JP5161414B2 - High strength magnesium alloy - Google Patents

High strength magnesium alloy Download PDF

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JP5161414B2
JP5161414B2 JP2002566397A JP2002566397A JP5161414B2 JP 5161414 B2 JP5161414 B2 JP 5161414B2 JP 2002566397 A JP2002566397 A JP 2002566397A JP 2002566397 A JP2002566397 A JP 2002566397A JP 5161414 B2 JP5161414 B2 JP 5161414B2
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能人 河村
明久 井上
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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
    • 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
    • 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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Description

本発明は、マグネシウム合金に関し、特に、微細結晶構造を有する高強度マグネシウム合金に関する。   The present invention relates to a magnesium alloy, and more particularly to a high-strength magnesium alloy having a fine crystal structure.

マグネシウム合金は、その軽量性に加えて比強度・比剛性に優れていることから軽量高強度材として注目されており、今後さらなる特性の向上を図ることが切望されている材料である。   Magnesium alloys are attracting attention as lightweight high-strength materials because they are superior in specific strength and specific rigidity in addition to their lightweight properties, and are a material that is desired to further improve their properties in the future.

さて、高強度の新しいマグネシウム合金を創製するためには、急速凝固法などの非平衡プロセスの適用が有効である。マグネシウム合金における急速凝固粉末冶金（ＲＳ Ｐ／Ｍ）法の適用例としては、ガスアトマイズ法により作製したアモルファス合金粉末の押出成形により作製したナノ結晶合金が報告されている。しかし、これらの材料は優れた引張り強度を示すが、伸びが小さいといった問題がある。一方、既存の合金組成に対してもＲＳ Ｐ／Ｍ法は適用されているが、著しい強度の向上は達成されていない。   In order to create a new high strength magnesium alloy, it is effective to apply a non-equilibrium process such as rapid solidification. As an application example of the rapidly solidified powder metallurgy (RS P / M) method in a magnesium alloy, a nanocrystalline alloy produced by extrusion molding of an amorphous alloy powder produced by a gas atomizing method has been reported. However, these materials exhibit excellent tensile strength but have a problem of low elongation. On the other hand, although the RSP / M method is applied to the existing alloy composition, a significant improvement in strength has not been achieved.

本発明の目的は、優れた引張り強度と良好な延性を有する高強度マグネシウム合金を提供することである。
上記目的を達成するために、本発明は、一般式で、Ｍｇ（１００−ｘ−ｙ）ＹｘＺｎｙ（１＜ｘ＜５，０．３＜ｙ＜６：ｘ，ｙはいずれも原子％）の組成を有し、１マイクロメートル以下の微細結晶組織を有することを特徴とする高強度マグネシウム合金である。
また、本発明は、Ｍｇ２４Ｙ５およびＹＺｎを有し、他はｈｃｐ−Ｍｇであり、それぞれが１マイクロメータ以下の微細結晶組織を有することを特徴とする高強度マグネシウム合金でもある。
これらの高強度マグネシウム合金において、液体から急速に凝固された粉末、薄帯又は細線を、せん断が付加されるように固化することで作製することができる。このようにして作製することにより、超塑性を発現することができる。 An object of the present invention is to provide a high strength magnesium alloy having excellent tensile strength and good ductility.
In order to achieve the above object, the present invention provides a general formula of Mg (100-xy) YxZny (1 <x <5, 0.3 <y <6: where x and y are atomic%). A high-strength magnesium alloy having a composition and a fine crystal structure of 1 micrometer or less.
The present invention is also a high-strength magnesium alloy having Mg 24 Y 5 and YZn, the other being hcp-Mg, each having a fine crystal structure of 1 micrometer or less.
In these high-strength magnesium alloys, powders, ribbons or fine wires rapidly solidified from a liquid can be produced by solidification so that shear is applied. Superplasticity can be expressed by producing in this way.

本発明の実施形態を、図面を参照して詳細に説明する。   Embodiments of the present invention will be described in detail with reference to the drawings.

