JP5558841B2 - Magnesium alloy for casting and method for producing magnesium casting - Google Patents
Magnesium alloy for casting and method for producing magnesium casting Download PDFInfo
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Description
本発明は、鋳造用マグネシウム合金及び該鋳造用マグネシウム合金を用いる鋳造体の製造方法に関する。 The present invention relates to a magnesium alloy for casting and a method for producing a cast body using the magnesium alloy for casting.
マグネシウム合金は、鉄、アルミニウムに比べて軽量であるため、鉄鋼材料や、アルミニウム合金材料からなる部材に代わる軽量代替材として用いることが検討されている。ところが、一般のマグネシウム合金は、２００〜２５０℃の高温域において、引張強度及び伸び等の機械的特性が低下し、鋳造ＡＣ８Ｂ−Ｔ６材、鍛造Ａ４０３２−Ｔ６材等の耐熱アルミニウム合金を上回る高温強度を得ることができない。 Since the magnesium alloy is lighter than iron and aluminum, it has been studied to use the magnesium alloy as a lightweight substitute material in place of a steel material or a member made of an aluminum alloy material. However, general magnesium alloys have high mechanical strength such as tensile strength and elongation at a high temperature range of 200 to 250 ° C., which is higher than heat-resistant aluminum alloys such as cast AC8B-T6 material and forged A4032-T6 material. Can't get.
そこで、従来、高温環境下において高強度を得ることができるマグネシウム合金として、Ｍｇ−Ｚｎ−Ｙ合金が知られている。例えば、Ｚｎ２原子％と、Ｙ２原子％とを含み、残部がＭｇと不可避の不純物とからなるＭｇ−Ｚｎ−Ｙ合金は、高温環境下において、アルミニウム合金に匹敵する前記高強度及び高延性を得ることができる。 Therefore, conventionally, an Mg—Zn—Y alloy is known as a magnesium alloy capable of obtaining high strength in a high temperature environment. For example, an Mg—Zn—Y alloy containing 2 atomic percent of Zn and 2 atomic percent of Y, with the balance being Mg and inevitable impurities, obtains the high strength and high ductility comparable to an aluminum alloy in a high temperature environment. be able to.
また、高温環境下において、前記従来のＭｇ−Ｚｎ−Ｙ合金を上回る高強度と高延性とを兼ね備える耐熱性マグネシウム合金として、例えば、全量に対して、Ｚｎ１〜３原子％と、Ｙ１〜３原子％と、Ｚｒ０．０１〜０．５原子％とを含み、残部がＭｇと不可避の不純物とからなるマグネシウム合金が提案されている（特許文献１参照）。前記耐熱性マグネシウム合金は、ＺｎとＹとの組成比Ｚｎ／Ｙが０．６〜１．３の範囲にあると共に、α−Ｍｇ相と金属間化合物Ｍｇ３Ｙ２Ｚｎ３相とが微細に分散し、かつ、α−Ｍｇ相及び金属間化合物Ｍｇ３Ｙ２Ｚｎ３相の間に長周期積層構造相が三次元網目状に形成されている。この結果、前記耐熱性マグネシウム合金によれば、２００〜２５０℃の高温域においても、高強度と高延性とを得ることができる。 Further, as a heat-resistant magnesium alloy having both high strength and high ductility exceeding the conventional Mg—Zn—Y alloy in a high temperature environment, for example, Zn 1 to 3 atom% and Y 1 to 3 atom with respect to the total amount And a magnesium alloy composed of Mg and unavoidable impurities are proposed (see Patent Document 1). The heat-resistant magnesium alloy has a composition ratio Zn / Y between Zn and Y in the range of 0.6 to 1.3, and an α-Mg phase and an intermetallic compound Mg 3 Y 2 Zn 3 phase are fine. A long-period laminated structure phase is formed in a three-dimensional network between the α-Mg phase and the intermetallic compound Mg 3 Y 2 Zn 3 phase. As a result, according to the heat-resistant magnesium alloy, high strength and high ductility can be obtained even in a high temperature range of 200 to 250 ° C.
しかしながら、特許文献１に記載の耐熱性マグネシウム合金は、前記高温域における高強度及び高延性を発現させるために、冷却速度を大きく保つことが必要とされ、肉厚の鋳造体では、前記高強度及び高延性を得ることが難しい。 However, the heat-resistant magnesium alloy described in Patent Document 1 is required to maintain a large cooling rate in order to develop high strength and high ductility in the high temperature range. And it is difficult to obtain high ductility.
