JP2007327115A - High-strength free-cutting aluminum alloy superior in toughness - Google Patents
High-strength free-cutting aluminum alloy superior in toughness Download PDFInfo
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本発明は、靭性に優れた高強度快削アルミニウム合金に関するものである。 The present invention relates to a high-strength free-cutting aluminum alloy having excellent toughness.
従来、切削性に優れたアルミニウム合金としては、Ａｌ−Ｃｕ系のＡ２０１１合金、Ａｌ−Ｍｇ−Ｓｉ系のＡＡ６２６２合金など、Ｐｂを添加したアルミニウム合金が使用されてきた（例えば、特許文献１参照）が、これらの合金は、１２５℃を超える温度環境において急激に靭性が低下するという問題があるとともに、近年、環境問題に配慮する観点から、Ｐｂを含まない快削アルミニウム合金が要求されるようになっており、Ａ２０１１合金の代替として、Ｐｂに代えてＳｎ、Ｂｉを添加したＡｌ−Ｃｕ合金（ＡＡ２１１１合金など）が提案され（例えば、特許文献２参照）、実用されるようになっている。 Conventionally, as an aluminum alloy excellent in machinability, an aluminum alloy to which Pb is added such as an Al-Cu-based A2011 alloy and an Al-Mg-Si-based AA6262 alloy has been used (for example, see Patent Document 1). However, these alloys have a problem that the toughness rapidly decreases in a temperature environment exceeding 125 ° C. In recent years, from the viewpoint of considering environmental problems, a free-cutting aluminum alloy containing no Pb is required. As an alternative to the A2011 alloy, an Al—Cu alloy (AA2111 alloy or the like) to which Sn and Bi are added instead of Pb has been proposed (see, for example, Patent Document 2) and is put into practical use.
上記ＡＡ２１１１合金など、Ｓｎ、Ｂｉを添加したＡｌ−Ｃｕ合金は、切削時の切粉が微細に分断し良好な切り屑処理性が得られ、強度特性においてはＡ２０１１合金に相当する引張強さ、耐力が得られるが、靭性値が高温および室温ともに低いという問題点があり、改善が要求されている。
本発明は、上記のＳｎ、Ｂｉを添加したＡｌ−Ｃｕ合金における問題点を解消するためになされたものであり、その目的は、高靭性を有するＡｌ−Ｃｕ系の高強度快削アルミニウム合金を提供することにある。 The present invention has been made to solve the problems in the Al—Cu alloys to which Sn and Bi are added, and an object of the present invention is to provide an Al—Cu-based high-strength free-cutting aluminum alloy having high toughness. It is to provide.
上記の目的を達成するための請求項１による靭性に優れた高強度快削アルミニウム合金は、Ｃｕ：４．０〜６．０％、Ｂｉ：０．１０〜２．０％、Ｐｂ：１０〜１９００ｐｐｍ、Ｆｅ：０．０４〜０．７％、Ｓｉ：０．０４〜０．４０％を含み、残部Ａｌおよび不可避不純物からなることを特徴とする。 The high-strength free-cutting aluminum alloy excellent in toughness according to claim 1 for achieving the above object is Cu: 4.0-6.0%, Bi: 0.10-2.0%, Pb: 10 It contains 1900 ppm, Fe: 0.04 to 0.7%, Si: 0.04 to 0.40%, and consists of the balance Al and inevitable impurities.
請求項２による靭性に優れた高強度快削アルミニウム合金は、Ｃｕ：４．０〜６．０％、Ｂｉ：０．１０〜２．０％、Ｓｎ：１０〜１１００ｐｐｍ、Ｆｅ：０．０４〜０．７％、Ｓｉ：０．０４〜０．４０％を含み、残部Ａｌおよび不可避不純物からなることを特徴とする。 The high-strength free-cutting aluminum alloy excellent in toughness according to claim 2 is Cu: 4.0-6.0%, Bi: 0.10-2.0%, Sn: 10-1100 ppm, Fe: 0.04- It is characterized by containing 0.7%, Si: 0.04 to 0.40%, and remaining Al and inevitable impurities.
