JP2019507248A - Age hardening type Al-Mg-Si based aluminum alloy - Google Patents

Age hardening type Al-Mg-Si based aluminum alloy Download PDF

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JP2019507248A
JP2019507248A JP2018537443A JP2018537443A JP2019507248A JP 2019507248 A JP2019507248 A JP 2019507248A JP 2018537443 A JP2018537443 A JP 2018537443A JP 2018537443 A JP2018537443 A JP 2018537443A JP 2019507248 A JP2019507248 A JP 2019507248A
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アントレコヴィッチ，ヘルムート
エーブナー，トーマス
フラグナー，ヴェルナー
カオフマン，ヘルムート
ポガチャー，シュテファン
トゾーネ，ラモーナ
ヨット． ウゴヴィッツァー，ペーター
ヨット． ウゴヴィッツァー，ペーター
ヴェリノス，マリオン
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Abstract

時効硬化型Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金について示す。リサイクルしやすく、放置安定性のある、特に人工時効硬化型のアルミニウム合金を得るために、前記アルミニウム合金が、０．６〜１重量％のマグネシウム（Ｍｇ）、０．２〜０．７重量％のケイ素（Ｓｉ）、０．１６〜０．７重量％の鉄（Ｆｅ）、０．０５〜０．４重量％の銅（Ｃｕ）、最大０．１５重量％のマンガン（Ｍｎ）、最大０．３５重量％のクロム（Ｃｒ）、最大０．２重量％のジルコン（Ｚｒ）、最大０．２５重量％の亜鉛（Ｚｎ）、最大０．１５重量％のチタン（Ｔｉ）、０．００５〜０．０７５重量％のスズ（Ｓｎ）および／またはインジウム（Ｉｎ）、ならびに残部アルミニウム、ならびに製造上不可避の不純物を含有し、このとき、Ｓｉ／Ｆｅの重量パーセント比が２．５未満であり、Ｓｉの含有量が、パラメータＡが０．１７〜０．４重量％の範囲にある下記の数式１【数１】に従って決定されることが提案される。【選択図】図２It shows about an age hardening type Al-Mg-Si type aluminum alloy. In order to obtain an aluminum alloy that is easy to recycle and is stable to stand, particularly an artificial age-hardening type aluminum alloy, the aluminum alloy contains 0.6 to 1% by weight of magnesium (Mg), 0.2 to 0.7% by weight. Silicon (Si), 0.16-0.7 wt% iron (Fe), 0.05-0.4 wt% copper (Cu), up to 0.15 wt% manganese (Mn), up to 0 .35 wt% chromium (Cr), up to 0.2 wt% zircon (Zr), up to 0.25 wt% zinc (Zn), up to 0.15 wt% titanium (Ti), 0.005- Containing 0.075 wt% tin (Sn) and / or indium (In), and the balance aluminum, as well as inevitable impurities in manufacture, wherein the weight percentage ratio of Si / Fe is less than 2.5; Si content is a parameter There is proposed to be determined according to Equation 1 Equation 1] below in the range of 0.17 to 0.4 wt%. [Selection] Figure 2

Description

本発明は時効硬化型Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金に関する。   The present invention relates to an age-hardening Al—Mg—Si-based aluminum alloy.

室温で放置することによって自然時効させたＡ６０６１（Ａｌ−Ｍｇ−Ｓｉ系）アルミニウム合金を改良するために、特許文献１は、アルミニウム合金の固溶体に空孔活性微量元素、すなわちスズ（Ｓｎ）および／またはインジウム（Ｉｎ）を添加することを提案している。   In order to improve the A6061 (Al-Mg-Si-based) aluminum alloy that has been naturally aged by being left at room temperature, Patent Document 1 discloses a vacancy-active trace element, ie, tin (Sn) and / or a solid solution of an aluminum alloy. Alternatively, it is proposed to add indium (In).

