JP3238516B2 - High strength magnesium alloy and method for producing the same - Google Patents
High strength magnesium alloy and method for producing the sameInfo
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- JP3238516B2 JP3238516B2 JP05402693A JP5402693A JP3238516B2 JP 3238516 B2 JP3238516 B2 JP 3238516B2 JP 05402693 A JP05402693 A JP 05402693A JP 5402693 A JP5402693 A JP 5402693A JP 3238516 B2 JP3238516 B2 JP 3238516B2
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- alloy
- magnesium alloy
- same
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Description
【０００１】[0001]
【産業上の利用分野】本発明は高強度マグネシウム合金
及びその製造法に関するものであり、さらに詳しく述べ
るならば微結晶マグネシウム合金の強度及び靭性を高め
る技術に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength magnesium alloy and a method for producing the same, and more particularly to a technique for increasing the strength and toughness of a microcrystalline magnesium alloy.
【０００２】[0002]
【従来の技術】本出願人らは特願平３−７４６８１号
（平成３年３月１４日出願）及び欧州公開特許公報０５
０３８８０号において、Ｍｇa Ｍb Ａｌc Ｘd Ｚe （た
だし、ＭはＬａ，Ｃｅ，及び／又はＭｍ（ミッシュメタ
ル）、ＸはＮｉ及び／Ｃｕ，ＺはＭｎ，Ｚｎ，Ｚｒ及び
／又はＴｉ，ａ＝７０〜９０ａｔ％，ｂ＝２〜１５ａｔ
％，ｄ＝２〜１５ａｔ％，ｅ＝０．１〜８ａｔ％、ａ＋
ｂ＋ｃ＋ｄ＋ｅ＝１００ａｔ％）からなる組成の高強度
耐熱性非晶質マグネシウム合金を提案した。この合金の
引張強度は実施例では約８０〜１００ｋｇ／ｍｍ2 であ
り、従来のマグネシウム合金よりも遥かに高い強度をも
っている。2. Description of the Related Art Applicants have filed Japanese Patent Application No. 3-74881 (filed on Mar. 14, 1991) and European Patent Publication No. 05.
No. 03880, Mga Mb Alc Xd Ze (where M is La, Ce, and / or Mm (mish metal), X is Ni and / or Cu, Z is Mn, Zn, Zr and / or Ti, a = 70 to 90 at%, b = 2 to 15 at
%, D = 2 to 15 at%, e = 0.1 to 8 at%, a +
A high-strength heat-resistant amorphous magnesium alloy having a composition of (b + c + d + e = 100 at%) was proposed. The tensile strength of this alloy is about 80 to 100 kg / mm 2 in the embodiment, and is much higher than that of the conventional magnesium alloy.
【０００３】[0003]
【発明が解決しようとする課題】しかしながら、上記の
マグネシウム合金は組織が非晶質であるために、形態が
箔などに限定されており、各種部品として実用する面で
は問題がある。したがって、本発明は強度が高く、靭性
にすぐれかつ各種形状に加工できるマグネシウム合金及
びその加工方法を提供することを目的とする。However, since the above magnesium alloy has an amorphous structure, its form is limited to foil or the like, and there is a problem in practical use as various parts. Accordingly, an object of the present invention is to provide a magnesium alloy having high strength, excellent toughness, and capable of being processed into various shapes, and a method for processing the same.
【０００４】上記した目的を達成する本発明の第一は、
一般式でＭｇaＺｎbＸc（ただし、ＸはＹ，Ｃｅ，Ｌ
ａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍｍ（ミッシュメタル）からな
る群から選ばれる１種または２種以上の元素、８７原子
％≦ａ≦９８原子％、ｂ及びｃは図１のＡ，Ｂ点を結ぶ
線上を除くＢ−Ｃ−Ｄ−Ｅ−Ｆ−Ａの線上及びＡ−Ｂ−
Ｃ−Ｄ−Ｅ−Ｆの線で囲まれた範囲であり、かつ０≦Ｙ
（イットリウム）≦４．５原子％、０≦Ｃｅ，Ｌａ，Ｎ
ｄ，Ｐｒ，Ｓｍ，Ｍｍ≦３原子％で表される組成を有
し、サブミクロンの微結晶からなる母相にＭｇ−Ｚｎ系
及びＭｇ−Ｘ系金属間化合物が分散したことを特徴とす
る靭性に優れた高強度マグネシウム合金粉末固化材であ
り、また本発明の第二は、一般式でＭｇaＺｎbＸc（た
だし、ＸはＹ，Ｃｅ，Ｌａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍｍ
（ミッシュメタル）からなる群から選ばれる１種または
２種以上の元素、８７原子％≦ａ≦９８原子％、ｂ及び
ｃは図１のＡ，Ｂ点を結ぶ線上を除くＢ−Ｃ−Ｄ−Ｅ−
Ｆ−Ａの線上及びＡ−Ｂ−Ｃ−Ｄ−Ｅ−Ｆの線で囲まれ
た範囲であり、かつ０≦Ｙ（イットリウム）≦４．５原
子％、０≦Ｃｅ，Ｌａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍｍ≦３原
子％で表される組成を有する合金溶湯を急冷凝固し、そ
の後該急冷凝固合金に３００〜４５０℃の温度で塑性加
工を施し、サブミクロンの微結晶からなる母相にＭｇ−
Ｚｎ系及びＭｇ−Ｘ系金属間化合物を分散させたことを
特徴とする高強度マグネシウム合金粉末固化材の製造方
法である。[0004] The first of the present invention to achieve the above object is as follows.
