JP2020007594A - Aluminum alloy material, manufacturing method of aluminum alloy cast material, and manufacturing method of aluminum alloy powder extrusion material - Google Patents
Aluminum alloy material, manufacturing method of aluminum alloy cast material, and manufacturing method of aluminum alloy powder extrusion material Download PDFInfo
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本発明は、高温における機械特性に優れたアルミニウム合金材、高温における機械特性に優れたアルミニウム合金鋳造材の製造方法、高温における機械特性に優れたアルミニウム合金粉末押出材の製造方法に関する。 The present invention relates to an aluminum alloy material having excellent mechanical properties at high temperature, a method for producing an aluminum alloy cast material having excellent mechanical properties at high temperature, and a method for producing an aluminum alloy powder extruded material having excellent mechanical properties at high temperature.
なお、本明細書および特許請求の範囲において、「示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度」とは、示差走査熱量曲線において４００℃以上の領域に複数個の発熱ピークが存在する場合には、これら複数個の発熱ピーク開始温度のうち、最も温度が低い発熱ピーク開始温度を意味するものとする。 In the present specification and the claims, "the exothermic peak onset temperature derived from the differential scanning calorimetric curve and the exothermic peak onset temperature of 400 ° C or higher" refers to the region of 400 ° C or higher in the differential scanning caloric curve. When a plurality of exothermic peaks are present, it means the lowest exothermic peak start temperature among the plurality of exothermic peak start temperatures.
四輪自動車、二輪自動車等の車両（以下、単に「自動車」という）に搭載される内燃機関では、内燃機関の軽量化による燃焼効率、出力等の向上を図るために、例えば、アルミニウム合金製のピストンが用いられる。特許文献１〜３には、アルミニウム合金製のピストン等のアルミニウム合金成形品の製造方法が開示されている。このような用途に用いられるアルミニウム合金には高温において高強度であることが要求される。高温で高強度を有するアルミニウム合金として、特許文献４には、重量％で、Ｓｉ：１０．０〜１４．０％、Ｃｕ：３．０〜６．０％、Ｍｇ：０．１〜１．０％、Ｆｅ：０．６〜１．８％、Ｎｉ：０．８〜３．０％、Ｍｎ：０．１〜０．７％、Ｔｉ：０．１〜０．７％、Ｚｒ：０．０５〜０．３％、Ｖ：０．０５〜０．５％を含有し、残部がＡｌおよび不可避不純物からなるアルミニウム合金が記載され、特許文献５には、Ｓｉ：１１．０〜１３．０質量％，Ｎｉ：４．５〜６．０質量％，Ｃｕ：３．５〜４．５質量％，Ｍｇ：０．８〜１．２質量％，Ｆｅ：０．２〜０．６５質量％，Ｍｎ：０．１０〜０．４０質量％、Ｐ：０．００３〜０．０１５質量％及びＣａ：０．００２質量％以下を含み、残部が実質的にＡｌからなり、含有ＦｅとＮｉの間でＦｅ≦−０．２５Ｎｉ＋１．７５の関係を満たすとともに、晶出物の平均粒径が５μｍ以下であるアルミニウム合金が提案されている。 BACKGROUND ART In an internal combustion engine mounted on a vehicle such as a four-wheeled vehicle or a two-wheeled vehicle (hereinafter simply referred to as an “automobile”), in order to improve combustion efficiency and output by reducing the weight of the internal combustion engine, for example, an aluminum alloy is used. A piston is used. Patent Literatures 1 to 3 disclose a method for manufacturing an aluminum alloy molded product such as an aluminum alloy piston. Aluminum alloys used for such applications are required to have high strength at high temperatures. Patent Document 4 discloses, as an aluminum alloy having high strength at a high temperature, Si: 10.0 to 14.0%, Cu: 3.0 to 6.0%, and Mg: 0.1 to 1. 0%, Fe: 0.6 to 1.8%, Ni: 0.8 to 3.0%, Mn: 0.1 to 0.7%, Ti: 0.1 to 0.7%, Zr: 0 An aluminum alloy containing 0.05 to 0.3%, V: 0.05 to 0.5%, and the balance consisting of Al and unavoidable impurities is described. 0 mass%, Ni: 4.5 to 6.0 mass%, Cu: 3.5 to 4.5 mass%, Mg: 0.8 to 1.2 mass%, Fe: 0.2 to 0.65 mass %, Mn: 0.10 to 0.40% by mass, P: 0.003 to 0.015% by mass, and Ca: 0.002% by mass or less, and the balance substantially consists of Al. i fulfills the relationship Fe ≦ -0.25Ni + 1.75 between the average particle size of the crystallized substances of aluminum alloys have been proposed is 5μm or less.
近年、内燃機関の燃焼効率、出力等について更なる向上を図るため、ピストン等の内燃機関の部品の材料に用いられるアルミニウム合金として、より一層高い温度において高強度を備えていることが求められるようになっている。具体的には、３００℃の高温度でも高強度を備えていることが要求されるようになってきている。これに対し、上記特許文献４に記載されたアルミニウム合金では、１５０℃の高温で高強度を有したものであり、上記特許文献５に記載されたアルミニウム合金では、２５０℃の高温で高強度を有したものである。 In recent years, in order to further improve the combustion efficiency, output, and the like of an internal combustion engine, it is required that an aluminum alloy used as a material of components of the internal combustion engine such as a piston has high strength at a higher temperature. It has become. Specifically, it has been required to have high strength even at a high temperature of 300 ° C. On the other hand, the aluminum alloy described in Patent Document 4 has high strength at a high temperature of 150 ° C., and the aluminum alloy described in Patent Document 5 has high strength at a high temperature of 250 ° C. It had.
本発明は、かかる技術的背景に鑑みてなされたものであって、３００℃の高温でも優れた機械特性を備えたアルミニウム合金材、３００℃の高温でも優れた機械特性を備えたアルミニウム合金鋳造材の製造方法、および３００℃の高温でも優れた機械特性を備えたアルミニウム合金粉末押出材の製造方法を提供することを目的とする。 The present invention has been made in view of such technical background, and is an aluminum alloy material having excellent mechanical properties even at a high temperature of 300 ° C., and an aluminum alloy cast material having excellent mechanical properties even at a high temperature of 300 ° C. It is an object of the present invention to provide a method for producing an aluminum alloy powder extruded material having excellent mechanical properties even at a high temperature of 300 ° C.
前記目的を達成するために、本発明は以下の手段を提供する。 In order to achieve the above object, the present invention provides the following means.
［１］Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなるアルミニウム合金材であって、
前記アルミニウム合金材についてのＸ線回折測定で得られるＸ線回折パターンにおけるＡｌ6Ｆｅ相の回折ピークの積分強度を「Ｑ1」（ｃｐｓ・ｄｅｇ）とし、Ａｌ相の（２００）面の回折ピークの積分強度を「Ｑ2」（ｃｐｓ・ｄｅｇ）としたとき、Ｑ1／Ｑ2の値が０．００６以下であることを特徴とするアルミニウム合金材。
[1] An aluminum alloy material containing Fe: 0.5% by mass to 8.0% by mass, Ti: 0.05% by mass to 2.0% by mass, and the balance being Al and unavoidable impurities,
The integrated intensity of the Al 6 Fe phase diffraction peak in the X-ray diffraction pattern obtained by the X-ray diffraction measurement of the aluminum alloy material is defined as “Q 1 ” (cps · deg), and the diffraction peak of the (200) plane of the Al phase. An aluminum alloy material, wherein the value of Q 1 / Q 2 is 0.006 or less, when the integrated intensity of the above is “Q 2 ” (cps · deg).
［２］前記アルミニウム合金は、さらに、Ｃｕ、Ｍｇ、Ｚｒ、Ｖ、Ｗ、Ｃｒ、Ｃｏ、Ｍｏ、Ｔａ、Ｈｆ、Ｎｂ、Ｎｉ、ＭｎおよびＣｅからなる群より選ばれる１種または２種以上の元素を、それぞれ０．０１質量％〜５．０質量％含有する前項１に記載のアルミニウム合金材。 [2] The aluminum alloy further comprises one or more members selected from the group consisting of Cu, Mg, Zr, V, W, Cr, Co, Mo, Ta, Hf, Nb, Ni, Mn and Ce. 2. The aluminum alloy material as described in the above item 1, wherein each of the elements contains 0.01% by mass to 5.0% by mass.
［３］前記アルミニウム合金は、さらに、Ｂを０．０００１質量％〜０．０３質量％含む前項１または２に記載のアルミニウム合金材。 [3] The aluminum alloy material according to the above 1 or 2, wherein the aluminum alloy further contains B in an amount of 0.0001% by mass to 0.03% by mass.