さらに、Ａ６０６１アルミニウム合金の特定の主要合金元素と副合金元素は、アルミニウム合金中のスズまたはインジウムの溶解度を低下させ、これが６０００系アルミニウム合金の室温での放置安定性に悪影響を及ぼすことが知られている（非特許文献１）。そのため、例えばＭｇ、Ｓｉ、Ｃｕ、またはＺｎの含有量が多い６０００系アルミニウム合金は溶解度を低下させ、一方、Ｆｅ、Ｔｉ、およびＭｎは溶解度を向上させるとされる。さらに、例えばＳｉとＭｇ間および／またはＣｕとＭｇ間の相互作用効果も、アルミニウム合金中のＳｎの溶解度に重要な役割を果たしている。   Furthermore, certain major alloy elements and suballoy elements of the A6061 aluminum alloy reduce the solubility of tin or indium in the aluminum alloy, which is known to adversely affect the room temperature stability of the 6000 series aluminum alloy at room temperature. (Non-Patent Document 1). Therefore, for example, a 6000 series aluminum alloy with a high content of Mg, Si, Cu, or Zn decreases the solubility, while Fe, Ti, and Mn improve the solubility. Furthermore, for example, the interaction effect between Si and Mg and / or Cu and Mg also plays an important role in the solubility of Sn in the aluminum alloy.

とはいえ、アルミニウム合金中の主要合金元素と副合金元素の含有量を任意に変化させることはできない。人工時効硬化能の望ましい高さ以外に、例えば成形性、強度、延性および／または耐食性といったその他の機械的および／または化学的要件を満たさなければならないからだ。これには、例えばアルミニウム合金中の主要合金元素を高濃度にして、特定の高温析出物を形成できるようにする必要がある。   However, the contents of the main alloy element and suballoy element in the aluminum alloy cannot be arbitrarily changed. In addition to the desired height of artificial age hardening, other mechanical and / or chemical requirements such as formability, strength, ductility and / or corrosion resistance must be met. For this purpose, for example, it is necessary to increase the concentration of the main alloy element in the aluminum alloy so that a specific high-temperature precipitate can be formed.

そのため、アルミニウム合金の組成の調整では、主要合金元素と副合金元素において、たいていは相対する分量比が必要となる。すなわち、一方で、アルミニウム合金中のＳｎの溶解度に有利で、室温での高い放置安定性を実現する分量比、他方で、アルミニウム合金の機械的および／または化学的特性値、すなわち性質に配慮しているものの、Ｓｎの溶解度にマイナスに作用することの多い分量比だ。   For this reason, adjustment of the composition of the aluminum alloy usually requires a relative proportion ratio between the main alloy element and the suballoy element. That is, on the one hand, it is advantageous for the solubility of Sn in the aluminum alloy, and on the other hand, it takes into account the mechanical and / or chemical characteristic value of the aluminum alloy, that is, the property, which realizes high standing stability at room temperature. However, it is a quantity ratio that often negatively affects the solubility of Sn.

国際公開第２０１３／１２４４７２号International Publication No. 2013/124472

Ｓｔｅｆａｎ Ｐｏｇａｔｓｃｈｅｒ ｅｔ． ａｌ， “Ｓｔａｔｉｓｔｉｃａｌ ａｎｄ ｔｈｅｒｍｏｄｙｎａｍｉｃ ｏｐｔｉｍｉｚａｔｉｏｎ ｏｆ ｔｒａｃｅ−ｅｌｅｍｅｎｔ ｍｏｄｉｆｉｅｄ Ａｌ−Ｍｇ−Ｓｉ−Ｃｕ Ａｌｌｏｙｓ”， Ｌｉｇｈｔ Ｍｅｔａｌｓ ２０１５， ｐ．２６５−２７０Stefan Pogatscher et. al, "Statistical and thermal optimization of trace-element modified Al-Mg-Si-Cu Alloys", Light Metals 2015, p. 265-270

