WO2010101122A1 - Magnesium alloy - Google Patents
Magnesium alloy Download PDFInfo
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- WO2010101122A1 WO2010101122A1 PCT/JP2010/053266 JP2010053266W WO2010101122A1 WO 2010101122 A1 WO2010101122 A1 WO 2010101122A1 JP 2010053266 W JP2010053266 W JP 2010053266W WO 2010101122 A1 WO2010101122 A1 WO 2010101122A1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C23/00—Extruding metal; Impact extrusion
- B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/04—Alloys based on magnesium with zinc or cadmium as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
- F02F—CYLINDERS, PISTONS OR CASINGS, FOR COMBUSTION ENGINES; ARRANGEMENTS OF SEALINGS IN COMBUSTION ENGINES
- F02F3/00—Pistons
- F02F3/0084—Pistons the pistons being constructed from specific materials
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
- F05C2201/00—Metals
- F05C2201/02—Light metals
- F05C2201/028—Magnesium
Definitions
- the present invention relates to a magnesium alloy. Specifically, the present invention relates to a magnesium alloy that can obtain high yield strength and high tensile strength.
- magnesium alloys have the lowest density, light weight, and high strength among the alloys in practical use, so they are being applied to electrical housings, automobile wheels, suspension parts, engine parts, etc. It has been.
- high mechanical properties are required for parts related to automobiles, and as a magnesium alloy to which elements such as Gd and Zn are added, materials of specific forms are manufactured by the single roll method and rapid solidification method. (For example, refer to Patent Document 1 and Patent Document 2).
- the yield strength of AZ and WE magnesium alloys used in recent years is about 300 MPa, and even in the case of an Mg—Zn—Y alloy, the yield strength is about 350 MPa and the tensile strength is about 390 MPa.
- the present invention was devised in view of the above points, and an object thereof is to provide a magnesium alloy capable of obtaining high yield strength and tensile strength without using special manufacturing equipment and processes. To do.
- the magnesium alloy of the present invention contains Zn, Y as essential components, and at least one of La, Ce, Nd, Pr, Sm, Yb as rare earth elements (RE).
- ⁇ Mg phase, and at least one compound of Mg—RE compound or Mg—Zn—RE compound, and the long-period laminate structure phase and the compound constitute a laminate structure, and the long-period laminate
- the thickness of the structural phase is 0.5 ⁇ m to 5 ⁇ m.
- the thickness of the long-period laminated structure phase (hereinafter referred to as “LPSO: Long Perioding Order”) in the alloy structure of the Mg—Zn—Y—RE alloy is 0.5 ⁇ m to 5 ⁇ m. This is because high yield strength ( ⁇ 0.2) and high tensile strength ( ⁇ UTS) are realized. Hereinafter, this point will be described.
- FIG. 2 shows the relationship between the volume fraction of LPSO and the yield strength (YS) in the alloy structure of the Mg—Zn—Y—RE alloy, and the volume of LPSO in the alloy structure of the Mg—Zn—Y—RE alloy.
- the relationship between a fraction and tensile strength (UTS) is shown.
- high yield strength and high tensile strength can be realized as the volume fraction of LPSO increases.
- the fact that the thickness of LPSO that forms a laminated structure together with the compound is thin means that the volume fraction of LPSO is small.
- the thickness of the LPSO is set to 0.5 ⁇ m or more. .
- the explanation is made by focusing on the fact that the fact that LPSO is thin means that the volume fraction of LPSO is small, but the fact that LPSO is thin means that the volume fraction of ⁇ Mg increases. This also means that an increase in ⁇ Mg leads to a decrease in yield strength and tensile strength.
- a yield strength higher than that of a conventional magnesium alloy is achieved, and further, a tensile strength higher than that of a conventional magnesium alloy is achieved. Can be realized.
- the thickness of LPSO that forms a laminated structure with the compound is large means that the volume fraction of LPSO is large.
- the thickness of LPSO exceeds 5 ⁇ m, the volume fraction of LPSO is too large, and the ductility of the Mg—Zn—Y—RE alloy is lowered. Therefore, in order to realize high yield strength and high tensile strength and to avoid a significant decrease in ductility, the thickness of LPSO is set to 5 ⁇ m or less.
- the thickness of at least one of the Mg-RE compound or the Mg-Zn-RE compound in the alloy structure of the Mg-Zn-Y-RE alloy is set to 0.01 ⁇ m to 2 ⁇ m, thereby further ensuring the reliability.
- FIG. 3 shows the relationship between the volume fraction of the compound in the alloy structure of the Mg—Zn—Y—RE alloy and the yield strength (YS), and the volume of the compound in the alloy structure of the Mg—Zn—Y—RE alloy.
- the relationship between a fraction and tensile strength (UTS) is shown.
- a predetermined range the range indicated by symbol A in FIG. 3
- high yield strength can be realized and high tensile strength can be realized. it can.
- the thickness of the compound constituting the laminated structure with LPSO is thin, it means that the volume fraction of the compound is small, and that the thickness of the compound is large means that the volume fraction of the compound is large. It means that.
- the thickness of a compound when the thickness of a compound is 0.01 micrometer or more and 2 micrometers or less, it will correspond to the range shown with the code
- FIG. 4 shows the relationship between the Zn content and the ductility ratio.
- the Zn component range is less than 2.5 at%.
- the ductility ratio can be ensured to be approximately 40% or more, which is more preferable.
- the magnesium alloy of the present invention can achieve high yield strength and high tensile strength.
- FIG. 1 is a photomicrograph showing the crystal structure of the Mg 97 Zn 1 Y 1 Yb 1 alloy.
- the magnesium alloy to which the present invention is applied is used for parts used in a high temperature atmosphere, such as automobile parts, in particular, pistons, valves, tappets, sprockets for internal combustion engines.
- the shape of the magnesium alloy is, for example, a plate shape or a rod shape, and is appropriately selected according to the shape of the component used.
- the magnesium alloy to which the present invention is applied contains Zn, Y as essential components and at least one of La, Ce, Nd, Pr, Sm, Yb as rare earth elements (RE), with the balance being Mg.
- Mg—Zn—Y—RE alloy composed of unavoidable impurities
- the alloy structure of Mg—Zn—Y—RE alloy includes LPSO, ⁇ Mg phase, Mg—RE compound or Mg It has at least one compound of -Zn-RE compounds.
- the magnesium alloy 1 shown in FIG. 1 has LPSO2, ⁇ Mg phase 3 and compound 4 in its alloy structure, and LPSO2 and compound 4 form a laminated structure (layered structure).
- the thickness of LPSO forming a laminated structure is 0.5 to 5 ⁇ m, and the thickness of the compound is 0.01 to 2 ⁇ m.
- the magnesium alloy of the present invention has an ⁇ Mg phase.
- the ⁇ Mg phase forms a lamellar phase with LPSO, which will be described later, in the cell structure of the Mg—Zn—Y—RE alloy (approximately 50 ⁇ m or more in average particle size) in the melt casting process.
- the ⁇ Mg phase has an average particle diameter of 2 ⁇ m in at least a part of the alloy structure of the Mg—Zn—Y—RE alloy (LPSO splitting portion) in a plastic working step performed in a high temperature atmosphere (hot). It is preferable to refine the following (a fine ⁇ Mg phase is precipitated).
- the magnesium alloy of the present invention has LPSO.
- LPSO is a precipitate that precipitates in the grain and boundary of the magnesium alloy, and is a structure in which the arrangement of bottom atomic layers in the HCP structure is repeated with a long periodic rule in the bottom normal direction, that is, a long period.
- the LPSO has a unit structure that is several times to 10 times as many as the original lattice, for example, a plurality of regular lattices are arranged, and a plurality of regular lattices are arranged again through an antiphase shift. It is made of a structure with a long period.
- LPSO appears in a slight temperature range between the regular phase and the irregular phase, and in the electron diffraction diagram, the reflection of the regular phase is split, and the position corresponds to a period of several to ten times. Diffraction spots appear on the screen. Such precipitation of LPSO improves the mechanical properties (tensile strength, yield strength and elongation) of the magnesium alloy.
- LPSO is an alloy structure of a cast material (Mg—Zn—Y—RE alloy), that is, a layered structure particle together with an ⁇ Mg phase in a cell structure in a melt casting process or a heat treatment process after melting and casting.
- a lamellar phase is formed.
- the LPSO is formed in a straight line, and the formation direction is formed in the same direction in the same cell structure, and is formed in different directions in the cell structures.
- a curved portion and a bent portion is formed on at least a part of the formed LPSO, and a divided portion in which the arrangement of the regular lattice is broken is formed.
- formation of such a curved part, a bending part, and a parting part to LPSO will be achieved by performing a plastic working process of hot plastic working a cast material or a heat-treated cast material.
- the precipitation of the fine ⁇ Mg phase refined to an average particle size of 2 ⁇ m or less in at least a part of the alloy structure of the Mg—Zn—Y—RE alloy (for example, the LPSO split portion) is also possible. This is achieved by performing a plastic working process. Note that the cell structure formed during casting by hot plastic working disappears.
- the magnesium alloy of the present invention has at least one compound of Mg-RE compound or Mg-Zn-RE compound. Specifically, for example, it has compounds such as Mg 41 Sm 5 , Mg 12 Ce, Mg 17 La 2 , Mg 12 Pr, and Mg 12 Nd. And the high yield strength and high tensile strength will be implement
- the structure is controlled so that the thickness of LPSO is 0.5 to 5 ⁇ m.