In the general formula, Mg a Zn b X c (where X is Y, Ce, L
One or more elements selected from the group consisting of a, Nd, Pr, Sm, and Mm (Misch metal), 87 at% ≦ a ≦ 98 at%, b and c are points A and B in FIG. Except on the connecting line, on the BCDEFA line and on the AB-
A range surrounded by a line of CDEF and 0 ≦ Y
(Yttrium) ≦ 4.5 atomic%, 0 ≦ Ce, La, N
It has a composition represented by d, Pr, Sm, and Mm ≦ 3 atomic%, and is characterized in that a Mg—Zn-based and Mg—X-based intermetallic compound is dispersed in a parent phase composed of submicron microcrystals. A high-strength magnesium alloy powder solidified material having excellent toughness. The second aspect of the present invention is a general formula of Mg a Zn b X c (where X is Y, Ce, La, Nd, Pr, Sm, Mm).
(Misch metal) One or more elements selected from the group consisting of 87 atomic% ≦ a ≦ 98 atomic%, b and c are BCD except for the line connecting points A and B in FIG. -E-
It is the range enclosed by the line of FA and the line of ABCDCEF, and 0 ≦ Y (yttrium) ≦ 4.5 atomic%, 0 ≦ Ce, La, Nd, Pr , Sm, Mm ≦ 3 atomic% is rapidly solidified, and then the rapidly solidified alloy is subjected to plastic working at a temperature of 300 to 450 ° C. to form a parent phase composed of submicron microcrystals. Mg-
A method for producing a high-strength magnesium alloy powder solidified material, in which Zn-based and Mg-X-based intermetallic compounds are dispersed.
【０００５】本発明の第一にかかるマグネシウム合金に
おいて、Ｍｇは母相となる微結晶をつくる元素である。
Ｍｇの量が８７原子％未満であると、軽量であるという
マグネシウム合金の特長が失われ、母相の結晶が粗大化
し、また靭性の低下などが招かれる。一方Ｍｇの量が９
８原子％を越えると母相中に析出する金属間化合物の量
が不足して強度の低下を招く。[0005] In the magnesium alloy according to the first aspect of the present invention, Mg is an element for forming microcrystals to be a parent phase.
If the amount of Mg is less than 87 atomic%, the feature of the magnesium alloy that it is lightweight is lost, the crystal of the parent phase becomes coarse, and the toughness is reduced. On the other hand, when the amount of Mg is 9
If it exceeds 8 atomic%, the amount of the intermetallic compound precipitated in the mother phase becomes insufficient, resulting in a decrease in strength.