そのため本発明の課題は、微量元素としてＳｎを含有するＡｌ−Ｍｇ−Ｓｉ系の時効硬化型アルミニウム合金の組成を変え、人工時効硬化のアルミニウム合金が、高い機械的および／または化学的性質と、室温での高い放置安定性とを兼ね備えられるようにすることである。さらに、このアルミニウム合金はとりわけ二次アルミニウムの使用に適しているとされる。   Therefore, the object of the present invention is to change the composition of an Al—Mg—Si age-hardening aluminum alloy containing Sn as a trace element, so that an artificial age-hardening aluminum alloy has high mechanical and / or chemical properties, It is to be able to combine high standing stability at room temperature. Furthermore, this aluminum alloy is particularly suitable for the use of secondary aluminum.

本発明は、アルミニウム合金が、０．６〜１重量％のマグネシウム（Ｍｇ）、０．２〜０．７重量％のケイ素（Ｓｉ）、０．１６〜０．７重量％の鉄（Ｆｅ）、０．０５〜０．４重量％の銅（Ｃｕ）、最大０．１５重量％（すなわち０〜０．１５重量％）のマンガン（Ｍｎ）、最大０．３５重量％（すなわち０〜０．３５重量％）のクロム（Ｃｒ）、最大０．２重量％（すなわち０〜０．２重量％）のジルコン（Ｚｒ）、最大０．２５重量％（すなわち０〜０．２５重量％）の亜鉛（Ｚｎ）、最大０．１５重量％（すなわち０〜０．１５重量％）のチタン（Ｔｉ）、０．００５〜０．０７５重量％のスズ（Ｓｎ）および／またはインジウム（Ｉｎ）、ならびに残部アルミニウム、ならびに製造上不可避の不純物を含有し、このとき、Ｓｉ／Ｆｅの重量パーセント比が２．５未満であり、Ｓｉの含有量が、パラメータＡが０．１７〜０．４重量％の範囲にある下記の数式１に従って決定されることによって、上記課題を解決する。   In the present invention, the aluminum alloy is composed of 0.6 to 1% by weight of magnesium (Mg), 0.2 to 0.7% by weight of silicon (Si), 0.16 to 0.7% by weight of iron (Fe). 0.05 to 0.4 weight percent copper (Cu), up to 0.15 weight percent (ie, 0 to 0.15 weight percent) manganese (Mn), up to 0.35 weight percent (ie, 0 to 0.0. 35 wt%) chromium (Cr), up to 0.2 wt% (ie 0-0.2 wt%) zircon (Zr), up to 0.25 wt% (ie 0-0.25 wt%) zinc (Zn), up to 0.15 wt% (ie 0-0.15 wt%) titanium (Ti), 0.005-0.075 wt% tin (Sn) and / or indium (In), and the balance Contains aluminum and impurities inevitable in production, and at this time, Si / F The weight percentage ratio is less than 2.5, and the content of Si is determined according to the following formula 1 in which the parameter A is in the range of 0.17 to 0.4% by weight, thereby solving the above problem. .

Ｓｉ含有量を０．２〜０．７重量％に、かつＦｅ含有量を０．１６〜０．７重量％に制限するのに加え、Ｓｉ含有量とＦｅ含有量を調整するよう規定することによって、この調整が、Ｓｉ／Ｆｅの重量パーセント比が２．５未満であることと、パラメータＡが０．１７〜０．４重量％の範囲にある下記の数式２を満足した場合に、Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金の放置安定性と人工時効硬化能に、とりわけ有利に影響を及ぼすことができる。   In addition to limiting the Si content to 0.2-0.7 wt% and the Fe content to 0.16-0.7 wt%, specify that the Si content and Fe content be adjusted Thus, when this adjustment satisfies the following formula 2 in which the weight percent ratio of Si / Fe is less than 2.5 and the parameter A is in the range of 0.17 to 0.4 wt%, Al -It can affect the standing stability and artificial age hardening ability of the Mg-Si based aluminum alloy particularly advantageously.