- the yield strength of a conventional magnesium alloy as an example, the yield strength of Mg 97 Zn 1 Y 2 is 350.4 MPa).
- a tensile strength higher than that of a conventional magnesium alloy as an example, the tensile strength of Mg 97 Zn 1 Y 2 is 397.2 MPa.
- a significant decrease in ductility is avoided by controlling the structure so that the thickness of LPSO is 5 ⁇ m or less.
- the structure is controlled so that the thickness of the compound (at least one compound of Mg—RE compound or Mg—Zn—RE compound) becomes 0.01 ⁇ m to 2 ⁇ m.
- the structure is controlled so that the component range of Zn is less than 2.5 at%. This is because such a structure control can avoid a significant decrease in ductility.
- it is thought that it is necessary to contain more additive elements.
- it is more preferable to control the structure of the Zn component range to 2 at% or less. By performing such structure control, it is possible to meet the above requirements, and also to ensure a ductility ratio of about 40%. Can do.
- Example shown here is an example and does not limit this invention.
- test pieces (1) to (6) shown below were prepared as magnesium alloys of the examples of the present invention.
- test pieces (7) to (12) were prepared as comparison data.
- Test piece 7 The Mg—Zn—Y alloy containing Zn at 1 at%, Y at 2 at%, the balance being Mg and inevitable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of ⁇ 29 mm ⁇ L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (7), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
- test pieces (1) to (12) obtained as described above were subjected to a tensile test at room temperature, and the results of evaluating the mechanical properties are shown in Table 1.
- the yield strength is 350.4 MPa and the tensile strength is 397.2 MPa in the case of the ternary alloy Mg—Zn—Y alloy.
- “LPSO and the compound have a laminated structure (layered structure), and the thickness of the LPSO is 0.5 to 5 ⁇ m. If the condition of “the thickness of the compound is 0.01 to 2 ⁇ m” is not satisfied, either the yield strength or the tensile strength is lower than that of the ternary alloy test piece (7).
- the yield strength is 349.8 MPa and the tensile strength is 365.9 MPa, and the yield strength and the tensile strength are lower than those of the test piece (7).
- the evaluation result of the test piece (9) shows that the yield strength is 304.4 MPa and the tensile strength is 374.8 MPa, and the yield strength and tensile strength are lower than those of the test piece (7).
- the evaluation result of the test piece (10) shows that the yield strength is 355.4 MPa and the tensile strength is 373.6 MPa, and the tensile strength is lower than that of the test piece (7).
- yield strength is 337.2 MPa and tensile strength is 369.1 MPa, and it turns out that the yield strength and tensile strength are falling rather than a test piece (7).
- the evaluation result of the test piece (12) shows that the yield strength is 325.6 MPa and the tensile strength is 364.6 MPa, and the yield strength and the tensile strength are lower than those of the test piece (7).
- LPSO and the compound have a laminated structure (layered structure), and the thickness of LPSO is 0.5 to 5 ⁇ m.
- the yield strength should be higher than that of the ternary specimen (7) having a yield strength of 350.4 MPa.
- the tensile strength higher than that of the ternary test piece (7) having a tensile strength of 397.2 MPa can be realized.
- the evaluation result of the test piece (7) of Table 1 which is a ternary alloy is used as a reference, and the test pieces (1) to (6) which are magnesium alloys of the examples of the present invention are tested. Yield strength and tensile strength higher than those of the specimen (7) can be realized, and the test specimens (8) to (12) which are magnesium alloys which are not examples of the present invention have yield strength or tensile strength higher than that of the specimen (7). The case where at least one of these is lowered is taken as an example.
- the ternary alloy achieves high yield strength and tensile strength by adjusting the conditions of the component ranges, and the magnesium alloy of the examples of the present invention is not necessarily higher in yield strength than the ternary alloy. It does not mean that the tensile strength is realized.
- LPSO and the compound have a laminated structure (layered structure), and the thickness of LPSO is 0.5 to 5 ⁇ m.
- the conditions such as “compound thickness is 0.01-2 ⁇ m” are satisfied, high yield strength and tensile strength can be realized, and “LPSO and compound have a laminated structure (layered structure), and the thickness of LPSO Is 0.5 to 5 ⁇ m and the thickness of the compound is 0.01 to 2 ⁇ m ”, it indicates that at least one of yield strength and tensile strength is reduced. .
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Abstract
Disclosed is a magnesium alloy having high yield strength and high tensile strength. Specifically disclosed is a magnesium alloy comprising an Mg-Zn-Y-RE-based alloy which contains Zn and Y as the essential components and also contains at least one element selected from La, Ce, Nd, Pr, Sm and Yb as the rare earth element (RE), with the remainder being Mg and unavoidable impurities. In the magnesium alloy, LPSO, an αMg phase and at least one compound selected from an Mg-RE compound and an Mg-Zn-RE compound are contained in an alloy structure of the Mg-Zn-Y-RE-based alloy. In the alloy, LPSO and the compound form a laminated structure, wherein the thickness of LPSO is 0.5 to 5 μm and the thickness of the compound is 0.01 to 2 μm.
Description
本発明はマグネシウム合金に関する。詳しくは、高い降伏強度を得ることができると共に、高い引張強度を得ることができるマグネシウム合金に係るものである。
The present invention relates to a magnesium alloy. Specifically, the present invention relates to a magnesium alloy that can obtain high yield strength and high tensile strength.
一般に、マグネシウム合金は、実用化されている合金の中で最も密度が低く軽量で強度も高いため、電気製品の筐体や、自動車のホイール、足回り部品、エンジン回り部品等への適用が進められている。
特に、自動車に関連する用途の部品においては、高い機械的特性が要求されるため、ＧｄやＺｎ等の元素を添加したマグネシウム合金として、片ロール法、急速凝固法により特定の形態の材料を製造することが行われている（例えば、特許文献１、特許文献２参照。）。 In general, magnesium alloys have the lowest density, light weight, and high strength among the alloys in practical use, so they are being applied to electrical housings, automobile wheels, suspension parts, engine parts, etc. It has been.
In particular, high mechanical properties are required for parts related to automobiles, and as a magnesium alloy to which elements such as Gd and Zn are added, materials of specific forms are manufactured by the single roll method and rapid solidification method. (For example, refer toPatent Document 1 and Patent Document 2).
特に、自動車に関連する用途の部品においては、高い機械的特性が要求されるため、ＧｄやＺｎ等の元素を添加したマグネシウム合金として、片ロール法、急速凝固法により特定の形態の材料を製造することが行われている（例えば、特許文献１、特許文献２参照。）。 In general, magnesium alloys have the lowest density, light weight, and high strength among the alloys in practical use, so they are being applied to electrical housings, automobile wheels, suspension parts, engine parts, etc. It has been.
In particular, high mechanical properties are required for parts related to automobiles, and as a magnesium alloy to which elements such as Gd and Zn are added, materials of specific forms are manufactured by the single roll method and rapid solidification method. (For example, refer to
しかし、上記したマグネシウム合金は、特定の製造方法においては高い機械的特性が得られるものの、特定の製造方法を実現するためには特殊な設備が必要であり、しかも、生産性が低いといった問題があり、更には、適用できる部材も限られるといった問題があった。
However, although the above-described magnesium alloy can obtain high mechanical properties in a specific manufacturing method, special equipment is required to realize the specific manufacturing method, and the productivity is low. In addition, there is a problem that applicable members are limited.
そこで、従来、マグネシウム合金を製造する場合、上記した特許文献１及び特許文献２に記載の様な特殊な設備あるいはプロセスを用いずに、生産性の高い通常の溶解鋳造から塑性加工（押出）を実施しても、実用上有用な機械的特性が得られる技術が提案されている（例えば、特許文献３参照。）。なお、特許文献３に開示されているマグネシウム合金は、３００ＭＰａ程度の引張強度を有していることが知られている。
Therefore, conventionally, when producing a magnesium alloy, plastic processing (extrusion) is performed from ordinary melt casting with high productivity without using special equipment or processes as described in Patent Document 1 and Patent Document 2 described above. A technique that can obtain practically useful mechanical characteristics even if implemented is proposed (for example, see Patent Document 3). In addition, it is known that the magnesium alloy disclosed in Patent Document 3 has a tensile strength of about 300 MPa.
また、近年使用されているＡＺ系、ＷＥ系マグネシウム合金の降伏強度は３００ＭＰａ程度であり、Ｍｇ－Ｚｎ－Ｙ系合金の場合であっても降伏強度は３５０ＭＰａ程度、引張強度は３９０ＭＰａ程度である。
Moreover, the yield strength of AZ and WE magnesium alloys used in recent years is about 300 MPa, and even in the case of an Mg—Zn—Y alloy, the yield strength is about 350 MPa and the tensile strength is about 390 MPa.
しかしながら、軽量化の目的でマグネシウム合金の自動車への応用を進めるためには、降伏強度及び引張強度を更に向上させることが要求されていた。
However, in order to advance the application of magnesium alloy to automobiles for the purpose of weight reduction, it has been required to further improve the yield strength and tensile strength.