また、鋳造体に対し熱処理を行うことにより強度を向上させることができるマグネシウム合金も知られているが、このようなマグネシウム合金では、所望の強度を得るためには熱処理が必要である。また、このようなマグネシウム合金では、時効温度以上の高温に加熱すると、過時効のために鋳造体の強度が著しく低下する。 Further, a magnesium alloy that can improve the strength by performing a heat treatment on the cast body is also known, but such a magnesium alloy requires a heat treatment to obtain a desired strength. In addition, when such a magnesium alloy is heated to a temperature higher than the aging temperature, the strength of the cast body is significantly reduced due to overaging.
そこで、本発明は、前記事情に鑑み、肉厚の鋳造体であっても２００〜２５０℃の高温域で高強度及び高延性を得ることができる耐熱性の鋳造用マグネシウム合金を提供することを目的とする。 Therefore, in view of the above circumstances, the present invention provides a heat-resistant magnesium alloy for casting that can obtain high strength and high ductility in a high temperature range of 200 to 250 ° C. even if it is a thick cast body. Objective.
また、本発明の目的は、前記鋳造用マグネシウム合金を用い、加熱処理や塑性変形を行うことなく鋳造のみにより前記高温域で高強度及び高延性を発現させることができるマグネシウム合金鋳造体の製造方法を提供することにもある。 Another object of the present invention is to provide a method for producing a magnesium alloy cast body, which uses the magnesium alloy for casting and can exhibit high strength and high ductility in the high temperature range only by casting without performing heat treatment or plastic deformation. There is also to provide.
さらに、本発明の目的は、前記製造方法により得られ、α−Ｍｇ相と、金属間化合物Ｍｇ３Ｙ２Ｚｎ３相と、長周期積層構造相とを備え、該長周期積層構造相の一部にＡｇが濃縮されていることを特徴とするマグネシウム合金鋳造体を提供することにもある。 Furthermore, an object of the present invention is obtained by the above production method, and includes an α-Mg phase, an intermetallic compound Mg 3 Y 2 Zn 3 phase, and a long-period multilayer structure phase. Another object of the present invention is to provide a magnesium alloy casting characterized in that Ag is concentrated in the part.
かかる目的を達成するために、本発明の鋳造用マグネシウム合金は、全量に対して、Ｚｎ１〜３原子％と、Ｙ１〜３原子％と、Ａｇ３原子％とを含み、残部がＭｇと不可避の不純物とからなることを特徴とする。 In order to achieve such an object, the magnesium alloy for casting of the present invention contains Zn 1 to 3 atomic%, Y 1 to 3 atomic%, and Ag 3 atomic% with respect to the total amount, and the balance is inevitable with Mg. It consists of impurities.
本発明の鋳造用マグネシウム合金は、鋳造のみにより成形することにより、α−Ｍｇ相と、粗大に析出した金属間化合物Ｍｇ３Ｙ２Ｚｎ３相と、三次元網目状に析出した長周期積層構造相とを備える金属組織からなるマグネシウム合金鋳造体を得ることができる。前記長周期積層構造相は、前記α−Ｍｇ相及び金属間化合物Ｍｇ３Ｙ２Ｚｎ３相の間に析出しており、該長周期積層構造相中の一部にＡｇが濃縮されている。この結果、本発明のマグネシウム合金鋳造体によれば、前記長周期積層構造相の一部に前記Ａｇを含む新規な相が形成され、該Ａｇを含む新規な相を備えることにより、肉厚の鋳造体であっても２００〜２５０℃の高温域で高強度及び高延性を得ることができる。 The magnesium alloy for casting according to the present invention is formed by casting alone to form an α-Mg phase, a coarsely precipitated intermetallic compound Mg 3 Y 2 Zn 3 phase, and a long-period laminated structure precipitated in a three-dimensional network. A magnesium alloy casting made of a metal structure having a phase can be obtained. The long-period multilayer structure phase is precipitated between the α-Mg phase and the intermetallic compound Mg 3 Y 2 Zn 3 phase, and Ag is concentrated in a part of the long-period multilayer structure phase. As a result, according to the magnesium alloy cast body of the present invention, a new phase containing Ag is formed in a part of the long-period laminated structure phase, and the thickness is increased by including the new phase containing Ag. Even in a cast body, high strength and high ductility can be obtained in a high temperature range of 200 to 250 ° C.