［４］前記アルミニウム合金材中にＡｌ−Ｆｅ系金属間化合物を含有し、前記アルミニウム合金材の断面組織構造において前記Ａｌ−Ｆｅ系金属間化合物の平均円相当直径が０．１μｍ〜３．０μｍの範囲である前項１〜３のいずれか１項に記載のアルミニウム合金材。 [4] The aluminum alloy material contains an Al-Fe intermetallic compound, and in the cross-sectional structure structure of the aluminum alloy material, the average circle equivalent diameter of the Al-Fe intermetallic compound is 0.1 µm to 3.0 µm. 4. The aluminum alloy material according to any one of the preceding items 1 to 3, which is in the range described above.
［５］Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなるアルミニウム合金の溶湯を得る溶湯形成工程と、
前記得られた溶湯を鋳造加工することによって鋳造材を得る鋳造工程と、
前記アルミニウム合金の示差走査熱量測定で得られる示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度を「Ｘ」（℃）としたとき、前記得られた鋳造材を２００℃〜Ｘ℃の範囲の温度で熱処理を行う熱処理工程と、を含むことを特徴とするアルミニウム合金鋳造材の製造方法。
[5] Molten metal formation containing 0.5% to 8.0% by mass of Fe and 0.05% to 2.0% by mass of Ti, with the balance being Al and unavoidable impurities. Process and
A casting step of obtaining a casting material by casting the obtained molten metal,
Assuming that an exothermic peak onset temperature derived from a differential scanning calorimetry curve obtained by differential scanning calorimetry of the aluminum alloy and which is 400 ° C. or higher is “X” (° C.), the obtained cast material is obtained. A heat treatment step of performing a heat treatment at a temperature in the range of 200 ° C to X ° C.
［６］前記アルミニウム合金溶湯は、さらに、Ｃｕ、Ｍｇ、Ｚｒ、Ｖ、Ｗ、Ｃｒ、Ｃｏ、Ｍｏ、Ｔａ、Ｈｆ、Ｎｂ、Ｎｉ、ＭｎおよびＣｅからなる群より選ばれる１種または２種以上の元素を、それぞれ０．０１質量％〜５．０質量％含有する前項５に記載のアルミニウム合金鋳造材の製造方法。 [6] The molten aluminum alloy further comprises one or more members selected from the group consisting of Cu, Mg, Zr, V, W, Cr, Co, Mo, Ta, Hf, Nb, Ni, Mn and Ce. 6. The method for producing an aluminum alloy cast material according to the above item 5, wherein the element is contained in an amount of 0.01% by mass to 5.0% by mass, respectively.
［７］前記アルミニウム合金溶湯は、さらに、さらに、Ｂを０．０００１質量％〜０．０３質量％含む前項５または６に記載のアルミニウム合金鋳造材の製造方法。 [7] The method for producing an aluminum alloy casting according to the above item 5 or 6, wherein the molten aluminum alloy further contains B in an amount of 0.0001% by mass to 0.03% by mass.
［８］Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなるアルミニウム合金粉末を圧縮成形して圧粉体を得る圧縮成形工程と、
前記アルミニウム合金粉末の示差走査熱量測定で得られる示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度を「Ｘ」（℃）としたとき、前記得られた圧粉体を２００℃〜Ｘ℃の範囲の温度で熱間押出しして押出材を得る押出工程と、
前記押出材を２００℃〜Ｘ℃の範囲の温度で熱処理を行う熱処理工程と、を含むことを特徴とするアルミニウム合金粉末押出材の製造方法。
[8] An aluminum alloy powder containing 0.5% to 8.0% by mass of Fe and 0.05% to 2.0% by mass of Ti and the balance of Al and inevitable impurities is compression-molded. A compression molding step of obtaining a green compact,
When an exothermic peak onset temperature derived from a differential scanning calorimetry curve obtained by differential scanning calorimetry of the aluminum alloy powder and which is 400 ° C. or more is defined as “X” (° C.), the obtained pressure is An extrusion step of hot extruding the powder at a temperature in the range of 200 ° C to X ° C to obtain an extruded material;
A method of heat-treating the extruded material at a temperature in the range of 200 ° C to X ° C.
［９］前記アルミニウム合金は、さらに、Ｃｕ、Ｍｇ、Ｚｒ、Ｖ、Ｗ、Ｃｒ、Ｃｏ、Ｍｏ、Ｔａ、Ｈｆ、Ｎｂ、Ｎｉ、ＭｎおよびＣｅからなる群より選ばれる１種または２種以上の元素を、それぞれ０．０１質量％〜５．０質量％含有する前項８に記載のアルミニウム合金粉末押出材の製造方法。 [9] The aluminum alloy further comprises one or more members selected from the group consisting of Cu, Mg, Zr, V, W, Cr, Co, Mo, Ta, Hf, Nb, Ni, Mn and Ce. 9. The method for producing an aluminum alloy powder extruded material according to item 8, wherein each of the elements contains 0.01% by mass to 5.0% by mass.
［１０］前記アルミニウム合金は、さらに、さらに、Ｂを０．０００１質量％〜０．０３質量％含む前項８または９に記載のアルミニウム合金粉末押出材の製造方法。 [10] The method for producing an aluminum alloy powder extruded material according to the above item 8 or 9, wherein the aluminum alloy further contains B in an amount of 0.0001% by mass to 0.03% by mass.
［１］の発明では、高温における機械特性に優れたアルミニウム合金材（鋳造材、押出材等）が提供される。 According to the invention [1], an aluminum alloy material (cast material, extruded material, etc.) having excellent mechanical properties at high temperatures is provided.
［２］の発明では、高温における機械特性をより向上させたアルミニウム合金材を提供できる。 According to the invention as recited in the aforementioned Item [2], an aluminum alloy material with further improved mechanical properties at high temperatures can be provided.
［３］の発明では、高温における機械特性をより一層向上させたアルミニウム合金材を提供できる。 According to the invention as recited in the aforementioned Item [3], an aluminum alloy material having further improved mechanical properties at high temperatures can be provided.
［４］の発明では、高温における機械特性をさらに向上させたアルミニウム合金材を提供できる。 According to the invention as recited in the aforementioned Item [4], an aluminum alloy material with further improved mechanical properties at high temperatures can be provided.
［５］の発明では、前記［１］の発明の構成を備えていて、高温における機械特性に優れたアルミニウム合金鋳造材を製造できる。 According to the invention as recited in the aforementioned Item [5], it is possible to manufacture an aluminum alloy casting having excellent mechanical properties at a high temperature, having the configuration of the invention as described in the above [1].
［６］の発明では、高温における機械特性をより向上させたアルミニウム合金鋳造材を製造できる。 According to the invention as recited in the aforementioned Item [6], it is possible to manufacture an aluminum alloy casting having improved mechanical properties at high temperatures.
［７］の発明では、高温における機械特性をより一層向上させたアルミニウム合金鋳造材を製造できる。 According to the invention as recited in the aforementioned Item [7], it is possible to manufacture an aluminum alloy casting having further improved mechanical properties at high temperatures.
［８］の発明では、前記［１］の発明の構成を備えていて、高温における機械特性に優れたアルミニウム合金粉末押出材を製造できる。 According to the invention as recited in the aforementioned Item [8], it is possible to manufacture an extruded aluminum alloy powder excellent in mechanical properties at high temperatures, having the configuration of the invention as described in the aforementioned [1].
［９］の発明では、高温における機械特性をより向上させたアルミニウム合金粉末押出材を製造できる。 According to the invention as recited in the aforementioned Item [9], an aluminum alloy powder extruded material having further improved mechanical properties at high temperatures can be produced.
［１０］の発明では、高温における機械特性をより一層向上させたアルミニウム合金粉末押出材を製造できる。 According to the invention as recited in the aforementioned Item [10], an extruded aluminum alloy powder having further improved mechanical properties at high temperatures can be produced.
