式で求められる強度低下率(%)が、10%未満である。なお、空冷の冷却速度は、1℃/秒程度であり、また、水冷の冷却速度は、30℃/秒程度である。なお、溶体化処理の条件又は時効処理の条件による引張強度の差異は、水冷と空冷との冷却速度の違いによる引張強度の差異に比べれば小さいので、上記強度低下率における水冷の場合と空冷の場合の溶体化処理及び時効処理については、同一の溶体化処理の条件及び同一の時効処理の条件で行っていればよい。 The Al—Cu—Mg-based aluminum alloy of the present invention has a Cu content of 0.5 to 2.5% by mass, preferably 0.8 to 2.0% by mass, and a Mg content of 0.2. It is about 1.3% by mass, preferably 0.25 to 1.0% by mass, and has a Mn content of 0.4 to 1.5% by mass, preferably 0.45 to 1.0% by mass. As a result, the difference between the tensile strength in the case of water cooling after the solution treatment and then the aging treatment and the tensile strength in the case of the air cooling after the solution treatment and then the aging treatment becomes small. As an index indicating this, the Al—Cu—Mg-based aluminum alloy of the present invention has “tensile strength when water-cooled at a cooling rate of about 30 ° C./sec after solution treatment and then aged (Ts (Ts)). Tensile strength (Ts (water cooling)) when water-cooled at a cooling rate of about 30 ° C / sec after solution treatment and then aging treatment for "water cooling))" and cooling at about 1 ° C / sec after solution treatment Ratio (%) of "difference from tensile strength (Ts (air cooling)) when air-cooled at a rate and then aged," that is, "((Ts (water cooling) -Ts (air cooling)) / Ts (water cooling)" )) The strength reduction rate (%) obtained by the formula “× 100” is less than 10%. The cooling rate for air cooling is about 1 ° C./sec, and the cooling rate for water cooling is about 30 ° C./sec. The difference in tensile strength due to the conditions of solution treatment or aging treatment is smaller than the difference in tensile strength due to the difference in cooling speed between water cooling and air cooling. In this case, the solution treatment and the aging treatment may be performed under the same solution treatment conditions and the same aging treatment conditions.
本発明のAl-Cu-Mg系アルミニウム合金のTs(空冷)、すなわち、溶体化処理、1℃/秒程度の冷却速度での空冷及び時効処理が施された後の引張強さは、好ましくは140MPa以上、特に好ましくは200MPa以上である。 The tensile strength of the Al—Cu—Mg-based aluminum alloy of the present invention after being subjected to Ts (air cooling), that is, solution treatment, air cooling at a cooling rate of about 1 ° C./sec, and aging treatment is preferable. It is 140 MPa or more, particularly preferably 200 MPa or more.
このように、本発明のAl-Cu-Mg系アルミニウム合金は、溶体化処理後に空冷されてから時効処理されたときの引張強度が、溶体化処理後に水冷されてから時効処理されたときの引張強度と比べ、若干低いものの、その差は小さく、溶体化処理後に、空冷されてから時効処理されても、溶体化処理後に、水冷されてから時効処理されたときと同程度の引張強度となるので、焼き入れ性に優れている。なお、本発明のAl-Cu-Mg系アルミニウム合金は、所定の形状に成形されて、溶体化処理された後、空冷されてから時効処理されてもよいし、あるいは、溶体化処理後に、水冷されてから時効処理されてもよい。 As described above, the Al—Cu—Mg-based aluminum alloy of the present invention has a tensile strength when it is air-cooled after the solution treatment and then aged, and a tensile strength when it is water-cooled after the solution treatment and then aged. Although it is slightly lower than the strength, the difference is small, and even if it is air-cooled and then aged after the solution treatment, the tensile strength is about the same as when it is water-cooled and then aged after the solution treatment. Therefore, it has excellent quenching properties. The Al—Cu—Mg-based aluminum alloy of the present invention may be formed into a predetermined shape, solution-cooled, then air-cooled and then aged, or may be water-cooled after the solution treatment. It may be prescription after it is done.
本発明のAl-Cu-Mg系アルミニウム合金は、常法に従って、所定の元素を所定の含有量で、溶解及び鋳造することにより製造される。 The Al—Cu—Mg-based aluminum alloy of the present invention is produced by melting and casting a predetermined element in a predetermined content according to a conventional method.