【０００６】ＺｎはＭｇとの金属間化合物を形成し、こ
の金属間化合物が微細なＭｇ母相中に微細に分散して靭
性を損なうことなく強度を高める。また、ＸはＹ，Ｃ
ｅ，Ｌａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍｍ（ミッシュメタル）
からなる群から選ばれる１種または２種以上の元素はＭ
ｇの母相を微細化するとともに、Ｍｇとの金属間化合物
を形成し、この金属間化合物が微細なＭｇ母相中に微細
に分散して靭性を損なうことなく強度を高める。これら
の元素の量は図１に示された範囲とすることが必要であ
る。すなわち、ＡＦＥ線より上側、ＥＤ線より右側及び
ＢＣＤ線より下側では分散する金属間化合物が粗大化し
て材料が脆くなるので、これらの線上あるいは線で囲ま
れた範囲内とする必要がある。[0006] Zn forms an intermetallic compound with Mg, and this intermetallic compound is finely dispersed in a fine Mg matrix to increase the strength without impairing the toughness. X is Y, C
e, La, Nd, Pr, Sm, Mm (Misch metal)
One or more elements selected from the group consisting of
In addition to miniaturizing the matrix of g, an intermetallic compound with Mg is formed, and the intermetallic compound is finely dispersed in the fine Mg matrix to increase the strength without impairing the toughness. It is necessary that the amounts of these elements be in the range shown in FIG. That is, since the dispersed intermetallic compound is coarsened above the AFE line, to the right of the ED line, and below the BCD line to make the material brittle, it is necessary to set the range above or within the range surrounded by these lines.
【０００７】さらに、Ｙ（イットリウム）を添加する場
合は本発明の合金で析出するＹ（イットリウム）とＭｇ
の金属間化合物は、Ｃｅ，Ｌａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍ
ｍとＭｇの金属間化合物に比べ、Ｘ元素の原子％が高
い。このためＹ（イットリウム）を添加する場合は４．
５原子％まで脆化することがない。他方Ｃｅ，Ｌａ，Ｎ
ｄ，Ｐｒ，Ｓｍ，Ｍｍの場合は上限を３原子％とする必
要がある。Furthermore, when Y (yttrium) is added, Y (yttrium) and Mg which precipitate in the alloy of the present invention are added.
Is an intermetallic compound of Ce, La, Nd, Pr, Sm, M
Atomic% of the X element is higher than that of the intermetallic compound of m and Mg. Therefore, when Y (yttrium) is added, 4.
No embrittlement up to 5 atomic%. On the other hand, Ce, La, N
In the case of d, Pr, Sm, and Mm, the upper limit needs to be 3 atomic%.
【０００８】続いて本発明のマグネシウム合金の組織を
説明する。この合金はＭｇ母相（Ｍｇの結晶構造をもつ
相）とＭｇ−Ｚｎ系及びＭｇ−Ｘ系金属間化合物の分散
相とから構成されており、分散相は母相中に微細に分散
している。Ｍｇ母相はサブミクロンの微結晶であり、こ
のなかにさらに微細な金属間化合物相が分散している。Next, the structure of the magnesium alloy of the present invention will be described. This alloy is composed of a Mg parent phase (a phase having a crystal structure of Mg) and a dispersed phase of an Mg-Zn-based or Mg-X-based intermetallic compound, and the dispersed phase is finely dispersed in the matrix. I have. The Mg parent phase is a submicron microcrystal, in which a finer intermetallic compound phase is dispersed.
【０００９】さらに、本発明の第二にかかるマグネシウ
ム合金の加工方法について説明する。この方法では上記
組成を有するＭｇ合金溶湯を急冷凝固する。得られた合
金は、Ｘ線回折法により特有のハローパターンを示す非
晶質組織、結晶特有の回折ピークを示す微細結晶質ある
いはハローパターンと回折ピークが混在する非結晶と結
晶質の混合組織のいずれかである。Further, a description will be given of a second method for processing a magnesium alloy according to the present invention. In this method, a molten Mg alloy having the above composition is rapidly solidified. The resulting alloys, amorphous structure showing a specific halo pattern by X-ray diffractometry, the diffraction peak fine crystalline or halo pattern showing a crystal characteristic diffraction peaks are mixed amorphous mixed structure of crystalline Is one of
【００１０】この合金を４５０℃以下の温度で加工を行
う。この加工により上記した組織の内非晶質組織は金属
間化合物が分散した微結晶組織に変わり、所望の組織が
得られる。また微細結晶質では若干の粒成長は起こる
が、再結晶による粗大化は起こらず所望の組織が得られ
る。加工は引抜、圧延、鍛造、押出などの塑性加工法に
よることができ、得られるバルク材は円柱、板、異形な
どの種々の形状である。以下、さらに本発明の実施態様
につき説明する。This alloy is processed at a temperature of 450 ° C. or less. By this processing, the amorphous structure among the above-mentioned structures is changed to a microcrystalline structure in which an intermetallic compound is dispersed, and a desired structure is obtained. In the case of the fine crystalline material, although a slight grain growth occurs, a desired structure can be obtained without coarsening due to recrystallization. The processing can be performed by a plastic working method such as drawing, rolling, forging, or extrusion, and the obtained bulk material has various shapes such as a cylinder, a plate, and an irregular shape. Hereinafter, embodiments of the present invention will be further described.
