JP2010248610A - High-strength magnesium alloy - Google Patents
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- 229910000861 Mg alloy Inorganic materials 0.000 title claims abstract description 61
- 229910052684 Cerium Inorganic materials 0.000 claims abstract description 10
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 10
- 229910052772 Samarium Inorganic materials 0.000 claims abstract description 10
- 229910052746 lanthanum Inorganic materials 0.000 claims abstract description 10
- 229910052777 Praseodymium Inorganic materials 0.000 claims abstract description 9
- 229910052769 Ytterbium Inorganic materials 0.000 claims abstract description 9
- 239000011777 magnesium Substances 0.000 claims abstract description 9
- 229910045601 alloy Inorganic materials 0.000 claims description 53
- 239000000956 alloy Substances 0.000 claims description 53
- 239000013078 crystal Substances 0.000 claims description 46
- 229910052727 yttrium Inorganic materials 0.000 claims description 7
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 2
- 229910052749 magnesium Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 abstract description 6
- 230000000052 comparative effect Effects 0.000 description 56
- 238000001125 extrusion Methods 0.000 description 48
- 239000000203 mixture Substances 0.000 description 47
- 238000000034 method Methods 0.000 description 41
- 238000010438 heat treatment Methods 0.000 description 27
- 238000005266 casting Methods 0.000 description 25
- 229910052761 rare earth metal Inorganic materials 0.000 description 12
- 239000000463 material Substances 0.000 description 7
- 238000009864 tensile test Methods 0.000 description 7
- 238000004519 manufacturing process Methods 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- 238000005242 forging Methods 0.000 description 4
- 229910052725 zinc Inorganic materials 0.000 description 4
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000000465 moulding Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 229910000946 Y alloy Inorganic materials 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 229910052688 Gadolinium Inorganic materials 0.000 description 1
- 206010037660 Pyrexia Diseases 0.000 description 1
- 229910000691 Re alloy Inorganic materials 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- -1 automobile wheels Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000002003 electron diffraction Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 239000012778 molding material Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000005192 partition Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000003252 repetitive effect Effects 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
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Abstract
Description
本発明は、高強度マグネシウム合金等に関し、より詳細には高温で優れた機械的特性を有することにより実用に供するレベルにある高強度マグネシウム合金等に関する。 The present invention relates to a high-strength magnesium alloy and the like, and more particularly, to a high-strength magnesium alloy and the like that are at a practical level by having excellent mechanical properties at high temperatures.
マグネシウム合金は、軽量で強度が高く、そのリサイクル性とあいまって、電気製品の筐体、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）。
Magnesium alloys are lightweight and high in strength, and combined with their recyclability, magnesium alloys are being applied to casings of electrical products, automobile wheels, suspension parts, engine parts, and the like.
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. (See, for example, Patent Document 1 and Patent Document 2).
しかしながら、一般に、マグネシウム合金は高温で機械的特性が脆弱な欠点がある。マグネシウム合金の応用分野を広めるためには、常温での機械的特性も重要だけれど、高温での機械的特性が重要となる。高温で優秀な機械的特性を有するマグネシウム合金は、より広く自動車などの産業分野に適用が可能となる。 However, in general, magnesium alloys have a drawback that mechanical properties are weak at high temperatures. In order to broaden the application field of magnesium alloys, mechanical properties at room temperature are important, but mechanical properties at high temperatures are important. Magnesium alloys having excellent mechanical properties at high temperatures can be more widely applied to industrial fields such as automobiles.
本発明の一態様は、高温で優れた機械的特性を有することにより実用に供するレベルにある高強度マグネシウム合金を提供することを課題とする。 An object of one embodiment of the present invention is to provide a high-strength magnesium alloy that is at a practically usable level by having excellent mechanical properties at high temperatures.
本発明の一態様に係る高強度マグネシウム合金は、常温より高い温度で使用される高強度マグネシウム合金であって、
Ｚｎをａ原子％含有し、Ｙをｂ原子％含有し、Ｌａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ及びＹｂからなる群から選択される少なくとも１つの元素を合計でｃ原子％含有し、残部がＭｇと不可避的不純物からなり、ａとｂとｃは下記式（１）〜（３）を満たすことを特徴とする。
（１）０＜ａ≦２．０
（２）１．０≦ｂ≦１．９５
（３）０．０５≦ｃ≦１．０
The high-strength magnesium alloy according to one aspect of the present invention is a high-strength magnesium alloy used at a temperature higher than room temperature,
Zn contains a atomic%, Y contains b atomic%, contains at least one element selected from the group consisting of La, Ce, Nd, Pr, Sm, and Yb in total, containing c atomic%, with the balance being Mg And a, b, and c satisfy the following formulas (1) to (3).
(1) 0 <a ≦ 2.0
(2) 1.0 ≦ b ≦ 1.95
(3) 0.05 ≦ c ≦ 1.0
また、本発明の一態様に係る高強度マグネシウム合金において、前記常温より高い温度は２５０℃であっても良い。ここで、「常温より高い温度である２５０℃で使用される」とは、常に２５０℃で使用される場合だけでなく、２５０℃で使用される可能性のある場合及び一時的に２５０℃で使用される場合も含む意味である。 In the high-strength magnesium alloy according to one embodiment of the present invention, the temperature higher than the normal temperature may be 250 ° C. Here, “used at 250 ° C., which is higher than normal temperature” means not only always used at 250 ° C. but also when it may be used at 250 ° C. and temporarily at 250 ° C. It also means when used.
また、上述した高強度マグネシウム合金は常温において長周期積層構造相を有する。
また、上述した高強度マグネシウム合金は３５０℃の温度で１時間の熱処理を施しても平均結晶粒径が１．７μｍ以下であることが可能である。
また、本発明の一態様に係る高強度マグネシウム合金は、自動車又は飛行機などの耐熱部品に用いることが好ましい。
Moreover, the high-strength magnesium alloy mentioned above has a long period laminated structure phase at normal temperature.
Further, the above-described high-strength magnesium alloy can have an average crystal grain size of 1.7 μm or less even when heat-treated at 350 ° C. for 1 hour.
The high-strength magnesium alloy according to one embodiment of the present invention is preferably used for a heat-resistant component such as an automobile or an airplane.
本発明の一態様を適用することで、高温で優れた機械的特性を有することにより実用に供するレベルにある高強度マグネシウム合金を提供することができる。 By applying one embodiment of the present invention, it is possible to provide a high-strength magnesium alloy that is at a practically usable level by having excellent mechanical properties at high temperatures.
以下では、本発明の実施の形態について図面を用いて詳細に説明する。ただし、本発明は以下の説明に限定されず、本発明の趣旨及びその範囲から逸脱することなくその形態及び詳細を様々に変更し得ることは、当業者であれば容易に理解される。従って、本発明は以下に示す実施の形態の記載内容に限定して解釈されるものではない。 Hereinafter, embodiments of the present invention will be described in detail with reference to the drawings. However, the present invention is not limited to the following description, and it will be easily understood by those skilled in the art that modes and details can be variously changed without departing from the spirit and scope of the present invention. Therefore, the present invention should not be construed as being limited to the description of the embodiments below.
本発明者らは、Ｚｎ及びＹを含有するマグネシウム合金に、Ｌａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ及びＹｂからなる群から選択される少なくとも１つの希土類元素（ＲＥ）を含有させることにより、前記希土類元素を含有させない場合に比べて高温で高強度が得られることを見出した。
つまり、Ｍｇ−Ｚｎ−Ｙ−ＲＥ系合金（ＲＥ：Ｌａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ及びＹｂ）は、Ｍｇ−Ｚｎ−Ｙ合金に比べて高温で高強度が得られることを確認した。
The inventors of the present invention have made the rare earth element (RE) selected from the group consisting of La, Ce, Nd, Pr, Sm, and Yb contained in a magnesium alloy containing Zn and Y, and thereby the rare earth element. It has been found that high strength can be obtained at a higher temperature than when no element is contained.
That is, it was confirmed that the Mg—Zn—Y—RE alloy (RE: La, Ce, Nd, Pr, Sm, and Yb) has higher strength at a higher temperature than the Mg—Zn—Y alloy.
（実施形態１）
本発明の実施形態１による高強度マグネシウム合金は、常温より高い温度（例えば２５０℃）で高強度及び高靭性を有するマグネシウム合金であって、Ｚｎをａ原子％含有し、Ｙをｂ原子％含有し、Ｌａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ及びＹｂからなる群から選択される少なくとも１つの希土類元素を合計でｃ原子％含有し、残部がＭｇ及び不可避的不純物からなり、ａとｂとｃは下記式（１）〜（３）を満たすものである。
（１）０＜ａ≦２．０
（２）１．０≦ｂ≦１．９５
（３）０．０５≦ｃ≦１．０
(Embodiment 1)
The high-strength magnesium alloy according to Embodiment 1 of the present invention is a magnesium alloy having high strength and high toughness at a temperature higher than room temperature (for example, 250 ° C.), containing Zn at a atom% and Y at b atom%. And a total of at least one rare earth element selected from the group consisting of La, Ce, Nd, Pr, Sm and Yb, containing at least c atom%, the balance being Mg and inevitable impurities, and a, b and c are The following formulas (1) to (3) are satisfied.
(1) 0 <a ≦ 2.0
(2) 1.0 ≦ b ≦ 1.95
(3) 0.05 ≦ c ≦ 1.0
この高強度マグネシウム合金は、常温において長周期積層構造相（ＬＰＳＯ：Long Period Stacking Order）を有している。 This high strength magnesium alloy has a long period stacking order (LPSO) at normal temperature.
また、高強度マグネシウム合金は、３５０℃の温度で１時間の熱処理を施しても平均結晶粒径が１．７μｍ以下である。この平均結晶粒径は、Ｚｎをａ原子％含有し、Ｙをｂ原子％含有し、残部がＭｇと不可避的不純物からなり、ａとｂは上記式（１）、（２）を満たすＭｇ−Ｚｎ−Ｙ合金を、３５０℃の温度で１時間の熱処理を施した場合の平均結晶粒径に比べて非常に小さい。 Further, the high-strength magnesium alloy has an average crystal grain size of 1.7 μm or less even when heat-treated at 350 ° C. for 1 hour. The average crystal grain size is such that Zn contains a atomic%, Y contains b atomic%, the balance is composed of Mg and inevitable impurities, and a and b satisfy the above formulas (1) and (2). The Zn—Y alloy is very small compared to the average grain size when heat-treated at 350 ° C. for 1 hour.