本発明のAl-Cu-Mg系アルミニウム合金材料は、0.5~2.5質量%のCu、0.2~1.3質量%のMg、及び0.4~1.5質量%のMnを含有し、残部Al及び不可避的不純物からなるアルミニウム合金であり、CuとMgの含有量の合計(Cu+Mg)が1.1~3.1質量%であるAl-Cu-Mg系アルミニウム合金で構成されていることを特徴とするAl-Cu-Mg系アルミニウム合金材料である。 The Al—Cu—Mg-based aluminum alloy material of the present invention contains 0.5 to 2.5% by mass of Cu, 0.2 to 1.3% by mass of Mg, and 0.4 to 1.5% by mass of Mn. It is an aluminum alloy containing the balance Al and unavoidable impurities, and is composed of an Al—Cu—Mg-based aluminum alloy in which the total content of Cu and Mg (Cu + Mg) is 1.1 to 3.1% by mass. It is an Al—Cu—Mg-based aluminum alloy material characterized by being made of.
すなわち、本発明のAl-Cu-Mg系アルミニウム合金材料は、常法に従って、所定の元素を所定の含有量で、溶解及び鋳造することにより製造されたアルミニウム合金鋳塊である本発明のAl-Cu-Mg系アルミニウム合金が、圧延加工又は押出加工されることにより、所定の形状に成形された加工材料である。 That is, the Al—Cu—Mg-based aluminum alloy material of the present invention is an aluminum alloy ingot produced by melting and casting a predetermined element in a predetermined content according to a conventional method. A Cu—Mg-based aluminum alloy is a processing material formed into a predetermined shape by rolling or extruding.
本発明のAl-Cu-Mg系アルミニウム合金材料は、Cu含有量が、0.5~2.5質量%、好ましくは0.8~2.0質量%であり、Mg含有量が、0.2~1.3質量%、好ましくは0.25~1.0質量%であり、且つ、Mn含有量が、0.4~1.5質量%、好ましくは0.45~1.0質量%であることにより、溶体化処理後に水冷されてから時効処理された場合の引張強さと、溶体化処理後に空冷されてから時効処理された場合の引張強さとの差が小さくなる。そのことを示す指標として、本発明のAl-Cu-Mg系アルミニウム合金材料は、「溶体化処理後に30℃/秒程度の冷却速度で水冷されてから時効処理された場合の引張強さ(Ts(水冷))」に対する「溶体化処理後に30℃/秒程度の冷却速度で水冷されてから時効処理された場合の引張強さ(Ts(水冷))と溶体化処理後に1℃/秒程度の冷却速度で空冷されてから時効処理された場合の引張強さ(Ts(空冷))との差」の割合(%)、すなわち、「((Ts(水冷)-Ts(空冷))/Ts(水冷))×100」の式で求められる強度低下率(%)が、10%未満である。なお、空冷の冷却速度は、1℃/秒程度であり、また、水冷の冷却速度は、30℃/秒程度である。 The Al—Cu—Mg-based aluminum alloy material of the present invention has a Cu content of 0.5 to 2.5% by mass, preferably 0.8 to 2.0% by mass, and has a Mg content of 0. It is 2 to 1.3% by mass, preferably 0.25 to 1.0% by mass, and has a Mn content of 0.4 to 1.5% by mass, preferably 0.45 to 1.0% by mass. Therefore, the difference between the tensile strength in the case of water cooling after the solution treatment and then the aging treatment and the tensile strength in the case of the air cooling after the solution treatment and then the aging treatment becomes small. As an index showing this, the Al—Cu—Mg-based aluminum alloy material of the present invention has “tensile strength (Ts) when it is water-cooled at a cooling rate of about 30 ° C./sec after solution treatment and then aged. (Water cooling)) ”is the tensile strength (Ts (water cooling)) when water-cooled at a cooling rate of about 30 ° C / sec after solution treatment and then aging treatment, and about 1 ° C / sec after solution treatment. The ratio (%) of the tensile strength (difference from the tensile strength (Ts (air cooling)) when air-cooled at the cooling rate and then aged, that is, "((Ts (water cooling) -Ts (air cooling))) / Ts ( The strength reduction rate (%) obtained by the formula of "water cooling)) x 100" is less than 10%. The cooling rate for air cooling is about 1 ° C./sec, and the cooling rate for water cooling is about 30 ° C./sec.