【００１１】Ｍｇ合金溶湯の急冷凝固は、一般的に急冷
凝固法として知られているガン法、ピストン・アンビル
法、あるいは連続的な薄帯を作製する遠心法、単ロール
法、双ロール法、あるいは粉末を作製するスプレー法、
細線を作製する回転液中紡糸法などによることができ
る。これらの方法の中でも、１０2 〜１０6 Ｋ／ｓの冷
却速度が容易に得られる単ロール法、双ロール法または
高圧ガス噴射法が特に適している。The quenching and solidification of the molten Mg alloy can be performed by a gun method, a piston-anvil method, a centrifugal method for producing a continuous ribbon, a single-roll method, a twin-roll method, which is generally known as a rapid solidification method. Or a spray method to make powder,
A spinning method in a rotating liquid for producing a fine wire can be used. Among these methods, a single roll method, a twin roll method, or a high pressure gas injection method, which can easily obtain a cooling rate of 10 2 to 10 6 K / s, is particularly suitable.
【００１２】単ロール法、双ロール法によりＭｇ合金薄
帯を作製するためには３００〜１００００ｒｐｍで回転
する直径３０〜３００ｍｍの銅製又は鋼製ノズルに合金
溶湯を噴射する。これにより幅が１〜３００ｍｍ，厚さ
が５〜５００μｍの薄帯が得られる。In order to produce an Mg alloy ribbon by a single roll method or a twin roll method, a molten alloy is injected into a copper or steel nozzle having a diameter of 30 to 300 mm rotating at 300 to 10000 rpm. Thereby, a ribbon having a width of 1 to 300 mm and a thickness of 5 to 500 μm is obtained.
【００１３】また、高圧ガス噴射法によりＭｇ合金薄帯
を得るには、溶湯ノズルから流下させた合金溶湯に４〜
１５ＭＰａの高圧窒素ガス、アルゴンガス、ヘリウムガ
スなどを吹きつけ、溶湯を微細に分断し同時に急冷凝固
させる。In order to obtain a Mg alloy ribbon by the high-pressure gas injection method, it is necessary to apply 4 to 4 times to the molten alloy flowing down from the molten metal nozzle.
A high-pressure nitrogen gas, argon gas, helium gas, or the like of 15 MPa is blown, and the molten metal is finely divided and simultaneously solidified by rapid cooling.
【００１４】上述の急冷凝固法で得られたＭｇ合金はそ
のまま塑性加工することも可能であるが、薄帯あるいは
細線の場合は粉砕した後銅、アルミニウム又はそれらの
合金製の缶に充填して塑性加工することが好ましい。こ
の際急冷凝固してから金属缶に充填するまでの急冷凝固
材の酸化を抑制するため酸素量１ｐｐｍ以下の高清浄度
の雰囲気中で急冷凝固粉末を取り扱うことが好ましい。
また金属缶に充填された粉末には塑性加工するに先立っ
て真空脱ガスを施すことが好ましい。加工温度は２００
℃以上であることが好ましい。２００℃未満の加工温度
では粉末の固化とバルク化が困難になる。The Mg alloy obtained by the above-mentioned rapid solidification method can be subjected to plastic working as it is. However, in the case of a thin ribbon or a thin wire, it is pulverized and then filled in a can made of copper, aluminum or an alloy thereof. Plastic working is preferred. At this time, it is preferable to handle the rapidly solidified powder in a highly clean atmosphere having an oxygen content of 1 ppm or less in order to suppress oxidation of the rapidly solidified material from rapid solidification to filling in a metal can.
Further, it is preferable that the powder filled in the metal can be subjected to vacuum degassing prior to plastic working. Processing temperature is 200
It is preferable that the temperature is not lower than ° C. If the processing temperature is less than 200 ° C., solidification and bulking of the powder become difficult.
【００１５】[0015]
【作用】母相組織を微結晶質とし、特定の金属間化合物
を母相に分散させたＭｇa Ｚｎb Ｘc 合金は強度と靭性
を兼備している。上記した組成では加工により組織の粗
大化が起こり難いので、高強度と高靭性を保ちつつ部品
に近い形状のバルク材を得ることができる。以下、実施
例により本発明をさらに詳しく説明する。The MgA Znb Xc alloy in which the matrix structure is microcrystalline and a specific intermetallic compound is dispersed in the matrix has both strength and toughness. With the above-described composition, the coarsening of the structure is unlikely to occur by processing, so that a bulk material having a shape close to a part can be obtained while maintaining high strength and high toughness. Hereinafter, the present invention will be described in more detail with reference to examples.