請求項３による靭性に優れた高強度快削アルミニウム合金は、Ｃｕ：４．０〜６．０％、Ｂｉ：０．１０〜２．０％、Ｐｂ：１０〜１９００ｐｐｍ、Ｓｎ：１０〜１１００ｐｐｍ、Ｆｅ：０．０４〜０．７％、Ｓｉ：０．０４〜０．４０％を含み、残部Ａｌおよび不可避不純物からなることを特徴とする。 The high strength free-cutting aluminum alloy excellent in toughness according to claim 3 is Cu: 4.0-6.0%, Bi: 0.10-2.0%, Pb: 10-1900 ppm, Sn: 10-1100 ppm, Fe: 0.04 to 0.7%, Si: 0.04 to 0.40% are included, and the balance is Al and inevitable impurities.
請求項４による靭性に優れた高強度快削アルミニウム合金は、Ｃｕ：４．０〜６．０％、Ｂｉ：０．６０〜２．０％、Ｆｅ：０．０４〜０．７％、Ｓｉ：０．０４〜０．４０％を含み、残部Ａｌおよび不可避不純物からなることを特徴とする。 The high-strength free-cutting aluminum alloy excellent in toughness according to claim 4 is Cu: 4.0-6.0%, Bi: 0.60-2.0%, Fe: 0.04-0.7%, Si : 0.04 to 0.40%, the balance being Al and inevitable impurities.
請求項５による靭性に優れた高強度快削アルミニウム合金は、請求項１〜４のいずれかにおいて、Ｍｇ：０．０３％以上０．２０％未満、Ｍｎ：０．２０％以下、Ｃｒ：０．２０％以下、Ｔｉ：０．２０％以下、Ｚｒ：０．２０％以下のうちの1種以上を含有することを特徴とする。 The high-strength free-cutting aluminum alloy excellent in toughness according to claim 5 is any one of claims 1 to 4, wherein Mg: 0.03% or more and less than 0.20%, Mn: 0.20% or less, Cr: 0 20% or less, Ti: 0.20% or less, and Zr: 0.20% or less.
本発明によれば、引張強さ３１０ＭＰａ以上、室温でのシャルピー衝撃値３０Ｊ／ｃｍ２以上、温度２００℃でのシャルピー衝撃値２５Ｊ／ｃｍ２以上の優れた強度、靭性をそなえたＡｌ−Ｃｕ系快削アルミニウム合金が提供される。 According to the present invention, an Al-Cu system having excellent strength and toughness having a tensile strength of 310 MPa or more, a Charpy impact value of 30 J / cm 2 or more at room temperature, and a Charpy impact value of 25 J / cm 2 or more at a temperature of 200 ° C. A free-cutting aluminum alloy is provided.
本発明に係る快削アルミニウム合金における各合金成分の意義および限定理由について説明すると、Ｃｕは、合金の強度を高めるよう機能する成分であり、熱処理により強度を向上させると共に、切り屑分断性を向上させる。Ｃｕの好ましい含有量は４．０〜６．０％の範囲であり、４．０％未満では時効処理における強度上昇効果が小さく、そのため切り屑の分断性も十分でない。６．０％を超えて含有するとＣｕの過飽和量が多くなり、強度の変化はないが靭性が低下する。Ｃｕのより好ましい含有範囲は４．５〜５．５％である。 Explaining the significance and reasons for limitation of each alloy component in the free-cutting aluminum alloy according to the present invention, Cu is a component that functions to increase the strength of the alloy, improves the strength by heat treatment, and improves the chip breaking property. Let The preferable content of Cu is in the range of 4.0 to 6.0%, and if it is less than 4.0%, the effect of increasing the strength in the aging treatment is small, so that the chip breaking property is not sufficient. If the content exceeds 6.0%, the amount of supersaturation of Cu increases, and there is no change in strength, but the toughness decreases. A more preferable content range of Cu is 4.5 to 5.5%.
