JPH08120301A - Production of solid-liquid coexisting metal for forming - Google Patents
Production of solid-liquid coexisting metal for formingInfo
- Publication number
- JPH08120301A JPH08120301A JP6285947A JP28594794A JPH08120301A JP H08120301 A JPH08120301 A JP H08120301A JP 6285947 A JP6285947 A JP 6285947A JP 28594794 A JP28594794 A JP 28594794A JP H08120301 A JPH08120301 A JP H08120301A
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- powder
- solid
- phase
- melting point
- liquid coexisting
- Prior art date
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、非樹枝状の固相が金属
液相中に均一に分布し、流動性に優れた、型成形、圧
延、鍛造、押し出し等の成形用固液共存金属の製造方法
に関するものである。FIELD OF THE INVENTION The present invention relates to a solid-liquid coexisting metal for molding such as molding, rolling, forging, and extrusion, in which a non-dendritic solid phase is uniformly distributed in a liquid metal phase and has excellent fluidity. The present invention relates to a manufacturing method of.
【０００２】[0002]
【従来の技術】非樹枝状晶の固相を有する固液共存金属
は、半液状であることから、成形が容易である、温度が
低いことから、型寿命が長くなる、収縮が少なく製品に
巣ができにくい、割れがない、等の利点があり、成形用
材料として注目されるようになった。樹枝状晶の固相を
有する固液共存金属を成形用材料に用いると、樹枝状晶
が絡み合った状態となり、割れが生じるなど問題があ
り、当然、非樹枝状晶を有するものとすることが望まれ
る。従来の非樹枝状の固相を有する固液共存金属を製造
する方法は、金属（一般には合金）を溶解し、その凝固
過程において攪拌子を用いて機械的に攪拌させたり、電
磁誘導攪拌コイルを用いて電磁気的に攪拌させることに
より、融液中に生成しつつある樹枝状の初晶をその枝部
を消失ないしは方向を変えることにより樹枝状に成長す
ることを妨げることで、非樹枝状晶を得る方法が一般的
である。前記機械的攪拌によるものは、例えば、特開平
４−１７９４４号公報に、また電磁気的攪拌によるもの
は、例えば、特開平４−３０５３３６号公報に記載があ
る。A solid-liquid coexisting metal having a non-dendritic solid phase is semi-liquid, which facilitates molding, and has a low temperature, which prolongs mold life and reduces shrinkage. It has attracted attention as a molding material because it has the advantages that it does not easily form cavities and that it does not crack. When a solid-liquid coexisting metal having a solid phase of dendrites is used as a molding material, there is a problem that dendrites become entangled with each other and cracks occur. Naturally, the dendrites may have non-dendritic crystals. desired. The conventional method for producing a solid-liquid coexisting metal having a non-dendritic solid phase is to dissolve a metal (generally an alloy) and mechanically stir it with a stirrer during the solidification process, or use an electromagnetic induction stirring coil. By electromagnetically stirring the dendritic primary crystals that are being formed in the melt by preventing the dendritic growth of the dendritic primary crystals by disappearing or changing the direction of the dendritic primary crystals. The method of obtaining crystals is common. The mechanical stirring is described in, for example, JP-A-4-17944, and the electromagnetic stirring is described in, for example, JP-A-4-305336.
【０００３】[0003]
【発明が解決しようとする課題】これらの方法において
は、金属を一旦溶解する必要があるため、自ずとその組
成には限りがあり、溶解度以上には溶質金属を配合する
ことはできなかった。また、非樹枝状晶の寸法は冷却速
度に強く依存するため、微細な非樹枝状晶を得るには冷
却をする必要があるが、強冷却をした場合には固相率が
増加するため粘性が大きくなり過ぎ、得られた固液共存
金属を連続的に排出することが困難になるという問題が
あった。また、機械的あるいは電磁気的攪拌により、非
樹枝状晶同志が衝突し、合体することにより粗大化した
り、寸法が不揃いになることが避けられなかった。In these methods, since it is necessary to dissolve the metal once, the composition is naturally limited, and solute metal cannot be blended at a level higher than the solubility. In addition, since the size of non-dendritic crystals strongly depends on the cooling rate, it is necessary to cool to obtain fine non-dendritic crystals. Was too large, and it was difficult to continuously discharge the obtained solid-liquid coexisting metal. In addition, it is unavoidable that non-dendritic crystals collide with each other due to mechanical or electromagnetic stirring, and coarsen or become irregular in size due to coalescence.