本発明においては、Ｍｇ−Ｚｎ−Ｙ急速凝固薄帯を用いて行った合金組成探査を行い、これら一連の組成探査の結果を基に、ガスアトマイズ法でＭｇ−Ｚｎ−Ｙ ＲＳ Ｐ／Ｍ材を作製して、機械的性質を詳しく測定した。この合金の機械的性質は、延性および引張り強度が大変すぐれている。   In the present invention, the alloy composition exploration performed using the Mg—Zn—Y rapidly solidified ribbon is performed, and based on the results of the series of composition exploration, the Mg—Zn—Y RS P / M material is obtained by the gas atomization method. Fabricated and mechanical properties were measured in detail. The mechanical properties of this alloy are very good in ductility and tensile strength.

さて、まず、合金組成探査について説明する。組成探査のためのマグネシウム合金の母合金は高周波溶解炉を用いて、Ａｒ雰囲気中で作製した。合金組成探査に用いた急速擬固薄帯は、単ロール式液体急冷法により作製した。得られた急速凝固薄帯に対して、ＲＳ Ｐ／Ｍ法における固化成形（押出成形）を想定した５７３Ｋおよび６７３Ｋにおける熱処理を施して、熱処理材を作製した。急速凝固材および熱処理材の組織はＸ線回折法により調べた。また、引張り強さおよび硬さなどの機械的性質は、インストロン引張り試験機およびマイクロビッカース硬さ試験機を用いて調べた。延性は１８０°密着曲げ試験により評価した。その合成組成探査の結果を、図面の第１図〜第３図を用いて説明する。なお、以下の記述で、合金の組成は、原子％で示している。   First, the alloy composition exploration will be described. A magnesium alloy master alloy for composition exploration was produced in an Ar atmosphere using a high-frequency melting furnace. The rapid quasi-solid ribbon used for exploration of alloy composition was prepared by a single roll liquid quenching method. The obtained rapidly solidified ribbon was subjected to heat treatment at 573K and 673K assuming solidification molding (extrusion molding) in the RS P / M method, and a heat treatment material was produced. The structures of the rapidly solidified material and the heat-treated material were examined by an X-ray diffraction method. Further, mechanical properties such as tensile strength and hardness were examined using an Instron tensile tester and a micro Vickers hardness tester. The ductility was evaluated by a 180 ° contact bending test. The result of the synthetic composition search will be described with reference to FIGS. In the following description, the composition of the alloy is shown in atomic%.

第１図〜第３図に、熱処理を行う前、５７３Ｋおよび６７３Ｋで熱処理した後のＭｇ−Ｚｎ−Ｙ急速凝固薄帯の硬さと延性を、それぞれの組成の合金に対して示す。これらの温度は、押出成形を行うための下限（５７３Ｋ）と上限（６７３Ｋ）の温度である。これらの図において、白抜きの丸として示したのは、１８０度曲げても折れない、延性が高いものを示している。１８０度近くで折れるものは、脆性を示す黒い丸として表した。半黒丸印は、１８０度曲げでは折れたが、１８０度近くまで曲げても折れない程度の良好な延性を示したものを示している。また、各丸印の下の数字は、ダイヤモンド・ピラミッド硬度数（ビッカース硬度）を示している。   FIGS. 1 to 3 show the hardness and ductility of Mg—Zn—Y rapidly solidified ribbons after heat treatment at 573 K and 673 K before the heat treatment, for the alloys of the respective compositions. These temperatures are the lower limit (573K) and the upper limit (673K) for performing extrusion molding. In these figures, the white circles indicate those that are not broken even when bent 180 degrees and that have high ductility. Those that broke near 180 degrees were represented as black circles indicating brittleness. The half-black circle mark shows a good ductility that is broken by bending at 180 degrees but not broken even when bent to near 180 degrees. The numbers under each circle indicate the diamond pyramid hardness number (Vickers hardness).

これらの図でわかるように、Ｍｇ−Ｚｎ−Ｙ合金は、熱処理後に良好な延性と高い硬さを示すことが分かった。   As can be seen from these figures, the Mg—Zn—Y alloy was found to exhibit good ductility and high hardness after heat treatment.