このようにＳｉ含有量とＦｅ含有量を厳密に調整したアルミニウム合金（そうした調整は、例えば図１の斜線部分で確認できる）は、すなわち上述の規定の上限により、アルミニウム合金の固溶体におけるスズおよび／またはインジウムの十分な溶解度を保証できる。そうすると、自然時効の際に析出挙動が遅延し、それによりアルミニウム合金の放置安定性が促進される。さらに調整の下限により、人工時効の際に十分な析出挙動を見込むことができ、それにより人工時効の際に高い強度値に達することができ、アルミニウム合金自体が、主要合金元素と副合金元素の含有量が高い６０００系アルミニウム合金で知られているような機械的性質と化学的性質を実現または改善できる。   Thus, the aluminum alloy in which the Si content and the Fe content are strictly adjusted (such adjustment can be confirmed in, for example, the hatched portion in FIG. 1), that is, the tin and / or the solid solution of the aluminum alloy by the upper limit specified above. Or sufficient solubility of indium can be guaranteed. As a result, the precipitation behavior is delayed during natural aging, thereby promoting the standing stability of the aluminum alloy. Furthermore, the lower limit of the adjustment allows sufficient precipitation behavior to be expected during artificial aging, so that high strength values can be reached during artificial aging, and the aluminum alloy itself is composed of the main alloy elements and suballoy elements. Mechanical and chemical properties such as are known for high content 6000 series aluminum alloys can be realized or improved.

しかしながら驚いたことに、この規定を用いると、自然時効硬化を抑制するためにＳｎを含有する既知の６０００系アルミニウム合金と比べて、室温で何倍も遅延した析出挙動が観察できることがわかった。確かに、Ｓｉ含有量が比較的少ないと、自然時効硬化の遅延を引き起こせることは知られているが、本発明に従ってＳｉ含有量を調整すると、この既知の効果をはるかに越え、アルミニウム合金は並外れて高い放置安定性を示す。   Surprisingly, however, it was found that when this rule is used, precipitation behavior delayed many times at room temperature can be observed as compared to known 6000 series aluminum alloys containing Sn in order to suppress spontaneous age hardening. Certainly, it is known that a relatively low Si content can cause a delay in natural age hardening, but adjusting the Si content according to the present invention far exceeds this known effect, and aluminum alloys It shows exceptionally high storage stability.

そのため本発明に従って、室温における放置安定性がとりわけ高く、人工時効硬化能に優れているというアルミニウム合金の利点を組み合わせることができる。   Therefore, according to the present invention, it is possible to combine the advantages of the aluminum alloy that the standing stability at room temperature is particularly high and the artificial age hardening ability is excellent.

さらに本発明によるこの組成は、Ｆｅ含有量が比較的多いことから、これについての二次アルミニウムの使用にもとりわけ適している可能性がある。   Furthermore, this composition according to the invention may be particularly suitable for the use of secondary aluminum for this because of the relatively high Fe content.

一般に、Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金には、それぞれ最大０．０５重量％、合わせて多くとも０．１５重量％の不純物が存在する可能性があると言及される。さらに一般に、例えばＭｎ、Ｃｒ、Ｚｒ、Ｚｎ、またはチタンで見られる最大重量％の指示は、０から始まると見なすことができると言及される。   In general, it is mentioned that Al-Mg-Si-based aluminum alloys may each contain up to 0.05% by weight of impurities, and at most 0.15% by weight in total. More generally, it is mentioned that the indication of the maximum weight percent found, for example, in Mn, Cr, Zr, Zn, or titanium can be regarded as starting from zero.

さらに完全を期すために、アルミニウムスクラップから得られたアルミニウムまたはアルミニウム合金は、二次アルミニウムと理解することができると言及される。   For the sake of completeness, it is mentioned that the aluminum or aluminum alloy obtained from aluminum scrap can be understood as secondary aluminum.