【０００４】このように金属を溶解して凝固過程で攪拌
により非樹枝状晶を得る手法では、金属（合金）の組成
を自由に選択することが出来ず、また、微細な非樹枝状
晶を得ようとすると、粘性の増大により容器からの排出
が困難になること等の問題がある。これらの問題の原因
は、凝固過程で晶出する樹枝状晶を利用していることに
ある。本発明は、用いる材料を一旦完全に溶解すること
なく、そして凝固過程で晶出する初晶を利用することな
く、組成を自由に選択することができ、微細で均一な非
樹枝状晶を有する、成形用の固液共存金属を製造する方
法を提案しようとするものである。In this way, in the method of dissolving the metal and obtaining the non-dendritic crystal by stirring in the solidification process, the composition of the metal (alloy) cannot be freely selected, and the fine non-dendritic crystal is not formed. If it is attempted to be obtained, there is a problem that it becomes difficult to discharge it from the container due to an increase in viscosity. The cause of these problems is the utilization of dendrites that crystallize out during the solidification process. INDUSTRIAL APPLICABILITY The present invention allows the composition to be freely selected without completely dissolving the material to be used and without using the primary crystal that crystallizes in the solidification process, and has a fine and uniform non-dendritic crystal. , A method for producing a solid-liquid coexisting metal for molding is proposed.
【０００５】[0005]
【課題を解決するための手段】本発明の手段は、金属又
は金属間化合物の融点の異なる粉末の２種以上を混合
し、その混合粉末を、混合した夫々の粉末の融点の中の
最も低い温度と最も高い温度との間の温度に加熱保持す
ることにより、少なくとも１種以上の粉末を溶融させる
ことを特徴とする。前記手段において、前記混合粉末の
中の少なくとも２種以上の粉末が、前記保持温度に加熱
する加熱過程の温度又は保持温度において反応し、元の
粉末組成とは異なる成分の固相と液相を生じるものとし
てもよい。Means for Solving the Problems According to the means of the present invention, two or more kinds of powders of metals or intermetallic compounds having different melting points are mixed, and the mixed powder is the lowest of melting points of the mixed powders. It is characterized in that at least one kind of powder is melted by heating and holding at a temperature between the temperature and the highest temperature. In the above means, at least two kinds of powders among the mixed powders react at the temperature of the heating process for heating to the holding temperature or at the holding temperature to form a solid phase and a liquid phase of components different from the original powder composition. It may occur.
【０００６】前記手段において、前記反応する粉末中の
高融点粉末の混合割合が、保持温度における平衡状態図
上の固相と液相の割合の固相割合より小さいものとする
のがよい。前記手段において、前記反応が少なくとも略
平衡状態に達するまで保持温度に保つのがよい。前記手
段において、前記反応する粉末中の高融点粉末の混合割
合が、保持温度における平衡状態図上の固相と液相の割
合の固相割合より大きいものとするのがよい。前記手段
において、前記高融点粉末が多孔質であるものとするの
がよい。前記多孔質の高融点粉末は還元鉄粉とするのが
よい。In the above means, the mixing ratio of the high melting point powder in the reacting powder is preferably smaller than the solid phase ratio of the solid phase and the liquid phase on the equilibrium diagram at the holding temperature. In the above-mentioned means, the holding temperature is preferably maintained until the reaction reaches at least a substantially equilibrium state. In the above means, the mixing ratio of the high melting point powder in the reacting powder is preferably higher than the solid phase ratio of the solid phase and the liquid phase on the equilibrium diagram at the holding temperature. In the above means, it is preferable that the high melting point powder is porous. The porous high melting point powder is preferably reduced iron powder.