本発明は、上記の点に鑑みて創案されたものであって、特殊な製造設備及びプロセスを使用することなく、高い降伏強度及び引張強度を得ることができるマグネシウム合金を提供することを目的とするものである。
The present invention was devised in view of the above points, and an object thereof is to provide a magnesium alloy capable of obtaining high yield strength and tensile strength without using special manufacturing equipment and processes. To do.
上記の目的を達成するために、本発明のマグネシウム合金では、必須成分としてＺｎ、Ｙ、及び、希土類元素（ＲＥ）としてＬａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ、Ｙｂのうち少なくとも１つ以上を含有し、残部がＭｇと不可避的不純物からなるＭｇ－Ｚｎ－Ｙ－ＲＥ系合金から構成されるマグネシウム合金であって、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中に、長周期積層構造相、αＭｇ相、及び、Ｍｇ－ＲＥ化合物若しくはＭｇ－Ｚｎ－ＲＥ化合物の少なくとも１つ以上の化合物を有すると共に、前記長周期積層構造相と前記化合物が積層構造を構成し、更に、前記長周期積層構造相の厚さが０．５μｍ～５μｍである。
In order to achieve the above object, the magnesium alloy of the present invention contains Zn, Y as essential components, and at least one of La, Ce, Nd, Pr, Sm, Yb as rare earth elements (RE). A magnesium alloy composed of an Mg—Zn—Y—RE alloy composed of Mg and inevitable impurities, and the long-period laminated structure phase in the alloy structure of the Mg—Zn—Y—RE alloy. , ΑMg phase, and at least one compound of Mg—RE compound or Mg—Zn—RE compound, and the long-period laminate structure phase and the compound constitute a laminate structure, and the long-period laminate The thickness of the structural phase is 0.5 μm to 5 μm.
ここで、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中の長周期積層構造相（以下、「ＬＰＳＯ：Ｌｏｎｇ Ｐｅｒｉｏｄ Ｓｔａｃｋｉｎｇ Ｏｒｄｅｒ」と称する。）の厚さを０．５μｍ～５μｍとしているのは、高い降伏強度（σ０．２）を実現すると共に、高い引張強度（σＵＴＳ）を実現するためである。以下、この点について説明を行う。
Here, the thickness of the long-period laminated structure phase (hereinafter referred to as “LPSO: Long Perioding Order”) in the alloy structure of the Mg—Zn—Y—RE alloy is 0.5 μm to 5 μm. This is because high yield strength (σ0.2) and high tensile strength (σUTS) are realized. Hereinafter, this point will be described.
図２にＭｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中のＬＰＳＯの体積分率と降伏強度（ＹＳ）との関係と、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中のＬＰＳＯの体積分率と引張強度（ＵＴＳ）との関係を示している。図２から明らかな様に、ＬＰＳＯの体積分率が増加するにつれて高い降伏強度と高い引張強度を実現することができる。
ここで、化合物と共に積層構造を構成しているＬＰＳＯの厚さが薄いということは、ＬＰＳＯの体積分率が小さいということを意味する。そして、ＬＰＳＯの厚さが０．５μｍ未満である場合には、ＬＰＳＯの体積分率が少なすぎるために、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の降伏強度が、従来のマグネシウム合金の降伏強度（一例として、Ｍｇ９７Ｚｎ１Ｙ２の降伏強度は３５０．４ＭＰａである。）よりも低下してしまう。同様に、ＬＰＳＯの厚さが０．５μｍ未満である場合には、ＬＰＳＯの体積分率が少なすぎるために、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の引張強度が、従来のマグネシウム合金の引張強度（一例として、Ｍｇ９７Ｚｎ１Ｙ２の引張強度は３９７．２ＭＰａである。）よりも低下してしまう。
従って、従来のマグネシウム合金の降伏強度よりも高い降伏強度を実現すると共に、従来のマグネシウム合金の引張強度よりも高い引張強度を実現するために、ＬＰＳＯの厚さを０．５μｍ以上としているのである。 FIG. 2 shows the relationship between the volume fraction of LPSO and the yield strength (YS) in the alloy structure of the Mg—Zn—Y—RE alloy, and the volume of LPSO in the alloy structure of the Mg—Zn—Y—RE alloy. The relationship between a fraction and tensile strength (UTS) is shown. As can be seen from FIG. 2, high yield strength and high tensile strength can be realized as the volume fraction of LPSO increases.
Here, the fact that the thickness of LPSO that forms a laminated structure together with the compound is thin means that the volume fraction of LPSO is small. When the LPSO thickness is less than 0.5 μm, the LPSO volume fraction is too small, so that the yield strength of the Mg—Zn—Y—RE alloy is less than the yield strength of the conventional magnesium alloy ( As an example, the yield strength of Mg 97 Zn 1 Y 2 is 350.4 MPa. Similarly, when the LPSO thickness is less than 0.5 μm, the volume fraction of LPSO is too small, so that the tensile strength of the Mg—Zn—Y—RE alloy is the tensile strength of the conventional magnesium alloy. (As an example, the tensile strength of Mg 97 Zn 1 Y 2 is 397.2 MPa.).
Therefore, in order to realize a yield strength higher than that of the conventional magnesium alloy and also to achieve a tensile strength higher than that of the conventional magnesium alloy, the thickness of the LPSO is set to 0.5 μm or more. .
ここで、化合物と共に積層構造を構成しているＬＰＳＯの厚さが薄いということは、ＬＰＳＯの体積分率が小さいということを意味する。そして、ＬＰＳＯの厚さが０．５μｍ未満である場合には、ＬＰＳＯの体積分率が少なすぎるために、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の降伏強度が、従来のマグネシウム合金の降伏強度（一例として、Ｍｇ９７Ｚｎ１Ｙ２の降伏強度は３５０．４ＭＰａである。）よりも低下してしまう。同様に、ＬＰＳＯの厚さが０．５μｍ未満である場合には、ＬＰＳＯの体積分率が少なすぎるために、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の引張強度が、従来のマグネシウム合金の引張強度（一例として、Ｍｇ９７Ｚｎ１Ｙ２の引張強度は３９７．２ＭＰａである。）よりも低下してしまう。
従って、従来のマグネシウム合金の降伏強度よりも高い降伏強度を実現すると共に、従来のマグネシウム合金の引張強度よりも高い引張強度を実現するために、ＬＰＳＯの厚さを０．５μｍ以上としているのである。 FIG. 2 shows the relationship between the volume fraction of LPSO and the yield strength (YS) in the alloy structure of the Mg—Zn—Y—RE alloy, and the volume of LPSO in the alloy structure of the Mg—Zn—Y—RE alloy. The relationship between a fraction and tensile strength (UTS) is shown. As can be seen from FIG. 2, high yield strength and high tensile strength can be realized as the volume fraction of LPSO increases.
Here, the fact that the thickness of LPSO that forms a laminated structure together with the compound is thin means that the volume fraction of LPSO is small. When the LPSO thickness is less than 0.5 μm, the LPSO volume fraction is too small, so that the yield strength of the Mg—Zn—Y—RE alloy is less than the yield strength of the conventional magnesium alloy ( As an example, the yield strength of Mg 97 Zn 1 Y 2 is 350.4 MPa. Similarly, when the LPSO thickness is less than 0.5 μm, the volume fraction of LPSO is too small, so that the tensile strength of the Mg—Zn—Y—RE alloy is the tensile strength of the conventional magnesium alloy. (As an example, the tensile strength of Mg 97 Zn 1 Y 2 is 397.2 MPa.).
Therefore, in order to realize a yield strength higher than that of the conventional magnesium alloy and also to achieve a tensile strength higher than that of the conventional magnesium alloy, the thickness of the LPSO is set to 0.5 μm or more. .
なお、ここでは、ＬＰＳＯが薄いということは、ＬＰＳＯの体積分率が小さいということに着目して説明を行っているが、ＬＰＳＯの厚さが薄いということは、αＭｇの体積分率が増加することをも意味しており、αＭｇが増加することによっても降伏強度や引張強度が低下することにつながる。いずれにしても、ＬＰＳＯの厚さを０．５μｍ以上とすることによって、従来のマグネシウム合金の降伏強度よりも高い降伏強度を実現し、更に、従来のマグネシウム合金の引張強度よりも高い引張強度を実現することができる。
Here, the explanation is made by focusing on the fact that the fact that LPSO is thin means that the volume fraction of LPSO is small, but the fact that LPSO is thin means that the volume fraction of αMg increases. This also means that an increase in αMg leads to a decrease in yield strength and tensile strength. In any case, by setting the thickness of LPSO to 0.5 μm or more, a yield strength higher than that of a conventional magnesium alloy is achieved, and further, a tensile strength higher than that of a conventional magnesium alloy is achieved. Can be realized.
ところで、上述の通り、ＬＰＳＯの体積分率が増加するにつれて高い降伏強度と高い引張強度を実現することができるのであるが、その反面、ＬＰＳＯの体積分率の増加につれて延性は低下することとなる。
ここで、化合物と共に積層構造を構成しているＬＰＳＯの厚さが厚いということは、ＬＰＳＯの体積分率が大きいことを意味する。そして、ＬＰＳＯの厚さが５μｍを超えた場合には、ＬＰＳＯの体積分率が大きすぎるために、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の延性が低下してしまう。
従って、高い降伏強度と高い引張強度を実現すると共に、延性の著しい低下を回避するために、ＬＰＳＯの厚さを５μｍ以下としているのである。 By the way, as described above, high yield strength and high tensile strength can be realized as the volume fraction of LPSO increases, but on the other hand, ductility decreases as the volume fraction of LPSO increases. .