アルミニウム合金の放置安定性と人工時効硬化能は、パラメータＡが０．２６〜０．３４重量％の範囲にある場合、さらに改善することができる。この規定により、すなわちＳｎの溶解度が比較的大きくなり、Ｓｉが、自然時効硬化にわずかな影響しか及ぼさないようにできる。それにより、室温において予想外に高い安定性を実現することができる。さらに、このように調整された合金は、この合金のＳｉ含有量が比較的低いにもかかわらず、（例えば高温保持による）人工時効硬化後に、驚くほど高い強度に達することができる。   The standing stability and artificial age hardening ability of the aluminum alloy can be further improved when the parameter A is in the range of 0.26 to 0.34% by weight. This definition, that is, the solubility of Sn is relatively large, so that Si has a slight effect on natural age hardening. Thereby, unexpectedly high stability can be realized at room temperature. Furthermore, alloys prepared in this way can reach surprisingly high strength after artificial age hardening (eg by holding at elevated temperatures), despite the relatively low Si content of the alloy.

パラメータＡが０．３重量％であるとき、最適な放置安定性と人工時効硬化能を示すことができる。   When the parameter A is 0.3% by weight, optimum standing stability and artificial age-hardening ability can be shown.

下記の数式３に従ってＳｉの含有量を決定すれば、Ｓｎの溶解度に影響を与える成分をさらに改善して互いに調整することができる。具体的には、ＴｉはＳｉと相を形成することができ、これがＳｎの溶解度によい影響を及ぼすことができる。それにより、アルミニウム合金の放置安定性がさらに改善できる。   If the Si content is determined according to the following Equation 3, the components affecting the solubility of Sn can be further improved and adjusted to each other. Specifically, Ti can form a phase with Si, which can positively affect the solubility of Sn. Thereby, the standing stability of the aluminum alloy can be further improved.

Ｓｉ／Ｆｅの重量パーセント比が２未満であれば、ＦｅによってＳｉの凝固が進むことにより、アルミニウム合金中の溶解Ｓｉの含有量を大幅に減少させることができる。それにより、Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金の固溶体におけるスズおよび／またはインジウムの溶解度を向上させることができ、放置安定性をさらに高めることができる。   If the weight percent ratio of Si / Fe is less than 2, solidification of Si proceeds by Fe, so that the content of dissolved Si in the aluminum alloy can be greatly reduced. Thereby, the solubility of tin and / or indium in the solid solution of the Al—Mg—Si based aluminum alloy can be improved, and the standing stability can be further enhanced.

Ｓｉ／Ｍｇの重量パーセント比が０．３〜０．９の範囲内にあるとき、Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金の固溶体におけるスズおよび／またはインジウムの溶解度を比較的高くすることができる。   When the weight percentage ratio of Si / Mg is in the range of 0.3 to 0.9, the solubility of tin and / or indium in the solid solution of the Al—Mg—Si based aluminum alloy can be made relatively high.

アルミニウム合金が少なくとも０．２５重量％の銅（Ｃｕ）を含有する場合、Ｃｕの含有量がこのように比較的高いことにより、Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金の固溶体におけるＳｎの溶解度に対するＭｇおよびＳｉの悪影響が相殺的に干渉され得る。   When the aluminum alloy contains at least 0.25 wt% copper (Cu), the relatively high Cu content results in Mg and Sn relative to the solubility of Sn in the solid solution of the Al-Mg-Si based aluminum alloy. The adverse effects of Si can be counterbalanced.

アルミニウム合金がアルミニウム混晶の固溶体中に０．００５〜０．０５重量％の範囲でスズ（Ｓｎ）を含有する場合、アルミニウム合金の優れた放置安定性を得ることができる。一般に、「固溶体」という用語は、合金元素が固体マトリックス中に分散している状態を指すことができると言及される。   When the aluminum alloy contains tin (Sn) in the aluminum mixed crystal solid solution in the range of 0.005 to 0.05% by weight, excellent standing stability of the aluminum alloy can be obtained. In general, the term “solid solution” is mentioned to be able to refer to a state in which alloying elements are dispersed in a solid matrix.