【０００７】[0007]
【作用】金属粉末は、例えば、鉄系粉末、アルミ合金粉
末、同軽合金粉末等であり、金属間化合物の粉末は、例
えば、金属間化合物はＦｅ−Ｓｉの粉末もようなもので
ある。前記加熱保持の所定の温度領域に加熱することに
より、その温度より融点の低い粉末は溶解して液相とな
り、その温度より融点の高い粉末は溶解せずそのまま固
相として残るため、結果として独立した融点の高い粉末
粒子を融点の低い液相が取り囲んだ、非樹枝状晶を有す
る固液共存金属が得られる。そして、材料を一旦完全に
溶解することがないため、溶質の溶解度とは関係なく、
自由に粉末の配合を選択することが可能となる。用いる
粉末同志が反応し元の粉末の組成とは異なる液相と固相
を生じる場合でも、固相と液相とが共存する温度領域に
保持する限り、固液共存金属を得ることができる。例え
ば、ＳＵＳ（ステンレス）の粉末と鋳鉄粉末を用いると
き、ＣがＳＵＳ中に拡散し、Ｃｒ、Ｎｉが鋳鉄中に入る
ような場合である。The metal powder is, for example, an iron-based powder, an aluminum alloy powder, the same light alloy powder, and the intermetallic compound powder is, for example, a Fe-Si powder. By heating to a predetermined temperature range of the heating and holding, the powder having a lower melting point than that temperature is dissolved and becomes a liquid phase, and the powder having a higher melting point than that temperature is not dissolved and remains as a solid phase as a result. A solid-liquid coexisting metal having a non-dendritic crystal in which a powder phase having a high melting point is surrounded by a liquid phase having a low melting point is obtained. And since the material is not completely dissolved once, regardless of the solubility of the solute,
It is possible to freely select the powder composition. Even when the powders to be used react with each other to generate a liquid phase and a solid phase different from the composition of the original powder, a solid-liquid coexisting metal can be obtained as long as the temperature is maintained in the temperature range in which the solid phase and the liquid phase coexist. For example, when using SUS (stainless steel) powder and cast iron powder, C diffuses into SUS and Cr and Ni enter into cast iron.
【０００８】高融点粉末の混合割合が、保持温度におけ
る平衡状態図上の固相と液相の割合の固相割合より小さ
いものとするのは、前記反応が、固相を成長させる反応
である。固相の断面形状は円または楕円に近い形状とな
る。すなわち、前記保持温度になる過程及び保持温度に
おいて、固相である高融点粉末の粒子内の表面付近に液
相中の元素が拡散して反応し、低融点合金となり、保持
温度における平衡状態になる過程で固相が成長する。こ
の時界面エネルギーを最小とするため、固相の粒が面積
を減少させるように球形へと変化する。前記反応が少な
くとも略平衡状態に達するまで保持温度に保つと、高融
点粉末であった固相の大きい粒径のものが小さい粒径の
ものを吸着する形で合体し粒径がやや大きくなる。この
場合も界面エネルギーを最小とするため、固相の粒が面
積を減少させるように球形に近いものとなる。高融点粉
末の混合割合が、保持温度における平衡状態図上の固相
と液相の割合の固相割合より大きいものとするのは、前
記反応が、固相を縮小させる反応である。固相の断面形
状は円または楕円に近い形状となる。すなわち、前記保
持温度になる過程及び保持温度において、固相である高
融点粉末の粒子内の表面付近に液相中の元素が拡散して
反応し、低融点合金となり、保持温度における平衡状態
になる過程で固相が減少する。この時も界面エネルギー
を最小とするため、固相の粒が面積を減少させるように
球形へと変化する。It is the reaction for growing the solid phase that the mixing ratio of the high melting point powder is smaller than the solid phase ratio of the solid phase and the liquid phase on the equilibrium diagram at the holding temperature. . The cross-sectional shape of the solid phase is a circle or an ellipse. That is, in the process of reaching the holding temperature and the holding temperature, the elements in the liquid phase diffuse and react near the surface inside the particles of the high melting point powder that is a solid phase, and become a low melting point alloy, and become in an equilibrium state at the