Here, the fact that the thickness of LPSO that forms a laminated structure with the compound is large means that the volume fraction of LPSO is large. When the thickness of LPSO exceeds 5 μm, the volume fraction of LPSO is too large, and the ductility of the Mg—Zn—Y—RE alloy is lowered.
Therefore, in order to realize high yield strength and high tensile strength and to avoid a significant decrease in ductility, the thickness of LPSO is set to 5 μm or less.
ここで、化合物と共に積層構造を構成しているＬＰＳＯの厚さが厚いということは、ＬＰＳＯの体積分率が大きいことを意味する。そして、ＬＰＳＯの厚さが５μｍを超えた場合には、ＬＰＳＯの体積分率が大きすぎるために、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の延性が低下してしまう。
従って、高い降伏強度と高い引張強度を実現すると共に、延性の著しい低下を回避するために、ＬＰＳＯの厚さを５μｍ以下としているのである。 By the way, as described above, high yield strength and high tensile strength can be realized as the volume fraction of LPSO increases, but on the other hand, ductility decreases as the volume fraction of LPSO increases. .
Here, the fact that the thickness of LPSO that forms a laminated structure with the compound is large means that the volume fraction of LPSO is large. When the thickness of LPSO exceeds 5 μm, the volume fraction of LPSO is too large, and the ductility of the Mg—Zn—Y—RE alloy is lowered.
Therefore, in order to realize high yield strength and high tensile strength and to avoid a significant decrease in ductility, the thickness of LPSO is set to 5 μm or less.
また、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中のＭｇ－ＲＥ化合物若しくはＭｇ－Ｚｎ－ＲＥ化合物の少なくとも１つ以上の化合物の厚さを０．０１μｍ～２μｍとすることで、更に確実に高い降伏強度を実現することができると共に、高い引張強度を実現することができる。以下、この点について説明を行う。
Further, the thickness of at least one of the Mg-RE compound or the Mg-Zn-RE compound in the alloy structure of the Mg-Zn-Y-RE alloy is set to 0.01 μm to 2 μm, thereby further ensuring the reliability. In addition, it is possible to realize a high yield strength and a high tensile strength. Hereinafter, this point will be described.
図３にＭｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中の化合物の体積分率と降伏強度（ＹＳ）との関係と、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中の化合物の体積分率と引張強度（ＵＴＳ）との関係を示している。図３から明らかな様に、化合物の体積分率が所定範囲（図３中符号Ａで示す範囲）に属する場合に、高い降伏強度を実現することができると共に、高い引張強度を実現することができる。
ここで、ＬＰＳＯと共に積層構造を構成している化合物の厚さが薄いということは化合物の体積分率が小さいということを意味し、化合物の厚さが厚いということは化合物の体積分率が大きいということを意味する。そして、化合物の厚さが０．０１μｍ以上２μｍ以下である場合には、概ね図３中符号Ａで示す範囲に該当することとなる。
従って、化合物の厚さが０．０１μｍ～２μｍとすると、更に確実に高い降伏強度を実現することができると共に、高い引張強度を実現することができるのである。 FIG. 3 shows the relationship between the volume fraction of the compound in the alloy structure of the Mg—Zn—Y—RE alloy and the yield strength (YS), and the volume of the compound in the alloy structure of the Mg—Zn—Y—RE alloy. The relationship between a fraction and tensile strength (UTS) is shown. As is clear from FIG. 3, when the volume fraction of the compound belongs to a predetermined range (the range indicated by symbol A in FIG. 3), high yield strength can be realized and high tensile strength can be realized. it can.
Here, when the thickness of the compound constituting the laminated structure with LPSO is thin, it means that the volume fraction of the compound is small, and that the thickness of the compound is large means that the volume fraction of the compound is large. It means that. And when the thickness of a compound is 0.01 micrometer or more and 2 micrometers or less, it will correspond to the range shown with the code | symbol A in FIG.
Therefore, when the thickness of the compound is 0.01 μm to 2 μm, a higher yield strength can be realized more reliably and a higher tensile strength can be realized.
ここで、ＬＰＳＯと共に積層構造を構成している化合物の厚さが薄いということは化合物の体積分率が小さいということを意味し、化合物の厚さが厚いということは化合物の体積分率が大きいということを意味する。そして、化合物の厚さが０．０１μｍ以上２μｍ以下である場合には、概ね図３中符号Ａで示す範囲に該当することとなる。
従って、化合物の厚さが０．０１μｍ～２μｍとすると、更に確実に高い降伏強度を実現することができると共に、高い引張強度を実現することができるのである。 FIG. 3 shows the relationship between the volume fraction of the compound in the alloy structure of the Mg—Zn—Y—RE alloy and the yield strength (YS), and the volume of the compound in the alloy structure of the Mg—Zn—Y—RE alloy. The relationship between a fraction and tensile strength (UTS) is shown. As is clear from FIG. 3, when the volume fraction of the compound belongs to a predetermined range (the range indicated by symbol A in FIG. 3), high yield strength can be realized and high tensile strength can be realized. it can.
Here, when the thickness of the compound constituting the laminated structure with LPSO is thin, it means that the volume fraction of the compound is small, and that the thickness of the compound is large means that the volume fraction of the compound is large. It means that. And when the thickness of a compound is 0.01 micrometer or more and 2 micrometers or less, it will correspond to the range shown with the code | symbol A in FIG.
Therefore, when the thickness of the compound is 0.01 μm to 2 μm, a higher yield strength can be realized more reliably and a higher tensile strength can be realized.
更に、Ｚｎの成分範囲を２．５ａｔ％未満とすると、延性の低下を抑制することができる。図４にＺｎの含有量と延性比との関係を示している。図４から明らかな様に、Ｚｎの含有量が２．５ａｔ％以上になると延性比が概ね３０％よりも低下することとなる。従って、高い降伏強度を実現し、高い引張強度を実現すると共に、延性の著しい低下を回避するためには、Ｚｎの成分範囲を２．５ａｔ％未満とする方が好ましい。なお、Ｚｎの成分範囲を２ａｔ％以下にすると、延性比が概ね４０％以上を確保することができるために、より一層好ましいといえる。
Furthermore, when the component range of Zn is less than 2.5 at%, a decrease in ductility can be suppressed. FIG. 4 shows the relationship between the Zn content and the ductility ratio. As is apparent from FIG. 4, when the Zn content is 2.5 at% or more, the ductility ratio is generally lower than 30%. Therefore, in order to achieve a high yield strength, a high tensile strength, and to avoid a significant decrease in ductility, it is preferable that the Zn component range is less than 2.5 at%. In addition, it can be said that when the component range of Zn is 2 at% or less, the ductility ratio can be ensured to be approximately 40% or more, which is more preferable.
本発明のマグネシウム合金では、高い降伏強度を実現することができると共に、高い引張強度をも実現することができる。
The magnesium alloy of the present invention can achieve high yield strength and high tensile strength.
以下、本発明の実施の形態について図面を参酌しながら説明し、本発明の理解に供する。
図１はＭｇ９７Ｚｎ１Ｙ１Ｙｂ１合金の結晶組織を示す顕微鏡写真である。 Hereinafter, embodiments of the present invention will be described with reference to the drawings to provide an understanding of the present invention.
FIG. 1 is a photomicrograph showing the crystal structure of the Mg 97 Zn 1 Y 1 Yb 1 alloy.
図１はＭｇ９７Ｚｎ１Ｙ１Ｙｂ１合金の結晶組織を示す顕微鏡写真である。 Hereinafter, embodiments of the present invention will be described with reference to the drawings to provide an understanding of the present invention.
FIG. 1 is a photomicrograph showing the crystal structure of the Mg 97 Zn 1 Y 1 Yb 1 alloy.
本発明を適用したマグネシウム合金は、高温雰囲気で使用される部品、例えば、自動車用部品、特に、内燃機関用ピストン、バルブ、タペット、スプロケット等に使用される。なお、マグネシウム合金の形状については、例えば、板状や棒状等であって、使用される部品の形状に応じて適宜選択されることとなる。
The magnesium alloy to which the present invention is applied is used for parts used in a high temperature atmosphere, such as automobile parts, in particular, pistons, valves, tappets, sprockets for internal combustion engines. The shape of the magnesium alloy is, for example, a plate shape or a rod shape, and is appropriately selected according to the shape of the component used.
さて、本発明を適用したマグネシウム合金は、必須成分としてＺｎ、Ｙ、及び、希土類元素（ＲＥ）としてＬａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ、Ｙｂのうち少なくとも１つ以上を含有し、残部がＭｇと不可避的不純物からなるＭｇ－Ｚｎ－Ｙ－ＲＥ系合金から構成されており、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中には、ＬＰＳＯ、αＭｇ相、及び、Ｍｇ－ＲＥ化合物若しくはＭｇ－Ｚｎ－ＲＥ化合物の少なくとも１つ以上の化合物を有している。
The magnesium alloy to which the present invention is applied contains Zn, Y as essential components and at least one of La, Ce, Nd, Pr, Sm, Yb as rare earth elements (RE), with the balance being Mg. Mg—Zn—Y—RE alloy composed of unavoidable impurities, and the alloy structure of Mg—Zn—Y—RE alloy includes LPSO, αMg phase, Mg—RE compound or Mg It has at least one compound of -Zn-RE compounds.