Ｂｉは、アルミニウムへの固溶量が極めて少ないため、アルミニウムマトリックス中に分散して存在する。Ｂｉは低融点元素であるため、切削時の加工発熱により、アルミニウムマトリックス中に分散しているＢｉの強度が低下して切欠き効果が生じ、切り屑が分断する。ＰｂあるいはＳｎをＢｉと共に複合添加する場合において、Ｂｉの好ましい含有量は０．１０〜２．０％の範囲であり、０．１０％未満では切り屑を分断する効果が少なく、２．０％を超えると合金の靭性が低下する。Ｂｉのより好ましい含有範囲は０．２０〜１．５％である。また、ＰｂあるいはＳｎを添加せずにＢｉを添加する場合のＢｉの好ましい範囲は０．６０〜２．０％であり、０．６０％未満ではその効果が少なく、２．０％を超えると靭性が低下する。この場合のＢｉのより好ましい含有範囲は０．７０〜１．６％である。 Bi is present in a state of being dispersed in the aluminum matrix because the amount of solid solution in aluminum is extremely small. Since Bi is a low melting point element, due to processing heat generated during cutting, the strength of Bi dispersed in the aluminum matrix is reduced to produce a notch effect, and chips are divided. In the case where Pb or Sn is added together with Bi, the preferred Bi content is in the range of 0.10 to 2.0%. If it is less than 0.10%, the effect of dividing chips is small, and 2.0% Exceeding this will reduce the toughness of the alloy. A more preferable range of Bi is 0.20 to 1.5%. Further, when Bi is added without adding Pb or Sn, the preferable range of Bi is 0.60 to 2.0%, and if it is less than 0.60%, the effect is small, and if it exceeds 2.0% Toughness decreases. In this case, the more preferable range of Bi is 0.70 to 1.6%.
Ｐｂは、Ｂｉと同様に低融点元素であり切り屑分断性を向上させるよう機能する。Ｐｂの好ましい含有量は１０〜１９００ｐｐｍで、１０ｐｐｍ未満では切り屑を分断させる効果が少なく、１９００ｐｐｍを超えると高温での靭性が低下する。Ｐｂのより好ましい含有範囲は２０〜１４００ｐｐｍである。 Pb is a low-melting point element like Bi and functions to improve the chip breaking property. The preferable content of Pb is 10 to 1900 ppm, and if it is less than 10 ppm, there is little effect of cutting off chips, and if it exceeds 1900 ppm, the toughness at high temperatures decreases. A more preferable content range of Pb is 20 to 1400 ppm.
Ｓｎは、Ｂｉと同様に低融点元素であり切り屑分断性を向上させるよう機能する。Ｓｎの好ましい含有量は１０〜１１００ｐｐｍの範囲であり、１０ｐｐｍ未満では切り屑を分断させる効果が少なく、１１００ｐｐｍを超えると靭性が低下する。Ｓｎのより好ましい含有範囲は２０〜５００ｐｐｍである。 Sn, like Bi, is a low melting point element and functions to improve chip separation. The preferable content of Sn is in the range of 10 to 1100 ppm. If it is less than 10 ppm, the effect of dividing the chips is small, and if it exceeds 1100 ppm, the toughness decreases. A more preferable content range of Sn is 20 to 500 ppm.
Ｓｉは、その一部がアルミニウム地金に不純物として含まれている元素であり、０．０４〜０．４％の範囲で含有させるのが好ましい。Ｓｉの含有量が０．０４％未満では、高純度のアルミニウム地金を使用する必要があるため地金コストの点で工業生産上問題である。０．４％を超えるとＡｌ−Ｓｉ−Ｆｅ系化合物が発生し易くなり靭性が低下する。 Si is an element part of which is contained as an impurity in the aluminum metal, and is preferably contained in the range of 0.04 to 0.4%. If the Si content is less than 0.04%, it is necessary to use high-purity aluminum ingots, which is a problem in industrial production in terms of ingot costs. If it exceeds 0.4%, an Al—Si—Fe-based compound is likely to be generated and the toughness is lowered.
Ｆｅは、その一部がアルミニウム地金に不純物として含まれている元素であり、０．０４〜０．７％の範囲で含有させるのが好ましい。Ｆｅの含有量が０．０４％未満では、高純度のアルミニウム地金を使用する必要があるため地金コストの点で工業生産上問題である。０．７％を超えると、Ａｌ−Ｓｉ−Ｆｅ系化合物が発生し易くなり靭性が低下する。 Fe is an element part of which is contained as an impurity in the aluminum ingot, and is preferably contained in the range of 0.04 to 0.7%. If the Fe content is less than 0.04%, it is necessary to use a high-purity aluminum ingot, which is a problem in industrial production in terms of the ingot cost. When it exceeds 0.7%, an Al—Si—Fe-based compound is easily generated and toughness is lowered.