前記希土類元素の合計含有量ｃが０．０５原子％超であると、特に高温引張強度が低下する傾向があるからである。
前記希土類元素の合計含有量ｃが１．０原子％未満であると、特に高温引張強度が低下する傾向があるからである。
This is because when the total content c of the rare earth elements is more than 0.05 atomic%, the high-temperature tensile strength tends to decrease particularly.
This is because when the total content c of the rare earth elements is less than 1.0 atomic%, the high-temperature tensile strength tends to decrease particularly.
また、前記Ｚｎの含有量の上限を２．０原子％とした理由は、Ｚｎの成分範囲を２．５原子％未満となる様に組織制御を行っており、この様な組織制御を行うことによって、図１３に示すように、延性の著しい低下を回避することができるためである。図１３の横軸は、Ｍｇ−Ｚｎ合金のＺｎ含有量であり、縦軸は伸び割合（％）であり、伸び割合(Elongation ratio)は、下記式によって求められる。
伸び割合（％）＝（elongation of alloy）／（elongation of standard alloy）×１００
Standard alloy：Ｍｇ９９−ｘＺｎ１Ｙｘ
The reason why the upper limit of the Zn content is 2.0 atomic% is that the structure control is performed so that the Zn component range is less than 2.5 atomic%. This is because, as shown in FIG. 13, it is possible to avoid a significant decrease in ductility. The horizontal axis in FIG. 13 is the Zn content of the Mg—Zn alloy, the vertical axis is the elongation ratio (%), and the elongation ratio (Elongation ratio) is obtained by the following equation.
Elongation rate (%) = (elongation of alloy) / (elongation of standard alloy) × 100
Standard alloy: Mg 99-x Zn 1 Y x
本実施形態の高強度マグネシウム合金では、前述した範囲の含有量を有するＺｎ、Ｙ及び希土類元素以外の成分がマグネシウムとなるが、合金特性に影響を与えない程度の不純物を含有しても良い。 In the high-strength magnesium alloy of this embodiment, components other than Zn, Y, and rare earth elements having a content in the range described above are magnesium, but may contain impurities that do not affect the alloy characteristics.
（実施形態２）
本発明の実施形態２による高強度マグネシウム合金の製造方法について説明する。
実施形態１の組成からなるマグネシウム合金を溶解して鋳造し、マグネシウム合金鋳造物を作る。鋳造時の冷却速度は０．０５Ｋ／秒以上１０００（１０３）Ｋ／秒以下であり、より好ましくは０．５Ｋ／秒以上１０００（１０３）Ｋ／秒以下である。このマグネシウム合金鋳造物としては、インゴットから所定形状に切り出したものを用いる。
(Embodiment 2)
The manufacturing method of the high strength magnesium alloy by Embodiment 2 of this invention is demonstrated.
A magnesium alloy having the composition of the first embodiment is melted and cast to make a magnesium alloy casting. The cooling rate during casting is 0.05 K / second or more and 1000 (10 3 ) K / second or less, and more preferably 0.5 K / second or more and 1000 (10 3 ) K / second or less. As this magnesium alloy casting, what was cut out into a predetermined shape from an ingot is used.
次いで、マグネシウム合金鋳造物に熱処理を施しても良い。この際の熱処理条件は、温度が２００℃〜５５０℃、処理時間が１分〜３６００分（又は６０時間）とすることが好ましい。 Next, the magnesium alloy casting may be subjected to heat treatment. The heat treatment conditions at this time are preferably a temperature of 200 ° C. to 550 ° C. and a treatment time of 1 minute to 3600 minutes (or 60 hours).
前記マグネシウム合金鋳造物はαＭｇ相を有している。
ここで、αＭｇ相は、溶解鋳造工程において、マグネシウム合金のセル構造内で、後述する長周期積層構造相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、合金組織中の少なくとも一部（長周期積層構造相の分断部）が微細化した（微細αＭｇ相が析出した）方が好ましい。
The magnesium alloy casting has an αMg phase.
Here, the αMg phase forms a lamellar phase and a long-period laminate structure phase described later in the cell structure of the magnesium alloy in the melt casting process. In addition, in the plastic working process performed in a high-temperature atmosphere (hot), the αMg phase is at least partially refined (partition of the long-period laminated structure phase) in the alloy structure (a fine αMg phase is precipitated). Is preferred.
また、マグネシウム合金鋳造物は長周期積層構造相の結晶組織を有する。ここで、長周期積層構造相相とは、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、長周期積層構造相は、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、長周期積層構造相は、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数倍の周期に対向する位置に回折斑点が現れることとなる。こうした長周期積層構造相の析出は、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）が向上する一つの原因である。 The magnesium alloy casting has a crystal structure of a long-period laminated structure phase. Here, the long-period laminated structure phase phase is a precipitate that precipitates in the grains and grain boundaries 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-period rule in the bottom normal direction. That is, it refers to a long-period structure. More specifically, the long-period layered structure phase is, for example, a plurality of regular lattices arranged several times, and a plurality of regular lattices are arranged again through an antiphase shift. A structure in which a unit structure is made and its period is long. Then, the long-period laminated structure phase appears in a slight temperature range between the regular phase and the irregular phase, and the reflection of the regular phase is split in the electron diffraction diagram, so that the period is several to several tens of times. A diffraction spot appears at a position opposite to. Precipitation of such a long-period laminated structure phase is one cause for improving the mechanical properties (tensile strength, yield strength and elongation) of the magnesium alloy.
また、長周期積層構造相は、溶解鋳造工程、又は、溶解、鋳造後の熱処理工程において、鋳造材の合金組織、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、長周期積層構造相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。 Further, the long-period laminated structure phase forms a lamellar phase that is a lamellar structure grain together with the αMg phase in the alloy structure of the cast material, that is, in the cell structure, in the melt casting process or the heat treatment process after melting and casting. . The long-period layered structure phase is formed in a straight line, and the formation direction is formed in the same direction in the same cell structure, and the cell structures are formed in different directions.
また、前記マグネシウム合金鋳造物は長周期積層構造相とαＭｇ相以外にその他の化合物相が含まれていることがある。 Further, the magnesium alloy casting may contain other compound phases in addition to the long-period laminated structure phase and the αMg phase.
次に、前記マグネシウム合金鋳造物に塑性加工を行う。この塑性加工の方法としては、例えば押出し、ＥＣＡＥ(equal-channel-angular-extrusion)加工法、圧延、引抜及び鍛造、これらの繰り返し加工、ＦＳＷ加工などを用いる。尚、前記塑性加工は、少なくとも一回の相当歪量が０超５以下であることが好ましい。ここで、多軸応力状態にある応力成分を、それに相当する単軸応力に換算した応力のことを相当応力といい、相当歪量とはこの相当応力をうけたときの歪み量である。 Next, plastic working is performed on the magnesium alloy casting. As the plastic working method, for example, extrusion, ECAE (equal-channel-angular-extrusion) processing, rolling, drawing and forging, repetitive processing thereof, FSW processing, and the like are used. In the plastic working, it is preferable that the equivalent strain amount at least once is more than 0 and 5 or less. Here, a stress component converted into a uniaxial stress corresponding to a stress component in a multiaxial stress state is referred to as equivalent stress, and the equivalent strain amount is a strain amount when the equivalent stress is applied.
押出しによる塑性加工を行う場合は、押出し温度を２００℃以上５００℃以下とし、押出しによる断面減少率を５％以上とすることが好ましい。 When performing plastic working by extrusion, it is preferable that the extrusion temperature is 200 ° C. or more and 500 ° C. or less, and the cross-sectional reduction rate by extrusion is 5% or more.
ＥＣＡＥ加工法は、試料に均一なひずみを導入するためにパス毎に試料長手方向を９０°ずつ回転させる方法である。具体的には、断面形状がＬ字状の成形孔を形成した成形用ダイの前記成形孔に、成形用材料であるマグネシウム合金鋳造物を強制的に進入させて、特にＬ状成形孔の９０°に曲げられた部分で前記マグネシウム合金鋳造物に応力を加えて強度及び靭性が優れた成形体を得る方法である。ＥＣＡＥのパス回数としては１〜８パスが好ましい。より好ましくは３〜５パスである。ＥＣＡＥの加工時の温度は２００℃以上５００℃以下が好ましい。 The ECAE processing method is a method of rotating the sample longitudinal direction by 90 ° for each pass in order to introduce a uniform strain to the sample. Specifically, a magnesium alloy cast material as a molding material is forcibly entered into the molding hole of the molding die in which a L-shaped molding hole is formed. This is a method of applying a stress to the magnesium alloy casting at a portion bent at a degree to obtain a molded body having excellent strength and toughness. The number of ECAE passes is preferably 1 to 8 passes. More preferably, it is 3 to 5 passes. The temperature during processing of ECAE is preferably 200 ° C. or more and 500 ° C. or less.
圧延による塑性加工を行う場合は、圧延温度を２００℃以上５００℃以下とし、圧下率を５％以上とすることが好ましい。 When performing plastic working by rolling, it is preferable that the rolling temperature is 200 ° C. or more and 500 ° C. or less, and the rolling reduction is 5% or more.
引抜加工による塑性加工を行う場合は、引抜加工を行う際の温度が２００℃以上５００℃以下、前記引抜加工の断面減少率が５％以上であることが好ましい。 When performing plastic working by drawing, it is preferable that the temperature at the time of drawing is 200 ° C. or more and 500 ° C. or less, and the cross-sectional reduction rate of the drawing is 5% or more.
鍛造による塑性加工を行う場合は、鍛造加工を行う際の温度が２００℃以上５００℃以下、前記鍛造加工の加工率が５％以上であることが好ましい。 When performing plastic working by forging, it is preferable that the temperature at the time of forging is 200 ° C. or more and 500 ° C. or less, and the processing rate of the forging is 5% or more.