ここで、図１で示すマグネシウム合金１は、その合金組織中に、ＬＰＳＯ２、αＭｇ相３及び化合物４とを有し、ＬＰＳＯ２と化合物４とが積層構造（層状構造）を形成している。なお、図１で示すマグネシウム合金では、積層構造をなすＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍである。
Here, the magnesium alloy 1 shown in FIG. 1 has LPSO2, αMg phase 3 and compound 4 in its alloy structure, and LPSO2 and compound 4 form a laminated structure (layered structure). In the magnesium alloy shown in FIG. 1, the thickness of LPSO forming a laminated structure is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm.
［αＭｇ相について］
先ず、本発明のマグネシウム合金は、αＭｇ相を有している。
ここで、αＭｇ相は、溶解鋳造工程において、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金のセル構造（概ね平均粒径５０μｍ以上）内で、後述するＬＰＳＯとラメラ相を形成する。なお、αＭｇ相は、高温雰囲気下（熱間）で行われる塑性加工工程において、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中の少なくとも一部（ＬＰＳＯの分断部）が、平均粒径２μｍ以下に微細化した（微細αＭｇ相が析出した）方が好ましい。 [About αMg phase]
First, the magnesium alloy of the present invention has an αMg phase.
Here, the αMg phase forms a lamellar phase with LPSO, which will be described later, in the cell structure of the Mg—Zn—Y—RE alloy (approximately 50 μm or more in average particle size) in the melt casting process. The αMg phase has an average particle diameter of 2 μm in at least a part of the alloy structure of the Mg—Zn—Y—RE alloy (LPSO splitting portion) in a plastic working step performed in a high temperature atmosphere (hot). It is preferable to refine the following (a fine αMg phase is precipitated).
先ず、本発明のマグネシウム合金は、αＭｇ相を有している。
ここで、αＭｇ相は、溶解鋳造工程において、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金のセル構造（概ね平均粒径５０μｍ以上）内で、後述するＬＰＳＯとラメラ相を形成する。なお、αＭｇ相は、高温雰囲気下（熱間）で行われる塑性加工工程において、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中の少なくとも一部（ＬＰＳＯの分断部）が、平均粒径２μｍ以下に微細化した（微細αＭｇ相が析出した）方が好ましい。 [About αMg phase]
First, the magnesium alloy of the present invention has an αMg phase.
Here, the αMg phase forms a lamellar phase with LPSO, which will be described later, in the cell structure of the Mg—Zn—Y—RE alloy (approximately 50 μm or more in average particle size) in the melt casting process. The αMg phase has an average particle diameter of 2 μm in at least a part of the alloy structure of the Mg—Zn—Y—RE alloy (LPSO splitting portion) in a plastic working step performed in a high temperature atmosphere (hot). It is preferable to refine the following (a fine αMg phase is precipitated).
［ＬＰＳＯについて］
また、本発明のマグネシウム合金は、ＬＰＳＯを有している。
ここで、ＬＰＳＯとは、マグネシウム合金の粒内及び粒界に析出する析出物であって、ＨＣＰ構造における底面原子層の並びが底面法線方向に長周期規則をもって繰り返される構造、即ち、長周期構造をいう。更に詳細には、ＬＰＳＯは、例えば、規則格子が複数個並び、逆位相のズレを介して再び規則格子が複数個並びといった具合に、元の格子の数倍から１０数倍の単位の構造が作られ、その周期が長い構造のものをいう。そして、ＬＰＳＯは、規則相と不規則相との間のわずかな温度範囲に出現し、電子回折した図には規則相の反射が分裂して、数倍から１０数倍の周期に対応する位置に回折斑点が現れることとなる。
こうしたＬＰＳＯの析出によって、マグネシウム合金の機械的特性（引張強度、降伏強度及び伸び）が向上することとなる。 [About LPSO]
The magnesium alloy of the present invention has LPSO.
Here, LPSO is a precipitate that precipitates in the grain and boundary of the magnesium alloy, and is a structure in which the arrangement of bottom atomic layers in the HCP structure is repeated with a long periodic rule in the bottom normal direction, that is, a long period. Refers to the structure. More specifically, the LPSO has a unit structure that is several times to 10 times as many as the original lattice, for example, a plurality of regular lattices are arranged, and a plurality of regular lattices are arranged again through an antiphase shift. It is made of a structure with a long period. LPSO appears in a slight temperature range between the regular phase and the irregular phase, and in the electron diffraction diagram, the reflection of the regular phase is split, and the position corresponds to a period of several to ten times. Diffraction spots appear on the screen.
Such precipitation of LPSO improves the mechanical properties (tensile strength, yield strength and elongation) of the magnesium alloy.
また、本発明のマグネシウム合金は、ＬＰＳＯを有している。
ここで、ＬＰＳＯとは、マグネシウム合金の粒内及び粒界に析出する析出物であって、ＨＣＰ構造における底面原子層の並びが底面法線方向に長周期規則をもって繰り返される構造、即ち、長周期構造をいう。更に詳細には、ＬＰＳＯは、例えば、規則格子が複数個並び、逆位相のズレを介して再び規則格子が複数個並びといった具合に、元の格子の数倍から１０数倍の単位の構造が作られ、その周期が長い構造のものをいう。そして、ＬＰＳＯは、規則相と不規則相との間のわずかな温度範囲に出現し、電子回折した図には規則相の反射が分裂して、数倍から１０数倍の周期に対応する位置に回折斑点が現れることとなる。
こうしたＬＰＳＯの析出によって、マグネシウム合金の機械的特性（引張強度、降伏強度及び伸び）が向上することとなる。 [About LPSO]
The magnesium alloy of the present invention has LPSO.
Here, LPSO is a precipitate that precipitates in the grain and boundary of the magnesium alloy, and is a structure in which the arrangement of bottom atomic layers in the HCP structure is repeated with a long periodic rule in the bottom normal direction, that is, a long period. Refers to the structure. More specifically, the LPSO has a unit structure that is several times to 10 times as many as the original lattice, for example, a plurality of regular lattices are arranged, and a plurality of regular lattices are arranged again through an antiphase shift. It is made of a structure with a long period. LPSO appears in a slight temperature range between the regular phase and the irregular phase, and in the electron diffraction diagram, the reflection of the regular phase is split, and the position corresponds to a period of several to ten times. Diffraction spots appear on the screen.
Such precipitation of LPSO improves the mechanical properties (tensile strength, yield strength and elongation) of the magnesium alloy.
また、ＬＰＳＯは、溶解鋳造工程、または、溶解、鋳造後の熱処理工程において、鋳造材（Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金）の合金組織、即ち、セル構造内で、αＭｇ相と共に層状組織粒であるラメラ相を形成する。そして、ＬＰＳＯは直線状に形成され、その形成方向は、同一セル構造内では同一方向に形成され、セル構造同士では互いに異なる方向に形成される。
In addition, LPSO is an alloy structure of a cast material (Mg—Zn—Y—RE alloy), that is, a layered structure particle together with an αMg phase in a cell structure in a melt casting process or a heat treatment process after melting and casting. A lamellar phase is formed. The LPSO is formed in a straight line, and the formation direction is formed in the same direction in the same cell structure, and is formed in different directions in the cell structures.
ところで、ＬＰＳＯが形成されたままの状態では、マグネシウム合金材の機械的性質が不充分であり、高い引張強度及び降伏強度を維持しながら、高い伸びを得ることができない。そのため、形成されたＬＰＳＯの少なくとも一部に湾曲部及び屈曲部のうち少なくとも一方を形成し、かつ、規則格子の並びが壊れた分断部を形成する。なお、こうしたＬＰＳＯへの湾曲部、屈曲部、分断部の形成は、鋳造材、または、熱処理された鋳造材を熱間塑性加工する塑性加工工程を行うことによって達成されることとなる。
By the way, in the state where LPSO is formed, the mechanical properties of the magnesium alloy material are insufficient, and high elongation cannot be obtained while maintaining high tensile strength and yield strength. Therefore, at least one of a curved portion and a bent portion is formed on at least a part of the formed LPSO, and a divided portion in which the arrangement of the regular lattice is broken is formed. In addition, formation of such a curved part, a bending part, and a parting part to LPSO will be achieved by performing a plastic working process of hot plastic working a cast material or a heat-treated cast material.
ここで、上述した様に、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中の少なくとも一部（例えば、ＬＰＳＯの分断部）における平均粒径２μｍ以下に微細化された微細αＭｇ相の析出も、塑性加工工程を行うことによって達成されることとなる。なお、熱間塑性加工によって鋳造時に形成されたセル構造は消失する。
Here, as described above, the precipitation of the fine αMg phase refined to an average particle size of 2 μm or less in at least a part of the alloy structure of the Mg—Zn—Y—RE alloy (for example, the LPSO split portion) is also possible. This is achieved by performing a plastic working process. Note that the cell structure formed during casting by hot plastic working disappears.