本発明に係るアルミニウム合金材は、Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなるアルミニウム合金材であって、前記アルミニウム合金材についてのＸ線回折測定で得られるＸ線回折パターンにおけるＡｌ6Ｆｅ相の回折ピークの積分強度を「Ｑ1」（ｃｐｓ・ｄｅｇ）とし、Ａｌ相の（２００）面の回折ピークの積分強度を「Ｑ2」（ｃｐｓ・ｄｅｇ）としたとき、積分強度の比率（Ｑ1／Ｑ2）が０．００６以下である構成（ただし、Ｑ1／Ｑ2の値が０であるものを除く）である。このような構成のアルミニウム合金材は、高温における機械特性に優れており、例えば、高温機械特性に優れたアルミニウム合金鋳造材、高温機械特性に優れたアルミニウム合金押出材等を提供できる。 An aluminum alloy material according to the present invention contains 0.5% to 8.0% by mass of Fe, 0.05% to 2.0% by mass of Ti, and the balance is Al and an unavoidable impurity. The integral intensity of the diffraction peak of the Al 6 Fe phase in the X-ray diffraction pattern obtained by the X-ray diffraction measurement of the aluminum alloy material is “Q 1 ” (cps · deg), ) When the integrated intensity of the diffraction peak on the plane is “Q 2 ” (cps · deg), the ratio (Q 1 / Q 2 ) of the integrated intensity is 0.006 or less (however, Q 1 / Q 2 Excluding those with a value of 0). The aluminum alloy material having such a configuration is excellent in mechanical properties at high temperatures, and for example, an aluminum alloy cast material excellent in high-temperature mechanical properties, an aluminum alloy extruded material excellent in high-temperature mechanical properties, and the like can be provided.
本発明では、前記アルミニウム合金材（鋳造材、押出材等）中にＡｌ−Ｆｅ系金属間化合物を含有し、前記アルミニウム合金材の断面組織構造においてＡｌ−Ｆｅ系金属間化合物の平均円相当直径が０．１μｍ〜３．０μｍの範囲であるのが好ましい。Ａｌ−Ｆｅ系金属間化合物の平均円相当直径が０．１μｍ以上であることで、分散強化の効果が十分に得られると共に、前記平均円相当直径が３．０μｍ以下であることで、粗大な金属間化合物を起点として破断するようなことがなくて十分な機械的特性を確保できる。中でも、前記アルミニウム合金材の断面組織構造においてＡｌ−Ｆｅ系金属間化合物の平均円相当直径が０．５μｍ〜２．０μｍの範囲であるのが特に好ましい。 In the present invention, the aluminum alloy material (cast material, extruded material, etc.) contains an Al-Fe intermetallic compound, and the average equivalent circle diameter of the Al-Fe intermetallic compound in the cross-sectional structure of the aluminum alloy material. Is preferably in the range of 0.1 μm to 3.0 μm. When the average equivalent circle diameter of the Al—Fe-based intermetallic compound is 0.1 μm or more, the effect of dispersion strengthening is sufficiently obtained, and when the average equivalent circle diameter is 3.0 μm or less, a coarse Sufficient mechanical properties can be ensured without breakage starting from the intermetallic compound. Among them, it is particularly preferable that the average circle equivalent diameter of the Al-Fe intermetallic compound in the cross-sectional structure of the aluminum alloy material is in the range of 0.5 µm to 2.0 µm.
前記Ａｌ−Ｆｅ系金属間化合物の円相当直径とは、前記アルミニウム合金材（鋳造材、押出材等）の断面のＳＥＭ写真（画像）におけるＡｌ−Ｆｅ系金属間化合物の面積と同じ面積を有する円の直径として換算した値である。 The equivalent circle diameter of the Al-Fe intermetallic compound has the same area as the area of the Al-Fe intermetallic compound in a SEM photograph (image) of a cross section of the aluminum alloy material (cast material, extruded material, etc.). It is a value converted as the diameter of a circle.
なお、本発明に係るアルミニウム合金材（鋳造材、押出材等）は、以下の製造方法で得られたアルミニウム合金鋳造材、以下の製造方法で得られたアルミニウム合金粉末押出材に限定されるものではなく、他の製造方法で得られたものも包含する。 The aluminum alloy material (cast material, extruded material, etc.) according to the present invention is limited to an aluminum alloy cast material obtained by the following manufacturing method and an aluminum alloy powder extruded material obtained by the following manufacturing method. But also includes those obtained by other manufacturing methods.
次に、本発明に係る、アルミニウム合金鋳造材の製造方法について説明する。本製造方法は、Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなるアルミニウム合金の溶湯を得る溶湯形成工程と、前記得られた溶湯を鋳造加工することによって鋳造材を得る鋳造工程と、前記アルミニウム合金の示差走査熱量測定で得られる示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度を「Ｘ」（℃）としたとき、前記得られた鋳造材を２００℃〜Ｘ℃の範囲の温度で熱処理を行う熱処理工程と、を含む。 Next, a method for producing an aluminum alloy casting according to the present invention will be described. This production method obtains a molten aluminum alloy containing 0.5% to 8.0% by mass of Fe and 0.05% to 2.0% by mass of Ti, with the balance being Al and unavoidable impurities. A step of forming a molten metal, a step of obtaining a cast material by casting the obtained molten metal, and an exothermic peak onset temperature derived from a differential scanning calorimetry curve obtained by differential scanning calorimetry of the aluminum alloy, wherein 400 A heat treatment step of subjecting the obtained cast material to a heat treatment at a temperature in the range of 200 ° C. to X ° C., where “X” (° C.) is the exothermic peak onset temperature of not less than 100 ° C.
前記溶湯形成工程では、Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなる組成となるように溶解調製されたアルミニウム合金溶湯を得る。 In the molten metal forming step, Fe: 0.5% to 8.0% by mass, Ti: 0.05% to 2.0% by mass, with the balance being Al and inevitable impurities. An aluminum alloy melt prepared by melting is obtained.
次に、前記得られた溶湯を鋳造加工することによって鋳造材を得る（鋳造工程）。鋳造方法としては、特に限定されるものではないが、水平連続鋳造法、ホットトップ鋳造法、縦型連続鋳造法およびＤＣ鋳造法からなる群より得らばれる鋳造法を適用するのが、鋳造性に優れている点で、望ましい。 Next, a casting is obtained by casting the obtained molten metal (casting step). The casting method is not particularly limited, but a casting method obtained from a group consisting of a horizontal continuous casting method, a hot top casting method, a vertical continuous casting method and a DC casting method is applied. It is desirable because it is excellent.
連続鋳造時における鋳造速度は、特に限定されないものの、水平連続鋳造法では鋳造速度を３００ｍｍ／分〜２０００ｍｍ／分に設定するのが好ましく、ホットトップ鋳造法、縦型連続鋳造法およびＤＣ鋳造法では、鋳造速度を８０ｍｍ／分〜４００ｍｍ／分に設定するのが好ましい。 Although the casting speed during continuous casting is not particularly limited, the casting speed is preferably set to 300 mm / min to 2000 mm / min in the horizontal continuous casting method, and in the hot top casting method, the vertical continuous casting method and the DC casting method, It is preferable to set the casting speed to 80 mm / min to 400 mm / min.
以下、連続鋳造法の一例として、ホットトップ鋳造装置を用いたホットトップ鋳造法により連続鋳造材を製造する場合について説明する。ホットトップ鋳造装置は、モールド（鋳型）、溶湯受容器（ヘッダー）等を備えている。モールドは、その内部に充満された冷却水により冷却されている。溶湯受容器は、一般に耐火物製であり、モールドの上側に配置されている。そして、溶湯受容器内に収容されている上記特定組成のアルミニウム合金の溶湯が、該溶湯受容器から、冷却されたモールド内に下方向に注入されると共に、モールドから噴出された冷却水により所定の冷却速度で冷却されて凝固し、更に水槽内の水に浸されて完全に凝固する。こうして棒状等の長尺の連続鋳造材が得られる。連続鋳造材の横断面形状は、特に限定されないが、例えば、円形状等が挙げられる。連続鋳造材の直径は、特に限定されるものではないが、１０ｍｍ〜３００ｍｍであるのが望ましい。 Hereinafter, as an example of the continuous casting method, a case where a continuous cast material is manufactured by a hot top casting method using a hot top casting apparatus will be described. The hot top casting apparatus includes a mold, a molten metal receiver (header), and the like. The mold is cooled by cooling water filled therein. The melt receiver is typically made of refractory material and is located above the mold. Then, the molten metal of the aluminum alloy having the specific composition accommodated in the molten metal receiver is poured downward from the molten metal receiver into the cooled mold, and is cooled by the cooling water jetted from the mold. It is cooled at the cooling rate of, and solidified, and further immersed in the water in the water tank to be completely solidified. Thus, a long continuous cast material such as a bar can be obtained. The cross-sectional shape of the continuous cast material is not particularly limited, and examples thereof include a circular shape. The diameter of the continuous cast material is not particularly limited, but is preferably from 10 mm to 300 mm.