上記のようにマグネシウム合金鋳造物に塑性加工を行った塑性加工物は、常温において長周期積層構造相の結晶組織を有する。この塑性加工によって長周期積層構造相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が形成され、かつ、規則格子の並びが壊れた分断部が形成される。これにより、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る。また、Ｌａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ及びＹｂの少なくとも一つの希土類元素をマグネシウム合金に含有させているため、常温より高い温度、例えば２５０℃で高い引張強度及び降伏強度を得ることができる。 A plastic workpiece obtained by plastic processing of a magnesium alloy casting as described above has a crystal structure of a long-period laminated structure phase at room temperature. By this plastic working, at least one of a curved portion and a bent portion is formed in at least a part of the long-period laminated structure phase, and a split portion in which the arrangement of the regular lattice is broken is formed. Thereby, high elongation can be obtained while maintaining high tensile strength and yield strength. Further, since at least one rare earth element of La, Ce, Nd, Pr, Sm and Yb is contained in the magnesium alloy, high tensile strength and yield strength can be obtained at a temperature higher than normal temperature, for example, 250 ° C.
なお、前記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。また、前記塑性加工物は、長周期積層構造相とαＭｇ相以外にその他の化合物相が含まれていることがある。 Note that the cell structure formed during casting by the plastic working disappears. Further, the plastic workpiece may contain other compound phases in addition to the long-period laminated structure phase and the αMg phase.
前記マグネシウム合金鋳造物に塑性加工を行った後の塑性加工物に熱処理を施しても良い。この熱処理条件は、温度が２００℃〜５５０℃、熱処理時間が１分〜３６００分（又は６０時間）とすることが好ましい。この熱処理を行った後の塑性加工物については、熱処理を行う前の塑性加工物に比べてビッカース硬度及び降伏強度がともに上昇する。また、熱処理後の塑性加工物にも熱処理前と同様に、常温において長周期積層構造の結晶組織を有している。 A heat treatment may be applied to the plastic workpiece after the magnesium alloy casting has been plastically processed. The heat treatment conditions are preferably a temperature of 200 ° C. to 550 ° C. and a heat treatment time of 1 minute to 3600 minutes (or 60 hours). About the plastic workpiece after performing this heat processing, both Vickers hardness and yield strength rise compared with the plastic workpiece before performing heat processing. Further, the plastic workpiece after the heat treatment also has a crystal structure of a long-period laminated structure at room temperature, as before the heat treatment.
上記実施の形態１及び２によれば、常温より高い高温で優れた機械的特性を有することにより高温で使用される用途に対して、強度が実用に供するレベルにある高強度マグネシウム合金を提供することができる。これにより、この高強度マグネシウム合金を自動車又は飛行機などの耐熱部品に用いることが可能となる。 According to the first and second embodiments, a high-strength magnesium alloy having a strength that is practically used for a use at a high temperature by having excellent mechanical properties at a high temperature higher than normal temperature is provided. be able to. This makes it possible to use this high-strength magnesium alloy for heat-resistant parts such as automobiles and airplanes.
（実施形態３）
本発明の実施形態３によるマグネシウム合金の製造方法について説明する。
実施形態２と同様の方法で、実施形態１の組成からなるマグネシウム合金を溶解して鋳造し、マグネシウム合金鋳造物を作る。次いで、マグネシウム合金鋳造物に均質化熱処理を施しても良い。
(Embodiment 3)
A method for producing a magnesium alloy according to Embodiment 3 of the present invention will be described.
In the same manner as in Embodiment 2, the magnesium alloy having the composition of Embodiment 1 is melted and cast to make a magnesium alloy casting. Next, the magnesium alloy casting may be subjected to a homogenization heat treatment.
次いで、このマグネシウム合金鋳造物を切削することによって複数の数ｍｍ角以下のチップ形状鋳造物を作製する。 Next, by cutting the magnesium alloy casting, a plurality of chip-shaped castings having a size of several mm square or less are produced.
次いで、チップ形状鋳造物を圧縮又は塑性加工法的手段を用いて予備成形し、熱処理を施しても良い。この際の熱処理条件は、温度が２００℃〜５５０℃、処理時間が１分〜３６００分（又は６０時間）とすることが好ましい。 The chip-shaped casting may then be pre-formed using compression or plastic working means and heat treated. The heat treatment conditions at this time are preferably a temperature of 200 ° C. to 550 ° C. and a treatment time of 1 minute to 3600 minutes (or 60 hours).
チップ形状の鋳造物は例えばチクソーモールドの原料に一般的に用いられている。
尚、チップ形状鋳造物とセラミック粒子とを混合したものを圧縮又は塑性加工法的手段を用いて予備成形し、熱処理を施しても良い。また、チップ形状鋳造物を予備成形する前に、付加的に強歪加工を施しても良い。
A chip-shaped casting is generally used as a raw material for, for example, a Chixso mold.
Note that a mixture of a chip-shaped casting and ceramic particles may be pre-formed using compression or plastic working means and subjected to heat treatment. Further, before the chip-shaped casting is preformed, a high strain processing may be additionally performed.
次に、前記チップ形状鋳造物に塑性加工を行う。この塑性加工の方法としては、実施形態２の場合と同様に種々の方法を用いることができる。
このように塑性加工を行った塑性加工物は、実施形態２と同様に、常温において長周期積層構造の結晶組織を有する。これにより、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る。また、Ｌａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ及びＹｂの少なくとも一つの希土類元素をマグネシウム合金に含有させているため、常温より高い温度、例えば２５０℃で高い引張強度及び降伏強度を得ることができる。
Next, plastic working is performed on the chip-shaped casting. As the plastic working method, various methods can be used as in the second embodiment.
The plastic workpiece subjected to plastic working in this way has a crystal structure of a long-period laminated structure at room temperature, as in the second embodiment. Thereby, high elongation can be obtained while maintaining high tensile strength and yield strength. Further, since at least one rare earth element of La, Ce, Nd, Pr, Sm and Yb is contained in the magnesium alloy, high tensile strength and yield strength can be obtained at a temperature higher than normal temperature, for example, 250 ° C.
前記チップ形状鋳造物に塑性加工を行った後の塑性加工物に熱処理を施しても良い。この熱処理条件は、温度が２００℃〜５５０℃、熱処理時間が１分〜３６００分（又は６０時間）とすることが好ましい。この熱処理を行った後の塑性加工物については、熱処理を行う前の塑性加工物に比べてビッカース硬度及び降伏強度がともに上昇する。また、熱処理後の塑性加工物にも熱処理前と同様に、常温において長周期積層構造の結晶組織を有する。 A heat treatment may be applied to the plastic workpiece after the chip-shaped casting has been plastically processed. The heat treatment conditions are preferably a temperature of 200 ° C. to 550 ° C. and a heat treatment time of 1 minute to 3600 minutes (or 60 hours). About the plastic workpiece after performing this heat processing, both Vickers hardness and yield strength rise compared with the plastic workpiece before performing heat processing. Further, the plastic workpiece after the heat treatment also has a crystal structure of a long-period laminated structure at room temperature, as before the heat treatment.
上記実施形態３においても上記実施形態１，２と同様の効果を得ることができる。 In the third embodiment, the same effect as in the first and second embodiments can be obtained.
また、上記実施形態３では、鋳造物を切削することによってチップ形状鋳造物を作製することにより、組織が微細化するので、実施形態２に比べてよりより高強度・高延性・高靭性の塑性加工物などを作製することが可能となる。また、本実施形態によるマグネシウム合金は実施形態２によるマグネシウム合金に比べてＺｎ及びＹがより低濃度であっても高強度及び高靭性の特性を得ることができる。 In the third embodiment, the structure is refined by producing a chip-shaped cast by cutting the cast, so that the plasticity is higher in strength, higher ductility, and higher toughness than in the second embodiment. A workpiece or the like can be manufactured. Further, the magnesium alloy according to the present embodiment can obtain characteristics of high strength and high toughness even when Zn and Y are in a lower concentration than the magnesium alloy according to the second embodiment.
以下、本発明の実施例について説明する。
まず、本発明の実施例によるマグネシウム合金の試験片を作製した。
Examples of the present invention will be described below.
First, a magnesium alloy test piece according to an embodiment of the present invention was prepared.
図１（Ａ）は、試験片１〜６を２５０℃の温度で引張試験を行い、機械的特性を評価した結果を示すグラフであり、図１（Ｂ）は、試験片７〜１２を２５０℃の温度で引張試験を行い、機械的特性を評価した結果を示すグラフである。図１（Ａ），（Ｂ）に示す「σＵＴＳ」は引張強度であり、「σ0.2」は降伏強度であり、「ＥＬ」は伸びである。試験片の製造方法は下記のとおりである。 FIG. 1 (A) is a graph showing the results of performing a tensile test on the test pieces 1 to 6 at a temperature of 250 ° C. and evaluating the mechanical properties, and FIG. It is a graph which shows the result of having performed the tension test at the temperature of 0 degreeC and evaluating the mechanical characteristic. “ΣUTS” shown in FIGS. 1A and 1B is tensile strength, “σ0.2” is yield strength, and “EL” is elongation. The manufacturing method of a test piece is as follows.
（試験片１）Ｍｇ96Ｚｎ2Ｙ1.9Ｌａ0.1
Ｚｎを２原子％、Ｙを１．９原子％、Ｌａを０．１原子％含有し、残部がＭｇと不可避的不純物からなるマグネシウム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）を作製した。次いで、押出温度３５０℃において押出比１０、押出速度２．５ｍｍ／秒として塑性加工（押出加工）を行ったものを製造した。
(Test piece 1) Mg96Zn2Y1.9La0.1
A magnesium alloy containing 2 atomic% of Zn, 1.9 atomic% of Y, and 0.1 atomic% of La, and the balance of Mg and inevitable impurities was put into a vacuum melting furnace and melted by flux refining. . Next, the heat-dissolved material was placed in a mold and cast to prepare an ingot (cast material) of φ29 mm × L60 mm. Next, a product subjected to plastic working (extrusion process) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 and an extrusion speed of 2.5 mm / second was produced.
（試験片２）Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1に変更し、その他は試験片１と同様の方法により試験片２を製造した。
(Test piece 2) Mg96Zn2Y1.9Ce0.1
Test piece 2 was manufactured in the same manner as test piece 1 except that the alloy composition of test piece 1 was changed to Mg96Zn2Y1.9Ce0.1.
（試験片３）Ｍｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1に変更し、その他は試験片１と同様の方法により試験片３を製造した。
(Test piece 3) Mg96Zn2Y1.9Nd0.1
Test piece 3 was produced in the same manner as test piece 1 except that the alloy composition of test piece 1 was changed to Mg96Zn2Y1.9Nd0.1.