次に、急速凝固粉末の作製とその固化成形を行った。固化成形まで行ったＭｇ−Ｚｎ−Ｙ合金は、第２図や第３図において、良好な延性と高硬度を示したＭｇ−Ｚｎ−Ｙ合金である、Ｍｇ９７Ｚｎ１Ｙ２合金（第２図，第３図のＡ）の組成を有するものを用いて行った。

＜Ｍｇ９７Ｚｎ１Ｙ２ＲＳ Ｐ／Ｍ材の作製と機械的性質＞ Next, a rapidly solidified powder was produced and solidified. The Mg—Zn—Y alloy which has been solidified and formed is an Mg 97 Zn 1 Y 2 alloy ( second alloy) which is an Mg—Zn—Y alloy showing good ductility and high hardness in FIGS. It carried out using what has the composition of A) of a figure and FIG.

<Preparation and mechanical properties of Mg 97 Zn 1 Y 2 RS P / M material>

急速凝固粉末の作製とその固化成形には、クローズドＰ／Ｍプロセッシング・システムを使用した。作製に使用したシステムを第４図及び第５図に示す。第４図は、ガス・アトマイズ法による急速凝固粉末の作製と、作製された粉末から、固化成形してビレットを作製する工程を示している。第５図は作製したビレットを押出成形するまでを示している。第４図および第５図を用いて、急速凝固粉末の作製と固化成形について、詳しく説明する。   A closed P / M processing system was used for the preparation of the rapidly solidified powder and its solidification molding. The system used for production is shown in FIG. 4 and FIG. FIG. 4 shows a process for producing a rapidly solidified powder by a gas atomization method and a process for producing a billet by solidification molding from the produced powder. FIG. 5 shows the process up to extruding the produced billet. The production and solidification of rapidly solidified powder will be described in detail with reference to FIG. 4 and FIG.

第４図において、高圧ガス・アトマイザ１００を用いて目的とする成分比のＭｇ−Ｚｎ−Ｙ合金の粉末を作製する。これは、まず、溶解室１１０中のるつぼ１１６中で、目的の成分比を有する合金を誘導コイル１１４により溶解する。この溶けた合金を、ストッパ１１２を上げて噴出させ、それにノズル１３２から高圧の不活性ガス（例えば、ヘリウム・ガスやアルゴン・ガス）を吹きつけて噴霧することで、合金の粉末を作製する。ノズル等はヒータ１３１で加熱されている。また、アトマイズ室１３０は、酸素分析器１６２や真空ゲージ１６４で監視されている。   In FIG. 4, a high-pressure gas atomizer 100 is used to produce Mg—Zn—Y alloy powder having a target component ratio. First, an alloy having a target component ratio is melted by the induction coil 114 in the crucible 116 in the melting chamber 110. The melted alloy is ejected by raising the stopper 112, and sprayed by spraying high pressure inert gas (for example, helium gas or argon gas) from the nozzle 132, thereby producing alloy powder. The nozzle and the like are heated by the heater 131. The atomizing chamber 130 is monitored by an oxygen analyzer 162 and a vacuum gauge 164.

作製した合金粉末は、サイクロン分級機１４０を介して、真空グローブ・ボックス２００中のホッパ２２０中に収集される。以後の処理は、この真空グローブ・ボックス２００の中で行われる。次に、真空グローブ・ボックス２００中で徐々に細かいふるい２３０にかけることにより、目的とする細かさの粉末を得る。本発明では、粒径３２μｍ以下の粉末を得ている。   The produced alloy powder is collected in a hopper 220 in a vacuum glove box 200 via a cyclone classifier 140. Subsequent processing is performed in the vacuum glove box 200. Next, by gradually passing through a fine sieve 230 in the vacuum glove box 200, a powder having a desired fineness is obtained. In the present invention, a powder having a particle size of 32 μm or less is obtained.

この合金の粉末から、ビレットを作製するために、まず、予備圧縮を真空ホットプレス機２４０を用いて行う。この場合の真空ホットプレス機は、３０トンのプレスを行うことができるものを用いた。   In order to produce a billet from the alloy powder, first, preliminary compression is performed using a vacuum hot press machine 240. In this case, a vacuum hot press machine capable of pressing 30 tons was used.