前記熱処理工程では、前記アルミニウム合金の示差走査熱量測定で得られる示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度を「Ｘ」（℃）としたとき、前記得られた鋳造材を２００℃〜Ｘ℃の範囲の温度で熱処理を行う。例えば、４００℃以上の温度領域における発熱ピーク開始温度が４３０℃である場合には、前記得られた鋳造材を２００℃〜４３０℃の範囲の温度で熱処理を行う。前記得られた鋳造材を２００℃〜Ｘ℃の範囲の温度で熱処理を行うことによって、粗大なＡｌ3Ｎｉ2の析出を防止できると共に、Ａｌ−Ｆｅ化合物の相変化を防ぐことができ、高温において優れた機械的特性を得ることができる。熱処理温度が２００℃未満では、例えばＭｇ2ＳｉやＣｕＡｌ2等の粗大な析出物をＡｌ母相中に固溶させることができないため、高温において優れた機械的特性を得ることができない。一方、熱処理温度がＸ℃を超えると、粗大なＡｌ3Ｎｉ2の析出を生じる上に、Ａｌ−Ｆｅ化合物の相変化により、高温において優れた機械的特性を得ることができない。中でも、熱処理温度は２２０℃〜Ｘ℃に設定するのが好ましい。前記熱処理工程における熱処理時間は、１時間〜１０時間に設定するのが好ましく、２時間〜５時間に設定するのがより好ましい。 In the heat treatment step, when an exothermic peak onset temperature derived from a differential scanning calorimetry curve obtained by differential scanning calorimetry of the aluminum alloy and the exothermic peak onset temperature of 400 ° C. or more is “X” (° C.), The obtained cast material is subjected to a heat treatment at a temperature in the range of 200C to XC. For example, when the exothermic peak start temperature in the temperature region of 400 ° C. or more is 430 ° C., the obtained cast material is subjected to heat treatment at a temperature in the range of 200 ° C. to 430 ° C. By subjecting the obtained cast material to a heat treatment at a temperature in the range of 200 ° C. to X ° C., it is possible to prevent coarse Al 3 Ni 2 from being precipitated and to prevent a phase change of the Al—Fe compound, And excellent mechanical properties can be obtained. If the heat treatment temperature is lower than 200 ° C., for example, coarse precipitates such as Mg 2 Si and CuAl 2 cannot be dissolved in the Al matrix, so that excellent mechanical properties cannot be obtained at high temperatures. On the other hand, if the heat treatment temperature exceeds X ° C., coarse Al 3 Ni 2 precipitates, and excellent mechanical properties cannot be obtained at high temperatures due to a phase change of the Al—Fe compound. Among them, the heat treatment temperature is preferably set to 220 ° C. to X ° C. The heat treatment time in the heat treatment step is preferably set to 1 hour to 10 hours, more preferably 2 hours to 5 hours.
上述した溶湯形成工程、鋳造工程、熱処理工程を経て得られた鋳造材１は、該鋳造材についてのＸ線回折測定で得られるＸ線回折パターンにおけるＡｌ6Ｆｅ相の回折ピークの積分強度を「Ｑ1」（ｃｐｓ・ｄｅｇ）とし、Ａｌ相の（２００）面の回折ピークの積分強度を「Ｑ2」（ｃｐｓ・ｄｅｇ）としたとき、積分強度の比率（Ｑ1／Ｑ2）が０．００６以下である構成になっており、得られた鋳造材１は、高温における機械特性（引張強度等）に優れている。更に、得られたアルミニウム合金鋳造材１は、該鋳造材中にＡｌ−Ｆｅ系金属間化合物を含有し、鋳造材の断面組織構造においてＡｌ−Ｆｅ系金属間化合物の平均円相当直径が０．１μｍ〜３．０μｍである構成になっている。 The cast material 1 obtained through the above-described melt forming step, casting step, and heat treatment step has an integrated intensity of the diffraction peak of the Al 6 Fe phase in the X-ray diffraction pattern obtained by the X-ray diffraction measurement on the cast material. Q 1 '(cps · deg) and then, when the integrated intensity of the diffraction peak of the Al phase (200) plane and "Q 2" (cps · deg), the ratio of the integrated intensity (Q 1 / Q 2) is 0 0.006 or less, and the obtained cast material 1 has excellent mechanical properties (such as tensile strength) at high temperatures. Furthermore, the obtained cast aluminum alloy material 1 contains an Al-Fe-based intermetallic compound in the cast material, and the average equivalent circle diameter of the Al-Fe-based intermetallic compound in the cross-sectional structure of the cast material is 0.1 mm. The structure is 1 μm to 3.0 μm.
次に、本発明に係る、アルミニウム合金粉末押出材の製造方法について説明する。本製造方法は、Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなるアルミニウム合金粉末を圧縮成形して圧粉体を得る圧縮成形工程と、前記アルミニウム合金粉末の示差走査熱量測定で得られる示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度を「Ｘ」（℃）としたとき、前記得られた圧粉体を２００℃〜Ｘ℃の範囲の温度で熱間押出しして押出材を得る押出工程と、前記押出材を２００℃〜Ｘ℃の範囲の温度で熱処理を行う熱処理工程と、を含む。 Next, a method for producing an extruded aluminum alloy powder according to the present invention will be described. This production method comprises compression-molding an aluminum alloy powder containing 0.5% to 8.0% by mass of Fe and 0.05% to 2.0% by mass of Ti and the balance of Al and inevitable impurities. A compression molding step of obtaining a green compact, and an exothermic peak onset temperature derived from a differential scanning calorimetry curve obtained by differential scanning calorimetry of the aluminum alloy powder, wherein the exothermic peak onset temperature of 400 ° C. or more is represented by “X”. (° C.), an extrusion step of hot-extruding the obtained green compact at a temperature in a range of 200 ° C. to X ° C. to obtain an extruded material, and extruding the extruded material in a range of 200 ° C. to X ° C. Heat treatment at a temperature.
まず、アルミニウム合金粉末の製法の一例について説明する。Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなるアルミニウム合金溶湯をアトマイズ法によって急冷凝固させて粉末化して、アルミニウム合金粉末（アルミニウム合金アトマイズ粉末）を得る（粉末化工程）。 First, an example of a method for producing an aluminum alloy powder will be described. An aluminum alloy melt containing Fe: 0.5% by mass to 8.0% by mass, Ti: 0.05% by mass to 2.0% by mass, and the balance consisting of Al and inevitable impurities is rapidly solidified by an atomizing method. Powdering is performed to obtain an aluminum alloy powder (aluminum alloy atomized powder) (powdering step).
前記粉末化工程では、上記特定組成のアルミニウム合金溶湯を通常の溶解法によって調製する。得られたアルミニウム合金溶湯をアトマイズ法によって粉末化する。アトマイズ法は、噴霧ノズルからの窒素ガス等のガス流によりアルミニウム合金溶湯の微小液滴をミスト化して噴霧し、微小液滴を急冷凝固させて微細なアルミニウム合金粉末を得る方法である。冷却速度は、１０2〜１０5℃／秒であるのが好ましい。平均粒子径が３０μｍ〜７０μｍのアルミニウム合金粉末が得られるようにするのがよい。得られたアルミニウム合金粉末は、篩を用いて分級するのが好ましい。上記アルミニウム合金粉末の製法は、その一例を示したものに過ぎず、特にこのような製法で製造されたアルミニウム合金粉末に限定されるものではなく、他の製法で得られたアルミニウム合金粉末を使用してもよい。 In the powdering step, a molten aluminum alloy having the above specific composition is prepared by a usual melting method. The obtained molten aluminum alloy is pulverized by an atomizing method. The atomization method is a method in which fine droplets of an aluminum alloy melt are atomized and sprayed by a gas flow such as nitrogen gas from a spray nozzle, and the fine droplets are rapidly cooled and solidified to obtain fine aluminum alloy powder. The cooling rate is preferably 10 2 to 10 5 ° C. / sec. It is preferable to obtain an aluminum alloy powder having an average particle diameter of 30 μm to 70 μm. The obtained aluminum alloy powder is preferably classified using a sieve. The method for producing the above aluminum alloy powder is merely an example, and is not particularly limited to the aluminum alloy powder produced by such a method, but uses an aluminum alloy powder obtained by another method. May be.
次に、前記粉末化工程で得られたアルミニウム合金粉末を圧縮成形して圧粉体を得る（圧縮成形工程）。一例を挙げると、２５０℃〜３００℃に加熱したアルミニウム合金粉末を、２３０℃〜２７０℃に加熱された金型内に充填し、所定形状に圧縮成形して圧粉体を得る。前記圧縮成形の圧力は、特に限定されないが、通常は、０．５トン／ｃｍ2〜３．０トン／ｃｍ2に設定するのが好ましい。また、相対密度が６０％〜９０％の圧粉体にするのが好ましい。前記圧粉体の形状は、特に限定されないが、次の押出工程を考慮して、円柱形状または円盤状とするのが好ましい。 Next, the aluminum alloy powder obtained in the powdering step is compression molded to obtain a green compact (compression molding step). As an example, an aluminum alloy powder heated to 250 ° C. to 300 ° C. is filled in a mold heated to 230 ° C. to 270 ° C., and compression molded into a predetermined shape to obtain a green compact. The pressure for the compression molding is not particularly limited, but is usually preferably set to 0.5 ton / cm 2 to 3.0 ton / cm 2 . Further, it is preferable to form a green compact having a relative density of 60% to 90%. The shape of the green compact is not particularly limited, but is preferably cylindrical or disk-shaped in consideration of the next extrusion step.