（試験片４）Ｍｇ96Ｚｎ2Ｙ1.9Ｐｒ0.1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｐｒ0.1に変更し、その他は試験片１と同様の方法により試験片４を製造した。
(Test piece 4) Mg96Zn2Y1.9Pr0.1
Test piece 4 was manufactured in the same manner as test piece 1 except that the alloy composition of test piece 1 was changed to Mg96Zn2Y1.9Pr0.1.
（試験片５）Ｍｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1に変更し、その他は試験片１と同様の方法により試験片５を製造した。
(Test piece 5) Mg96Zn2Y1.9Sm0.1
Test piece 5 was manufactured in the same manner as test piece 1 except that the alloy composition of test piece 1 was changed to Mg96Zn2Y1.9Sm0.1.
（試験片６）Ｍｇ96Ｚｎ2Ｙ1.9Ｙｂ0.1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｙｂ0.1に変更し、その他は試験片１と同様の方法により試験片６を製造した。
(Test piece 6) Mg96Zn2Y1.9Yb0.1
A test piece 6 was produced in the same manner as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.9Yb0.1.
（試験片７）Ｍｇ96Ｚｎ2Ｙ1Ｌａ1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1Ｌａ1に変更し、その他は試験片１と同様の方法により試験片７を製造した。
(Test piece 7) Mg96Zn2Y1La1
The test piece 7 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1La1.
（試験片８）Ｍｇ96Ｚｎ2Ｙ1Ｃｅ1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1Ｃｅ1に変更し、その他は試験片１と同様の方法により試験片８を製造した。
(Test piece 8) Mg96Zn2Y1Ce1
The test piece 8 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1Ce1.
（試験片９）Ｍｇ96Ｚｎ2Ｙ1Ｎｄ1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1Ｎｄ1に変更し、その他は試験片１と同様の方法により試験片９を製造した。
(Test piece 9) Mg96Zn2Y1Nd1
A test piece 9 was produced in the same manner as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1Nd1.
（試験片１０）Ｍｇ96Ｚｎ2Ｙ1Ｐｒ1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1Ｐｒ1に変更し、その他は試験片１と同様の方法により試験片１０を製造した。
(Test piece 10) Mg96Zn2Y1Pr1
The test piece 10 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1Pr1.
（試験片１１）Ｍｇ96Ｚｎ2Ｙ1Ｓｍ1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1Ｓｍ1に変更し、その他は試験片１と同様の方法により試験片１１を製造した。
(Test piece 11) Mg96Zn2Y1Sm1
The test piece 11 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1Sm1.
（試験片１２）Ｍｇ96Ｚｎ2Ｙ1Ｙｂ1
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｙｂ0.1に変更し、その他は試験片１と同様の方法により試験片１２を製造した。
(Test piece 12) Mg96Zn2Y1Yb1
The test piece 12 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.9Yb0.1.
図２は、試験片５、１１、１３〜１５及び比較片１を室温及び２５０℃の温度で引張試験を行い、機械的特性を評価した結果を示すグラフである。 FIG. 2 is a graph showing the results of performing a tensile test on the test pieces 5, 11, 13 to 15 and the comparative piece 1 at room temperature and 250 ° C. and evaluating the mechanical properties.
図２に示す参照符号１１は室温での引張強度を示すものであり、参照符号１２は室温での降伏強度を示すものであり、参照符号１３は２５０℃の温度での引張強度を示すものであり、参照符号１４は２５０℃の温度での降伏強度を示すものであり、参照符号１５は２５０℃の温度での伸びを示すものであり、参照符号１６は室温での伸びを示すものである。 Reference numeral 11 shown in FIG. 2 indicates the tensile strength at room temperature, reference numeral 12 indicates the yield strength at room temperature, and reference numeral 13 indicates the tensile strength at a temperature of 250 ° C. Yes, reference numeral 14 indicates the yield strength at a temperature of 250 ° C., reference numeral 15 indicates the elongation at a temperature of 250 ° C., and reference numeral 16 indicates the elongation at room temperature. .
（比較片１）Ｍｇ96Ｚｎ2Ｙ2
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ2に変更し、その他は試験片１と同様の方法により比較片１を製造した。
(Comparative piece 1) Mg96Zn2Y2
The alloy composition of the test piece 1 was changed to Mg96Zn2Y2, and the comparison piece 1 was manufactured by the same method as the test piece 1 except for the above.
（試験片１３）Ｍｇ96Ｚｎ2Ｙ1.75Ｓｍ0.25
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.75Ｓｍ0.25に変更し、その他は試験片１と同様の方法により試験片１３を製造した。
(Test piece 13) Mg96Zn2Y1.75Sm0.25
The test piece 13 was manufactured in the same manner as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.75Sm0.25.
（試験片１４）Ｍｇ96Ｚｎ2Ｙ1.5Ｓｍ0.5
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.5Ｓｍ0.5に変更し、その他は試験片１と同様の方法により試験片１４を製造した。
(Test piece 14) Mg96Zn2Y1.5Sm0.5
The test piece 14 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.5Sm0.5.
（試験片１５）Ｍｇ96Ｚｎ2Ｙ1.25Ｓｍ0.75
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.25Ｓｍ0.75に変更し、その他は試験片１と同様の方法により試験片１５を製造した。
(Test piece 15) Mg96Zn2Y1.25Sm0.75
The test piece 15 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.25Sm0.75.
図３は、試験片２、８、１６〜１８及び比較片１を室温及び２５０℃の温度で引張試験を行い、機械的特性を評価した結果を示すグラフである。 FIG. 3 is a graph showing the results of performing a tensile test on the test pieces 2, 8, 16 to 18 and the comparative piece 1 at room temperature and a temperature of 250 ° C. and evaluating the mechanical properties.
図３に示す参照符号１７は室温での引張強度を示すものであり、参照符号１８は室温での降伏強度を示すものであり、参照符号１９は２５０℃の温度での引張強度を示すものであり、参照符号２０は２５０℃の温度での降伏強度を示すものであり、参照符号２１は２５０℃の温度での伸びを示すものであり、参照符号２２は室温での伸びを示すものである。 Reference numeral 17 shown in FIG. 3 indicates the tensile strength at room temperature, reference numeral 18 indicates the yield strength at room temperature, and reference numeral 19 indicates the tensile strength at a temperature of 250 ° C. Yes, reference numeral 20 indicates the yield strength at a temperature of 250 ° C., reference numeral 21 indicates the elongation at a temperature of 250 ° C., and reference numeral 22 indicates the elongation at room temperature. .
（試験片１６）Ｍｇ96Ｚｎ2Ｙ1.75ｃＣｅ0.25
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.75Ｃｅ0.25に変更し、その他は試験片１と同様の方法により試験片１６を製造した。
(Test piece 16) Mg96Zn2Y1.75cCe0.25
The test piece 16 was manufactured in the same manner as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.75Ce0.25.
（試験片１７）Ｍｇ96Ｚｎ2Ｙ1.5ＣｅＳｍ0.5
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.5Ｃｅ0.5に変更し、その他は試験片１と同様の方法により試験片１７を製造した。
(Test piece 17) Mg96Zn2Y1.5CeSm0.5
The test piece 17 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.5Ce0.5.
（試験片１８）Ｍｇ96Ｚｎ2Ｙ1.25Ｃｅ0.75
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.25Ｃｅ0.75に変更し、その他は試験片１と同様の方法により試験片１８を製造した。
(Test piece 18) Mg96Zn2Y1.25Ce0.75
The test piece 18 was manufactured by the same method as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.25Ce0.75.
図４は、図２に示す参照符号１３〜１５それぞれの引張強度、降伏強度、伸び及び図３に示す参照符号１９〜２１それぞれの引張強度、降伏強度、伸びをグラフに示した図である。 FIG. 4 is a graph showing the tensile strength, yield strength, and elongation of reference numerals 13 to 15 shown in FIG. 2 and the tensile strength, yield strength, and elongation of reference numerals 19 to 21 shown in FIG.
（試験片１８−１）Ｍｇ96Ｚｎ2Ｙ1.95Ｃｅ0.05
試験片１の合金組成をＭｇ96Ｚｎ2Ｙ1.95Ｃｅ0.05に変更し、その他は試験片１と同様の方法により試験片１８−１を製造した。
試験片１８−１に２５０℃の温度で引張試験を行い、機械的特性を評価した結果、降伏強度は２６０ＭＰａであり、引張強度は３０１ＭＰａであり、伸びは１３％であった。
図１〜図４及び試験片１８−１の機械的特性によれば、Ｍｇ96Ｚｎ2Ｙ2-xＲＥx（ＲＥ：Ｌａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ及びＹｂ、0.05≦x＜1.0）が、Ｍｇ96Ｚｎ2Ｙ2に比べて２５０℃の高温で高強度が得られることが確認できた。
(Test piece 18-1) Mg96Zn2Y1.95Ce0.05
A test piece 18-1 was produced in the same manner as the test piece 1 except that the alloy composition of the test piece 1 was changed to Mg96Zn2Y1.95Ce0.05.
As a result of performing a tensile test on the test piece 18-1 at a temperature of 250 ° C. and evaluating the mechanical properties, the yield strength was 260 MPa, the tensile strength was 301 MPa, and the elongation was 13%.
1-4 and the mechanical properties of test piece 18-1, Mg96Zn2Y2-xREx (RE: La, Ce, Nd, Pr, Sm and Yb, 0.05≤x <1.0) is 250 compared to Mg96Zn2Y2. It was confirmed that high strength was obtained at a high temperature of ° C.
図５は、２５０℃の温度におけるＬＰＳＯ（長周期積層構造相）の体積分率と引張強度、降伏強度及び伸びそれぞれとの関係を示すグラフである。このグラフは、前記の試験片２、５、８、１１、１３〜１８及び比較片１それぞれに２５０℃の温度で引張試験を行った結果によって作成されたものである。 FIG. 5 is a graph showing the relationship between the volume fraction of LPSO (long-period laminated structure phase) at a temperature of 250 ° C., the tensile strength, the yield strength, and the elongation. This graph is created based on the result of a tensile test performed on each of the test pieces 2, 5, 8, 11, 13 to 18 and the comparative piece 1 at a temperature of 250 ° C.