まず、合金粉末をホットプレス機２４０を用いて銅の缶２５４に充填し、上からキャップ２５２をかぶせる。キャップ２５２と缶２５４とを、回転盤２５８で回転しながら、溶接機２５６で溶接してビレット２６０を作製する。このビレット２６０の漏れチェックのため、バルブ２６２を介して真空ポンプに接続することで、ビレット２６０の漏れをチェックする。漏れが無かった場合、バルブ２６２を閉じて、バルブ２６２を付けたまま容器ごと、真空グローブ・ボックス２００のエントランス・ボックス２８０から合金のビレット２６０を取り出す。   First, the alloy powder is filled into a copper can 254 using a hot press machine 240, and a cap 252 is covered from above. The cap 252 and the can 254 are welded by a welding machine 256 while being rotated by a turntable 258 to produce a billet 260. In order to check the leakage of the billet 260, the leakage of the billet 260 is checked by connecting to the vacuum pump via the valve 262. If there is no leak, the valve 262 is closed and the alloy billet 260 is removed from the entrance box 280 of the vacuum glove box 200 with the valve 262 attached.

取り出したビレット２６０は、第５図に示すように、加熱炉にいれて予備加熱を行いながら、真空ポンプに接続してガス抜きを行う。次にビレット２６０のキャップを圧搾してから、スポット溶接機３４０でスポット溶接して、ビレット２６０と外部との接続を遮断する（第５図（ｂ）参照）。そして、容器ごと、合金のビレットを押出プレス機４００にかけて、最終形状に成形する（第５図（ｃ）参照）。押出プレス機は、メイン・プレス（メイン・ステム４５０側）は１００トン、バック・プレス（バック・ステム４７０側）は２０トンの性能を有し、ヒータ４１０でコンテナ４２０を加熱することで、押出温度を設定することができる。   As shown in FIG. 5, the taken billet 260 is connected to a vacuum pump and degassed while being preheated in a heating furnace. Next, after the cap of the billet 260 is squeezed, it is spot welded by the spot welder 340, and the connection between the billet 260 and the outside is cut off (see FIG. 5B). Then, for each container, the billet of the alloy is passed through the extrusion press 400 and formed into a final shape (see FIG. 5 (c)). The extrusion press has a performance of 100 tons for the main press (on the main stem 450 side) and 20 tons on the back press (on the back stem 470 side). The temperature can be set.

本発明の急速凝固粉末は、上述のように、高圧Ｈｅガスアトマイズ法により作製した。そして、作製した粒径３２μｍ以下の粉末を銅製の缶に充填し、それを真空封入することでビレットを作製し、押出温度６２３〜７２３Ｋ、押出し比１０：１の押出成形により固化成形を行った。この押出成形により、粉末に圧力とせん断が加わり、緻密化と粉末間の結合が達成される。なお、圧延法や鍛造法による成形でもせん断が生じる。急速凝固粉末および押出材の組織はＸ線回折法およびＴＥＭ観察により調べた。引張り試験は、インストロン引張り試験機を用いて初期ひずみ速度５×１０−４ｓ−１で行った。 The rapidly solidified powder of the present invention was produced by the high pressure He gas atomization method as described above. Then, the produced powder with a particle size of 32 μm or less was filled into a copper can, and it was vacuum-sealed to produce a billet, and solidified by extrusion molding at an extrusion temperature of 623 to 723 K and an extrusion ratio of 10: 1. . By this extrusion, pressure and shear are applied to the powder to achieve densification and bonding between the powders. It should be noted that shearing occurs even in forming by a rolling method or a forging method. The structures of the rapidly solidified powder and the extruded material were examined by X-ray diffraction and TEM observation. The tensile test was performed at an initial strain rate of 5 × 10 −4 s −1 using an Instron tensile tester.