本発明の鋳造用マグネシウム合金において、Ａｇの含有量が全量に対して３原子％未満では、前記マグネシウム合金鋳造体の高温域での強度を、Ａｇを全く含まないマグネシウム合金鋳造体に対して２倍近い強度とする効果がない。一方、構造部材は通常１％以上の伸びが要求されるが、本発明の鋳造用マグネシウム合金において、Ａｇの含有量が全量に対して３原子％を超えると、前記マグネシウム合金鋳造体の伸びを１％以上とすることができない。 In the magnesium alloy for casting of the present invention, when the Ag content is less than 3 atomic% with respect to the total amount, the strength of the magnesium alloy cast body at a high temperature range is 2 with respect to the magnesium alloy cast body containing no Ag. There is no effect of nearly double the strength . On the other hand, the structural member is usually required to have an elongation of 1% or more. However, in the magnesium alloy for casting of the present invention, when the Ag content exceeds 3 atomic%, the elongation of the magnesium alloy cast body is increased. It cannot be made 1% or more.
また、本発明のマグネシウム合金鋳造体は、前記鋳造用マグネシウム合金を鋳造のみにより成形してなり、加熱処理や塑性変形を行うことなく前記高温域で高強度及び高延性が発現するので、加熱処理や塑性変形に要する時間やコストを不要とすることができる。 Further, the magnesium alloy cast body of the present invention is formed by molding the magnesium alloy for casting only by casting, and exhibits high strength and high ductility at the high temperature range without performing heat treatment or plastic deformation. And the time and cost required for plastic deformation can be eliminated.
次に、添付の図面を参照しながら本発明の実施の形態についてさらに詳しく説明する。 Next, embodiments of the present invention will be described in more detail with reference to the accompanying drawings.
本実施形態では、まず、全量に対して、Ｚｎ１〜３原子％と、Ｙ１〜３原子％と、Ａｇ３原子％とを含み、残部がＭｇと不可避の不純物とからなる合金材料を、６００〜９００℃の温度で溶融し、溶融合金を得る。 In the present embodiment, first, an alloy material containing Zn 1 to 3 atomic%, Y 1 to 3 atomic%, and Ag 3 atomic%, with the balance being Mg and inevitable impurities, is 600 to It melts at a temperature of 900 ° C. to obtain a molten alloy.
次に、前記溶融合金を金型に注入して鋳造を行う。前記鋳造は、例えば、鉄製の金型を用い、重力鋳造方式により、前記溶融合金を７８０℃前後の温度で該金型に鋳込むことにより行う。 Next, the molten alloy is poured into a mold and cast. The casting is performed, for example, by using an iron mold and casting the molten alloy into the mold at a temperature of about 780 ° C. by a gravity casting method.
この結果、全量に対して、Ｚｎ１〜３原子％と、Ｙ１〜３原子％と、Ａｇ３原子％とを含み、残部がＭｇと不可避の不純物とからなるマグネシウム合金鋳造体を、時効のための加熱処理や塑性加工を行うことなく得ることができる。前記マグネシウム合金鋳造体は、α−Ｍｇ相と、金属間化合物Ｍｇ３Ｙ２Ｚｎ３相と、前記α−Ｍｇ相及び金属間化合物Ｍｇ３Ｙ２Ｚｎ３相の間に析出した長周期積層構造相とを備えると共に、該長周期積層構造相の一部にＡｇが濃縮されている。 As a result, with respect to the total amount, a magnesium alloy cast body containing 1 to 3 atomic percent of Zn, 1 to 3 atomic percent of Y, and 3 atomic percent of Ag, and the balance of Mg and inevitable impurities is used for aging. It can be obtained without performing heat treatment or plastic working. The magnesium alloy casting has an α-Mg phase, an intermetallic compound Mg 3 Y 2 Zn 3 phase, and a long-period laminated structure precipitated between the α-Mg phase and the intermetallic compound Mg 3 Y 2 Zn 3 phase. And Ag is concentrated in a part of the long-period laminated structure phase.
前記マグネシウム合金鋳造体は、前記長周期積層構造相中にＡｇを含む新規な相が形成されており、このＡｇを含む新規な相により、２００〜２５０℃の高温域においても、高強度及び高延性を得ることができる。 In the magnesium alloy casting, a new phase containing Ag is formed in the long-period laminated structure phase, and the new phase containing Ag enables high strength and high strength even in a high temperature range of 200 to 250 ° C. Ductility can be obtained.
次に、前述のようにして、全量に対して、Ｚｎ２原子％と、Ｙ２原子％と、Ａｇ０〜３原子％とを含み、残部がＭｇからなるマグネシウム合金鋳造体を鋳造し、２５℃及び２００℃におけるロックウェル硬さと２５℃における伸びとを測定した。図１にＡｇの含有量とロックウェル硬さとの関係を、図２にＡｇの含有量と伸びとの関係をそれぞれ示す。 Next, as described above, a magnesium alloy cast body containing 2 atomic percent of Zn, 2 atomic percent of Y, and 0 to 3 atomic percent of Ag, with the balance being Mg, is cast at 25 ° C. and 200 atomic percent. The Rockwell hardness at 0 ° C. and the elongation at 25 ° C. were measured. FIG. 1 shows the relationship between the Ag content and Rockwell hardness, and FIG. 2 shows the relationship between the Ag content and elongation.