【００１６】[0016]
【実施例】実施例１ 表１に化学組成を示す本発明実施例のＮｏ.１〜３及び
参考例Ｎｏ.４のＭｇ合金をＡｒ雰囲気中で高周波溶解
して、母合金を溶製した。この母合金をＡｒ雰囲気中で
高周波炉で７７５℃で溶解した後、９.８ＭＰａのＡｒ
ガスで高圧ガス噴射法により微細な結晶質金属からなる
粉末とした。EXAMPLES Example 1 Nos. 1 to 3 of Examples of the present invention whose chemical compositions are shown in Table 1 and
The Mg alloy of Reference Example No. 4 was subjected to high frequency melting in an Ar atmosphere to produce a mother alloy. This master alloy was melted at 775 ° C. in a high-frequency furnace in an Ar atmosphere, and then 9.8 MPa Ar was melted.
The powder was made of fine crystalline metal by high-pressure gas injection with a gas.
【００１７】アトマイズされた粉末のうち粒径の小さい
ものはより急冷されており、析出粒子が小さく、また添
加元素の固溶量も大きい。そこで、得られた粉末を分級
し、２５μｍ以下の粉末を温度３００〜４００℃、加圧
力４００〜１０００ＭＰａ押出比１０：１で押出を行
い、直径６ｍｍ，長さ２７０ｍｍ，密度１００％の円柱
材を得た。なお粉末作製から押出までの段階で粉末が暴
露された雰囲気は酸素分圧、水蒸気分圧がともに１ｐｐ
ｍ以下の高清浄度雰囲気であった。Among the atomized powders, those having a small particle diameter are more rapidly cooled, and the precipitated particles are small and the solid solution amount of the added element is large. Then, the obtained powder is classified, and a powder having a diameter of 25 μm or less is extruded at a temperature of 300 to 400 ° C. and a pressure of 400 to 1000 MPa at an extrusion ratio of 10: 1 to obtain a cylindrical material having a diameter of 6 mm, a length of 270 mm and a density of 100%. Obtained. The atmosphere to which the powder was exposed during the stages from powder preparation to extrusion had an oxygen partial pressure and a water vapor partial pressure of 1 pp both.
m or less.
【００１８】円柱材をＸ線回折したところ、表１に示す
金属間化合物がＭｇ相と共に観察された。またＭｇ母相
の平均粒径は約０．３μｍ，金属間化合物の平均粒径は
約５０ｎｍであり、微細な母相中に微細な金属間化合物
が分散していることがＴＥＭで観察された。When the columnar material was subjected to X-ray diffraction, intermetallic compounds shown in Table 1 were observed together with the Mg phase. The average particle size of the Mg matrix was about 0.3 μm and the average grain size of the intermetallic compound was about 50 nm, and it was observed by TEM that the fine intermetallic compound was dispersed in the fine matrix. .
【００１９】次に円柱材をインストロン型引張試験機に
よる引張試験に供した。この結果も表１に示す。本発明
のＭｇ合金の引張強度は６００〜７００ＭＰａであって
極めて高い値であることがわかる。Next, the columnar material was subjected to a tensile test using an Instron type tensile tester. The results are also shown in Table 1. It turns out that the tensile strength of the Mg alloy of the present invention is 600 to 700 MPa, which is an extremely high value.
【００２０】[0020]
【表１】 組成 押出 金属間化合物相 引張 硬さ 温度℃ 耐力MPa Hv 1 Mg95Zn2Mm3 300 Mg17La2, Mg12Nd, CeMg12, Mg2Zn3 726 152 2 Mg92Zn5Mm3 400 同上 620 150 3 Mg92Zn10Mm2 375 同上 610 130 4 Mg95.5Y2.5Mm2 325 Mg17La2, Mg12Nd, CeMg12, Mg24Y5 600 160 [Table 1] Composition Extrusion Intermetallic phase Tensile hardness Temperature ℃ MP a Hv 1 Mg95Zn2Mm3 300 Mg17La2, Mg12Nd, CeMg12, Mg2Zn3 726 152 2 Mg92Zn5Mm3 400 Same as above 620 150 3 Mg92Zn10Mm2 375 Same as above 610 130 4 Mg95.5Y2.5Mm2 325 Mg17La2, Mg12Nd, CeMg12 160
【００２１】実施例２ 表２に化学組成を示すＭｇ合金を実施例１と同様の方法
により溶解し、同様の条件で急冷凝固して微細結晶質の
合金を作製した。この粉末を実施例１と同様の条件で熱
間押出成形して円柱材を作製した。この円柱材のビッカ
ース硬度を測定した結果を表２に示す。Example 2 An Mg alloy having a chemical composition shown in Table 2 was melted in the same manner as in Example 1 and rapidly solidified under the same conditions to produce a fine crystalline alloy. This powder was subjected to hot extrusion under the same conditions as in Example 1 to produce a columnar material. Table 2 shows the results of measuring the Vickers hardness of the cylindrical material.