第６図に種々の温度で押出成形することにより作製したＭｇ９７Ｚｎ１Ｙ２材の引張り降伏強度（０．２％耐力）と伸びを示す。第６図の横軸は押出成形の温度を示している。第７図にそのＸ線のスペクトル回折の結果を示す。第８図には、様々の雰囲気温度でのＭｇ９７Ｚｎ１Ｙ２材（５７３Ｋで押出成形）の引張り降伏強度と伸びを示す。第９図に、周囲温度６２３ＫにおけるＭｇ９７Ｚｎ１Ｙ２材（５７３Ｋ，押出比１０で押出成形）のひずみ率に対する伸びと応力を示す。また、Ｍｇ９７Ｚｎ１Ｙ２材（５７３Ｋ，押出比１０で押出成形）の電子顕微鏡写真を第１０図に示す。 FIG. 6 shows the tensile yield strength (0.2% yield strength) and elongation of Mg 97 Zn 1 Y 2 material produced by extrusion molding at various temperatures. The horizontal axis in FIG. 6 represents the extrusion temperature. FIG. 7 shows the result of X-ray spectral diffraction. FIG. 8 shows the tensile yield strength and elongation of Mg 97 Zn 1 Y 2 material (extruded at 573 K) at various atmospheric temperatures. FIG. 9 shows the elongation and stress with respect to the strain rate of the Mg 97 Zn 1 Y 2 material (573K, extrusion molding at an extrusion ratio of 10) at an ambient temperature of 623K. FIG. 10 shows an electron micrograph of the Mg 97 Zn 1 Y 2 material (573K, extrusion molding at an extrusion ratio of 10).

この第６図から、Ｍｇ９７Ｚｎ１Ｙ２ＲＳ Ｐ／Ｍ材の降伏強度と伸びが押出温度に依存していることがわかる。押出温度が高まると引張り降伏強度が低下するのは、結晶粒径が大きくなるためである。しかし、Ｍｇ９７Ｚｎ１Ｙ２ＲＳ Ｐ／Ｍ材は、いずれの押出温度においても、４００ＭＰａ以上の高い降伏強度を示した。特に、押出温度５７３Ｋで作製したＰ／Ｍ材は、６２５ＭＰａの最大降伏強度、６０６ＭＰａの降伏強度、５％の伸びを示し、高強度と高延性を併せ持つＲＳ Ｐ／Ｍマグネシウム合金を開発することができた。 From FIG. 6, it can be seen that the yield strength and elongation of the Mg 97 Zn 1 Y 2 RS P / M material depend on the extrusion temperature. The reason why the tensile yield strength decreases as the extrusion temperature increases is because the crystal grain size increases. However, the Mg 97 Zn 1 Y 2 RS P / M material showed a high yield strength of 400 MPa or more at any extrusion temperature. In particular, a P / M material produced at an extrusion temperature of 573 K exhibits a maximum yield strength of 625 MPa, a yield strength of 606 MPa, and an elongation of 5%, and an RSP / M magnesium alloy having both high strength and high ductility can be developed. did it.

第７図にはＸ線回折の結果が示されている。これでわかるように、ガス・アトマイズ法により作製された粉末のスペクトラム（第７図（ａ）参照）には、ｈｃｐ−ＭｇとＹＺｎが検出されているが、押出成形された合金材（第７図（ｂ）〜（ｅ）参照）では、全て、ｈｃｐ−Ｍｇ、Ｍｇ２４Ｙ５およびＹＺｎが検出されている。 FIG. 7 shows the result of X-ray diffraction. As can be seen, hcp-Mg and YZn are detected in the spectrum of the powder produced by the gas atomization method (see FIG. 7A), but the extruded alloy material (No. 7 In all the figures (b) to (e), hcp-Mg, Mg 24 Y 5 and YZn are detected.

第８図において、市販のマグネシウム合金（ＷＥ５４−Ｔ６）と本発明のマグネシウム合金の引張り強さの周囲温度依存性を示している。作製したＭｇ９７Ｚｎ１Ｙ２ＲＳ Ｐ／Ｍ材は、市販のマグネシウム合金より良好な引張り強さを、大部分の周囲温度で示している。 FIG. 8 shows the ambient temperature dependence of the tensile strength of a commercially available magnesium alloy (WE54-T6) and the magnesium alloy of the present invention. The produced Mg 97 Zn 1 Y 2 RS P / M material exhibits better tensile strength than most commercially available magnesium alloys at most ambient temperatures.