［化合物について］
また、本発明のマグネシウム合金は、Ｍｇ－ＲＥ化合物若しくはＭｇ－Ｚｎ－ＲＥ化合物の少なくとも１つ以上の化合物を有している。具体的には、例えば、Ｍｇ４１Ｓｍ５、Ｍｇ１２Ｃｅ、Ｍｇ１７Ｌａ２、Ｍｇ１２Ｐｒ、Ｍｇ１２Ｎｄといった化合物を有している。
そして、こうした化合物の分散度合いが高いことによって、高い降伏強度と高い引張強度が実現することとなる。 [Compound]
Further, the magnesium alloy of the present invention has at least one compound of Mg-RE compound or Mg-Zn-RE compound. Specifically, for example, it has compounds such as Mg 41 Sm 5 , Mg 12 Ce, Mg 17 La 2 , Mg 12 Pr, and Mg 12 Nd.
And the high yield strength and high tensile strength will be implement | achieved by the dispersion degree of such a compound being high.
また、本発明のマグネシウム合金は、Ｍｇ－ＲＥ化合物若しくはＭｇ－Ｚｎ－ＲＥ化合物の少なくとも１つ以上の化合物を有している。具体的には、例えば、Ｍｇ４１Ｓｍ５、Ｍｇ１２Ｃｅ、Ｍｇ１７Ｌａ２、Ｍｇ１２Ｐｒ、Ｍｇ１２Ｎｄといった化合物を有している。
そして、こうした化合物の分散度合いが高いことによって、高い降伏強度と高い引張強度が実現することとなる。 [Compound]
Further, the magnesium alloy of the present invention has at least one compound of Mg-RE compound or Mg-Zn-RE compound. Specifically, for example, it has compounds such as Mg 41 Sm 5 , Mg 12 Ce, Mg 17 La 2 , Mg 12 Pr, and Mg 12 Nd.
And the high yield strength and high tensile strength will be implement | achieved by the dispersion degree of such a compound being high.
［ＬＰＳＯの厚さについて］
本発明のマグネシウム合金では、ＬＰＳＯの厚さが０．５～５μｍとなる様に組織制御を行っている。
ここで、ＬＰＳＯの厚さが０．５μｍ以上となる様に組織制御を行うことによって、従来のマグネシウム合金の降伏強度（一例として、Ｍｇ９７Ｚｎ１Ｙ２の降伏強度は３５０．４ＭＰａである。）よりも高い降伏強度を実現すると共に、従来のマグネシウム合金の引張強度（一例として、Ｍｇ９７Ｚｎ１Ｙ２の引張強度は３９７．２ＭＰａである。）よりも高い引張強度を実現することとなる。また、ＬＰＳＯの厚さが５μｍ以下となる様に組織制御を行うことによって、延性の著しい低下を回避している。 [LPSO thickness]
In the magnesium alloy of the present invention, the structure is controlled so that the thickness of LPSO is 0.5 to 5 μm.
Here, by controlling the structure so that the thickness of LPSO becomes 0.5 μm or more, the yield strength of a conventional magnesium alloy (as an example, the yield strength of Mg 97 Zn 1 Y 2 is 350.4 MPa). ) And a tensile strength higher than that of a conventional magnesium alloy (as an example, the tensile strength of Mg 97 Zn 1 Y 2 is 397.2 MPa). . In addition, a significant decrease in ductility is avoided by controlling the structure so that the thickness of LPSO is 5 μm or less.
本発明のマグネシウム合金では、ＬＰＳＯの厚さが０．５～５μｍとなる様に組織制御を行っている。
ここで、ＬＰＳＯの厚さが０．５μｍ以上となる様に組織制御を行うことによって、従来のマグネシウム合金の降伏強度（一例として、Ｍｇ９７Ｚｎ１Ｙ２の降伏強度は３５０．４ＭＰａである。）よりも高い降伏強度を実現すると共に、従来のマグネシウム合金の引張強度（一例として、Ｍｇ９７Ｚｎ１Ｙ２の引張強度は３９７．２ＭＰａである。）よりも高い引張強度を実現することとなる。また、ＬＰＳＯの厚さが５μｍ以下となる様に組織制御を行うことによって、延性の著しい低下を回避している。 [LPSO thickness]
In the magnesium alloy of the present invention, the structure is controlled so that the thickness of LPSO is 0.5 to 5 μm.
Here, by controlling the structure so that the thickness of LPSO becomes 0.5 μm or more, the yield strength of a conventional magnesium alloy (as an example, the yield strength of Mg 97 Zn 1 Y 2 is 350.4 MPa). ) And a tensile strength higher than that of a conventional magnesium alloy (as an example, the tensile strength of Mg 97 Zn 1 Y 2 is 397.2 MPa). . In addition, a significant decrease in ductility is avoided by controlling the structure so that the thickness of LPSO is 5 μm or less.
［化合物の厚さについて］
本発明のマグネシウム合金では、化合物（Ｍｇ－ＲＥ化合物若しくはＭｇ－Ｚｎ－ＲＥ化合物の少なくとも１つ以上の化合物）の厚さが０．０１μｍ～２μｍとなる様に組織制御を行っている。
この様な組織制御を行うことによって、確実に高い降伏強度を実現することができると共に、高い引張強度を実現することができることとなる。 [About compound thickness]
In the magnesium alloy of the present invention, the structure is controlled so that the thickness of the compound (at least one compound of Mg—RE compound or Mg—Zn—RE compound) becomes 0.01 μm to 2 μm.
By performing such structure control, a high yield strength can be surely realized and a high tensile strength can be realized.
本発明のマグネシウム合金では、化合物（Ｍｇ－ＲＥ化合物若しくはＭｇ－Ｚｎ－ＲＥ化合物の少なくとも１つ以上の化合物）の厚さが０．０１μｍ～２μｍとなる様に組織制御を行っている。
この様な組織制御を行うことによって、確実に高い降伏強度を実現することができると共に、高い引張強度を実現することができることとなる。 [About compound thickness]
In the magnesium alloy of the present invention, the structure is controlled so that the thickness of the compound (at least one compound of Mg—RE compound or Mg—Zn—RE compound) becomes 0.01 μm to 2 μm.
By performing such structure control, a high yield strength can be surely realized and a high tensile strength can be realized.
［Ｚｎの成分範囲について］
本発明のマグネシウム合金では、Ｚｎの成分範囲が２．５ａｔ％未満となる様に組織制御を行っている。この様な組織制御を行うことによって、延性の著しい低下を回避することができるためである。
なお、ＬＰＳＯと金属間化合物をより多く存在させるためには、より多くの添加元素を含有させる必要があるとも考えられる。しかし、多くの添加元素を含有させた場合にはコスト面で不利となってしまうために、添加元素量はできる限り制限したいといった要求がある。したがって、Ｚｎの成分範囲を２ａｔ％以下に組織制御することがより好ましく、こうした組織制御を行うことによって、上記の要求にも応じることができ、更には、延性比も約４０％を確保することができる。 [Zn component range]
In the magnesium alloy of the present invention, the structure is controlled so that the component range of Zn is less than 2.5 at%. This is because such a structure control can avoid a significant decrease in ductility.
In addition, in order to make LPSO and an intermetallic compound more exist, it is thought that it is necessary to contain more additive elements. However, when many additive elements are contained, there is a cost disadvantage, and there is a demand for limiting the amount of additive elements as much as possible. Therefore, it is more preferable to control the structure of the Zn component range to 2 at% or less. By performing such structure control, it is possible to meet the above requirements, and also to ensure a ductility ratio of about 40%. Can do.
本発明のマグネシウム合金では、Ｚｎの成分範囲が２．５ａｔ％未満となる様に組織制御を行っている。この様な組織制御を行うことによって、延性の著しい低下を回避することができるためである。
なお、ＬＰＳＯと金属間化合物をより多く存在させるためには、より多くの添加元素を含有させる必要があるとも考えられる。しかし、多くの添加元素を含有させた場合にはコスト面で不利となってしまうために、添加元素量はできる限り制限したいといった要求がある。したがって、Ｚｎの成分範囲を２ａｔ％以下に組織制御することがより好ましく、こうした組織制御を行うことによって、上記の要求にも応じることができ、更には、延性比も約４０％を確保することができる。 [Zn component range]
In the magnesium alloy of the present invention, the structure is controlled so that the component range of Zn is less than 2.5 at%. This is because such a structure control can avoid a significant decrease in ductility.
In addition, in order to make LPSO and an intermetallic compound more exist, it is thought that it is necessary to contain more additive elements. However, when many additive elements are contained, there is a cost disadvantage, and there is a demand for limiting the amount of additive elements as much as possible. Therefore, it is more preferable to control the structure of the Zn component range to 2 at% or less. By performing such structure control, it is possible to meet the above requirements, and also to ensure a ductility ratio of about 40%. Can do.
以下、本発明の実施例について説明を行う。なお、ここで示す実施例は一例であり本発明を限定するものではない。
Hereinafter, examples of the present invention will be described. In addition, the Example shown here is an example and does not limit this invention.
先ず、本発明の実施例のマグネシウム合金として、以下に示す（１）～（６）の試験片を作成した。
First, test pieces (1) to (6) shown below were prepared as magnesium alloys of the examples of the present invention.