本発明のAl-Cu-Mg系アルミニウム合金材料は、溶体化処理された後、空冷又は水冷され、次いで、人工時効処理が施されて、所望の引張強度を有するアルミニウム合金材料となる。 The Al—Cu—Mg-based aluminum alloy material of the present invention is subjected to solution heat treatment, air cooling or water cooling, and then artificial aging treatment to obtain an aluminum alloy material having a desired tensile strength.
溶体化処理条件としては、特に制限されないが、溶体化処理温度は、好ましくは460~510℃、特に好ましくは485~505℃であり、溶体化処理時間は、好ましくは0.1~6時間、特に好ましくは1~5時間である。 The solution treatment conditions are not particularly limited, but the solution treatment temperature is preferably 460 to 510 ° C, particularly preferably 485 to 505 ° C, and the solution treatment time is preferably 0.1 to 6 hours. Particularly preferably, it is 1 to 5 hours.
溶体化処理を行った材料を空冷する場合、冷却速度は、0.1~5℃/秒、好ましくは0.5~5℃/秒である。また、溶体化処理を行った材料を水冷する場合、冷却速度は、10~50℃/秒、好ましくは20~50℃/秒である。 When the solution-treated material is air-cooled, the cooling rate is 0.1 to 5 ° C./sec, preferably 0.5 to 5 ° C./sec. When the solution-treated material is water-cooled, the cooling rate is 10 to 50 ° C./sec, preferably 20 to 50 ° C./sec.
人工時効処理条件としては、特に制限されないが、人工時効温度は、好ましくは150~210℃、特に好ましくは170~210℃であり、人工時効処理時間は、好ましくは5~24時間、特に好ましくは8~24時間である。 The artificial aging treatment conditions are not particularly limited, but the artificial aging temperature is preferably 150 to 210 ° C., particularly preferably 170 to 210 ° C., and the artificial aging treatment time is preferably 5 to 24 hours, particularly preferably. 8 to 24 hours.
本発明のAl-Cu-Mg系アルミニウム合金材料を、溶体化処理、空冷及び時効処理した後のアルミニウム合金の引張強さは、好ましくは140MPa以上、特に好ましくは200MPa以上である。また、本発明のAl-Cu-Mg系アルミニウム合金材料を、溶体化処理、水冷及び時効処理を行った後の引張強さは、好ましくは150MPa以上、特に好ましくは210MPa以上である。 The tensile strength of the aluminum alloy after solution treatment, air cooling and aging treatment of the Al—Cu—Mg-based aluminum alloy material of the present invention is preferably 140 MPa or more, particularly preferably 200 MPa or more. Further, the tensile strength of the Al—Cu—Mg-based aluminum alloy material of the present invention after being solution-treated, water-cooled and aged is preferably 150 MPa or more, particularly preferably 210 MPa or more.
以下に、実施例を示して、本発明を具体的に説明するが、本発明は、以下に示す実施例に限定されるものではない。 Hereinafter, the present invention will be specifically described with reference to examples, but the present invention is not limited to the examples shown below.
表1に示す組成を有するアルミニウム合金A~Qを溶解し、連続鋳造により直径90mmのビレット形状を造塊した。得られたビレットに、500℃で8時間の均質化処理した後、400℃で35mm×3mmのフラットバー形状に熱間押出を行った。次いで、以下の方法1及び方法2により、試験材(試験材(水冷)、試験材(空冷))を得た。得られた試験材に対し、以下の方法により、機械的性質、強度低下率(%)を評価した。結果を表2に示す。 Aluminum alloys A to Q having the compositions shown in Table 1 were melted, and a billet shape having a diameter of 90 mm was ingot by continuous casting. The obtained billet was homogenized at 500 ° C. for 8 hours, and then hot extruded into a flat bar shape of 35 mm × 3 mm at 400 ° C. Then, a test material (test material (water-cooled), test material (air-cooled)) was obtained by the following methods 1 and 2. The mechanical properties and strength reduction rate (%) of the obtained test material were evaluated by the following methods. The results are shown in Table 2.