【００２２】また同じ組成をもつ合金を単ロール法でリ
ボン材に作製し、これを熱間押出温度に相当する温度に
加熱して押出材と同じ組織にした後、密着曲げにより靭
性を評価した。密着曲げ試験ではリボン材が破壊するこ
となく密着曲げ可能かどうかを調べた。密着曲げ可能な
材料は靭性をもつｄｕｃｔｉｌｅ材料であり、不可能な
材料は脆い材料である。この結果も表２に示す。An alloy having the same composition was prepared into a ribbon material by a single roll method, heated to a temperature corresponding to the hot extrusion temperature to obtain the same structure as the extruded material, and the toughness was evaluated by tight bending. . In the contact bending test, it was examined whether the ribbon material could be contact bent without breaking. A material that can be closely bent is a ductile material having toughness, and an impossible material is a brittle material. The results are also shown in Table 2.
【００２３】[0023]
【表２】 No 組成 押出 金属間化合物相 密着 硬さ 温度℃ 曲げ Hv 5 Mg89Zn10Mm1 300 Mg17La2, Mg12Nd, CeMg12, Mg2Zn3 可能 123 6 Mg87Zn10Mm3 400 同上 可能 180 7 Mg91.5Zn7.5Mm1 300 同上 可能 121 8 Mg90.5Zn7.5Mm2 300 同上 可能 130 9 Mg93Zn5Mm2 400 同上 可能 125 10 Mg94Zn5Mm1 300 同上 可能 115 11 Mg94.5Zn2.5Mm3 300 同上 可能 154 12 Mg95.5Zn2.5Mm2 300 同上 可能 151 [Table 2] No Composition Extrusion Intermetallic Compound Phase Adhesion Hardness Temperature ℃ Bending Hv 5 Mg89Zn10Mm1 300 Mg17La2, Mg12Nd, CeMg12, Mg2Zn3 possible 123 6 Mg87Zn10Mm3 400 Same as above possible 180 7 Mg91.5Zn7.5Mm1 300 Same as above possible 121 8 Mg90.5Zn7.5Mm2 300 Same as above possible 130 9 Mg93Zn5Mm2 10300 above 94 above Same as above Possible 115 11 Mg94.5Zn2.5Mm3 300 Same as above Possible 154 12 Mg95.5Zn2.5Mm2 300 Same as above Possible 151
【００２４】比較例１ 実施例２と同様の試験を表３に組成を示すＭｇ合金につ
いて行った。結果を表３に示す。Comparative Example 1 The same test as in Example 2 was performed on an Mg alloy having the composition shown in Table 3. Table 3 shows the results.
【００２５】[0025]
【表３】 No 組成 押出 金属間化合物相 密着 硬さ 温度℃ 曲げ Hv 13 Mg86Zn10Mm4 300 Mg17La2, Mg12Nd, CeMg12, Mg2Zn3 不可 301 14 Mg86Zn10Mm4 400 同上 不可 230 15 Mg88.5Zn7.5Mm4 300 同上 不可 283 16 Mg88.5Zn7.5Mm4 400 同上 不可 227 17 Mg90Zn5Mm5 300 同上 不可 271 18 Mg90Zn5Mm5 400 同上 不可 231 19 Mg90Zn10 300 同上 不可 96 20 Mg95Zn5 300 （Ｍｇのみ） 可能 70 21 Mg97Zn2Mm1 300 Mg17La2, Mg12Nd, CeMg12, Mg2Zn3 可能 68 比較例の材料はすべて脆いかあるいは硬度が低い材料で
あることがわかった。[Table 3] No Composition Extrusion Intermetallic Compound Phase Adhesion Hardness Temperature ℃ Bending Hv 13 Mg86Zn10Mm4 300 Mg17La2, Mg12Nd, CeMg12, Mg2Zn3 Not possible 301 14 Mg86Zn10Mm4 400 Same as above Not possible 230 230 Not possible 231 19 Mg90Zn10 300 Same as above Not possible 96 20 Mg95Zn5 300 (Mg only) Possible 70 21 Mg97Zn2Mm1 300 Mg17La2, Mg12Nd, CeMg12, Mg2Zn3 Possible 68 All of the comparative examples were found to be brittle or low in hardness.