好ましくは、アルミニウム合金は６０００系に属する。好ましくは、アルミニウム合金はＥＮ ＡＷ−６０６１アルミニウム合金である。   Preferably, the aluminum alloy belongs to the 6000 series. Preferably, the aluminum alloy is EN AW-6061 aluminum alloy.

アルミニウム合金が最大０．０５重量％のクロム（Ｃｒ）と０．０５重量％超のジルコン（Ｚｒ）を含有する場合、Ｓｎの焼入れ感受性を低下させ、比較的遅い焼入れ速度でも、Ｓｎをアルミニウム混晶の固溶体中に保持することができる。さらにそれにより、厚板でも、最適な放置安定性と人工時効硬化能を得ることができる。   If the aluminum alloy contains up to 0.05 wt% chromium (Cr) and more than 0.05 wt% zircon (Zr), it reduces the Sn susceptibility to quenching, even at relatively slow quenching rates. It can be held in a solid solution of crystals. In addition, even with a thick plate, optimum standing stability and artificial age hardening can be obtained.

アルミニウム合金は、場合によっては腐食挙動を改善するために、少なくとも０．０２重量％のクロム（Ｃｒ）を含有することができる。   The aluminum alloy can optionally contain at least 0.02 wt% chromium (Cr) to improve the corrosion behavior.

アルミニウム合金中のＳｉとＦｅの含有量を示す表である。It is a table | surface which shows content of Si and Fe in an aluminum alloy. アルミニウム合金の放置期間［ｄ］とブリネル硬さ［ＨＢＷ］を示す表である。It is a table | surface which shows the leaving period [d] and Brinell hardness [HBW] of an aluminum alloy. アルミニウム合金の人工時効温度［℃］とブリネル硬さ［ＨＢＷ］を示す表である。It is a table | surface which shows the artificial aging temperature [degreeC] and Brinell hardness [HBW] of an aluminum alloy.

得られた効果を証明するために、さまざまなＡｌ−Ｍｇ−Ｓｉ系（６０００系）アルミニウム合金からなる薄板を作製した。試験した合金の組成を表１に示す。   In order to prove the obtained effect, thin plates made of various Al—Mg—Si (6000) aluminum alloys were produced. The composition of the tested alloys is shown in Table 1.

表１のアルミニウム合金１は、基本的に微量元素Ｓｎを添加した後の標準合金ＡＡ６０６１に相当し、スズの代わりに、インジウムまたはＳｎとＩｎとの組み合わせを使用することが考えられる。合金２は６０００系の本発明による組成物であり、Ｆｅ含有量が比較的高いため、比較的リサイクルしやすい。   The aluminum alloy 1 in Table 1 basically corresponds to the standard alloy AA6061 after adding the trace element Sn, and it is conceivable to use indium or a combination of Sn and In instead of tin. Alloy 2 is a 6000-based composition according to the present invention and is relatively easy to recycle because of its relatively high Fe content.

アルミニウム合金１は、本発明に従って調整されたＳｉ／Ｆｅ含有量から明らかに外れており、これは例えば図１で確認することができる。アルミニウム合金２は、この調整されたＳｉ／Ｆｅ含有量のほぼ中央に位置している。   The aluminum alloy 1 is clearly deviated from the Si / Fe content adjusted according to the present invention, which can be confirmed, for example, in FIG. The aluminum alloy 2 is located approximately at the center of the adjusted Si / Fe content.