図１から、Ａｇの含有量が３原子％未満では、２５℃及び２００℃の温度環境下でロックウェル硬さを、Ａｇを全く含まないマグネシウム合金鋳造体に対して２倍近い強度とする効果が得られないことが明らかである。また、図２から、Ａｇの含有量が３原子％を超えると、構造部材に必要とされる１％以上の伸びを、２５℃では得ることができないことが明らかである。 From FIG. 1, when the Ag content is less than 3 atomic% , the effect of making the Rockwell hardness nearly double that of a magnesium alloy casting containing no Ag at 25 ° C. and 200 ° C. It is clear that cannot be obtained. Moreover, it is clear from FIG. 2 that when the Ag content exceeds 3 atomic%, the elongation of 1% or more required for the structural member cannot be obtained at 25 ° C.
次に、本発明の実施例と比較例とを示す。 Next, examples of the present invention and comparative examples will be described.
本実施例では、まず、全量に対して、Ｚｎ２原子％と、Ｙ２原子％と、Ａｇ３原子％とを含み、残部がＭｇからなる合金材料を、６００〜９００℃の温度で溶融し、溶融合金を得た。 In this example, first, an alloy material containing 2 atomic% of Zn, 2 atomic% of Y and 3 atomic% of Ag with the balance being Mg is melted at a temperature of 600 to 900 ° C. Got.
次に、前記溶融合金を鉄製の金型を用い、重力鋳造方式により、前記溶融合金を７８０℃前後の温度で該金型に鋳込むことにより鋳造を行った。この結果、全量に対して、Ｚｎ２原子％と、Ｙ２原子％と、Ａｇ３原子％とを含み、残部がＭｇからなる厚肉のマグネシウム合金鋳造体を、時効のための加熱処理や塑性加工を行うことなく得ることができた。 Next, the molten alloy was cast by casting the molten alloy into the mold at a temperature of about 780 ° C. by a gravity casting method using an iron mold. As a result, with respect to the total amount, a thick magnesium alloy cast body containing Zn 2 atom%, Y2 atom%, and Ag 3 atom% with the balance being Mg is subjected to heat treatment and plastic working for aging. I was able to get it without.
本実施例で得られた前記マグネシウム合金鋳造体の金属組織の電子顕微鏡写真を図３（ａ）及び図３（ｂ）に示す。また、本実施例で得られた前記マグネシウム合金鋳造体の金属組織のＸ線回折結果を図５（ａ）に示す。 3A and 3B show electron micrographs of the metal structure of the magnesium alloy casting obtained in this example. Moreover, the X-ray-diffraction result of the metal structure of the said magnesium alloy casting obtained in the present Example is shown to Fig.5 (a).
尚、本実施例で得られた前記マグネシウム合金鋳造体は、図１及び図２のグラフにおいて、Ａｇ＝３の場合に当たる。
〔比較例〕
本比較例では、Ａｇを全く含まない合金材料を用いた以外は、前記実施例と全く同一にして厚肉のマグネシウム合金鋳造体を得た。
The magnesium alloy cast obtained in this example corresponds to the case of Ag = 3 in the graphs of FIGS.
[Comparative example]
In this comparative example, a thick magnesium alloy casting was obtained in exactly the same manner as in the above example except that an alloy material containing no Ag was used.
本比較例で得られた前記マグネシウム合金鋳造体の金属組織の電子顕微鏡写真を図４（ａ）及び図４（ｂ）に示す。また、本比較例で得られた前記マグネシウム合金鋳造体の金属組織のＸ線回折結果を図５（ｂ）に示す。 4A and 4B show electron micrographs of the metal structure of the magnesium alloy casting obtained in this comparative example. Moreover, the X-ray-diffraction result of the metal structure of the said magnesium alloy casting obtained by this comparative example is shown in FIG.5 (b).
尚、本比較例で得られた前記マグネシウム合金鋳造体は、図１及び図２のグラフにおいて、Ａｇ＝０の場合に当たる。 The magnesium alloy cast obtained in this comparative example corresponds to the case of Ag = 0 in the graphs of FIGS.