【００２６】[0026]
【発明の効果】以上説明したように、本発明のＭｇ合金
は高い強度と靭性を兼備し、かつ円柱材などのバルク材
料として提供されるから高い比強度が要求される部品に
好適に適用できるものである。As described above, the Mg alloy of the present invention has both high strength and toughness and is provided as a bulk material such as a columnar material, so that it can be suitably applied to parts requiring high specific strength. Things.
【図１】 本発明のZnとX成分の範囲に、本願実施例のN
o.５，６，１０の組成点を付記したグラフである。FIG. 1 shows the range of Zn and X components of the present invention,
It is the graph which added the composition point of o.5,6,10.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｃ２２Ｆ 1/00 ６３０ Ｃ２２Ｆ 1/00 ６３０Ｋ ６８１ ６８１ ６８３ ６８３ ６９４ ６９４Ｂ 1/06 1/06 (72)発明者 増本 健 宮城県仙台市青葉区上杉３丁目８番22号 (72)発明者 井上 明久 宮城県仙台市青葉区川内無番地 川内住 宅11−806 (72)発明者 堀切 秀彦 東京都中央区八重洲１丁目９番９号 帝 国ピストンリング株式会社内 (72)発明者 加藤 晃 愛知県豊田市トヨタ町１番地 トヨタ自 動車株式会社内 (56)参考文献 特開 平６−41701（ＪＰ，Ａ) 特開 平５−306424（ＪＰ，Ａ) 特開 平５−70880（ＪＰ，Ａ) 特開 平３−47941（ＪＰ，Ａ) 特開 平３−10041（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 23/00 - 23/06 C22F 1/06 ────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 7 Identification code FI C22F 1/00 630 C22F 1/00 630K 681 681 683 683 694 694 694B 1/06 1/06 (72) Inventor Ken Masumoto Sendai, Miyagi 3-8-22 Uesugi, Aoba-ku, Aichi-ku (72) Inventor Akihisa Inoue No.1, Kawauchi, Aoba-ku, Sendai-shi, Miyagi 11-806 (72) Inventor Hidehiko Horikiri 1-9-9, Yaesu, Chuo-ku, Tokyo Inside Teikoku Piston Ring Co., Ltd. (72) Inventor Akira Kato 1 Toyota Town, Toyota City, Aichi Prefecture Inside Toyota Motor Co., Ltd. (56) References JP-A-6-41701 (JP, A) JP-A-5-306424 (JP, A) JP-A-5-70880 (JP, A) JP-A-3-47941 (JP, A) JP-A-3-10041 (JP, A) (58) Fields investigated (Int. Cl. 7) , DB ) C22C 23/00 - 23/06 C22F 1/06
Claims (2)
Ｙ，Ｃｅ，Ｌａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍｍ（ミッシュメ
タル）からなる群から選ばれる１種または２種以上の元
素、８７原子％≦ａ≦９８原子％、ｂ及びｃは図１の
Ａ，Ｂ点を結ぶ線上を除くＢ−Ｃ−Ｄ−Ｅ−Ｆ−Ａの線
上及びＡ−Ｂ−Ｃ−Ｄ−Ｅ−Ｆの線で囲まれた範囲であ
り、かつ０≦Ｙ（イットリウム）≦４．５原子％、０≦
Ｃｅ，Ｌａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍｍ≦３原子％で表さ
れる組成を有し、サブミクロンの微結晶からなる母相に
Ｍｇ−Ｚｎ系及びＭｇ−Ｘ系金属間化合物が分散したこ
とを特徴とする靭性に優れた高強度マグネシウム合金粉
末固化材。In the general formula, Mg a Zn b X c (where X is one or more elements selected from the group consisting of Y, Ce, La, Nd, Pr, Sm, Mm (Misch metal)) , 87 at% ≦ a ≦ 98 at%, b and c are on the line of BCDDEFA except for the line connecting the points A and B in FIG. 1 and ABCDE. -F, and 0 ≦ Y (yttrium) ≦ 4.5 atomic%, 0 ≦
It has a composition represented by Ce, La, Nd, Pr, Sm, and Mm ≦ 3 atomic%, and a Mg—Zn-based and Mg—X-based intermetallic compound is dispersed in a parent phase composed of submicron microcrystals. High strength magnesium alloy powder solidified material with excellent toughness characterized by:
Ｙ，Ｃｅ，Ｌａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍｍ（ミッシュメ
タル）からなる群から選ばれる１種または２種以上の元
素、８７原子％≦ａ≦９８原子％、ｂ及びｃは図１の
Ａ，Ｂ点を結ぶ線上を除くＢ−Ｃ−Ｄ−Ｅ−Ｆ−Ａの線
上及びＡ−Ｂ−Ｃ−Ｄ−Ｅ−Ｆの線で囲まれた範囲であ
り、かつ０≦Ｙ（イットリウム）≦４．５原子％、０≦
Ｃｅ，Ｌａ，Ｎｄ，Ｐｒ，Ｓｍ，Ｍｍ≦３原子％で表さ
れる組成を有する合金溶湯を急冷凝固し、その後該急冷
凝固合金に３００〜４５０℃の温度で塑性加工を施し、
サブミクロンの微結晶からなる母相にＭｇ−Ｚｎ系及び
Ｍｇ−Ｘ系金属間化合物を分散させたことを特徴とする