次いで、前記圧縮成形工程で得られた圧粉体を熱間押出しして押出材を得る（押出工程）。前記圧粉体には、必要に応じて面削等の機械加工を施してから、脱ガス処理を施し、加熱して押出工程に供する。押出に際しては、例えば、圧粉体を押出コンテナ内に挿入して押出ラムにより加圧力を加え、押出ダイスから例えば丸棒形状に押出して押出材を得る。この時、前記アルミニウム合金粉末の示差走査熱量測定で得られる示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度を「Ｘ」（℃）としたとき、前記圧粉体を２００℃〜Ｘ℃の範囲の温度で熱間押出しして押出材を得る。例えば、４００℃以上の温度領域において発熱ピーク開始温度が４３０℃である場合には、前記圧粉体を２００℃〜４３０℃の範囲の温度で熱間押出しして押出材を得る。熱間で押し出すことによって圧粉体の塑性変形が進行し、アルミニウム合金粉末（粒子）同士が結合して一体化した押出材が得られる。前記押出の際に、押出圧力は１０ＭＰａ〜２５ＭＰａに設定するのが好ましい。 Next, the green compact obtained in the compression molding step is hot-extruded to obtain an extruded material (extrusion step). The green compact is subjected to machining such as facing if necessary, then degassed, heated, and subjected to an extrusion process. At the time of extrusion, for example, a green compact is inserted into an extrusion container, a pressing force is applied by an extrusion ram, and the extruded material is extruded from an extrusion die into, for example, a round bar shape. At this time, when the exothermic peak onset temperature derived from the differential scanning calorimetry curve obtained by the differential scanning calorimetry of the aluminum alloy powder and the exothermic peak onset temperature of 400 ° C. or higher is “X” (° C.), The powder is hot extruded at a temperature in the range of 200C to XC to obtain an extruded material. For example, when the exothermic peak start temperature is 430 ° C. in a temperature range of 400 ° C. or more, the extruded material is obtained by hot extruding the green compact at a temperature in a range of 200 ° C. to 430 ° C. By extruding hot, plastic deformation of the green compact proceeds, and an extruded material in which the aluminum alloy powders (particles) are bonded together and integrated is obtained. At the time of the extrusion, the extrusion pressure is preferably set to 10 MPa to 25 MPa.
前記熱処理工程では、前記得られた押出材を２００℃〜Ｘ℃の範囲の温度で熱処理を行う。このような特定範囲の温度にて熱処理を行うことによって、残留応力を十分に除去できる。熱処理温度が２００℃未満では、残留応力を十分に除去できず、十分な引張強度等が得られない。一方、熱処理温度がＸ℃を超えると、粗大なＡｌ3Ｎｉ2の析出を生じる上に、Ａｌ−Ｆｅ化合物の相変化により、高温において優れた機械的特性を得ることができない。中でも、熱処理温度は２５０℃〜Ｘ℃に設定するのが好ましい。前記熱処理工程における熱処理時間は、１時間〜１０時間に設定するのが好ましく、２時間〜５時間に設定するのがより好ましい。 In the heat treatment step, the obtained extruded material is heat-treated at a temperature in the range of 200C to XC. By performing the heat treatment at such a specific range of temperature, the residual stress can be sufficiently removed. If the heat treatment temperature is lower than 200 ° C., the residual stress cannot be sufficiently removed, and sufficient tensile strength cannot be obtained. On the other hand, if the heat treatment temperature exceeds X ° C., coarse Al 3 Ni 2 precipitates, and excellent mechanical properties cannot be obtained at high temperatures due to a phase change of the Al—Fe compound. Above all, the heat treatment temperature is preferably set to 250 ° C to X ° C. The heat treatment time in the heat treatment step is preferably set to 1 hour to 10 hours, more preferably 2 hours to 5 hours.
上述した圧縮成形工程、押出工程、熱処理工程を経て得られたアルミニウム合金粉末押出材１０は、該押出材についてのＸ線回折測定で得られるＸ線回折パターンにおけるＡｌ6Ｆｅ相の回折ピークの積分強度を「Ｑ1」（ｃｐｓ・ｄｅｇ）とし、Ａｌ相の（２００）面の回折ピークの積分強度を「Ｑ2」（ｃｐｓ・ｄｅｇ）としたとき、積分強度の比率（Ｑ1／Ｑ2）が０．００６以下である構成になっており、得られた押出材１０は、高温における機械特性（引張強度等）に優れている。更に、得られたアルミニウム合金粉末押出材１０は、該押出材中にＡｌ−Ｆｅ系金属間化合物を含有し、押出材の断面組織構造においてＡｌ−Ｆｅ系金属間化合物の平均円相当直径が０．１μｍ〜３．０μｍである構成になっている。 The aluminum alloy powder extruded material 10 obtained through the above-described compression molding step, extrusion step, and heat treatment step is obtained by integrating the diffraction peak of the Al 6 Fe phase in the X-ray diffraction pattern obtained by the X-ray diffraction measurement on the extruded material. When the intensity is “Q 1 ” (cps · deg) and the integrated intensity of the diffraction peak of the (200) plane of the Al phase is “Q 2 ” (cps · deg), the ratio of the integrated intensity (Q 1 / Q 2) ) Is 0.006 or less, and the obtained extruded material 10 has excellent mechanical properties (such as tensile strength) at high temperatures. Further, the obtained extruded aluminum alloy powder 10 contains an Al-Fe-based intermetallic compound in the extruded material, and the cross-sectional structure of the extruded material has an average circle-equivalent diameter of the Al-Fe-based intermetallic compound of 0. It is configured to be from 0.1 μm to 3.0 μm.
次に、上述した本発明に係るアルミニウム合金材およびアルミニウム合金鋳造材の製造方法、アルミニウム合金粉末押出材の製造方法における「アルミニウム合金」の組成について以下詳述する。前記アルミニウム合金は、Ｆｅ：０．５質量％〜８．０質量％、Ｔｉ：０．０５質量％〜２．０質量％を含有し、残部がＡｌ及び不可避不純物からなるアルミニウム合金である。 Next, the composition of the “aluminum alloy” in the method for producing the aluminum alloy material and the cast aluminum alloy material according to the present invention and the method for producing the extruded aluminum alloy powder according to the present invention will be described in detail below. The aluminum alloy is an aluminum alloy containing 0.5% by mass to 8.0% by mass of Fe and 0.05% by mass to 2.0% by mass of Ti, with the balance being Al and unavoidable impurities.
前記Ｆｅ（成分）は、高い融点を有するＡｌ−Ｆｅ系金属間化合物を生成し、例えば２００℃〜３５０℃の高い温度域での機械特性を向上させることができる元素である。前記アルミニウム合金におけるＦｅ含有率は、０．５質量％〜８．０質量％の範囲とする。Ｆｅ含有率が０．５質量％未満になると、アルミニウム合金材、アルミニウム合金鋳造材、アルミニウム合金粉末押出材等の製品の強度が低下する。一方、Ｆｅ含有率が８．０質量％を超えると、アルミニウム合金材、アルミニウム合金鋳造材、アルミニウム合金粉末押出材等の製品の延性が低下し、前記製品として高温での機械特性に優れたものを得ることができない。中でも、前記アルミニウム合金におけるＦｅ含有率は、０．７質量％〜６．０質量％の範囲であるのが好ましい。 The Fe (component) is an element capable of generating an Al-Fe-based intermetallic compound having a high melting point and improving mechanical properties in a high temperature range of, for example, 200C to 350C. The Fe content in the aluminum alloy is in the range of 0.5% by mass to 8.0% by mass. When the Fe content is less than 0.5% by mass, the strength of products such as an aluminum alloy material, an aluminum alloy casting, and an aluminum alloy powder extruded material is reduced. On the other hand, if the Fe content exceeds 8.0% by mass, the ductility of products such as aluminum alloy materials, aluminum alloy castings, and aluminum alloy powder extruded materials is reduced, and the products have excellent mechanical properties at high temperatures. Can not get. Among them, the Fe content in the aluminum alloy is preferably in the range of 0.7% by mass to 6.0% by mass.