アルミニウム合金１と２の両方を、溶体化熱処理によって固溶化し、焼入れしたのち、室温で時効することで自然時効硬化処理を、次いで人工時効硬化処理を行った。溶体化熱処理は５３０℃超の温度で、焼入れは２０℃／秒超の焼入れ速度で行った。合金１と２の両方に、１８０日間［ｄ］の放置期間、すなわち自然時効硬化処理と、さまざまな温度での３０分間の人工時効硬化処理を実施した。自然時効硬化処理中、または人工時効硬化処理後にブリネル硬さ［ＨＢＷ］を測定した。   Both aluminum alloys 1 and 2 were solid-solubilized by solution heat treatment, quenched, and then subjected to natural age hardening treatment by aging at room temperature, and then artificial age hardening treatment. The solution heat treatment was performed at a temperature exceeding 530 ° C., and the quenching was performed at a quenching rate exceeding 20 ° C./second. Both alloys 1 and 2 were subjected to a standing period of 180 days [d], that is, a natural age hardening treatment and an artificial age hardening treatment for 30 minutes at various temperatures. Brinell hardness [HBW] was measured during the natural age hardening treatment or after the artificial age hardening treatment.

放置安定性については、室温での放置で、合金１がすでに１４日後に比較的激しく時効硬化していることが図２で確認できる。これは、長い放置期間にわたって見てみると、不利なことに、ブリネル硬さが比較的高く上昇していることになり、かつ人工時効硬化前に変形に成形に不利に作用する。   With respect to the standing stability, it can be confirmed in FIG. 2 that the alloy 1 has been relatively hardened by aging after 14 days after standing at room temperature. This has the disadvantage that the Brinell hardness has risen relatively high when viewed over a long standing period and adversely affects the deformation before the artificial age hardening.

それとは対照的に、合金２では、およそ１８０日後にようやく自然時効硬化が始まっていることが明確になり、それにより本発明による合金２は、とりわけ放置安定性があると考えられる。このような驚くほど高い放置安定性は、これまで６０００系合金ではまだ観察されていなかった。これは、焼入れ後の柔らかい状態における合金の処理時間に、想定外の著しい効用をもたらす。   In contrast, it becomes clear that alloy 2 finally begins spontaneous age hardening after approximately 180 days, so that alloy 2 according to the present invention is considered to be particularly stable. Such a surprisingly high storage stability has not been observed so far for 6000 series alloys. This results in an unexpected significant utility in the processing time of the alloy in the soft state after quenching.

それに続く人工時効硬化では、図３で２つの合金を比較すると、合金２は低めの時効温度では、ブリネル硬さにおいてさしあたり合金１に遅れを取っていることが確認できる。時効温度が高くなると、合金１のブリネル硬さを明らかに超えることができる。   In the subsequent artificial age hardening, when the two alloys are compared in FIG. 3, it can be confirmed that the alloy 2 is delayed from the alloy 1 for the time being in the Brinell hardness at a lower aging temperature. As the aging temperature increases, the Brinell hardness of Alloy 1 can be clearly exceeded.

Claims (11)