(方法1)押出成形された試験材に、500℃で1時間の溶体化処理を行い、次いで、水冷(冷却速度:30℃/秒)により室温まで冷却した。その後、190℃で8時間の人工時効処理を施し、試験材(水冷)を得た。
(方法2)押出成形された試験材に、500℃で1時間の溶体化処理を行い、次いで、空冷(冷却速度:1℃/秒)により室温まで冷却した。その後、190℃で8時間の人工時効処理を施し、試験材(空冷)を得た。
(Method 1) The extruded test material was subjected to solution treatment at 500 ° C. for 1 hour, and then cooled to room temperature by water cooling (cooling rate: 30 ° C./sec). Then, it was subjected to artificial aging treatment at 190 ° C. for 8 hours to obtain a test material (water-cooled).
(Method 2) The extruded test material was subjected to solution treatment at 500 ° C. for 1 hour, and then cooled to room temperature by air cooling (cooling rate: 1 ° C./sec). Then, it was subjected to artificial aging treatment at 190 ° C. for 8 hours to obtain a test material (air cooling).
(機械的性質)
試験材の長さ方向中央部よりサンプルを切り出して試験片を作製し、JIS Z-2241に準拠して引張試験を行い、機械的性質を評価した。
(強度低下率の計算式)
強度低下率(%)=((試験材(水冷)の引張強度-試験材(空冷)の引張強度)/試験材(水冷)の引張強度)×100
(mechanical nature)
A sample was cut out from the central part in the length direction of the test material to prepare a test piece, and a tensile test was performed in accordance with JIS Z-2241 to evaluate the mechanical properties.
(Calculation formula for strength reduction rate)
Strength reduction rate (%) = ((tensile strength of test material (water-cooled) -tensile strength of test material (air-cooled)) / tensile strength of test material (water-cooled)) x 100
表2に示すように、実施例の合金A~Iはいずれも溶体化処理後に空冷を施しても、水冷を施した場合との強度差が小さく、優れた焼き入れ性を有しており、強度低下率が10%未満であり、合格となった。 As shown in Table 2, all of the alloys A to I of Examples have a small difference in strength from the case of water cooling even if they are air-cooled after the solution treatment, and have excellent hardenability. The strength reduction rate was less than 10%, and the result was passed.
これに対して、比較例の合金JはCu含有量が少ないため、合金LはMg含有量が少ないため、合金NはCu+Mg量が少ないため、非熱処理型合金と同程度の強度しか得られず、不合格となった。 On the other hand, since the alloy J in the comparative example has a low Cu content, the alloy L has a low Mg content, and the alloy N has a low Cu + Mg content, so that only the same strength as the non-heat-treated alloy can be obtained. , Was rejected.
また、比較例の合金KはCu含有量が多いため、合金MはMg含有量が多いため、合金OはCu+Mg量が多いために、焼き入れ性が低くなり、強度低下率が10%以上となり、不合格となった。 Further, since the alloy K in the comparative example has a high Cu content, the alloy M has a high Mg content, and the alloy O has a high Cu + Mg content, so that the hardenability is low and the strength reduction rate is 10% or more. , Was rejected.
また、比較例の合金PはMn含有量が少ないため、同程度のCu、Mg量を有する実施例の合金Bと比較して、Mn添加による強度向上効果が得られなかった。 Further, since the alloy P of the comparative example has a small Mn content, the effect of improving the strength by adding Mn could not be obtained as compared with the alloy B of the example having the same amount of Cu and Mg.
また、比較例の合金QはMn含有量が多いために、熱間の変形抵抗が上昇し、熱間押出を行うことができなかった。 Further, since the alloy Q of the comparative example has a high Mn content, the deformation resistance between heats increases, and hot extrusion cannot be performed.
Claims (2)
0.5~2.5質量%のCu、0.2~1.3質量%のMg、及び0.4~1.5質量%のMnを含有し、Siの含有量が0.25質量%以下、Feの含有量が0.25質量%以下、Crの含有量が0.10質量%以下、Znの含有量が0.10質量%以下、Tiの含有量が0.05質量%以下であり、残部Al及び不可避的不純物からなるアルミニウム合金であり、
CuとMgの含有量の合計(Cu+Mg)が1.1~3.1質量%であり、
下記式:
((Ts(水冷)-Ts(空冷))/Ts(水冷))×100
(式中、Ts(水冷)は、500℃で1時間溶体化処理後に30℃/秒の冷却速度で水冷されてから190℃で8時間時効処理された場合の引張強さを示し、Ts(空冷)は、500℃で1時間溶体化処理後に1℃/秒の冷却速度で空冷されてから190℃で8時間時効処理された場合の引張強さを示す。)
で求められる強度低下率(%)が10%未満であり、
Ts(空冷)が140MPa以上であること、
を特徴とするAl-Cu-Mg系アルミニウム合金。 It is a heat treatment type Al-Cu-Mg based aluminum alloy.