Ｍｇは、アルミニウムマトリックス中に固溶あるいはＡｌ、Ｃｕと化合物を形成して析出し、合金の強度を高める。Ｍｇの好ましい含有量は０．０３％以上０．２０％未満の範囲であり、０．２０％以上含有するとＭｇとＢｉの化合物を形成し、低融点元素としてのアルミニウムマトリックス中の（単体）Ｂｉ量を減少させるため、切り屑分断性が低下する。Ｍｇのより好ましい含有範囲は０．０５〜０．１５％である。 Mg is dissolved in the aluminum matrix or forms a compound with Al and Cu and precipitates to increase the strength of the alloy. The preferable content of Mg is in the range of 0.03% or more and less than 0.20%. When the content is 0.20% or more, a compound of Mg and Bi is formed, and (single) Bi in the aluminum matrix as a low melting point element is formed. Since the amount is reduced, chip breaking properties are reduced. A more preferable content range of Mg is 0.05 to 0.15%.
Ｍｎ、Ｃｒ、Ｔｉ、Ｚｒは、合金の結晶粒を微細化し強度を向上するよう機能し、Ｍｎ、Ｃｒ、Ｔｉ、Ｚｒは、それぞれ単体で０．２０％以下添加することにより結晶粒の微細化が得られる。それぞれ単体で０．２０％を超えると粗大な化合物が形成し靭性が低下する。Ｍｎ、Ｃｒ、Ｔｉ、Ｚｒのより好ましい含有範囲は、Ｍｎ：０．０５〜０．１８％、Ｃｒ：０．０５〜０．１８％、Ｔｉ：０．００２〜０．０６％、Ｚｒ：０．０２〜０．２０％である。 Mn, Cr, Ti, and Zr function to refine the crystal grains of the alloy and improve the strength, and Mn, Cr, Ti, and Zr are each refined by adding 0.20% or less as a single substance. Is obtained. If each exceeds 0.20%, a coarse compound is formed and the toughness is lowered. More preferable content ranges of Mn, Cr, Ti, and Zr are: Mn: 0.05 to 0.18%, Cr: 0.05 to 0.18%, Ti: 0.002 to 0.06%, Zr: 0 0.02 to 0.20%.
本発明による快削性アルミニウム合金は、例えば、連続鋳造によりビレットに造塊し、得られたビレットを均質化処理した後、熱間押出加工を行い、溶体化処理した後、引抜き加工を施して棒状に加工し、時効処理を行うことにより製造される。 The free-cutting aluminum alloy according to the present invention is formed into a billet by continuous casting, for example, and after homogenizing the obtained billet, hot extrusion is performed, solution treatment is performed, and then drawing is performed. Manufactured by processing into a rod shape and aging treatment.
以下、本発明の実施例を比較例と対比して説明し、その効果を実証する。なお、これらの実施例は、本発明の好ましい一実施態様を説明するためのものであって、本発明はこれに限定されるものではない。 Examples of the present invention will be described below in comparison with comparative examples to demonstrate the effects. In addition, these Examples are for describing one preferable embodiment of the present invention, and the present invention is not limited thereto.
実施例１
連続鋳造により、表１に示す成分組成（Ｎｏ．０〜２１に示す組成）を有するアルミニウム合金ビレット（直径９０ｍｍ）を造塊し、得られたビレットを５００℃で８ｈ均質化処理を施した後、４５０℃の温度で熱間押出加工を行って直径２０ｍｍの押出棒を作製した。
Example 1
After agglomerating aluminum alloy billets (diameter 90 mm) having the component compositions shown in Table 1 (compositions shown in No. 0 to 21) by continuous casting and subjecting the obtained billets to a homogenization treatment at 500 ° C. for 8 hours Then, hot extrusion at a temperature of 450 ° C. was performed to produce an extruded rod having a diameter of 20 mm.
得られた押出棒について、５２０℃の温度で溶体化処理を行った後、直径１７ｍｍまで引抜き加工し、時効処理を施して試験材（Ｎｏ．０〜２１）とし、以下に示す引張試験、シャルピー衝撃試験および切削試験を行った。試験結果を表２に示す。なお、試験材Ｎｏ．０は、引抜き加工後、室温で７日間自然時効を行ってＴ３材とし、試験材Ｎｏ．１〜２１は、引抜き加工後、１６０℃で２０ｈの時効処理を行ってＴ８材とした。 The obtained extruded rod was subjected to a solution treatment at a temperature of 520 ° C., then drawn to a diameter of 17 mm, and subjected to an aging treatment to obtain a test material (No. 0 to 21). An impact test and a cutting test were performed. The test results are shown in Table 2. The test material No. No. 0 is a T3 material that is naturally aged at room temperature for 7 days after drawing. Nos. 1 to 21 were subjected to aging treatment at 160 ° C. for 20 hours after drawing and were made into T8 materials.