図５に示す参照符号２３は、Ｍｇ96Ｚｎ2Ｙ2-xＣｅx合金である試験片のＬＰＳＯの体積分率と引張強度との関係を示すものであり、ＬＰＳＯの体積分率の低い順に試験片２、１６、１７、１８、８のデータが記載されている。
参照符号２４は、Ｍｇ96Ｚｎ2Ｙ2-xＣｅx合金である試験片のＬＰＳＯの体積分率と引張強度との関係を示すものであり、ＬＰＳＯの体積分率の低い順に試験片２、１６、１７、１８、８のデータが記載されている。
参照符号２５は、Ｍｇ96Ｚｎ2Ｙ2-xＣｅx合金である試験片のＬＰＳＯの体積分率と引張強度との関係を示すものであり、ＬＰＳＯの体積分率の低い順に試験片２、１６、１７、１８、８のデータが記載されている。
Reference numeral 23 shown in FIG. 5 indicates the relationship between the LPSO volume fraction and the tensile strength of a test piece which is an Mg96Zn2Y2-xCex alloy, and the test pieces 2, 16, 17 are in descending order of the LPSO volume fraction. , 18, 8 are described.
Reference numeral 24 indicates the relationship between the LPSO volume fraction and the tensile strength of the test piece which is a Mg96Zn2Y2-xCex alloy, and the test pieces 2, 16, 17, 18, 8 are in order of increasing LPSO volume fraction. The data of is described.
Reference numeral 25 indicates the relationship between the LPSO volume fraction and the tensile strength of the test piece, which is a Mg96Zn2Y2-xCex alloy, and the test pieces 2, 16, 17, 18, 8 in descending order of the LPSO volume fraction. The data of is described.
図５に示す参照符号２６は、Ｍｇ96Ｚｎ2Ｙ2-xＳｍx合金である試験片のＬＰＳＯの体積分率と引張強度との関係を示すものであり、ＬＰＳＯの体積分率の低い順に試験片１１、５、１３、１４、１５のデータが記載されている。
参照符号２７は、Ｍｇ96Ｚｎ2Ｙ2-xＳｍx合金である試験片のＬＰＳＯの体積分率と引張強度との関係を示すものであり、ＬＰＳＯの体積分率の低い順に試験片１１、５、１３、１４、１５のデータが記載されている。
参照符号２８は、Ｍｇ96Ｚｎ2Ｙ2-xＳｍx合金である試験片のＬＰＳＯの体積分率と引張強度との関係を示すものであり、ＬＰＳＯの体積分率の低い順に試験片１１、５、１３、１４、１５のデータが記載されている。
Reference numeral 26 shown in FIG. 5 indicates the relationship between the LPSO volume fraction and the tensile strength of a test piece that is an Mg96Zn2Y2-xSmx alloy, and the test pieces 11, 5, 13 are in order of increasing LPSO volume fraction. , 14, 15 are described.
Reference numeral 27 indicates the relationship between the volume fraction of LPSO and the tensile strength of the test piece which is an Mg96Zn2Y2-xSmx alloy, and the test pieces 11, 5, 13, 14, 15 in order of increasing volume fraction of LPSO. The data of is described.
Reference numeral 28 indicates the relationship between the volume fraction of LPSO and the tensile strength of a test piece that is an Mg96Zn2Y2-xSmx alloy, and the test pieces 11, 5, 13, 14, 15 in order of increasing volume fraction of LPSO. The data of is described.
図６（Ａ）は、図１（Ａ）と同一のグラフであり、図６（Ｂ）は、試験片１９〜２４を２５０℃の温度で引張試験を行い、機械的特性を評価した結果を示すグラフである。図６（Ａ），（Ｂ）に示す「σＵＴＳ」は引張強度であり、「σ0.2」は降伏強度であり、「ＥＬ」は伸びである。試験片の製造方法は下記のとおりである。 FIG. 6 (A) is the same graph as FIG. 1 (A), and FIG. 6 (B) shows the results of performing a tensile test on the test pieces 19 to 24 at a temperature of 250 ° C. and evaluating the mechanical properties. It is a graph to show. “ΣUTS” shown in FIGS. 6A and 6B is tensile strength, “σ0.2” is yield strength, and “EL” is elongation. The manufacturing method of a test piece is as follows.
（試験片１９）Ｍｇ96Ｚｎ2Ｙ1.9Ｌａ0.1
押出加工の押出速度を３．７ｍｍ／秒に変更し、その他は試験片１と同様の方法及び組成により試験片１９を製造した。
(Test piece 19) Mg96Zn2Y1.9La0.1
The test piece 19 was manufactured by the same method and composition as the test piece 1 except that the extrusion speed of the extrusion process was changed to 3.7 mm / sec.
（試験片２０）Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1
押出加工の押出速度を３．７ｍｍ／秒に変更し、その他は試験片２と同様の方法及び組成により試験片２０を製造した。
(Test piece 20) Mg96Zn2Y1.9Ce0.1
The test piece 20 was manufactured by the same method and composition as the test piece 2 except that the extrusion speed of the extrusion process was changed to 3.7 mm / sec.
（試験片２１）Ｍｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1
押出加工の押出速度を３．７ｍｍ／秒に変更し、その他は試験片３と同様の方法及び組成により試験片２１を製造した。
(Test piece 21) Mg96Zn2Y1.9Nd0.1
A test piece 21 was produced by the same method and composition as the test piece 3 except that the extrusion speed of the extrusion process was changed to 3.7 mm / second.
（試験片２２）Ｍｇ96Ｚｎ2Ｙ1.9Ｐｒ0.1
押出加工の押出速度を３．７ｍｍ／秒に変更し、その他は試験片４と同様の方法及び組成により試験片２２を製造した。
(Test piece 22) Mg96Zn2Y1.9Pr0.1
The test piece 22 was manufactured by the same method and composition as the test piece 4 except that the extrusion speed of the extrusion process was changed to 3.7 mm / second.
（試験片２３）Ｍｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1
押出加工の押出速度を３．７ｍｍ／秒に変更し、その他は試験片５と同様の方法及び組成により試験片２３を製造した。
(Test piece 23) Mg96Zn2Y1.9Sm0.1
The test piece 23 was manufactured by the same method and composition as the test piece 5 except that the extrusion speed of the extrusion process was changed to 3.7 mm / sec.
（試験片２４）Ｍｇ96Ｚｎ2Ｙ1.9Ｙｂ0.1
押出加工の押出速度を３．７ｍｍ／秒に変更し、その他は試験片６と同様の方法及び組成により試験片２４を製造した。
(Test piece 24) Mg96Zn2Y1.9Yb0.1
A test piece 24 was produced by the same method and composition as the test piece 6 except that the extrusion speed of the extrusion process was changed to 3.7 mm / second.
図７（Ａ）は、図６（Ｂ）と同一のグラフであり、図７（Ｂ）は、試験片２５〜３０を２５０℃の温度で引張試験を行い、機械的特性を評価した結果を示すグラフである。図７（Ａ），（Ｂ）に示す「σＵＴＳ」は引張強度であり、「σ0.2」は降伏強度であり、「ＥＬ」は伸びである。試験片の製造方法は下記のとおりである。 FIG. 7 (A) is the same graph as FIG. 6 (B), and FIG. 7 (B) shows the result of performing a tensile test on the test pieces 25 to 30 at a temperature of 250 ° C. and evaluating the mechanical properties. It is a graph to show. “ΣUTS” shown in FIGS. 7A and 7B is tensile strength, “σ0.2” is yield strength, and “EL” is elongation. The manufacturing method of a test piece is as follows.
（試験片２５）Ｍｇ96Ｚｎ2Ｙ1.5Ｌａ0.5
試験片１９の合金組成をＭｇ96Ｚｎ2Ｙ1.5Ｌａ0.5に変更し、その他は試験片１９と同様の方法により試験片２５を製造した。
(Test piece 25) Mg96Zn2Y1.5La0.5
A test piece 25 was produced in the same manner as the test piece 19 except that the alloy composition of the test piece 19 was changed to Mg96Zn2Y1.5La0.5.
（試験片２６）Ｍｇ96Ｚｎ2Ｙ1.5Ｃｅ0.5
試験片１９の合金組成をＭｇ96Ｚｎ2Ｙ1.5Ｃｅ0.5に変更し、その他は試験片１９と同様の方法により試験片２６を製造した。
(Test piece 26) Mg96Zn2Y1.5Ce0.5
The test piece 26 was manufactured in the same manner as the test piece 19 except that the alloy composition of the test piece 19 was changed to Mg96Zn2Y1.5Ce0.5.
（試験片２７）Ｍｇ96Ｚｎ2Ｙ1.5Ｎｄ0.5
試験片１９の合金組成をＭｇ96Ｚｎ2Ｙ1.5Ｎｄ0.5に変更し、その他は試験片１９と同様の方法により試験片２７を製造した。
(Test piece 27) Mg96Zn2Y1.5Nd0.5
A test piece 27 was manufactured in the same manner as the test piece 19 except that the alloy composition of the test piece 19 was changed to Mg96Zn2Y1.5Nd0.5.
（試験片２８）Ｍｇ96Ｚｎ2Ｙ1.5Ｐｒ0.5
試験片１９の合金組成をＭｇ96Ｚｎ2Ｙ1.5Ｐｒ0.5に変更し、その他は試験片１９と同様の方法により試験片２８を製造した。
(Test piece 28) Mg96Zn2Y1.5Pr0.5
A test piece 28 was manufactured in the same manner as the test piece 19 except that the alloy composition of the test piece 19 was changed to Mg96Zn2Y1.5Pr0.5.
（試験片２９）Ｍｇ96Ｚｎ2Ｙ1.5Ｓｍ0.5
試験片１９の合金組成をＭｇ96Ｚｎ2Ｙ1.5Ｓｍ0.5に変更し、その他は試験片１９と同様の方法により試験片２９を製造した。
(Test piece 29) Mg96Zn2Y1.5Sm0.5
A test piece 29 was produced in the same manner as the test piece 19 except that the alloy composition of the test piece 19 was changed to Mg96Zn2Y1.5Sm0.5.
（試験片３０）Ｍｇ96Ｚｎ2Ｙ1.5Ｙｂ0.5
試験片１９の合金組成をＭｇ96Ｚｎ2Ｙ1.5Ｙｂ0.5に変更し、その他は試験片１９と同様の方法により試験片３０を製造した。
(Test piece 30) Mg96Zn2Y1.5Yb0.5
The test piece 30 was manufactured in the same manner as the test piece 19 except that the alloy composition of the test piece 19 was changed to Mg96Zn2Y1.5Yb0.5.