第９図では、作製したマグネシウム合金であるＭｇ９７Ｚｎ１Ｙ２ＲＳ Ｐ／Ｍ材が、超塑性を有していることを示している。「超塑性」とは、雰囲気温度、加える歪速度が何であれ、その伸びが２００％を超えると同時に、歪速度に対する流動応力の勾配（ｍ値）が０．３以上であることを意味している。特に１×１０−２ｓ−１以上の歪速度で出現する超塑性は高速超塑性と言われている。第９図の下の図では、１×１０−２ｓ−１以上で３００％以上の伸びを示しており、最大で７５０％の伸びが５×１０−３ｓ−１で得られている。また、上の図ではｍ値が０．４であることを示しており、作製したマグネシウム合金が高速超塑性を有していることがわかる。 FIG. 9 shows that the produced Mg 97 Zn 1 Y 2 RS P / M material, which is a magnesium alloy, has superplasticity. “Superplasticity” means that the elongation (m value) with respect to the strain rate is 0.3 or more at the same time as the elongation exceeds 200% whatever the ambient temperature and the applied strain rate. Yes. In particular, superplasticity that appears at a strain rate of 1 × 10 −2 s −1 or higher is said to be high-speed superplasticity. In the lower figure of FIG. 9, the elongation of 300% or more is shown at 1 × 10 −2 s −1 or more, and the maximum elongation of 750% is obtained at 5 × 10 −3 s −1 . Moreover, in the upper figure, it has shown that m value is 0.4, and it turns out that the produced magnesium alloy has high-speed superplasticity.

第１０図に示す顕微鏡写真でわかるように、この作製したマグネシウム合金の組成物は、約２００ｎｍの微粒子で構成されている。この微粒子は、ガスアトマイズで作製した粉体の結晶組織ではなく、成形物としての結晶組織であり、六方最密構造（ｈｃｐ）のマグネシウムと、他の化合物の混相である。第１０図の電子顕微鏡の写真における他の化合物は、第７図に示すＸ線回折のスペクトル回折から、Ｍｇ２４Ｙ５およびＹＺｎである。 As can be seen from the micrograph shown in FIG. 10, the produced magnesium alloy composition is composed of fine particles of about 200 nm. The fine particles are not a crystal structure of a powder produced by gas atomization but a crystal structure as a molded product, and are a mixed phase of magnesium having a hexagonal close-packed structure (hcp) and other compounds. The other compounds in the electron microscope photograph of FIG. 10 are Mg 24 Y 5 and YZn from the spectral diffraction of X-ray diffraction shown in FIG.

第１１図に、本発明で作製したマグネシウム合金と、既存のマグネシウム合金との伸びと引張り降伏強度の比較を示す。第１１図において、既存のＩ／Ｍ（ingot metallurgy）法で作製したマグネシウム合金（ＡＺ９１，ＺＫ６０等），急速凝固粉末冶金（ＲＳ Ｐ／Ｍ）で作製したマグネシウム合金（ＡＺ９１，ＺＫ６１等），本発明以外の組成の急速凝固粉末冶金（ＲＳ Ｐ／Ｍ）によるナノ結晶マグネシウム合金，本発明の組成を有する微細結晶組織を有するＲＳ Ｐ／Ｍ法のマグネシウム合金を比較している。この図でわかるように、本発明のマグネシウム合金は、他の製法や組成のマグネシウム合金と比較して、引張り降伏強度や伸びに対して大変良好な性能を有している。   FIG. 11 shows a comparison of elongation and tensile yield strength between the magnesium alloy produced in the present invention and the existing magnesium alloy. In FIG. 11, a magnesium alloy (AZ91, ZK60, etc.) produced by an existing I / M (ingot metallurgy) method, a magnesium alloy (AZ91, ZK61, etc.) produced by rapid solidification powder metallurgy (RS P / M), this Comparison is made between a nanocrystalline magnesium alloy by rapid solidification powder metallurgy (RS P / M) having a composition other than that of the invention and a magnesium alloy by RSP / M method having a fine crystal structure having the composition of the present invention. As can be seen from this figure, the magnesium alloy of the present invention has very good performance with respect to tensile yield strength and elongation as compared with magnesium alloys of other production methods and compositions.