図３（ａ）から、前記実施例で得られたマグネシウム合金鋳造体は、その金属組織中にα−Ｍｇ相１と、金属間化合物Ｍｇ３Ｙ２Ｚｎ３相２と、α−Ｍｇ相１及び金属間化合物Ｍｇ３Ｙ２Ｚｎ３相２の間に析出した長周期積層構造相３とを備えている。そして、前記実施例で得られたマグネシウム合金鋳造体は、図３（ｂ）に図３（ａ）の一部を拡大して示すように、長周期積層構造相３の一部にＡｇが濃縮されて形成されたＡｇを含む新たな相４を備えている。 From FIG. 3A, the magnesium alloy casting obtained in the above example has an α-Mg phase 1, an intermetallic compound Mg 3 Y 2 Zn 3 phase 2 and an α-Mg phase 1 in its metal structure. And an intermetallic compound Mg 3 Y 2 Zn 3 phase 2, and a long-period laminated structure phase 3 deposited between them. In the magnesium alloy casting obtained in the above example, Ag is concentrated in a part of the long-period laminated structure phase 3 as shown in FIG. 3 (b) with an enlarged part of FIG. 3 (a). And a new phase 4 containing the formed Ag.
一方、図４（ａ）と、図４（ａ）の一部を拡大して示す図４（ｂ）とから、前記比較例で得られたマグネシウム合金鋳造体は、その金属組織中にα−Ｍｇ相１と、金属間化合物Ｍｇ３Ｙ２Ｚｎ３相２と、α−Ｍｇ相１及び金属間化合物Ｍｇ３Ｙ２Ｚｎ３相２の間に析出した長周期積層構造相３とを備えるのみで、長周期積層構造相３中にＡｇが濃縮された相４は形成されていないことが明らかである。 On the other hand, from FIG. 4 (a) and FIG. 4 (b) showing an enlarged view of part of FIG. 4 (a), the magnesium alloy casting obtained in the comparative example has α- Only provided with Mg phase 1, intermetallic compound Mg 3 Y 2 Zn 3 phase 2, and long-period laminated structure phase 3 deposited between α-Mg phase 1 and intermetallic compound Mg 3 Y 2 Zn 3 phase 2 Thus, it is apparent that the phase 4 enriched with Ag in the long-period laminated structure phase 3 is not formed.
また、図５（ａ）に示す前記実施例で得られたマグネシウム合金鋳造体のＸ線回折結果は、図５（ｂ）に示す前記比較例で得られたマグネシウム合金鋳造体のＸ線回折結果と同一のピーク（◇、●、▲で示す）を備えるとともに、さらにこれとは異なるピーク（★で示す）を備えることが明らかである。ここで、◇で示すピークはα−Ｍｇ相、●で示すピークは金属間化合物Ｍｇ３Ｙ２Ｚｎ３相、▲で示すピークは長周期積層構造相である。従って、図５（ａ）に★で示すピークは、長周期積層構造相３中にＡｇが濃縮されることにより形成されたＡｇを含む新規な相４に対応するものと考えられる。 Moreover, the X-ray diffraction result of the magnesium alloy cast body obtained in the example shown in FIG. 5A is the X-ray diffraction result of the magnesium alloy cast body obtained in the comparative example shown in FIG. It is clear that the same peak (shown by ◇, ●, ▲) and a different peak (shown by ★) are provided. Here, the peak indicated by ◇ is the α-Mg phase, the peak indicated by ● is the intermetallic compound Mg 3 Y 2 Zn 3 phase, and the peak indicated by ▲ is the long-period stacked structure phase. Therefore, it is considered that the peak indicated by * in FIG. 5A corresponds to the novel phase 4 containing Ag formed by the Ag concentration in the long-period laminated structure phase 3.
そして、前記実施例で得られたマグネシウム合金鋳造体は、図１に示すように、前記比較例で得られたマグネシウム合金鋳造体に比較して２倍近い強度を備えていることが明らかである。また、前記実施例で得られたマグネシウム合金鋳造体は、図２に示すように、構造部材に要求される１％以上の伸びを備えていることが明らかである。 Then, as shown in FIG. 1, it is clear that the magnesium alloy cast obtained in the above example has nearly twice the strength as compared with the magnesium alloy cast obtained in the comparative example. . Moreover, as shown in FIG. 2, it is clear that the magnesium alloy casting obtained in the above example has an elongation of 1% or more required for the structural member.
１…α−Ｍｇ相、 ２…金属間化合物Ｍｇ３Ｙ２Ｚｎ３相、 ３…長周期積層構造相、 ４…Ａｇを含む新規な相。 1 ... alpha-Mg phase, 2 ... intermetallic compound Mg 3 Y 2 Zn 3 phase, 3 ... the long period stacking ordered structure phase, novel phase containing 4 ... Ag.
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