図８（Ａ）は、比較片１に３００℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図８（Ｂ）は、比較片１に３５０℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図８（Ｃ）は、比較片１に４００℃の温度で１時間の熱処理を施した後の結晶組織写真である。 FIG. 8A is a photograph of the crystal structure after heat-treating the comparative piece 1 at a temperature of 300 ° C. for 1 hour, and FIG. 8B shows the comparative piece 1 having a temperature of 350 ° C. for 1 hour. FIG. 8C is a photograph of the crystal structure after heat treatment is performed on the comparative piece 1 at a temperature of 400 ° C. for 1 hour.
図９（Ａ）は、試験片１に３００℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図９（Ｂ）は、試験片１に３５０℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図９（Ｃ）は、試験片１に４００℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図９（Ｄ）は、試験片２に３００℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図９（Ｅ）は、試験片２に３５０℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図９（Ｆ）は、試験片２に４００℃の温度で１時間の熱処理を施した後の結晶組織写真である。 FIG. 9 (A) is a photograph of the crystal structure after heat-treating the test piece 1 at a temperature of 300 ° C. for 1 hour, and FIG. 9 (B) shows the test piece 1 at a temperature of 350 ° C. for 1 hour. FIG. 9C is a photograph of the crystal structure after the heat treatment, and FIG. 9C is a photograph of the crystal structure after the test piece 1 is heat treated at a temperature of 400 ° C. for 1 hour. FIG. 9E is a crystal structure photograph after subjecting test piece 2 to heat treatment at a temperature of 300 ° C. for 1 hour, and FIG. 9 (E) shows crystals after heat treatment of test piece 2 at a temperature of 350 ° C. for one hour. FIG. 9 (F) is a photograph of the crystal structure after subjecting the test piece 2 to heat treatment at a temperature of 400 ° C. for 1 hour.
図１０（Ａ）は、試験片３に３００℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図１０（Ｂ）は、試験片３に３５０℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図１０（Ｃ）は、試験片３に４００℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図１０（Ｄ）は、試験片５に３００℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図１０（Ｅ）は、試験片５に３５０℃の温度で１時間の熱処理を施した後の結晶組織写真であり、図１０（Ｆ）は、試験片５に４００℃の温度で１時間の熱処理を施した後の結晶組織写真である。 FIG. 10 (A) is a photograph of the crystal structure after heat-treating the test piece 3 at a temperature of 300 ° C. for 1 hour, and FIG. 10 (B) shows the test piece 3 at a temperature of 350 ° C. for 1 hour. FIG. 10C is a photograph of the crystal structure after the heat treatment, and FIG. 10C is a photograph of the crystal structure after the heat treatment for 1 hour at a temperature of 400 ° C. FIG. 10E is a crystal structure photograph after the test piece 5 is heat-treated at 300 ° C. for 1 hour, and FIG. 10 (E) is a crystal after the test piece 5 is heat-treated at 350 ° C. for 1 hour. FIG. 10 (F) is a photograph of the crystal structure after heat-treating the test piece 5 at a temperature of 400 ° C. for 1 hour.
図１１（Ａ）〜（Ｃ）は、図８（Ａ）〜（Ｃ）と同一の写真であり、図１１（Ｄ）〜（Ｆ）は、図９（Ｄ）〜（Ｆ）と同一の写真である。 11A to 11C are the same photographs as FIGS. 8A to 8C, and FIGS. 11D to 11F are the same as FIGS. 9D to 9F. It is a photograph.
図１２は、平均結晶粒径と熱処理温度との関係を示すグラフであり、図８（Ａ）〜（Ｃ）、図９（Ａ）〜（Ｆ）、図１０（Ａ）〜（Ｆ）それぞれの試験片の平均結晶粒径と熱処理温度との関係が示されている。 FIG. 12 is a graph showing the relationship between the average crystal grain size and the heat treatment temperature. FIGS. 8 (A) to (C), FIGS. 9 (A) to (F), and FIGS. 10 (A) to (F). The relationship between the average crystal grain size of the test piece and the heat treatment temperature is shown.
図１２によれば、Ｍｇ96Ｚｎ2Ｙ1.9ＲＥ0.1合金（ＲＥ：Ｌａ、Ｃｅ、Ｎｄ、Ｓｍ）の３５０℃の温度での熱処理後の結晶粒径が、Ｍｇ96Ｚｎ2Ｙ2合金の３５０℃の温度での熱処理後の結晶粒径に比べて非常に小さいことが分かる。 According to FIG. 12, the crystal grain size of the Mg96Zn2Y1.9RE0.1 alloy (RE: La, Ce, Nd, Sm) after the heat treatment at a temperature of 350 ° C. is the same as that of the Mg96Zn2Y2 alloy after the heat treatment at a temperature of 350 ° C. It can be seen that it is very small compared to the crystal grain size.
図１４は、２００℃の温度に保持した試験片３１、３２及び比較片２それぞれに１５０ＭＰａの荷重をかけて１０００時間のクリープ試験を行い、２００℃の温度に保持した比較片２に９０ＭＰａの荷重をかけて１０００時間のクリープ試験を行い、それらの結果であるクリープ特性（時間と変形量との関係）を示すグラフである。図１５は、図１４に示すグラフの０〜１００時間までを拡大したグラフである。 FIG. 14 shows that a creep test for 1000 hours is performed by applying a load of 150 MPa to each of the test pieces 31 and 32 and the comparative piece 2 held at a temperature of 200 ° C., and a load of 90 MPa is applied to the comparative piece 2 held at a temperature of 200 ° C. 5 is a graph showing a creep characteristic (relationship between time and deformation amount) as a result of performing a creep test for 1000 hours over time. FIG. 15 is an enlarged graph of 0 to 100 hours of the graph shown in FIG.
（試験片３１）Ｍｇ96Ｚｎ2Ｙ1.9Ｌａ0.1
Ｚｎを２原子％、Ｙを１．９原子％、Ｌａを０．１原子％含有し、残部がＭｇと不可避的不純物からなるマグネシウム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）を作製した。次いで、押出温度３５０℃において押出比１０、押出速度２．５ｍｍ／秒として塑性加工（押出加工）を行ったものを製造した。
(Test piece 31) Mg96Zn2Y1.9La0.1
A magnesium alloy containing 2 atomic% of Zn, 1.9 atomic% of Y, and 0.1 atomic% of La, and the balance of Mg and inevitable impurities was put into a vacuum melting furnace and melted by flux refining. . Next, the heat-dissolved material was placed in a mold and cast to prepare an ingot (cast material) of φ29 mm × L60 mm. Next, a product subjected to plastic working (extrusion process) at an extrusion temperature of 350 ° C. with an extrusion ratio of 10 and an extrusion speed of 2.5 mm / second was produced.
（試験片３２）Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1
試験片３１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1に変更し、その他は試験片３１と同様の方法により試験片３２を製造した。
(Test piece 32) Mg96Zn2Y1.9Ce0.1
The test piece 32 was manufactured by the same method as the test piece 31 except that the alloy composition of the test piece 31 was changed to Mg96Zn2Y1.9Ce0.1.
（比較片２）Ｍｇ96Ｚｎ2Ｙ2
試験片３１の合金組成をＭｇ96Ｚｎ2Ｙ2に変更し、その他は試験片３１と同様の方法により比較片２を製造した。
(Comparative piece 2) Mg96Zn2Y2
The alloy composition of the test piece 31 was changed to Mg96Zn2Y2, and the comparative piece 2 was manufactured by the same method as the test piece 31 except for the above.
図１４及び図１５によれば、Ｍｇ96Ｚｎ2Ｙ1.9Ｌａ0.1（試験片３１）、Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1（試験片３２）がＭｇ96Ｚｎ2Ｙ2（比較片２）に比べて２００℃で優れたクリープ特性を示すことが確認された。 14 and 15, Mg96Zn2Y1.9La0.1 (test piece 31) and Mg96Zn2Y1.9Ce0.1 (test piece 32) exhibit excellent creep characteristics at 200 ° C. compared to Mg96Zn2Y2 (comparative piece 2). Was confirmed.
図１６は、試験片３１、３２及び比較片２に図１４に示す荷重１５０ＭＰａ・１０００時間のクリープ試験を行った後の結晶組織写真である。 FIG. 16 is a photograph of the crystal structure after the test pieces 31 and 32 and the comparative piece 2 were subjected to a creep test with a load of 150 MPa · 1000 hours shown in FIG.
図１７は、比較片２に図１４に示す荷重９０ＭＰａ・１０００時間のクリープ試験を行った後のサンプルの外観写真、及び試験片３１、３２及び比較片２に図１４に示す荷重１５０ＭＰａ・１０００時間のクリープ試験を行った後のサンプルの外観写真である。 FIG. 17 is a photograph of the appearance of the sample after the creep test of the load 90 MPa · 1000 hours shown in FIG. 14 is performed on the comparative piece 2, and the load 150 MPa · 1000 hours shown in FIG. 14 on the test pieces 31 and 32 and the comparative piece 2. It is the external appearance photograph of the sample after performing the creep test of.
図１６によれば、Ｍｇ96Ｚｎ2Ｙ2（比較片２）の組織変化がＭｇ96Ｚｎ2Ｙ1.9Ｌａ0.1（試験片３１）、Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1（試験片３２）より多いことが分かる。
また、図１７によれば、クリープ実験後、Ｍｇ96Ｚｎ2Ｙ2（比較片２）よりＭｇ96Ｚｎ2Ｙ1.9Ｌａ0.1（試験片３１）、Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1（試験片３２）が表面の酸化物の量が少ないことが分かる。
According to FIG. 16, it can be seen that the structure change of Mg96Zn2Y2 (Comparative specimen 2) is larger than that of Mg96Zn2Y1.9La0.1 (test specimen 31) and Mg96Zn2Y1.9Ce0.1 (test specimen 32).
Also, according to FIG. 17, after the creep experiment, Mg96Zn2Y1.9La0.1 (test piece 31) and Mg96Zn2Y1.9Ce0.1 (test piece 32) have less oxide on the surface than Mg96Zn2Y2 (comparative piece 2). I understand.