［試験片（１）］
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｌａを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｌａ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（１）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (1)]
Mg—Zn—Y—La alloy containing 2 at% Zn, 1 at% Y, 1 at% La, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (1), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｌａを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｌａ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（１）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (1)]
Mg—Zn—Y—La alloy containing 2 at% Zn, 1 at% Y, 1 at% La, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (1), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
［試験片（２）］
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｃｅを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｃｅ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（２）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (2)]
Mg—Zn—Y—Ce alloy containing 2 at% Zn, 1 at% Y, 1 at% Ce and the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (2), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｃｅを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｃｅ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（２）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (2)]
Mg—Zn—Y—Ce alloy containing 2 at% Zn, 1 at% Y, 1 at% Ce and the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (2), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
［試験片（３）］
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｌａを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｌａ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（３）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (3)]
Mg—Zn—Y—La alloy containing Zn at 1 at%, Y at 1 at%, La at 1 at%, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (3), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｌａを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｌａ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（３）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (3)]
Mg—Zn—Y—La alloy containing Zn at 1 at%, Y at 1 at%, La at 1 at%, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (3), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
［試験片（４）］
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｃｅを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｃｅ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（４）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (4)]
Mg—Zn—Y—Ce alloy containing Zn at 1 at%, Y at 1 at%, Ce at 1 at%, the balance being Mg and inevitable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (4), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｃｅを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｃｅ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（４）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (4)]
Mg—Zn—Y—Ce alloy containing Zn at 1 at%, Y at 1 at%, Ce at 1 at%, the balance being Mg and inevitable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (4), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
［試験片（５）］
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｐｒを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｐｒ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（５）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (5)]
Mg—Zn—Y—Pr alloy containing Zn at 1 at%, Y at 1 at%, Pr at 1 at%, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (5), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｐｒを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｐｒ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（５）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (5)]
Mg—Zn—Y—Pr alloy containing Zn at 1 at%, Y at 1 at%, Pr at 1 at%, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (5), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
［試験片（６）］
Ｚｎを１ａｔ％、Ｙを１．５ａｔ％、Ｌａを０．５ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｌａ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（６）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (6)]
Zn is 1 at%, Y is 1.5 at%, La is 0.5 at%, and the balance is Mg and Mg—Zn—Y—La alloy of inevitable impurities is put into a vacuum melting furnace and melted by flux refining. It was. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (6), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
Ｚｎを１ａｔ％、Ｙを１．５ａｔ％、Ｌａを０．５ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｌａ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（６）では、ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍとなる様に組織制御を行った。 [Specimen (6)]
Zn is 1 at%, Y is 1.5 at%, La is 0.5 at%, and the balance is Mg and Mg—Zn—Y—La alloy of inevitable impurities is put into a vacuum melting furnace and melted by flux refining. It was. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (6), LPSO and the compound have a laminated structure (layered structure), the thickness of LPSO is 0.5 to 5 μm, and the thickness of the compound is 0.01 to 2 μm. Tissue control was performed.
また、比較データとして、以下に示す（７）～（１２）の試験片を作成した。
Moreover, the following test pieces (7) to (12) were prepared as comparison data.
［試験片７］
Ｚｎを１ａｔ％、Ｙを２ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（７）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Test piece 7]
The Mg—Zn—Y alloy containing Zn at 1 at%, Y at 2 at%, the balance being Mg and inevitable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (7), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
Ｚｎを１ａｔ％、Ｙを２ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（７）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Test piece 7]
The Mg—Zn—Y alloy containing Zn at 1 at%, Y at 2 at%, the balance being Mg and inevitable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (7), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
［試験片（８）］
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｎｄを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｎｄ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（８）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (8)]
Mg—Zn—Y—Nd alloy containing 2 at% Zn, 1 at% Y, 1 at% Nd, and the balance Mg and unavoidable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (8), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｎｄを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｎｄ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（８）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (8)]
Mg—Zn—Y—Nd alloy containing 2 at% Zn, 1 at% Y, 1 at% Nd, and the balance Mg and unavoidable impurities was put into a vacuum melting furnace, and melting was performed by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (8), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
［試験片（９）］
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｓｍを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｓｍ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（９）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (9)]
Mg—Zn—Y—Sm alloy containing 2 at% Zn, 1 at% Y, 1 at% Sm, and the balance Mg and inevitable impurities being put into a vacuum melting furnace was melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (9), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｓｍを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｓｍ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（９）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (9)]
Mg—Zn—Y—Sm alloy containing 2 at% Zn, 1 at% Y, 1 at% Sm, and the balance Mg and inevitable impurities being put into a vacuum melting furnace was melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (9), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
［試験片（１０）］
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｙｂを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｙｂ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（１０）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (10)]
An Mg—Zn—Y—Yb alloy containing 2 at% Zn, 1 at% Y, 1 at% Yb, and the balance Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (10), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
Ｚｎを２ａｔ％、Ｙを１ａｔ％、Ｙｂを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｙｂ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（１０）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (10)]
An Mg—Zn—Y—Yb alloy containing 2 at% Zn, 1 at% Y, 1 at% Yb, and the balance Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (10), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
［試験片（１１）］
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｎｄを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｎｄ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（１１）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (11)]
Mg—Zn—Y—Nd alloy containing Zn at 1 at%, Y at 1 at%, Nd at 1 at%, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (11), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｎｄを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｎｄ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（１１）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (11)]
Mg—Zn—Y—Nd alloy containing Zn at 1 at%, Y at 1 at%, Nd at 1 at%, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (11), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
［試験片（１２）］
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｓｍを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｓｍ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（１２）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (12)]
Mg—Zn—Y—Sm alloy containing Zn at 1 at%, Y at 1 at%, Sm at 1 at%, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (12), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
Ｚｎを１ａｔ％、Ｙを１ａｔ％、Ｓｍを１ａｔ％とし、残部がＭｇと不可避的不純物のＭｇ－Ｚｎ－Ｙ－Ｓｍ合金を真空溶解炉に投入し、フラックス精錬により溶解を行った。次に、加熱溶解した材料を金型に入れて鋳造し、φ２９ｍｍ×Ｌ６０ｍｍのインゴット（鋳造材）を作成した。続いて、押出温度３５０℃において押出比１０として塑性加工（押出加工）を行ったものを製造した。なお、試験片（１２）では、ＬＰＳＯと化合物とは積層構造（層状構造）をなさない様に組織制御を行った。 [Specimen (12)]
Mg—Zn—Y—Sm alloy containing Zn at 1 at%, Y at 1 at%, Sm at 1 at%, the balance being Mg and unavoidable impurities was put into a vacuum melting furnace and melted by flux refining. Next, the heat-dissolved material was cast in a mold to prepare an ingot (cast material) of φ29 mm × L60 mm. Subsequently, a product subjected to plastic working (extrusion) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 was produced. In the test piece (12), the structure was controlled so that LPSO and the compound did not form a laminated structure (layered structure).
以上の様にして得られた試験片（１）～（１２）を室温にて引張試験を行い、機械的特性を評価した結果を表１に示す。
The test pieces (1) to (12) obtained as described above were subjected to a tensile test at room temperature, and the results of evaluating the mechanical properties are shown in Table 1.
表１の試験片（７）の評価結果から明らかな様に、３元系合金であるＭｇ－Ｚｎ－Ｙ合金の場合には、降伏強度が３５０．４ＭＰａ、引張強度が３９７．２ＭＰａである。
ここで、表１の試験片（８）～（１２）の評価結果から明らかな様に、「ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍである」といった条件を満たしていない場合には、３元系合金である試験片（７）よりも降伏強度若しくは引張強度のいずれか一方が低下していることが分かる。具体的には、試験片（８）の評価結果では、降伏強度が３４９．８ＭＰａ、引張強度が３６５．９ＭＰａであり、試験片（７）よりも降伏強度及び引張強度が低下していることが分かる。また、試験片（９）の評価結果では、降伏強度が３０４．４ＭＰａ、引張強度が３７４．８ＭＰａであり、試験片（７）よりも降伏強度及び引張強度が低下していることが分かる。また、試験片（１０）の評価結果では、降伏強度が３５５．４ＭＰａ、引張強度が３７３．６ＭＰａであり、試験片（７）よりも引張強度が低下していることが分かる。また、試験片（１１）の評価結果では、降伏強度が３３７．２ＭＰａ、引張強度が３６９．１ＭＰａであり、試験片（７）よりも降伏強度及び引張強度が低下していることが分かる。また、試験片（１２）の評価結果では、降伏強度が３２５．６ＭＰａ、引張強度が３６４．６ＭＰａであり、試験片（７）よりも降伏強度及び引張強度が低下していることが分かる。 As is apparent from the evaluation result of the test piece (7) in Table 1, the yield strength is 350.4 MPa and the tensile strength is 397.2 MPa in the case of the ternary alloy Mg—Zn—Y alloy.