引張試験：ＪＩＳ Ｚ ２２０１の金属材料引張試験片４号試験片の備考２による試験片を作製し、ＪＩＳ Ｚ ２２４１に準拠して引張試験を行った。 Tensile test: A test piece according to Remark 2 of a metal material tensile test piece No. 4 test piece of JIS Z 2201 was prepared, and a tensile test was performed in accordance with JIS Z 2241.
シャルピー衝撃試験：ＪＩＳ Ｚ ２２０２の金属材料衝撃試験片Ｕノッチ試験片を作製し、ＪＩＳ Ｚ ２２４２に準拠してシャルピー衝撃試験（試験温度：室温）を行った。また、高温の靭性を測定するために、ＪＩＳ Ｚ ２２０２の金属材料衝撃試験片Ｕノッチ試験片を加熱炉内で２００℃の温度に３０分間保持した後、加熱炉から取出し、室温での保持５秒以内に、上記と同じシャルピー衝撃試験を行った。 Charpy impact test: A metal material impact test piece U-notch test piece of JIS Z 2202 was produced, and a Charpy impact test (test temperature: room temperature) was performed in accordance with JIS Z 2242. Further, in order to measure high temperature toughness, a metal material impact test piece U-notch test piece of JIS Z 2202 was held in a heating furnace at a temperature of 200 ° C. for 30 minutes, and then taken out from the heating furnace and held at room temperature. Within seconds, the same Charpy impact test was performed as above.
切削試験：直径１７ｍｍの試験材を、直径１５ｍｍまで外削して、その際に排出される切り屑の長さを測定し、切り屑の排出され易さ（切り屑処理性）で切削性を評価した。具体的には、切削時の試験材の回転数１５００ｒｐｍ、送り０．１０ｍｍ／ｒｅｖ．、切り込み深さ１ｍｍとし、バイトはスローアウェイチップ（頂角６０°正三角形チップ、逃げ角０°、一般切削用勝手付き型ブレーカ、ＰＶＤコーティング）を用い、切削油を使用しない条件で切削試験を行い、切粉の長さが全て１００ｍｍ未満の場合は切削性良好（○）、長さ１００ｍｍ以上の切粉が発生した場合は切削性不良（×）と評価した。 Cutting test: Test material with a diameter of 17 mm is cut to a diameter of 15 mm, the length of the chips discharged at that time is measured, and the machinability is determined by the ease of chip discharge (chip processing). evaluated. Specifically, the rotational speed of the test material during cutting is 1500 rpm, the feed is 0.10 mm / rev. The cutting depth is 1mm, and the cutting tool uses a throw-away tip (vertical angle 60 ° equilateral triangle tip, clearance angle 0 °, general-purpose cutting breaker, PVD coating) and does not use cutting oil. It was evaluated that when all the chips were less than 100 mm in length, good machinability (◯), and when chips with a length of 100 mm or more were generated, machinability was poor (x).
表２にみられるように、本発明に従う試験材Ｎｏ．０は、従来の鉛入り快削合金棒Ａ２０１１−Ｔ３材のＪＩＳの規格である引張強さ３１０ＭＰａ以上を満足し、切り屑は微細に分断され良好な切削性が得られた。さらに、室温でのシャルピー衝撃値は３０Ｊ／ｃｍ２以上、温度２００℃でのシャルピー衝撃値は２５Ｊ／ｃｍ２以上であり高い靭性が得られた。 As can be seen in Table 2, the test material No. 0 satisfied the tensile strength of 310 MPa or more, which is the JIS standard for the conventional lead-containing free-cutting alloy rod A2011-T3, and the chips were finely divided and good machinability was obtained. Furthermore, the Charpy impact value at room temperature was 30 J / cm 2 or more, and the Charpy impact value at a temperature of 200 ° C. was 25 J / cm 2 or more, and high toughness was obtained.
試験材Ｎｏ．１〜２１は、従来の鉛入り快削合金棒Ａ２０１１−Ｔ８材のＪＩＳの規格である引張強さ３７５ＭＰａ以上を満足し、また、切削性については、いずれも切り屑が微細に分断され良好な結果が得られた。さらに、室温でのシャルピー衝撃値は３０Ｊ／ｃｍ２以上、温度２００℃でのシャルピー衝撃値は２５Ｊ／ｃｍ２以上であり高い靭性が得られた。 Test material No. 1 to 21 satisfy the tensile strength of 375 MPa or more, which is the JIS standard for the conventional lead-containing free-cutting alloy rod A2011-T8, and the machinability is good because all chips are finely divided. Results were obtained. Furthermore, the Charpy impact value at room temperature was 30 J / cm 2 or more, and the Charpy impact value at a temperature of 200 ° C. was 25 J / cm 2 or more, and high toughness was obtained.