本発明のマグネシウム合金は、高強度と高延性を有している。本発明のマグネシウム合金を用いることにより、マグネシウム合金の軽量性を生かすことで、高強度と高延性が必要な部材における軽量化を図ることができる。   The magnesium alloy of the present invention has high strength and high ductility. By using the magnesium alloy of the present invention, it is possible to reduce the weight of a member that requires high strength and high ductility by taking advantage of the light weight of the magnesium alloy.

Ｍｇ−Ｚｎ−Ｙ 三元系急速凝固薄帯の急速凝固状態における硬さと延性を示す図である。It is a figure which shows the hardness and ductility in the rapid solidification state of a Mg-Zn-Y ternary system rapid solidification ribbon. Ｍｇ−Ｚｎ−Ｙ 三元系急速凝固薄帯の５７３Ｋでの熱処理状態における硬さと延性を示す図である。It is a figure which shows the hardness and ductility in the heat processing state by 573K of a Mg-Zn-Y ternary system rapid solidification ribbon. Ｍｇ−Ｚｎ−Ｙ 三元系急速凝固薄帯の６７３Ｋでの熱処理状態における硬さと延性を示す図である。It is a figure which shows the hardness and ductility in the heat processing state of 673K of a Mg-Zn-Y ternary system rapid solidification ribbon. ガス・アトマイジング法による急速凝固粉末作製と押出ビレットの作製を行うシステムを示す図である。It is a figure which shows the system which performs quick-solidification powder preparation by gas atomizing method, and preparation of an extrusion billet. ビレットを加熱押圧して、固化成形する過程を示す図である。It is a figure which shows the process of heat-pressing a billet and solidifying and forming. 種々の温度で押出成形した合金に対する引張り降伏強度と伸びを示すグラフである。2 is a graph showing tensile yield strength and elongation for alloys extruded at various temperatures. Ｘ線回折によるスペクトルを示す図である。It is a figure which shows the spectrum by X-ray diffraction. 押出成形した合金に対する様々の雰囲気温度での引張り降伏強度と伸びを示すグラフである。It is a graph which shows the tensile yield strength and elongation in various atmospheric temperature with respect to the extruded alloy. 押出成形した合金が超塑性を有していることを示すグラフである。It is a graph which shows that the extruded alloy has superplasticity. 押出成形した合金の電子顕微鏡による写真を示す図である。It is a figure which shows the photograph by the electron microscope of the extruded alloy. 本発明のマグネシウム合金と他のマグネシウム合金の引張り降伏強度と伸びの比較を示す図である。It is a figure which shows the comparison of the tensile yield strength and elongation of the magnesium alloy of this invention, and another magnesium alloy.

符号の説明Explanation of symbols

１００：高圧ガス・アトマイザ， １１０：溶解室， １１２：ストッパ，
１１４：誘導コイル， １１６：るつぼ， １３０：アトマイズ室，
１３１：ヒータ， １３２：ノズル， １４０：サイクロン分級機，
１５０：フィルタ， １６２，１６６：酸素分析器， １６４：真空ゲージ，
２００：真空グローブ・ボックス， ２１０：アルゴンガス・リファイナ，
２２０：ホッパ， ２３０：ふるい， ２４０：真空ホットプレス機，
２４２：真空室， ２４４：パンチ， ２４６：型， ２４８：ヒータ，
２５２：キャップ， ２５４：缶， ２５６：溶接機， ２５８：回転盤，
２６０：ビレット， ２６２：バルブ， ２７０：酸化ボックス，
２８０：エントランス・ボックス， ２９２：真空ゲージ， ２９４：湿度計，
２９６：酸素分析器， ３４０：スポット溶接機， ４００：押出プレス機，
４１０：ヒータ， ４２０：コンテナ， ４３０：型（ダイ），
４５０：メイン・ステム， ４６０：ダイ・バッカー，
４７０：バック・ステム 100: High pressure gas atomizer, 110: Dissolution chamber, 112: Stopper,
114: induction coil, 116: crucible, 130: atomizing room,
131: heater, 132: nozzle, 140: cyclone classifier,
150: Filter, 162, 166: Oxygen analyzer, 164: Vacuum gauge,
200: Vacuum glove box, 210: Argon gas refiner,
220: Hopper, 230: Sieve, 240: Vacuum hot press machine,
242: Vacuum chamber, 244: Punch, 246: Mold, 248: Heater,
252: Cap, 254: Can, 256: Welder, 258: Turntable,
260: billet, 262: valve, 270: oxidation box,
280: Entrance box, 292: Vacuum gauge, 294: Hygrometer,
296: Oxygen analyzer, 340: Spot welder, 400: Extrusion press,
410: heater, 420: container, 430: mold (die),
450: Main stem, 460: Die backer,
470: Back stem