holding temperature. The solid phase grows in the process. At this time, in order to minimize the interfacial energy, the solid-phase grains change into spheres so as to reduce the area. If the holding temperature is maintained until the reaction reaches at least a substantially equilibrium state, the high melting point powder having a large solid phase particle size is coalesced in the form of adsorbing the small particle size particle and the particle size is slightly increased. In this case as well, the interfacial energy is minimized, so that the solid-phase particles have a nearly spherical shape so as to reduce the area. It is a reaction for reducing the solid phase that the mixing ratio of the high melting point powder is higher than the solid phase ratio of the solid phase and the liquid phase on the equilibrium diagram at the holding temperature. The cross-sectional shape of the solid phase is a circle or an ellipse. That is, in the process of reaching the holding temperature and the holding temperature, the elements in the liquid phase diffuse and react near the surface inside the particles of the high melting point powder that is a solid phase, and become a low melting point alloy, and become in an equilibrium state at the holding temperature. The solid phase decreases in the process. At this time as well, since the interfacial energy is minimized, the solid-phase grains change into spherical shapes so as to reduce the area.
【０００９】前記高融点粉末が多孔質であると、粒の形
が異形であり、肉の薄い部分のあることから、固相内に
拡散してくる元素により、固相表面付近に融点の低い部
分が生じることによって固相の粒が分断されてより小さ
い粒径のものとなる。この場合も粒は球形に近づこうと
する。還元鉄粉は入手しやすいから、多孔質の高融点粉
末が鉄であるときは、コスト的に有利である。When the high melting point powder is porous, the shape of the grains is irregular and there is a thin portion of the meat. Therefore, the element that diffuses into the solid phase has a low melting point near the surface of the solid phase. Due to the generation of the portion, the solid phase particles are divided into smaller particles. In this case as well, the grains try to approach a spherical shape. Since reduced iron powder is easily available, cost is advantageous when the porous high melting point powder is iron.
【００１０】[0010]
実施例１ 本発明を鉄系合金に適用した実施例を示す。簡単にする
ために用いる金属粉末は次の２種類とした。すなわち、
高融点粉末として、９９ｗｔ％以上のＦｅ粉末、平均粒
径１５０μｍ、融点１３５６°Ｃ、低融点粉末として、
４．２ｗｔ％Ｃ−０．６ｗｔ％Ｓｉ−Ｆｅ合金粉末、平
均粒径５０μｍ、融点１１４７°Ｃ、を用いた。用いた
金属粉末粒子の外観形状を図２（高融点金属粉末）、図
３（低融点合金粉末）に示す。Example 1 An example in which the present invention is applied to an iron-based alloy will be shown. The following two types of metal powders were used for simplicity. That is,
As the high melting point powder, 99% by weight or more of Fe powder, the average particle size of 150 μm, the melting point of 1356 ° C., the low melting point powder,
4.2 wt% C-0.6 wt% Si-Fe alloy powder, average particle size 50 μm, and melting point 1147 ° C. were used. The appearance of the metal powder particles used is shown in FIG. 2 (high melting point metal powder) and FIG. 3 (low melting point alloy powder).