高強度マグネシウム合金粉末固化材の製造方法。2. A compound represented by the general formula: Mg a Zn b X c (where X is one or more elements selected from the group consisting of Y, Ce, La, Nd, Pr, Sm, and Mm (Misch metal)) , 87 atomic% ≦ a ≦ 98 atomic%, b and c in FIG. 1
BCDDEFA line excluding the line connecting points A and B
It is a range surrounded by the upper and ABCDEF lines , and 0 ≦ Y (yttrium) ≦ 4.5 atomic%, 0 ≦
An alloy melt having a composition represented by Ce, La, Nd, Pr, Sm, and Mm ≦ 3 atomic% is rapidly solidified, and then the rapidly solidified alloy is subjected to plastic working at a temperature of 300 to 450 ° C.
Mg-Zn based and
A method for producing a high-strength magnesium alloy powder solidified material, wherein an Mg-X-based intermetallic compound is dispersed .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP05402693A JP3238516B2 (en) | 1993-03-15 | 1993-03-15 | High strength magnesium alloy and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP05402693A JP3238516B2 (en) | 1993-03-15 | 1993-03-15 | High strength magnesium alloy and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH073375A JPH073375A (en) | 1995-01-06 |
| JP3238516B2 true JP3238516B2 (en) | 2001-12-17 |
Family
ID=12959080
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP05402693A Expired - Lifetime JP3238516B2 (en) | 1993-03-15 | 1993-03-15 | High strength magnesium alloy and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3238516B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US10184165B2 (en) | 2003-11-26 | 2019-01-22 | Yoshihito Kawamura | High strength and high toughness magnesium alloy and method of producing the same |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2807400B2 (en) * | 1993-08-04 | 1998-10-08 | ワイケイケイ株式会社 | High strength magnesium-based alloy material and method of manufacturing the same |
| JP5161414B2 (en) * | 2001-01-26 | 2013-03-13 | 能人 河村 | High strength magnesium alloy |
| JP3592310B2 (en) | 2001-06-05 | 2004-11-24 | 住友電工スチールワイヤー株式会社 | Magnesium-based alloy wire and method of manufacturing the same |
| WO2004085689A1 (en) * | 2003-03-25 | 2004-10-07 | Yoshihito Kawamura | Magnesium alloy of high strength and high toughness and method for production thereof |
| US7841380B2 (en) | 2004-06-30 | 2010-11-30 | Sumitomo Electric Industries, Ltd. | Producing method for magnesium alloy material |
| WO2006095999A1 (en) * | 2005-03-08 | 2006-09-14 | Dong-Hyun Bae | Mg alloys containing misch metal, manufacturing method of wrought mg alloys containing misch metal, and wrought mg alloys thereby |
| US8636853B2 (en) | 2007-03-26 | 2014-01-28 | Toyota Jidosha Kabushiki Kaisha | Mg alloy and method of production of same |
-
1993
- 1993-03-15 JP JP05402693A patent/JP3238516B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US10184165B2 (en) | 2003-11-26 | 2019-01-22 | Yoshihito Kawamura | High strength and high toughness magnesium alloy and method of producing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH073375A (en) | 1995-01-06 |
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