Claims (2)

一般式で、Ｍｇ （１００−ｘ−ｙ） Ｙ ｘ Ｚｎ ｙ （１＜ｘ＜５，０．３＜ｙ＜６：ｘ、ｙはいずれも原子％）の組成を有し、１マイクロメートル以下の微細結晶組織を有するマグネシウム合金であって、該マグネシウム合金は４００ＭＰａ以上の降伏強度（０．２％耐力）を示し且つ５％以上の伸びを示すものであり、
当該高強度マグネシウム合金が、急速凝固粉末冶金成形物で、Ｍｇ２４Ｙ５およびＹＺｎを有し、他はｈｃｐ−Ｍｇであり、それぞれが１マイクロメータ以下の微細結晶組織を有すると共に、高速超塑性を有していることを特徴とする高強度マグネシウム合金。It is a general formula and has a composition of Mg (100-xy) Y x Zn y (1 <x <5, 0.3 <y <6: where x and y are atomic%), and 1 micrometer or less A magnesium alloy having a fine crystal structure of, wherein the magnesium alloy exhibits a yield strength (0.2% yield strength) of 400 MPa or more and an elongation of 5% or more,
The high-strength magnesium alloy is a rapidly solidified powder metallurgical molded product having Mg 24 Y 5 and YZn, the other being hcp-Mg, each having a fine crystal structure of 1 micrometer or less, and high-speed superplasticity A high-strength magnesium alloy characterized by having 当該高強度マグネシウム合金において、液体から急速に凝固された粉末、薄帯又は細線を、せん断が付加されるようにして固化させることで、作製されていることを特徴とする請求項１に記載の高強度マグネシウム合金。  The high-strength magnesium alloy is produced by solidifying powder, ribbon or fine wire rapidly solidified from a liquid by applying shear. High strength magnesium alloy.
JP2002566397A 2001-01-26 2001-01-26 High strength magnesium alloy Expired - Fee Related JP5161414B2 (en)

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WO2005052204A1 (en) 2003-11-26 2005-06-09 Yoshihito Kawamura High strength and high toughness magnesium alloy and method for production thereof
JP4139841B2 (en) * 2004-09-30 2008-08-27 能人 河村 Casting and production method of magnesium alloy
JP2009144215A (en) * 2007-12-17 2009-07-02 Japan Steel Works Ltd:The Heat resistant magnesium alloy material and its manufacturing method
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JPH0347941A (en) * 1989-07-13 1991-02-28 Yoshida Kogyo Kk <Ykk> High strength magnesium base alloy
JPH05306424A (en) * 1992-04-30 1993-11-19 Yoshida Kogyo Kk <Ykk> High strength magnesium-base alloy and its laminated and solidified material
JPH0641701A (en) * 1991-09-06 1994-02-15 Takeshi Masumoto High strength amorphous magnesium alloy and its manufacture
JPH073375A (en) * 1993-03-15 1995-01-06 Takeshi Masumoto High strength magnesium alloy and production thereof

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JPH0347941A (en) * 1989-07-13 1991-02-28 Yoshida Kogyo Kk <Ykk> High strength magnesium base alloy
JPH0641701A (en) * 1991-09-06 1994-02-15 Takeshi Masumoto High strength amorphous magnesium alloy and its manufacture
JPH05306424A (en) * 1992-04-30 1993-11-19 Yoshida Kogyo Kk <Ykk> High strength magnesium-base alloy and its laminated and solidified material
JPH073375A (en) * 1993-03-15 1995-01-06 Takeshi Masumoto High strength magnesium alloy and production thereof

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