【００１１】前記高融点粉末と低融点粉末を重量割合で
３対７となるように配合し、ボールミルにより２４時間
混練後、３kgf/cm2 の成形圧にて成形し、多数の圧粉体
を作成した。この圧粉体を１１７５°Ｃに保持した均熱
炉に挿入し、圧粉体の表面温度が１１７５°Ｃに達して
から、６０ｓｅｃ、及び１２００ｓｅｃ経過後に５個ず
つ炉から速やかに取り出し、水中冷却により組織の凍結
を行い、組織を観察した。その組織観察結果を図１に示
す。いずれの保持時間においても微細な球状のオーステ
ナイト（固相）を鋳鉄溶湯（液相）が取り囲んだ組織と
なっている。非樹枝状晶の粒径は６０ｓｅｃ保持のもの
で約５０μｍ、１２００ｓｅｃ保持のもので約７０μｍ
と微細であった。さらに得られたオーステナイトは元の
高融点粉末の形状とは異なり、その形状は凹凸はなくな
り、より球に近くなっていることが確認できる。The high melting point powder and the low melting point powder were mixed in a weight ratio of 3: 7, kneaded in a ball mill for 24 hours, and then molded at a molding pressure of 3 kgf / cm 2 to obtain a large number of green compacts. Created. This green compact was inserted into a soaking furnace that was maintained at 1175 ° C, and after 60 seconds and 1200 seconds had elapsed since the surface temperature of the green compact reached 1175 ° C, 5 pieces were quickly taken out of the furnace and cooled in water. The tissue was frozen by and the tissue was observed. The results of observation of the structure are shown in FIG. At any holding time, the structure is such that fine spherical austenite (solid phase) is surrounded by molten cast iron (liquid phase). The particle size of non-dendritic crystal is about 50 μm when it is kept for 60 sec and about 70 μm when it is kept for 1200 sec.
Was fine. Further, it can be confirmed that the obtained austenite is different from the original shape of the high melting point powder in that the shape has no unevenness and is closer to a sphere.
【００１２】これを図４に示す鉄−炭素２元系の平衡状
態図に従い考察する。本実施例に示す配合は約３ｗｔ％
Ｃ−Ｆｅ成分に相当するが、この組成のものを溶融状態
より冷却し、１１７５°Ｃに保持した場合は、図のＣ組
成の固相オーステナイトはデンドライト状になる。とこ
ろが本実施例では、前記圧粉体を１１７５°Ｃに保持す
ると、低融点粉末が溶解するとともに炭素濃度の高い低
融点粉末から炭素濃度の低い高融点粉末側に炭素の拡散
がおこるため、高融点粉末はオーステナイトへと変化す
る。長時間保持により平衡状態に達すると、最終的には
Ｄ組織のオーステナイトからなる固液共存金属が得られ
る。ここで今回の試験に用いた高融点粉末の割合は約３
０ｖｏｌ％であるので、液相より高融点粉末を元とする
オーステナイトが粒成長することで、平衡状態図の固相
と液相の割合である５０ｖｏｌ％−５０ｖｏｌ％に近付
く。本実施例の場合、６０ｓｅｃでは未だ平衡状態には
至っておらず、その途中の段階であるため１２００ｓｅ
ｃ保持のものの粒径と比較すると小さくなっていると判
断される。１２００ｓｅｃ以上保持しても粒径は変化し
なかった。ここで、高融点粉末は互いに独立した非樹枝
状晶であるため、炭素の拡散によって変化したオーステ
ナイトも非樹枝状晶であり、その界面エネルギーを最小
とするため、表面積を減らすように球形へと変化してい
る。さらに、攪拌等による粒同志の衝突がおこらないた
め、粒の合体による粗大化はおこり難い。This will be considered according to the equilibrium diagram of the iron-carbon binary system shown in FIG. The formulation shown in this example is about 3 wt%
Corresponding to the C-Fe component, when this composition is cooled from the molten state and kept at 1175 ° C, the solid phase austenite of the C composition in the figure becomes dendrite-like. However, in the present embodiment, when the green compact is maintained at 1175 ° C., the low melting point powder is melted and carbon is diffused from the low melting point powder having a high carbon concentration to the high melting point powder side having a low carbon concentration. The melting point powder changes to austenite. When the equilibrium state is reached by holding for a long time, a solid-liquid coexisting metal consisting of austenite of the D structure is finally obtained. Here, the ratio of the high melting point powder used in this test is about 3
Since it is 0 vol%, the austenite based on the powder having a higher melting point than the liquid phase grows to approach 50 vol% -50 vol% which is the ratio of the solid phase and the liquid phase in the equilibrium diagram. In the case of the present embodiment, the equilibrium state has not yet been reached at 60 seconds, and since it is an intermediate stage, 1200 se
It is judged that the particle size is smaller than that of the particles having c. The particle size did not change even after being held for 1200 seconds or longer. Here, since the high-melting-point powder is a non-dendritic crystal independent of each other, the austenite changed by the diffusion of carbon is also a non-dendritic crystal, and its interfacial energy is minimized so that the surface area is reduced to a spherical shape. Is changing. Further, since the grains do not collide with each other due to stirring or the like, coarsening due to coalescence of grains is unlikely to occur.