時効硬化型Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金であって、
０．６〜１重量％のマグネシウム（Ｍｇ）、
０．２〜０．７重量％のケイ素（Ｓｉ）、
０．１６〜０．７重量％の鉄（Ｆｅ）、
０．０５〜０．４重量％の銅（Ｃｕ）、
最大０．１５重量％のマンガン（Ｍｎ）、
最大０．３５重量％のクロム（Ｃｒ）、
最大０．２重量％のジルコン（Ｚｒ）、
最大０．２５重量％の亜鉛（Ｚｎ）、
最大０．１５重量％のチタン（Ｔｉ）、
０．００５〜０．０７５重量％のスズ（Ｓｎ）および／またはインジウム（Ｉｎ）、
ならびに残部アルミニウム、ならびに製造上不可避の不純物を含有し、このとき、
Ｓｉ／Ｆｅの重量パーセント比が２．５未満であり、
Ｓｉの含有量が、パラメータＡが０．１７〜０．４重量％の範囲にある下記の数式１
に従って決定されるアルミニウム合金。 Age-hardening Al-Mg-Si-based aluminum alloy,
0.6-1 wt% magnesium (Mg),
0.2-0.7 wt% silicon (Si),
0.16 to 0.7% by weight of iron (Fe),
0.05 to 0.4% by weight of copper (Cu),
Up to 0.15 wt% manganese (Mn),
Up to 0.35 wt% chromium (Cr),
Up to 0.2% by weight of zircon (Zr),
Up to 0.25 wt% zinc (Zn),
Up to 0.15 wt% titanium (Ti),
0.005 to 0.075 wt% tin (Sn) and / or indium (In),
As well as the balance aluminum, and impurities inevitable in production,
The weight percent ratio of Si / Fe is less than 2.5;
The following formula 1 in which the Si content is such that the parameter A is in the range of 0.17 to 0.4 wt%
Aluminum alloy determined according to. 前記パラメータＡが０．２６〜０．３４重量％の範囲にあることを特徴とする、請求項１に記載のアルミニウム合金。   The aluminum alloy according to claim 1, wherein the parameter A is in the range of 0.26 to 0.34 wt%. 前記パラメータＡが０．３重量％である、請求項１または２に記載のアルミニウム合金。   The aluminum alloy according to claim 1 or 2, wherein the parameter A is 0.3% by weight. Ｓｉの含有量が、下記の数式２
に従って決定されることを特徴とする、請求項１〜３のうちいずれか一項に記載のアルミニウム合金。 The content of Si is the following formula 2
The aluminum alloy according to claim 1, wherein the aluminum alloy is determined according to claim 1. Ｓｉ／Ｆｅの重量パーセント比が２未満であることを特徴とする、請求項１〜４のうちいずれか一項に記載のアルミニウム合金。   The aluminum alloy according to claim 1, wherein the weight percentage ratio of Si / Fe is less than 2. 5. Ｓｉ／Ｍｇの重量パーセント比が０．３〜０．９の範囲にあることを特徴とする、請求項１〜５のうちいずれか一項に記載のアルミニウム合金。   The aluminum alloy according to any one of claims 1 to 5, characterized in that the weight percentage ratio of Si / Mg is in the range of 0.3 to 0.9. 前記アルミニウム合金が、少なくとも０．２５重量％の銅（Ｃｕ）を含有することを特徴とする、請求項１〜６のうちいずれか一項に記載のアルミニウム合金。   The aluminum alloy according to claim 1, wherein the aluminum alloy contains at least 0.25% by weight of copper (Cu). 前記アルミニウム合金が、アルミニウム混晶の固溶体中に０．００５〜０．０５重量％の範囲でスズ（Ｓｎ）を含有することを特徴とする、請求項１〜７のうちいずれか一項に記載のアルミニウム合金。   The said aluminum alloy contains tin (Sn) in the range of 0.005-0.05 weight% in the solid solution of an aluminum mixed crystal, It is any one of Claims 1-7 characterized by the above-mentioned. Aluminum alloy. 前記アルミニウム合金が６０００系に属することを特徴とする、請求項１〜８のうちいずれか一項に記載のアルミニウム合金。   The aluminum alloy according to any one of claims 1 to 8, wherein the aluminum alloy belongs to the 6000 series. 前記アルミニウム合金が、最大０．０５重量％のクロム（Ｃｒ）と０．０５重量％超のジルコン（Ｚｒ）を含有することを特徴とする、請求項１〜９のうちいずれか一項に記載のアルミニウム合金。   10. The aluminum alloy according to any one of claims 1 to 9, characterized in that it contains up to 0.05 wt% chromium (Cr) and more than 0.05 wt% zircon (Zr). Aluminum alloy. 前記アルミニウム合金が少なくとも０．０２重量％のクロム（Ｃｒ）を含有することを特徴とする、請求項１〜１０のうちいずれか一項に記載のアルミニウム合金。   The aluminum alloy according to any one of claims 1 to 10, characterized in that the aluminum alloy contains at least 0.02 wt% chromium (Cr).
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