Here, as is clear from the evaluation results of the test pieces (8) to (12) in Table 1, “LPSO and the compound have a laminated structure (layered structure), and the thickness of the LPSO is 0.5 to 5 μm. If the condition of “the thickness of the compound is 0.01 to 2 μm” is not satisfied, either the yield strength or the tensile strength is lower than that of the ternary alloy test piece (7). I understand that Specifically, in the evaluation result of the test piece (8), the yield strength is 349.8 MPa and the tensile strength is 365.9 MPa, and the yield strength and the tensile strength are lower than those of the test piece (7). I understand. The evaluation result of the test piece (9) shows that the yield strength is 304.4 MPa and the tensile strength is 374.8 MPa, and the yield strength and tensile strength are lower than those of the test piece (7). The evaluation result of the test piece (10) shows that the yield strength is 355.4 MPa and the tensile strength is 373.6 MPa, and the tensile strength is lower than that of the test piece (7). Moreover, in the evaluation result of a test piece (11), yield strength is 337.2 MPa and tensile strength is 369.1 MPa, and it turns out that the yield strength and tensile strength are falling rather than a test piece (7). The evaluation result of the test piece (12) shows that the yield strength is 325.6 MPa and the tensile strength is 364.6 MPa, and the yield strength and the tensile strength are lower than those of the test piece (7).
ここで、表１の試験片（８）～（１２）の評価結果から明らかな様に、「ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍである」といった条件を満たしていない場合には、３元系合金である試験片（７）よりも降伏強度若しくは引張強度のいずれか一方が低下していることが分かる。具体的には、試験片（８）の評価結果では、降伏強度が３４９．８ＭＰａ、引張強度が３６５．９ＭＰａであり、試験片（７）よりも降伏強度及び引張強度が低下していることが分かる。また、試験片（９）の評価結果では、降伏強度が３０４．４ＭＰａ、引張強度が３７４．８ＭＰａであり、試験片（７）よりも降伏強度及び引張強度が低下していることが分かる。また、試験片（１０）の評価結果では、降伏強度が３５５．４ＭＰａ、引張強度が３７３．６ＭＰａであり、試験片（７）よりも引張強度が低下していることが分かる。また、試験片（１１）の評価結果では、降伏強度が３３７．２ＭＰａ、引張強度が３６９．１ＭＰａであり、試験片（７）よりも降伏強度及び引張強度が低下していることが分かる。また、試験片（１２）の評価結果では、降伏強度が３２５．６ＭＰａ、引張強度が３６４．６ＭＰａであり、試験片（７）よりも降伏強度及び引張強度が低下していることが分かる。 As is apparent from the evaluation result of the test piece (7) in Table 1, the yield strength is 350.4 MPa and the tensile strength is 397.2 MPa in the case of the ternary alloy Mg—Zn—Y alloy.
Here, as is clear from the evaluation results of the test pieces (8) to (12) in Table 1, “LPSO and the compound have a laminated structure (layered structure), and the thickness of the LPSO is 0.5 to 5 μm. If the condition of “the thickness of the compound is 0.01 to 2 μm” is not satisfied, either the yield strength or the tensile strength is lower than that of the ternary alloy test piece (7). I understand that Specifically, in the evaluation result of the test piece (8), the yield strength is 349.8 MPa and the tensile strength is 365.9 MPa, and the yield strength and the tensile strength are lower than those of the test piece (7). I understand. The evaluation result of the test piece (9) shows that the yield strength is 304.4 MPa and the tensile strength is 374.8 MPa, and the yield strength and tensile strength are lower than those of the test piece (7). The evaluation result of the test piece (10) shows that the yield strength is 355.4 MPa and the tensile strength is 373.6 MPa, and the tensile strength is lower than that of the test piece (7). Moreover, in the evaluation result of a test piece (11), yield strength is 337.2 MPa and tensile strength is 369.1 MPa, and it turns out that the yield strength and tensile strength are falling rather than a test piece (7). The evaluation result of the test piece (12) shows that the yield strength is 325.6 MPa and the tensile strength is 364.6 MPa, and the yield strength and the tensile strength are lower than those of the test piece (7).
一方、表１の試験片（１）～（６）の評価結果から明らかな様に、「ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍである」といった条件を満たしている場合には、降伏強度が３５０．４ＭＰａである３元系の試験片（７）よりも高い降伏強度を実現することができると共に、引張強度が３９７．２ＭＰａである３元系の試験片（７）よりも高い引張強度を実現することができる。
On the other hand, as apparent from the evaluation results of test pieces (1) to (6) in Table 1, “LPSO and the compound have a laminated structure (layered structure), and the thickness of LPSO is 0.5 to 5 μm. When the conditions such as “the thickness of the compound is 0.01 to 2 μm” are satisfied, the yield strength should be higher than that of the ternary specimen (7) having a yield strength of 350.4 MPa. The tensile strength higher than that of the ternary test piece (7) having a tensile strength of 397.2 MPa can be realized.
なお、本実施例では、３元系合金である表１の試験片（７）の評価結果が基準となり、本発明の実施例のマグネシウム合金である試験片（１）～（６）については試験片（７）よりも高い降伏強度と引張強度が実現でき、本発明の実施例ではないマグネシウム合金である試験片（８）～（１２）については試験片（７）よりも降伏強度若しくは引張強度の少なくとも一方が低下している場合を例に挙げている。
In this example, the evaluation result of the test piece (7) of Table 1 which is a ternary alloy is used as a reference, and the test pieces (1) to (6) which are magnesium alloys of the examples of the present invention are tested. Yield strength and tensile strength higher than those of the specimen (7) can be realized, and the test specimens (8) to (12) which are magnesium alloys which are not examples of the present invention have yield strength or tensile strength higher than that of the specimen (7). The case where at least one of these is lowered is taken as an example.
しかし、成分範囲の条件を調整することによって、３元系合金が高い降伏強度及び引張強度を実現することが考えられ、本発明の実施例のマグネシウム合金が必ずしも３元系合金よりも高い降伏強度及び引張強度を実現するというものではない。
However, it is conceivable that the ternary alloy achieves high yield strength and tensile strength by adjusting the conditions of the component ranges, and the magnesium alloy of the examples of the present invention is not necessarily higher in yield strength than the ternary alloy. It does not mean that the tensile strength is realized.
即ち、本実施例では、Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金から構成されるマグネシウム合金について、「ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍである」といった条件を満足する場合は高い降伏強度及び引張強度が実現でき、「ＬＰＳＯと化合物とが積層構造（層状構造）をなし、ＬＰＳＯの厚さが０．５～５μｍであり、化合物の厚さが０．０１～２μｍである」といった条件を満足しない場合は降伏強度若しくは引張強度の少なくとも一方が低下してしまうということを示すものである。
That is, in this example, regarding a magnesium alloy composed of an Mg—Zn—Y—RE alloy, “LPSO and the compound have a laminated structure (layered structure), and the thickness of LPSO is 0.5 to 5 μm. Yes, when the conditions such as “compound thickness is 0.01-2 μm” are satisfied, high yield strength and tensile strength can be realized, and “LPSO and compound have a laminated structure (layered structure), and the thickness of LPSO Is 0.5 to 5 μm and the thickness of the compound is 0.01 to 2 μm ”, it indicates that at least one of yield strength and tensile strength is reduced. .
１ マグネシウム合金
２ ＬＰＳＯ
３ αＭg相
４ 化合物 1Magnesium alloy 2 LPSO
3αMg phase 4 Compound
２ ＬＰＳＯ
３ αＭg相
４ 化合物 1
3
Claims (4)
- 必須成分としてＺｎ、Ｙ、及び、希土類元素（ＲＥ）としてＬａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ、Ｙｂのうち少なくとも１つ以上を含有し、残部がＭｇと不可避的不純物からなるＭｇ－Ｚｎ－Ｙ－ＲＥ系合金から構成されるマグネシウム合金であって、
Ｍｇ－Ｚｎ－Ｙ－ＲＥ系合金の合金組織中に、長周期積層構造相、αＭｇ相、及び、Ｍｇ－ＲＥ化合物若しくはＭｇ－Ｚｎ－ＲＥ化合物の少なくとも１つ以上の化合物を有すると共に、
前記長周期積層構造相と前記化合物が積層構造を構成し、
更に、前記長周期積層構造相の厚さが０．５μｍ～５μｍである
マグネシウム合金。 Mg—Zn—Y containing Zn, Y as essential components and at least one of La, Ce, Nd, Pr, Sm, Yb as rare earth elements (RE), with the balance being Mg and inevitable impurities A magnesium alloy composed of a RE-based alloy,
The alloy structure of the Mg—Zn—Y—RE alloy has a long-period stacked structure phase, an αMg phase, and at least one compound of Mg—RE compound or Mg—Zn—RE compound,
The long-period laminate structure phase and the compound constitute a laminate structure,
Furthermore, the magnesium alloy in which the thickness of the long-period laminated structure phase is 0.5 μm to 5 μm. - 前記化合物の厚さが０．０１μｍ～２μｍである
請求項１に記載のマグネシウム合金。 2. The magnesium alloy according to claim 1, wherein the thickness of the compound is 0.01 μm to 2 μm. - 前記Ｚｎは成分範囲が２．５原子％未満である
請求項１または請求項２に記載のマグネシウム合金。 The magnesium alloy according to claim 1 or 2, wherein the Zn has a component range of less than 2.5 atomic%. - 前記Ｚｎは成分範囲が２原子％以下である
請求項１または請求項２に記載のマグネシウム合金。 The magnesium alloy according to claim 1 or 2, wherein the Zn has a component range of 2 atomic% or less.
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| CN111101041A (en) * | 2020-01-13 | 2020-05-05 | 长沙理工大学 | Magnesium-yttrium-zinc hydrogen storage magnesium alloy and preparation method thereof |
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