【００１３】なお、実施例１の変形例として、高融点粉
末と低融点粉末の重量割合を前記とは逆に７対３とした
ときは、平衡状態図の固相と液相の割合である５０ｖｏ
ｌ％−５０ｖｏｌ％に近付くことから、高融点粉末を元
とするオーステナイトが液相に移る。従って、固相部分
が減少する。As a modification of the first embodiment, when the weight ratio of the high melting point powder and the low melting point powder is set to 7 to 3 contrary to the above, it is the ratio of the solid phase and the liquid phase in the equilibrium diagram. 50vo
Since it approaches 1% -50% by volume, austenite based on the high melting point powder moves to the liquid phase. Therefore, the solid phase portion is reduced.
【００１４】実施例２ Ｆｅ粉末とＦｅ−Ｃ−Ｓｉ金属間化合物粉末による実施
例である。用いた金属粉末は、高融点粉末として、９９
ｗｔ％以上のＦｅ粉末、平均粒径５０μｍ、融点約１５
３６°Ｃ、低融点粉末として、０．８ｗｔ％Ｃ−１８ｗ
ｔ％Ｓｉ−Ｆｅ合金粉末、平均粒径５０μｍ、融点１１
８０°Ｃ、である。用いた金属粉末粒子の外観形状を図
６（高融点金属粉末）、図７（低融点合金粉末）に示
す。前記高融点粉末と低融点粉末の重量割合を３対７と
なるように配合し、ボールミルにより２４時間混練後、
３kgf/cm2 の成形圧にて成形し圧粉体を作成した。この
圧粉体を１１９５°Ｃに保持した均熱炉に挿入し、圧粉
体の表面温度が１１９５°Ｃに達してから、３００ｓｅ
ｃ経過後に炉より速やかに取り出し、空冷し組織を観察
した。その結果を図５に示すが、粒状のフェライトとそ
の周囲に黒鉛が晶出した組織が得られた。この場合、１
１８０°Ｃにて低融点粉末が溶融し、高融点粉末粒子を
取り囲むが、その固液界面を介しＳｉが高融点粉末に拡
散することで、高融点粉末はＳｉ組成のフェライトへと
変化している。また、高融点粉末を元とするフェライト
は界面エネルギーが最小となるように、形状が球形へと
変化していることが確認された。Example 2 This is an example using Fe powder and Fe-C-Si intermetallic compound powder. The metal powder used was 99% as a high melting point powder.
Fe powder of wt% or more, average particle size 50 μm, melting point about 15
As a low melting point powder at 36 ° C, 0.8 wt% C-18w
t% Si-Fe alloy powder, average particle size 50 μm, melting point 11
80 ° C. The appearance of the metal powder particles used is shown in FIG. 6 (high melting point metal powder) and FIG. 7 (low melting point alloy powder). The high-melting point powder and the low-melting point powder were mixed in a weight ratio of 3: 7 and kneaded in a ball mill for 24 hours,
A green compact was prepared by molding at a molding pressure of 3 kgf / cm 2 . This green compact was inserted into a soaking furnace maintained at 1195 ° C, and after the surface temperature of the green compact reached 1195 ° C, 300 se
After the lapse of c, it was immediately taken out of the furnace, air-cooled, and the structure was observed. The results are shown in FIG. 5, and a structure in which graphite was crystallized around the granular ferrite was obtained. In this case, 1
The low melting point powder melts at 180 ° C. and surrounds the high melting point powder particles, but Si diffuses through the solid-liquid interface into the high melting point powder, and the high melting point powder changes to ferrite of Si composition. There is. It was also confirmed that the ferrite based on the high melting point powder has changed into a spherical shape so that the interfacial energy is minimized.