図１８は、２００℃の温度に保持した試験片３３、３４及び比較片２それぞれに２１０ＭＰａの荷重をかけて５０時間のクリープ試験を行い、その結果であるクリープ特性（時間と変形量との関係）を示すグラフである。 FIG. 18 shows a result of a 50 hour creep test with a load of 210 MPa applied to each of test pieces 33 and 34 and comparative piece 2 held at a temperature of 200 ° C., and the resulting creep characteristics (relationship between time and deformation amount). ).
（試験片３３）Ｍｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1
試験片３１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1に変更し、その他は試験片３１と同様の方法により試験片３３を製造した。
(Test piece 33) Mg96Zn2Y1.9Sm0.1
A test piece 33 was manufactured in the same manner as the test piece 31 except that the alloy composition of the test piece 31 was changed to Mg96Zn2Y1.9Sm0.1.
（試験片３４）Ｍｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1
試験片３１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1に変更し、その他は試験片３１と同様の方法により試験片３４を製造した。
(Test piece 34) Mg96Zn2Y1.9Nd0.1
A test piece 34 was manufactured in the same manner as the test piece 31 except that the alloy composition of the test piece 31 was changed to Mg96Zn2Y1.9Nd0.1.
図１５に示す５０時間のクリープ特性が図１４に示す１０００時間のクリープ特性とほぼ同じ傾向を示すことから、図１８に示す５０時間のクリープ特性についても、それより長時間のクリープ特性とほぼ同じ傾向を示すことが期待される。 Since the 50-hour creep characteristics shown in FIG. 15 show almost the same tendency as the 1000-hour creep characteristics shown in FIG. 14, the 50-hour creep characteristics shown in FIG. 18 are almost the same as the long-term creep characteristics. It is expected to show a trend.
図１８によれば、Ｍｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1（試験片３３）、Ｍｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1（試験片３４）がＭｇ96Ｚｎ2Ｙ2（比較片２）に比べて２００℃で優れたクリープ特性を示すことが確認された。 According to FIG. 18, it was confirmed that Mg96Zn2Y1.9Sm0.1 (test piece 33) and Mg96Zn2Y1.9Nd0.1 (test piece 34) show excellent creep characteristics at 200 ° C. compared to Mg96Zn2Y2 (comparative piece 2). It was.
図１９は、試験片３３、３４及び比較片２に図１８に示す荷重２１０ＭＰａ・５０時間のクリープ試験を行った後の結晶組織写真である。 FIG. 19 is a photograph of the crystal structure after the test pieces 33 and 34 and the comparative piece 2 were subjected to a creep test with a load of 210 MPa · 50 hours shown in FIG.
図１９によれば、Ｍｇ96Ｚｎ2Ｙ2（比較片２）の組織変化が、Ｍｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1（試験片３３）、Ｍｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1（試験片３４）より多いことが分かる。 According to FIG. 19, it can be seen that the structure change of Mg96Zn2Y2 (Comparative specimen 2) is larger than that of Mg96Zn2Y1.9Sm0.1 (test specimen 33) and Mg96Zn2Y1.9Nd0.1 (test specimen 34).
図２０は、２２５℃の温度に保持した比較片２、３それぞれに１６０ＭＰａの荷重をかけて５０時間のクリープ試験を行い、その結果であるクリープ特性（時間と変形量との関係）を示すグラフである。 FIG. 20 is a graph showing creep characteristics (relationship between time and deformation amount) as a result of a creep test for 50 hours with a load of 160 MPa applied to each of comparative pieces 2 and 3 held at a temperature of 225 ° C. It is.
図２０によれば、Ｍｇ96Ｚｎ2Ｙ2（比較片２）がＭｇ97Ｚｎ1Ｙ2（比較片３）に比べて２２５℃で優れたクリープ特性を示すことが確認された。 According to FIG. 20, it was confirmed that Mg96Zn2Y2 (Comparative piece 2) showed excellent creep characteristics at 225 ° C. compared to Mg97Zn1Y2 (Comparative piece 3).
（比較片３）Ｍｇ97Ｚｎ1Ｙ2
試験片３１の合金組成をＭｇ97Ｚｎ1Ｙ2に変更し、その他は試験片３１と同様の方法により比較片３を製造した。
(Comparative piece 3) Mg97Zn1Y2
The alloy composition of the test piece 31 was changed to Mg97Zn1Y2, and the comparison piece 3 was manufactured in the same manner as the test piece 31 except for the above.
図２１は、比較片２、３に図２０に示す荷重１６０ＭＰａ・５０時間のクリープ試験を行った後の結晶組織写真である。
図２１によれば、クリープ試験後のＭｇ97Ｚｎ1Ｙ2（比較片３）の組織変化が、Ｍｇ96Ｚｎ2Ｙ2（比較片２）より多いことが分かる。
FIG. 21 is a photograph of the crystal structure after the comparative specimens 2 and 3 were subjected to a creep test with a load of 160 MPa · 50 hours shown in FIG.
According to FIG. 21, it can be seen that the structure change of Mg97Zn1Y2 (comparative piece 3) after the creep test is larger than that of Mg96Zn2Y2 (comparative piece 2).
図２２は、２２５℃の温度に保持した試験片３５〜３８及び比較片４それぞれに１６０ＭＰａの荷重をかけて５０時間のクリープ試験を行い、その結果であるクリープ特性（時間と変形量との関係）を示すグラフである。 FIG. 22 shows the result of creep test (relationship between time and amount of deformation) as a result of performing a creep test for 50 hours by applying a load of 160 MPa to each of the test pieces 35 to 38 and the comparative piece 4 held at a temperature of 225 ° C. ).
（試験片３５）Ｍｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1
比較片３の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1に変更し、押出速度を２．９ｍｍ／秒に変更し、その他は比較片３と同様の方法により試験片３５を製造した。
(Test piece 35) Mg96Zn2Y1.9Nd0.1
The test piece 35 was manufactured in the same manner as the comparative piece 3 except that the alloy composition of the comparative piece 3 was changed to Mg96Zn2Y1.9Nd0.1, the extrusion speed was changed to 2.9 mm / sec.
（試験片３６）Ｍｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1
試験片３１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1に変更し、押出速度を２．９ｍｍ／秒に変更し、その他は試験片３１と同様の方法により試験片３６を製造した。
(Test piece 36) Mg96Zn2Y1.9Sm0.1
A test piece 36 was manufactured in the same manner as the test piece 31 except that the alloy composition of the test piece 31 was changed to Mg96Zn2Y1.9Sm0.1, the extrusion speed was changed to 2.9 mm / sec.
（試験片３７）Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1
試験片３１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1に変更し、押出速度を２．９ｍｍ／秒に変更し、その他は試験片３１と同様の方法により試験片３７を製造した。
(Test piece 37) Mg96Zn2Y1.9Ce0.1
A test piece 37 was manufactured in the same manner as the test piece 31 except that the alloy composition of the test piece 31 was changed to Mg96Zn2Y1.9Ce0.1, the extrusion speed was changed to 2.9 mm / sec.
（試験片３８）Ｍｇ96Ｚｎ2Ｙ1.9Ｌａ0.1
試験片３１の合金組成をＭｇ96Ｚｎ2Ｙ1.9Ｌａ0.1に変更し、押出速度を２．９ｍｍ／秒に変更し、その他は試験片３１と同様の方法により試験片３８を製造した。
(Test piece 38) Mg96Zn2Y1.9La0.1
A test piece 38 was produced in the same manner as the test piece 31 except that the alloy composition of the test piece 31 was changed to Mg96Zn2Y1.9La0.1, the extrusion speed was changed to 2.9 mm / sec.
（比較片４）Ｍｇ96Ｚｎ2Ｙ2
試験片３１の押出速度を２．９ｍｍ／秒に変更し、その他は試験片３１と同様の方法により比較片４を製造した。
(Comparison piece 4) Mg96Zn2Y2
The extrusion speed of the test piece 31 was changed to 2.9 mm / sec, and the other comparison pieces 4 were produced in the same manner as the test piece 31.
図２２によれば、試験片３５〜３８が比較片４に比べて２２５℃で優れたクリープ特性を示すことが確認された。 According to FIG. 22, it was confirmed that the test pieces 35 to 38 exhibited excellent creep characteristics at 225 ° C. as compared with the comparative piece 4.
図２３は、２２５℃の温度に保持した試験片３９〜４２及び比較片５それぞれに１６０ＭＰａの荷重をかけて５０時間のクリープ試験を行い、その結果であるクリープ特性（時間と変形量との関係）を示すグラフである。 FIG. 23 shows a creep property (relationship between time and deformation) as a result of performing a creep test for 50 hours by applying a load of 160 MPa to each of the test pieces 39 to 42 and the comparative piece 5 held at a temperature of 225 ° C. ).
（試験片３９）Ｍｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1
試験片３５の押出速度を３．３ｍｍ／秒に変更し、その他は試験片３５と同様の方法により試験片３９を製造した。
(Test piece 39) Mg96Zn2Y1.9Nd0.1
The test piece 39 was manufactured by the same method as the test piece 35 except that the extrusion speed of the test piece 35 was changed to 3.3 mm / sec.
（試験片４０）Ｍｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1
試験片３６の押出速度を３．３ｍｍ／秒に変更し、その他は試験片３６と同様の方法により試験片４０を製造した。
(Test piece 40) Mg96Zn2Y1.9Sm0.1
The test piece 40 was manufactured by the same method as the test piece 36 except that the extrusion speed of the test piece 36 was changed to 3.3 mm / sec.
（試験片４１）Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1
試験片３７の押出速度を３．３ｍｍ／秒に変更し、その他は試験片３７と同様の方法により試験片４１を製造した。
(Test piece 41) Mg96Zn2Y1.9Ce0.1
The test piece 41 was manufactured by the same method as the test piece 37 except that the extrusion speed of the test piece 37 was changed to 3.3 mm / sec.
（試験片４２）Ｍｇ96Ｚｎ2Ｙ1.9Ｌａ0.1
試験片３８の押出速度を３．３ｍｍ／秒に変更し、その他は試験片３８と同様の方法により試験片４２を製造した。
(Test piece 42) Mg96Zn2Y1.9La0.1
The test piece 42 was manufactured by the same method as the test piece 38 except that the extrusion speed of the test piece 38 was changed to 3.3 mm / sec.