前記Ｔｉ（成分）は、Ａｌマトリックス中での拡散係数が小さいので、クリープ特性を向上させることができる元素である。前記アルミニウム合金におけるＴｉ含有率は、０．０５質量％〜２．０質量％の範囲とする。Ｔｉ含有率が０．０５質量％未満になると、析出強化及び分散強化の効果を発揮できない。一方、Ｔｉ含有率が２．０質量％を超えると、延性が低下して、高温において優れた機械的特性を得ることができない。中でも、前記アルミニウム合金におけるＴｉ含有率は、０．５質量％〜１．０質量％の範囲であるのが好ましい。 The Ti (component) is an element that has a small diffusion coefficient in the Al matrix and thus can improve the creep characteristics. The Ti content in the aluminum alloy is in the range of 0.05% by mass to 2.0% by mass. If the Ti content is less than 0.05% by mass, the effects of precipitation strengthening and dispersion strengthening cannot be exhibited. On the other hand, if the Ti content exceeds 2.0% by mass, ductility is reduced, and excellent mechanical properties cannot be obtained at high temperatures. In particular, the Ti content in the aluminum alloy is preferably in the range of 0.5% by mass to 1.0% by mass.
前記アルミニウム合金には、さらにＳｉを含有せしめてもよい。Ｓｉを含有させる場合には、Ｓｉ含有率は、１０．５質量％〜１２．０質量％に設定するのが好ましい。 The aluminum alloy may further contain Si. When Si is contained, the Si content is preferably set to 10.5% by mass to 12.0% by mass.
前記アルミニウム合金は、さらに、Ｃｕ、Ｍｇ、Ｚｒ、Ｖ、Ｗ、Ｃｒ、Ｃｏ、Ｍｏ、Ｔａ、Ｈｆ、Ｎｂ、Ｎｉ、ＭｎおよびＣｅからなる群より選ばれる１種または２種以上の元素を、それぞれ０．０１質量％〜５．０質量％含有する構成（組成）としてもよい。このような組成とすることで、高温における機械特性をより向上させることができる。Ｃｕを含有させる場合には、Ｃｕ含有率は、４．０質量％〜５．０質量％に設定するのが好ましい。Ｍｇを含有させる場合には、Ｍｇ含有率は、０．４質量％〜０．６質量％に設定するのが好ましい。Ｎｉを含有させる場合には、Ｎｉ含有率は、３．０質量％〜５．０質量％に設定するのが好ましい。Ｍｎを含有させる場合には、Ｍｎ含有率は、０．０１質量％〜０．１質量％に設定するのが好ましい。 The aluminum alloy further comprises one or more elements selected from the group consisting of Cu, Mg, Zr, V, W, Cr, Co, Mo, Ta, Hf, Nb, Ni, Mn, and Ce, The composition (composition) may be 0.01% by mass to 5.0% by mass. With such a composition, mechanical properties at high temperatures can be further improved. When Cu is contained, the Cu content is preferably set to 4.0% by mass to 5.0% by mass. When Mg is contained, the Mg content is preferably set to 0.4% by mass to 0.6% by mass. When Ni is contained, the Ni content is preferably set to 3.0% by mass to 5.0% by mass. When Mn is contained, the Mn content is preferably set to 0.01% by mass to 0.1% by mass.
前記アルミニウム合金は、さらに、Ｂ（硼素）を０．０００１質量％〜０．０３質量％含む構成（組成）としてもよい。Ｂを上記特定含有率で含有せしめた組成とすることにより、結晶粒を微細化し、機械的特性をさらに向上できる。 The aluminum alloy may have a configuration (composition) further containing 0.0001% by mass to 0.03% by mass of B (boron). By making the composition containing B at the above specific content, the crystal grains can be refined and the mechanical properties can be further improved.
次に、本発明の具体的実施例について説明するが、本発明はこれら実施例のものに特に限定されるものではない。 Next, specific examples of the present invention will be described, but the present invention is not particularly limited to these examples.
＜実施例１＞
Ｆｅ：０．７０質量％、Ｓｉ：１１．２０質量％、Ｃｕ：５．００質量％、Ｍｇ：０．５０質量％、Ｎｉ：４．８０質量％、Ｍｎ：０．０１質量％、Ｔｉ：０．１５質量％、Ａｌ：７７．６４質量％を含有し、不可避不純物を含有するアルミニウム合金を得た。このアルミニウム合金について示差走査熱量測定を行って得られた示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度は、４３０℃であった（図３、表１参照）。
<Example 1>
Fe: 0.70% by mass, Si: 11.20% by mass, Cu: 5.00% by mass, Mg: 0.50% by mass, Ni: 4.80% by mass, Mn: 0.01% by mass, Ti: An aluminum alloy containing 0.15% by mass and Al: 77.64% by mass and containing unavoidable impurities was obtained. The exothermic peak onset temperature derived from the differential scanning calorimetry curve obtained by performing differential scanning calorimetry on this aluminum alloy, and the exothermic peak onset temperature of 400 ° C. or higher was 430 ° C. (see FIG. 3 and Table 1). ).
次に、前記アルミニウム合金を加熱してアルミニウム合金溶湯を得た後、該アルミニウム合金溶湯をホットトップ鋳造法によって鋳造径５７ｍｍで連続鋳造を行うことによって連続鋳造材を得た。得られた連続鋳造材に対して３７０℃で５時間の熱処理を行った後、空冷した。空冷後の連続鋳造材を長さ８０ｍｍに切断して、図１に示す円柱形状の鋳造材１を得た。 Next, after the aluminum alloy was heated to obtain a molten aluminum alloy, the molten aluminum alloy was continuously cast with a casting diameter of 57 mm by a hot top casting method to obtain a continuously cast material. The obtained continuous cast material was heat-treated at 370 ° C. for 5 hours, and then air-cooled. The air-cooled continuous cast material was cut into a length of 80 mm to obtain a cylindrical cast material 1 shown in FIG.
＜実施例２〜８＞
前記アルミニウム合金溶湯を形成するためのアルミニウム合金として、表１に示す合金組成（不可避不純物を含有する）のアルミニウム合金を用いると共に、表１に示す熱処理温度で５時間の熱処理を行った以外は、実施例１と同様にして、図１に示す円柱形状の鋳造材１を得た。なお、各アルミニウム合金について示差走査熱量測定を行って得られた示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度は、それぞれ表１に示した。
<Examples 2 to 8>
As an aluminum alloy for forming the molten aluminum alloy, an aluminum alloy having an alloy composition (containing unavoidable impurities) shown in Table 1 was used, and a heat treatment was performed at a heat treatment temperature shown in Table 1 for 5 hours. In the same manner as in Example 1, a cylindrical cast material 1 shown in FIG. 1 was obtained. The exothermic peak onset temperatures derived from the differential scanning calorimetry curves obtained by performing the differential scanning calorimetry on each aluminum alloy and exothermic peak onset temperatures of 400 ° C. or higher are shown in Table 1.
＜実施例９〜１２＞
前記アルミニウム合金溶湯を形成するためのアルミニウム合金として、表２に示す合金組成（不可避不純物を含有する）のアルミニウム合金を用いると共に、表２に示す熱処理温度で５時間の熱処理を行った以外は、実施例１と同様にして、図１に示す円柱形状の鋳造材１を得た。なお、各アルミニウム合金について示差走査熱量測定を行って得られた示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度は、それぞれ表２に示した。
<Examples 9 to 12>
As an aluminum alloy for forming the aluminum alloy melt, an aluminum alloy having an alloy composition (containing unavoidable impurities) shown in Table 2 was used, and a heat treatment was performed at a heat treatment temperature shown in Table 2 for 5 hours. In the same manner as in Example 1, a cylindrical cast material 1 shown in FIG. 1 was obtained. The exothermic peak onset temperatures derived from the differential scanning calorimetry curves obtained by performing the differential scanning calorimetry on each aluminum alloy and exothermic peak onset temperatures of 400 ° C. or more are shown in Table 2.
＜実施例１３＞
Ｆｅ：０．７０質量％、Ｓｉ：１１．２０質量％、Ｃｕ：５．００質量％、Ｍｇ：０．５０質量％、Ｎｉ：４．８０質量％、Ｍｎ：０．０１質量％、Ｔｉ：１．３０質量％、Ａｌ：７６．４９質量％を含有し、不可避不純物を含有するアルミニウム合金を加熱して１０００℃のアルミニウム合金溶湯を得た後、該アルミニウム合金溶湯をガスにてアトマイズして急冷凝固させて粉末化して、平均粒子径が３０μｍ〜７０μｍのアルミニウム合金粉末（アルミニウム合金アトマイズ粉末）を得た。得られたアルミニウム合金粉末について示差走査熱量測定を行って得られた示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度は、４７６℃であった。
<Example 13>
Fe: 0.70% by mass, Si: 11.20% by mass, Cu: 5.00% by mass, Mg: 0.50% by mass, Ni: 4.80% by mass, Mn: 0.01% by mass, Ti: After heating an aluminum alloy containing 1.30% by mass and 76: 49% by mass of Al and containing inevitable impurities to obtain a molten aluminum alloy at 1000 ° C, the molten aluminum alloy was atomized with gas. The powder was quenched and solidified to obtain an aluminum alloy powder (aluminum alloy atomized powder) having an average particle diameter of 30 μm to 70 μm. An exothermic peak onset temperature derived from a differential scanning calorimetry curve obtained by performing differential scanning calorimetry on the obtained aluminum alloy powder, and an exothermic peak onset temperature of 400 ° C. or higher was 476 ° C.