It contains 0.5 to 2.5% by mass of Cu, 0.2 to 1.3% by mass of Mg, and 0.4 to 1.5% by mass of Mn, and has a Si content of 0.25% by mass. Hereinafter, when the Fe content is 0.25% by mass or less, the Cr content is 0.10% by mass or less, the Zn content is 0.10% by mass or less, and the Ti content is 0.05% by mass or less. Yes, it is an aluminum alloy consisting of the balance Al and unavoidable impurities.
The total content of Cu and Mg (Cu + Mg) is 1.1 to 3.1% by mass.
The following formula:
((Ts (water cooling) -Ts (air cooling)) / Ts (water cooling)) x 100
(In the formula, Ts (water cooling) indicates the tensile strength when water-cooled at 500 ° C. for 1 hour , then water-cooled at a cooling rate of 30 ° C./sec, and then aged at 190 ° C. for 8 hours . (Air cooling) indicates the tensile strength when air-cooled at a cooling rate of 1 ° C./sec after solution treatment at 500 ° C. for 1 hour and then aged at 190 ° C. for 8 hours .)
The strength reduction rate (%) required in is less than 10%,
Ts (air cooling) is 140 MPa or more,
An Al—Cu—Mg-based aluminum alloy characterized by.
0.5~2.5質量%のCu、0.2~1.3質量%のMg、及び0.4~1.5質量%のMnを含有し、Siの含有量が0.25質量%以下、Feの含有量が0.25質量%以下、Crの含有量が0.10質量%以下、Znの含有量が0.10質量%以下、Tiの含有量が0.05質量%以下であり、残部Al及び不可避的不純物からなるアルミニウム合金であり、CuとMgの含有量の合計(Cu+Mg)が1.1~3.1質量%であり、下記式:
((Ts(水冷)-Ts(空冷))/Ts(水冷))×100
(式中、Ts(水冷)は、500℃で1時間溶体化処理後に30℃/秒の冷却速度で水冷されてから190℃で8時間時効処理された場合の引張強さを示し、Ts(空冷)は、500℃で1時間溶体化処理後に1℃/秒の冷却速度で空冷されてから190℃で8時間時効処理された場合の引張強さを示す。)
で求められる強度低下率(%)が10%未満であり、Ts(空冷)が140MPa以上であるAl-Cu-Mg系アルミニウム合金で構成されていることを特徴とするAl-Cu-Mg系アルミニウム合金材料。 It is a heat treatment type Al-Cu-Mg based aluminum alloy.
It contains 0.5 to 2.5% by mass of Cu, 0.2 to 1.3% by mass of Mg, and 0.4 to 1.5% by mass of Mn, and has a Si content of 0.25% by mass. Hereinafter, when the Fe content is 0.25% by mass or less, the Cr content is 0.10% by mass or less, the Zn content is 0.10% by mass or less, and the Ti content is 0.05% by mass or less. It is an aluminum alloy consisting of the balance Al and unavoidable impurities, and the total content of Cu and Mg (Cu + Mg) is 1.1 to 3.1% by mass, and the following formula:
((Ts (water cooling) -Ts (air cooling)) / Ts (water cooling)) x 100
(In the formula, Ts (water cooling) indicates the tensile strength when water-cooled at 500 ° C. for 1 hour , then water-cooled at a cooling rate of 30 ° C./sec, and then aged at 190 ° C. for 8 hours . (Air cooling) indicates the tensile strength when air-cooled at a cooling rate of 1 ° C./sec after solution treatment at 500 ° C. for 1 hour and then aged at 190 ° C. for 8 hours .)
Al—Cu—Mg-based aluminum, which is composed of an Al—Cu—Mg-based aluminum alloy having a strength reduction rate (%) obtained in 1) of less than 10% and a Ts (air cooling) of 140 MPa or more. Alloy material.
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