（比較片５）Ｍｇ96Ｚｎ2Ｙ2
比較片４の押出速度を３．３ｍｍ／秒に変更し、その他は比較片４と同様の方法により比較片５を製造した。
(Comparative piece 5) Mg96Zn2Y2
The extrusion speed of the comparative piece 4 was changed to 3.3 mm / second, and the comparative piece 5 was manufactured by the same method as the comparative piece 4 except for the others.
図２３によれば、試験片３９〜４２が比較片６に比べて２２５℃で優れたクリープ特性を示すことが確認された。 According to FIG. 23, it was confirmed that the test pieces 39 to 42 exhibited excellent creep characteristics at 225 ° C. as compared with the comparative piece 6.
図２４は、２２５℃の温度に保持した試験片４３〜４６及び比較片６それぞれに１６０ＭＰａの荷重をかけて５０時間のクリープ試験を行い、その結果であるクリープ特性（時間と変形量との関係）を示すグラフである。 FIG. 24 shows the result of creep test (relationship between time and amount of deformation) as a result of performing a creep test for 50 hours by applying a load of 160 MPa to each of test pieces 43 to 46 and comparative piece 6 held at a temperature of 225 ° C. ).
（試験片４３）Ｍｇ96Ｚｎ2Ｙ1.9Ｎｄ0.1
試験片３５の押出速度を３．７ｍｍ／秒に変更し、その他は試験片３５と同様の方法により試験片４３を製造した。
(Test piece 43) Mg96Zn2Y1.9Nd0.1
The test piece 43 was manufactured by the same method as the test piece 35 except that the extrusion speed of the test piece 35 was changed to 3.7 mm / sec.
（試験片４４）Ｍｇ96Ｚｎ2Ｙ1.9Ｓｍ0.1
試験片３６の押出速度を３．７ｍｍ／秒に変更し、その他は試験片３６と同様の方法により試験片４４を製造した。
(Test piece 44) Mg96Zn2Y1.9Sm0.1
A test piece 44 was manufactured in the same manner as the test piece 36 except that the extrusion speed of the test piece 36 was changed to 3.7 mm / sec.
（試験片４５）Ｍｇ96Ｚｎ2Ｙ1.9Ｃｅ0.1
試験片３７の押出速度を３．７ｍｍ／秒に変更し、その他は試験片３７と同様の方法により試験片４５を製造した。
(Test piece 45) Mg96Zn2Y1.9Ce0.1
The test piece 45 was manufactured by the same method as the test piece 37 except that the extrusion speed of the test piece 37 was changed to 3.7 mm / sec.
（試験片４６）Ｍｇ96Ｚｎ2Ｙ1.9Ｌａ0.1
試験片３８の押出速度を３．７ｍｍ／秒に変更し、その他は試験片３８と同様の方法により試験片４６を製造した。
(Test piece 46) Mg96Zn2Y1.9La0.1
The test piece 46 was manufactured in the same manner as the test piece 38 except that the extrusion speed of the test piece 38 was changed to 3.7 mm / sec.
（比較片６）Ｍｇ96Ｚｎ2Ｙ2
比較片４の押出速度を３．７ｍｍ／秒に変更し、その他は比較片４と同様の方法により比較片６を製造した。
(Comparative piece 6) Mg96Zn2Y2
The extrusion speed of the comparative piece 4 was changed to 3.7 mm / sec, and the comparative piece 6 was manufactured in the same manner as the comparative piece 4 except for the others.
図２４によれば、試験片４３〜４６が比較片６に比べて２２５℃で優れたクリープ特性を示すことが確認された。
また、図２２〜図２４によれば、試験片を作製する際の押出速度が遅いほうが、試験片全体的にクリープ特性が良くなることが分かる。
According to FIG. 24, it was confirmed that the test pieces 43 to 46 showed excellent creep characteristics at 225 ° C. as compared with the comparative piece 6.
Moreover, according to FIGS. 22-24, it turns out that the one where the extrusion speed at the time of producing a test piece is slow improves creep characteristics as a whole test piece.
図２５は、図２０に示す比較片２、図２２に示す試験片３８及び比較片４、図２３に示す試験片４２及び比較片５、図２４に示す試験片４６及び比較片６それぞれのクリープ特性を示すグラフである。
図２５によれば、合金組成がＭｇ96Ｚｎ2Ｙ2の比較片は押出速度が高くなるに従いクリープ特性が悪くなるのに対し、合金組成がＭｇ96Ｚｎ2Ｙ1.9Ｌａ0.1の試験片は押出速度と関係なくクリープ特性が良いことが確認された。
FIG. 25 shows the creep of the comparative piece 2 shown in FIG. 20, the test piece 38 and the comparative piece 4 shown in FIG. 22, the test piece 42 and the comparative piece 5 shown in FIG. 23, and the test piece 46 and the comparative piece 6 shown in FIG. It is a graph which shows a characteristic.
According to FIG. 25, the comparative specimen with the alloy composition Mg96Zn2Y2 deteriorates in creep characteristics as the extrusion speed increases, whereas the specimen with the alloy composition Mg96Zn2Y1.9La0.1 has good creep characteristics regardless of the extrusion speed. It was confirmed.
図２６は、図２２に示すクリープ試験を行った後の比較片４、図２３に示すクリープ試験を行った後の比較片５、図２４に示すクリープ試験を行った後の比較片６それぞれの結晶組織写真である。図２７は、図２２に示すクリープ試験を行った後の試験片３８、図２３に示すクリープ試験を行った後の試験片４２、図２４に示すクリープ試験を行った後の試験片４６それぞれの結晶組織写真である。 26 shows the comparison piece 4 after the creep test shown in FIG. 22, the comparison piece 5 after the creep test shown in FIG. 23, and the comparison piece 6 after the creep test shown in FIG. It is a crystal structure photograph. 27 shows a test piece 38 after the creep test shown in FIG. 22, a test piece 42 after the creep test shown in FIG. 23, and a test piece 46 after the creep test shown in FIG. It is a crystal structure photograph.
図２８は、平均結晶粒径と押出速度との関係を示すグラフであり、図２０に示す比較片２、図２２に示す試験片３８及び比較片４、図２３に示す試験片４２及び比較片５、図２４に示す試験片４６及び比較片６それぞれのクリープ試験後の平均結晶粒径と押出速度との関係が示されている。 FIG. 28 is a graph showing the relationship between the average crystal grain size and the extrusion speed. The comparative piece 2 shown in FIG. 20, the test piece 38 and the comparative piece 4 shown in FIG. 22, the test piece 42 and the comparative piece shown in FIG. 5, the relationship between the average crystal grain size after the creep test and the extrusion rate of each of the test piece 46 and the comparison piece 6 shown in FIG. 24 is shown.
図２６及び図２８によれば、合金組成がＭｇ96Ｚｎ2Ｙ2のクリープ試験後の比較片は、押出速度が高くなるに従い、結晶粒径が大きくなることが分かる。
また、図２６〜図２８によれば、合金組成がＭｇ96Ｚｎ2Ｙ1.9Ｌａ0.1のクリープ試験後の試験片は、押出速度が高くなっても結晶粒径の変化がＭｇ96Ｚｎ2Ｙ2に比べて少ないことが分かる。
26 and 28, it can be seen that the comparative specimen after the creep test having an alloy composition of Mg96Zn2Y2 has a larger crystal grain size as the extrusion rate increases.
Further, according to FIGS. 26 to 28, it can be seen that the test piece after the creep test with an alloy composition of Mg96Zn2Y1.9La0.1 has a smaller change in crystal grain size compared with Mg96Zn2Y2 even when the extrusion rate is increased.
１１，１７ 室温での引張強度
１２，１８ 室温での降伏強度
１３，１９ ２５０℃の温度での引張強度
１４，２０ ２５０℃の温度での降伏強度
１５，２１ ２５０℃の温度での伸び
１６，２２ 室温での伸び
２３，２６ ＬＰＳＯの体積分率と引張強度との関係
２４，２７ ＬＰＳＯの体積分率と降伏強度との関係
２５，２８ ＬＰＳＯの体積分率と伸びとの関係
11,17 Tensile strength at room temperature 12,18 Yield strength at room temperature 13,19 Tensile strength at a temperature of 250 ° C. 14,20 Yield strength at a temperature of 250 ° C. 15,21 Elongation at a temperature of 250 ° C. 16, 22 Elongation at room temperature 23,26 Relationship between volume fraction of LPSO and tensile strength 24,27 Relationship between volume fraction of LPSO and yield strength 25,28 Relationship between volume fraction of LPSO and elongation
Claims (4)
Ｚｎをａ原子％含有し、Ｙをｂ原子％含有し、Ｌａ、Ｃｅ、Ｎｄ、Ｐｒ、Ｓｍ及びＹｂからなる群から選択される少なくとも１つの元素を合計でｃ原子％含有し、残部がＭｇと不可避的不純物からなり、ａとｂとｃは下記式（１）〜（３）を満たすことを特徴とする高強度マグネシウム合金。
（１）０＜ａ≦２．０
（２）１．０≦ｂ≦１．９５
（３）０．０５≦ｃ≦１．０ A high-strength magnesium alloy used at a temperature higher than room temperature,
Zn contains a atomic%, Y contains b atomic%, contains at least one element selected from the group consisting of La, Ce, Nd, Pr, Sm, and Yb in total, containing c atomic%, with the balance being Mg A high-strength magnesium alloy characterized in that a, b, and c satisfy the following formulas (1) to (3).
(1) 0 <a ≦ 2.0
(2) 1.0 ≦ b ≦ 1.95
(3) 0.05 ≦ c ≦ 1.0
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| JP2013018027A (en) * | 2011-07-11 | 2013-01-31 | Kobe Steel Ltd | Method for manufacturing magnesium alloy material, and magnesium alloy material manufactured thereby |
| JP2019151925A (en) * | 2018-02-28 | 2019-09-12 | 国立大学法人 熊本大学 | Flame retardant magnesium alloy and manufacturing method therefor |
| CN113337765A (en) * | 2021-05-27 | 2021-09-03 | 长春理工大学 | High-temperature and high-pressure creep-resistant die-casting magnesium alloy and preparation method thereof |
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| CN107354357B (en) * | 2017-06-28 | 2019-10-25 | 中国科学院长春应用化学研究所 | A kind of wrought magnesium alloy and preparation method thereof |
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