次に、得られたアルミニウム合金粉末を２８０℃の温度に予熱し、この予熱したアルミニウム合金粉末を、同じ２８０℃に加熱保持した金型内に充填し、１．５トン／ｃｍ2の圧力で圧縮成形して、直径２１０ｍｍ、長さ２５０ｍｍの円柱形状の圧粉体（成形体）を得た。次に、得られた圧粉体を旋盤にて直径２０３ｍｍまで面削して、圧粉体のビレットを得た。 Next, the obtained aluminum alloy powder is preheated to a temperature of 280 ° C., and the preheated aluminum alloy powder is filled in a mold heated and maintained at the same 280 ° C., and is subjected to a pressure of 1.5 ton / cm 2 . By compression molding, a cylindrical green compact (compact) having a diameter of 210 mm and a length of 250 mm was obtained. Next, the obtained green compact was chamfered to a diameter of 203 mm with a lathe to obtain a billet of the green compact.
次に、得られたビレットを４３０℃に加熱し、この加熱ビレットを、４００℃に加熱保持された内径２１０ｍｍの押出コンテナ中に挿入し、内径８３ｍｍのダイスで間接押出法により押出比６．４で押出して押出材を得た後、該押出材に対して３００℃で２時間の熱処理を行った後、空冷して、図２に示す押出材１０を得た。 Next, the obtained billet is heated to 430 ° C., and the heated billet is inserted into an extrusion container having an inner diameter of 210 mm heated and maintained at 400 ° C., and an extrusion ratio of 6.4 is obtained by an indirect extrusion method with a die having an inner diameter of 83 mm. After extruding to obtain an extruded material, the extruded material was subjected to a heat treatment at 300 ° C. for 2 hours, and then air-cooled to obtain an extruded material 10 shown in FIG.
＜実施例１４〜１６＞
前記アルミニウム合金溶湯を形成するためのアルミニウム合金として、表２に示す合金組成（不可避不純物を含有する）のアルミニウム合金を用いると共に、表２に示す熱処理温度で２時間の熱処理を行った以外は、実施例１３と同様にして、図２に示す押出材１０を得た。なお、各アルミニウム合金粉末について示差走査熱量測定を行って得られた示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度は、それぞれ表２に示した。
<Examples 14 to 16>
As an aluminum alloy for forming the molten aluminum alloy, an aluminum alloy having an alloy composition (containing unavoidable impurities) shown in Table 2 was used, and heat treatment was performed at a heat treatment temperature shown in Table 2 for 2 hours. Extruded material 10 shown in FIG. 2 was obtained in the same manner as in Example 13. The exothermic peak onset temperatures derived from the differential scanning calorimetry curves obtained by performing the differential scanning calorimetry on each aluminum alloy powder, and the exothermic peak onset temperatures of 400 ° C. or higher are shown in Table 2.
＜比較例１〜９＞
前記アルミニウム合金溶湯を形成するためのアルミニウム合金として、表３に示す合金組成（不可避不純物を含有する）のアルミニウム合金を用いると共に、表３に示す熱処理温度で２時間の熱処理を行った以外は、実施例１と同様にして、円柱形状の鋳造材を得た。なお、各アルミニウム合金について示差走査熱量測定を行って得られた示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度は、それぞれ表３に示した。
<Comparative Examples 1 to 9>
As an aluminum alloy for forming the molten aluminum alloy, an aluminum alloy having an alloy composition (containing unavoidable impurities) shown in Table 3 was used, and a heat treatment was performed at a heat treatment temperature shown in Table 3 for 2 hours. In the same manner as in Example 1, a cylindrical cast material was obtained. Table 3 shows the exothermic peak onset temperature derived from the differential scanning calorimetry curve obtained by performing the differential scanning calorimetry on each aluminum alloy, and is 400 ° C. or higher.
＜比較例１０〜１３＞
前記アルミニウム合金溶湯を形成するためのアルミニウム合金として、表４に示す合金組成（不可避不純物を含有する）のアルミニウム合金を用いると共に、表４に示す熱処理温度で２時間の熱処理を行った以外は、実施例１と同様にして、円柱形状の鋳造材を得た。なお、各アルミニウム合金について示差走査熱量測定を行って得られた示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度は、それぞれ表４に示した。
<Comparative Examples 10 to 13>
As an aluminum alloy for forming the aluminum alloy melt, an aluminum alloy having an alloy composition (containing unavoidable impurities) shown in Table 4 was used, and heat treatment was performed at a heat treatment temperature shown in Table 4 for 2 hours. In the same manner as in Example 1, a cylindrical cast material was obtained. Table 4 shows the exothermic peak onset temperatures derived from the differential scanning calorimetry curves obtained by performing the differential scanning calorimetry on each aluminum alloy and exothermic peak onset temperatures of 400 ° C. or higher.
＜比較例１４〜１７＞
前記アルミニウム合金溶湯を形成するためのアルミニウム合金として、表４に示す合金組成（不可避不純物を含有する）のアルミニウム合金を用いると共に、表４に示す熱処理温度で２時間の熱処理を行った以外は、実施例１３と同様にして、図２に示す押出材を得た。なお、各アルミニウム合金粉末について示差走査熱量測定を行って得られた示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度は、それぞれ表４に示した。
<Comparative Examples 14 to 17>
As an aluminum alloy for forming the aluminum alloy melt, an aluminum alloy having an alloy composition (containing unavoidable impurities) shown in Table 4 was used, and heat treatment was performed at a heat treatment temperature shown in Table 4 for 2 hours. An extruded material shown in FIG. 2 was obtained in the same manner as in Example 13. The exothermic peak onset temperature derived from the differential scanning calorimetry curve obtained by performing the differential scanning calorimetry on each aluminum alloy powder, and the exothermic peak onset temperature of 400 ° C. or higher is shown in Table 4.
なお、表１〜４中の各元素欄において「−」の表記は、検出限界（０．００５質量％）未満の数値であること（即ち当該元素が検出されなかったこと）を示している。 In addition, in each element column in Tables 1 to 4, the notation "-" indicates that the value is less than the detection limit (0.005% by mass) (that is, the element was not detected).
また、表１〜４中の「金属間化合物の平均円相当直径（μｍ）」は、各鋳造材、各押出材のマトリックス中に存在するＡｌ−Ｆｅ系金属間化合物の平均円相当直径（μｍ）である。この「金属間化合物の平均円相当直径（μｍ）」は、得られたアルミニウム合金鋳造材（円柱体）、アルミニウム合金押出材（円柱体）のＬ方向（長さ方向即ち軸線方向）の中央部（中間二等分位置）から縦１０ｍｍ×横１０ｍｍ×厚さ１０ｍｍの大きさの組織観察用サンプル片を切り出し、このサンプル片を断面試料作製装置（Cross section polisher）を用いてミクロ研磨し、このミクロ研磨後のサンプル片のＳＥＭ写真（走査電子顕微鏡写真）を撮影し、この写真画像から金属間化合物の平均円相当直径（μｍ）を求めた（評価した）。前記ＳＥＭ写真における視野１．５８１５ｍｍ2の範囲に存在する１０個のＡｌ−Ｆｅ系金属間化合物についての平均円相当直径を求めた。 The “average equivalent circle diameter of intermetallic compound (μm)” in Tables 1 to 4 means the average equivalent circle diameter (μm) of Al—Fe intermetallic compound present in the matrix of each cast material and each extruded material. ). The “average equivalent circle diameter of the intermetallic compound (μm)” refers to the center of the obtained aluminum alloy cast material (cylindrical body) and aluminum alloy extruded material (cylindrical body) in the L direction (length direction, ie, axial direction). From the (intermediate bisecting position), a sample piece for tissue observation having a size of 10 mm in length × 10 mm in width × 10 mm in thickness was cut out, and the sample piece was micro-polished using a cross section sample preparation device (Cross section polisher). An SEM photograph (scanning electron microscope photograph) of the sample piece after micro-polishing was taken, and an average circle equivalent diameter (μm) of the intermetallic compound was determined (evaluated) from the photograph image. To obtain an average circle equivalent diameter of about 10 Al-Fe intermetallic compound present in the range of a viewing 1.5815Mm 2 in the SEM photograph.