比較例１
連続鋳造により、表３に示す成分組成（Ｎｏ．２２〜３４に示す組成）を有するアルミニウム合金ビレット（直径９０ｍｍ）を造塊し、得られたビレットを５００℃で８ｈ均質化処理を施した後、４５０℃の温度で熱間押出加工を行って直径２０ｍｍの押出棒を作製した。得られた押出棒について、５２０℃の温度で溶体化処理を行った後、直径１７ｍｍまで引抜き加工し、１６０℃で２０ｈの時効処理を行ってＴ８材とした。なお、表３において、本発明の条件を外れたものには下線を付した。
Comparative Example 1
After ingot casting an aluminum alloy billet (diameter 90 mm) having the component composition shown in Table 3 (composition shown in No. 22 to 34) by continuous casting, and subjecting the obtained billet to a homogenization treatment at 500 ° C. for 8 hours Then, hot extrusion at a temperature of 450 ° C. was performed to produce an extruded rod having a diameter of 20 mm. The obtained extruded bar was subjected to a solution treatment at a temperature of 520 ° C., then drawn to a diameter of 17 mm, and an aging treatment at 160 ° C. for 20 hours to obtain a T8 material. In Table 3, those outside the conditions of the present invention are underlined.
得られたＴ８材を試験材として、実施例１と同様の方法で引張試験、シャルピー衝撃試験および切削試験を行った。試験結果を表４に示す。 Using the obtained T8 material as a test material, a tensile test, a Charpy impact test, and a cutting test were performed in the same manner as in Example 1. The test results are shown in Table 4.
表４に示すように、試験材Ｎｏ．２２はＣｕ含有量が少ないため引張強さが低く、切り屑もつながり易かった。Ｎｏ．２３、Ｎｏ．２５、Ｎｏ．２９、Ｎｏ．３１、Ｎｏ．３２は、それぞれＣｕ、Ｂｉ、Ｓｎ、Ｆｅ、Ｓｉの含有量が多いため、Ｎｏ．３０はＰｂとＳｎの含有量が多いため、また、Ｎｏ．３４はＣｒ、Ｍｎ、Ｔｉ、Ｚｒの含有量が多いため、室温でのシャルピー衝撃値が３０Ｊ／ｃｍ２未満、温度２００℃でのシャルピー衝撃値が２５Ｊ／ｃｍ２未満となり、靭性が劣っていた。 As shown in Table 4, the test material No. No. 22 had a low Cu content, so the tensile strength was low, and chips were easily connected. No. 23, no. 25, no. 29, no. 31, no. No. 32 has a large content of Cu, Bi, Sn, Fe, and Si, respectively. No. 30 has a high content of Pb and Sn. Since No. 34 has a large content of Cr, Mn, Ti, and Zr, the Charpy impact value at room temperature was less than 30 J / cm 2 and the Charpy impact value at a temperature of 200 ° C. was less than 25 J / cm 2 . .
試験材Ｎｏ．２４、Ｎｏ．２６、Ｎｏ．２８は、それぞれＢｉ、Ｐｂ、ＰｂとＳｎの含有量が低いため切り屑分断性が劣っていた。Ｎｏ．２７はＰｂの含有量が多いため、２００℃でのシャルピー衝撃値が低かった。Ｎｏ．３３はＭｇ含有量が多いため切り屑分断性が劣っていた。 Test material No. 24, no. 26, no. No. 28 had inferior chip breaking properties due to low contents of Bi, Pb, Pb and Sn, respectively. No. Since No. 27 has a high Pb content, the Charpy impact value at 200 ° C. was low. No. Since No. 33 had much Mg content, the chip parting property was inferior.
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| WO2011071024A1 (en) * | 2009-12-11 | 2011-06-16 | 住友電気工業株式会社 | Magnesium alloy material |
| US9103010B2 (en) | 2009-12-11 | 2015-08-11 | Sumitomo Electric Industries, Ltd. | Magnesium alloy structural member |
| US9181608B2 (en) | 2010-02-08 | 2015-11-10 | Sumitomo Electric Industries, Ltd. | Magnesium alloy sheet |
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