＜アルミニウム合金材のＡｌ相及びＡｌ6Ｆｅ相の回折ピークの積分強度測定法＞
各アルミニウム合金鋳造材、各アルミニウム合金押出材について株式会社リガク製Ｘ線回折装置（SmartLab）を用いてＸ線回折測定を行った。なお、鋳造材や押出材の横断面中央部から１０ｍｍ×１０ｍｍ×厚さ２ｍｍの板状体を採取して、これをＸ線回折測定試料として用いた。Ｘ線回折測定により得られたＸ線回折パターンにおいてＡｌ相の（２００）面の回折ピークを同定し、該Ａｌ相の（２００）面の回折ピーク強度の積分値（回折ピークの積分強度Ｑ2）を求めると共に、Ａｌ6Ｆｅ相の回折ピークを同定し、このＡｌ6Ｆｅ相の回折ピーク強度の積分値（回折ピークの積分強度Ｑ1）を求め、これらよりＱ1／Ｑ2の値を求めた。これらの結果を表１〜４に示した。
<Method for measuring integrated intensity of diffraction peaks of Al phase and Al 6 Fe phase of aluminum alloy material>
X-ray diffraction measurement was performed for each aluminum alloy cast material and each aluminum alloy extruded material using an X-ray diffractometer (SmartLab) manufactured by Rigaku Corporation. A 10 mm × 10 mm × 2 mm thick plate was sampled from the center of the cross section of the cast or extruded material and used as an X-ray diffraction measurement sample. In the X-ray diffraction pattern obtained by the X-ray diffraction measurement, the diffraction peak of the (200) plane of the Al phase is identified, and the integrated value of the diffraction peak intensity of the (200) plane of the Al phase (the integrated intensity of the diffraction peak Q 2) ), The diffraction peak of the Al 6 Fe phase is identified, the integrated value of the diffraction peak intensity of the Al 6 Fe phase (the integrated intensity Q 1 of the diffraction peak) is determined, and the value of Q 1 / Q 2 is calculated from these values. I asked. The results are shown in Tables 1 to 4.
上記のようにして得られた各アルミニウム合金鋳造材・各アルミニウム合金押出材について下記評価法に基づいて高温での引張強度を評価した。その結果を表１〜４に示す。 The tensile strength at high temperatures of each cast aluminum alloy and each extruded aluminum alloy obtained as described above was evaluated based on the following evaluation method. The results are shown in Tables 1 to 4.
＜高温での引張強度評価法＞
得られたアルミニウム合金鋳造材、アルミニウム合金押出材を、標点間距離２０ｍｍ、平行部直径４ｍｍの引張試験片に加工して、該引張試験片の高温引張試験を行うことによって高温引張強度（３００℃での引張強度）を測定した。前記高温引張試験は、高温引張試験片を３００℃に１００時間保持した後に３００℃の測定環境下で試験を行った。この結果（３００℃での引張強度）を表１〜４に示す。
<Tensile strength evaluation method at high temperature>
The obtained aluminum alloy cast material and aluminum alloy extruded material are processed into a tensile test piece having a gauge length of 20 mm and a parallel portion diameter of 4 mm, and a high-temperature tensile test is performed on the tensile test piece to obtain a high-temperature tensile strength (300 mm). ° C tensile strength) was measured. The high-temperature tensile test was performed in a measurement environment at 300 ° C. after holding the high-temperature tensile test specimen at 300 ° C. for 100 hours. The results (tensile strength at 300 ° C.) are shown in Tables 1 to 4.
表から明らかなように、本発明に係る実施例１〜１６のアルミニウム合金材（鋳造材、押出材）は、高温（３００℃）における機械特性に優れていた。 As is clear from the table, the aluminum alloy materials (cast materials and extruded materials) of Examples 1 to 16 according to the present invention had excellent mechanical properties at high temperatures (300 ° C.).
これに対し、本発明の規定範囲を逸脱する比較例１〜１７のアルミニウム合金押出材は、高温（３００℃）での機械特性に劣っていた。 On the other hand, the aluminum alloy extruded materials of Comparative Examples 1 to 17 which deviate from the specified range of the present invention were inferior in mechanical properties at high temperatures (300 ° C.).
本発明に係るアルミニウム合金材、本発明に係る製造方法で得られたアルミニウム合金鋳造材、および本発明に係る製造方法で得られたアルミニウム合金粉末粉末押出材は、高温における機械特性に優れているから、例えば、自動車等の内燃機関に使用されるエンジンピストン等の、高温下で高速で摺動する摺動部材（摺動部品）等として好適に用いられるが、特にこのような用途に限定されるものではない。 The aluminum alloy material according to the present invention, the cast aluminum alloy material obtained by the manufacturing method according to the present invention, and the extruded aluminum alloy powder powder obtained by the manufacturing method according to the present invention have excellent mechanical properties at high temperatures. Therefore, it is preferably used as a sliding member (sliding component) that slides at high temperature and at high speed, such as an engine piston used in an internal combustion engine of an automobile or the like, but is particularly limited to such an application. Not something.
１…アルミニウム合金鋳造材（アルミニウム合金材）
１０…アルミニウム合金粉末押出材（アルミニウム合金材）
1. Cast aluminum alloy (aluminum alloy)
10 ... Aluminum alloy powder extruded material (aluminum alloy material)
Claims (10)
前記アルミニウム合金材についてのＸ線回折測定で得られるＸ線回折パターンにおけるＡｌ6Ｆｅ相の回折ピークの積分強度を「Ｑ1」（ｃｐｓ・ｄｅｇ）とし、Ａｌ相の（２００）面の回折ピークの積分強度を「Ｑ2」（ｃｐｓ・ｄｅｇ）としたとき、Ｑ1／Ｑ2の値が０．００６以下であることを特徴とするアルミニウム合金材。 An aluminum alloy material containing Fe: 0.5% by mass to 8.0% by mass, Ti: 0.05% by mass to 2.0% by mass, and the balance being Al and inevitable impurities;
The integrated intensity of the Al 6 Fe phase diffraction peak in the X-ray diffraction pattern obtained by the X-ray diffraction measurement of the aluminum alloy material is defined as “Q 1 ” (cps · deg), and the diffraction peak of the (200) plane of the Al phase. An aluminum alloy material, wherein the value of Q 1 / Q 2 is 0.006 or less, when the integrated intensity of the above is “Q 2 ” (cps · deg).
前記得られた溶湯を鋳造加工することによって鋳造材を得る鋳造工程と、
前記アルミニウム合金の示差走査熱量測定で得られる示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度を「Ｘ」（℃）としたとき、前記得られた鋳造材を２００℃〜Ｘ℃の範囲の温度で熱処理を行う熱処理工程と、を含むことを特徴とするアルミニウム合金鋳造材の製造方法。 A molten metal forming step of obtaining a molten aluminum alloy containing 0.5% to 8.0% by mass of Fe and 0.05% to 2.0% by mass of Ti and the balance of Al and inevitable impurities;
A casting step of obtaining a casting material by casting the obtained molten metal,
Assuming that an exothermic peak onset temperature derived from a differential scanning calorimetry curve obtained by differential scanning calorimetry of the aluminum alloy and which is 400 ° C. or higher is “X” (° C.), the obtained cast material is obtained. A heat treatment step of performing a heat treatment at a temperature in the range of 200 ° C to X ° C.
前記アルミニウム合金粉末の示差走査熱量測定で得られる示差走査熱量曲線から導き出される発熱ピーク開始温度であって４００℃以上の発熱ピーク開始温度を「Ｘ」（℃）としたとき、前記得られた圧粉体を２００℃〜Ｘ℃の範囲の温度で熱間押出しして押出材を得る押出工程と、
前記押出材を２００℃〜Ｘ℃の範囲の温度で熱処理を行う熱処理工程と、を含むことを特徴とするアルミニウム合金粉末押出材の製造方法。 Green compact containing aluminum alloy powder containing 0.5% to 8.0% by mass of Fe and 0.05% to 2.0% by mass of Ti and the balance of Al and inevitable impurities Compression molding process to obtain
When an exothermic peak onset temperature derived from a differential scanning calorimetry curve obtained by differential scanning calorimetry of the aluminum alloy powder and which is 400 ° C. or more is defined as “X” (° C.), the obtained pressure is An extrusion step of hot extruding the powder at a temperature in the range of 200 ° C to X ° C to obtain an extruded material;
A method of heat-treating the extruded material at a temperature in the range of 200 ° C to X ° C.
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