【００１５】[0015]
【発明の効果】請求項１に記載の発明によれば、従来の
溶解では不可能な組成の金属（合金）においても非樹枝
状晶を有する固液共存金属の製造が可能となる。そし
て、その固相は微細で均一な粒径とすることができる。
請求項２に記載の発明によれば、元の粉末組成とは異な
る成分の固相と液相を生じるから、成形用固液共存金属
の用途が拡大する。請求項３、請求項４、請求項５に記
載の発明によれば、材料粉末は微細なものを得ることが
可能であるから、微細で均一な球形に近い非樹枝状晶を
有する固液共存金属の製造が可能となる。従って、流動
性が要求される固液共存金属において有効である。請求
項６、請求項７に記載の発明によれば、材料の高融点粉
末の粒径よりも固相の粒径が大幅に小さく、球形に近い
非樹枝状晶を有する固液共存金属の製造が可能となる。According to the first aspect of the present invention, it is possible to produce a solid-liquid coexisting metal having a non-dendritic crystal even in a metal (alloy) having a composition that cannot be obtained by conventional melting. The solid phase can have a fine and uniform particle size.
According to the second aspect of the present invention, the solid phase and the liquid phase of the components different from the original powder composition are generated, so that the applications of the solid-liquid coexisting metal for molding are expanded. According to the inventions of claim 3, claim 4, and claim 5, since it is possible to obtain a fine material powder, solid-liquid coexistence having fine and uniform non-dendritic crystals close to a spherical shape. It enables the production of metals. Therefore, it is effective for a solid-liquid coexisting metal that requires fluidity. According to the inventions of claims 6 and 7, the production of a solid-liquid coexisting metal having a non-dendritic crystal whose particle size in the solid phase is significantly smaller than that of the high melting point powder of the material and which is close to spherical. Is possible.
【図１】本発明の実施例１で得られた固液共存金属の組
織を凍結した顕微鏡組織を示す図面代用写真であり、
（ａ）は保持時間６０ｓｅｃのもの、（ｂ）は保持時間
１２００ｓｅｃのものである。1 is a drawing-substituting photograph showing a microscopic structure obtained by freezing the structure of a solid-liquid coexisting metal obtained in Example 1 of the present invention,
(A) shows a holding time of 60 sec, and (b) shows a holding time of 1200 sec.
【図２】同実施例１に使用した高融点金属粉末粒子の形
状を示す図面代用顕微鏡写真である。2 is a drawing-substitute micrograph showing the shape of refractory metal powder particles used in Example 1. FIG.
【図３】同実施例１に使用した低融点金属粉末粒子の形
状を示す図面代用顕微鏡写真である。3 is a drawing-substitute micrograph showing the shape of low-melting metal powder particles used in Example 1. FIG.
【図４】同実施例１の説明に使用したＦｅ−Ｃ系状態図
である。FIG. 4 is an Fe—C system phase diagram used for the description of Example 1.
【図５】本発明の実施例２で得られた固液共存金属の組
織を凍結した顕微鏡組織写真である。FIG. 5 is a micrograph of a microstructure obtained by freezing the structure of a solid-liquid coexisting metal obtained in Example 2 of the present invention.
【図６】同実施例２に使用した高融点金属粉末粒子の形
状を示す図面代用顕微鏡写真である。6 is a drawing-substitute micrograph showing the shape of refractory metal powder particles used in Example 2. FIG.
【図７】同実施例２に使用した低融点金属粉末粒子の形
状を示す図面代用顕微鏡写真である。FIG. 7 is a drawing-substitute micrograph showing the shape of low-melting point metal powder particles used in Example 2.
フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｂ２２Ｆ 3/18 3/20 (72)発明者 辻川 正人 大阪府堺市学園町１番１号 大阪府立大学 内 (72)発明者 川本 信 大阪府堺市学園町１番１号 大阪府立大学 内 (72)発明者 露口 裕義 大阪府堺市学園町１番１号 大阪府立大学 内Continuation of the front page (51) Int.Cl. 6 Identification number Office reference number FI Technical display location B22F 3/18 3/20 (72) Inventor Masato Tsujikawa 1-1 Gakuencho, Sakai-shi, Osaka Prefectural University (72) Inventor Shin Kawamoto 1-1 Gakuencho, Sakai City, Osaka Prefecture Osaka Prefectural University (72) Inventor Hiroyoshi Tsuruguchi 1-1, Gakuencho, Sakai City Osaka Prefecture
Claims (7)
末の２種以上を混合し、その混合粉末を、混合した夫々
の粉末の融点の中の最も低い温度と最も高い温度との間
の温度に加熱保持することにより、少なくとも１種以上
の粉末を溶融させることを特徴とする成形用固液共存金
属の製造方法。1. A mixture of two or more kinds of powders of metals or intermetallic compounds having different melting points, and the mixed powder is a temperature between the lowest temperature and the highest temperature of the melting points of the respective mixed powders. A method for producing a solid-liquid coexisting metal for molding, which comprises melting at least one kind of powder by heating and holding the powder.
製造方法において、前記混合粉末の中の少なくとも２種
以上の粉末が、前記保持温度に加熱する加熱過程の温度
又は保持温度において反応し、元の粉末組成とは異なる
成分の固相と液相を生じるものであることを特徴とする
成形用固液共存金属の製造方法。2. The method for producing a solid-liquid coexisting metal for molding according to claim 1, wherein at least two kinds of powders in the mixed powder are heated to the holding temperature at a heating process temperature or holding temperature. A method for producing a solid-liquid coexisting metal for molding, which reacts to produce a solid phase and a liquid phase of components different from the original powder composition.
製造方法において、前記反応する粉末中の高融点粉末の
混合割合が、前記保持温度における平衡状態図上の固相
と液相の割合の固相割合より小さいことを特徴とする成
形用固液共存金属の製造方法。3. The method for producing a solid-liquid coexisting metal for molding according to claim 2, wherein the mixing ratio of the high melting point powder in the reacting powder is such that the solid phase and the liquid phase on the equilibrium diagram at the holding temperature. The solid-liquid coexisting metal for molding is characterized by being smaller than the solid-phase proportion.
製造方法において、前記反応が少なくとも略平衡状態に
達するまで保持温度に保つことを特徴とする成形用固液
共存金属の製造方法。4. The method for producing a solid-liquid coexisting metal for molding according to claim 2, wherein the holding temperature is maintained until the reaction reaches at least a substantially equilibrium state. .
製造方法において、前記反応する粉末中の高融点粉末の
混合割合が、前記保持温度における平衡状態図上の固相
と液相の割合の固相割合より大きいことを特徴とする成
形用固液共存金属の製造方法。5. The method for producing a solid-liquid coexisting metal for molding according to claim 2, wherein the mixing ratio of the high melting point powder in the reacting powder is such that the solid phase and the liquid phase on the equilibrium diagram at the holding temperature. The solid-liquid coexisting metal for molding is characterized in that it is larger than the solid-phase proportion.
４、又は請求項５に記載の成形用固液共存金属の製造方
法において、前記高融点粉末が多孔質であることを特徴
とする成形用固液共存金属の製造方法。6. The method for producing a solid-liquid coexisting metal for molding according to claim 1, claim 2, claim 3, claim 4, or claim 5, wherein the high melting point powder is porous. A method for producing a solid-liquid coexisting metal for molding which is characterized.
製造方法において、前記多孔質の高融点粉末が還元鉄粉
であることを特徴とする成形用固液共存金属の製造方
法。7. The method for producing a solid-liquid coexisting metal for molding according to claim 6, wherein the porous high melting point powder is a reduced iron powder.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28594794A JP3824670B2 (en) | 1994-10-25 | 1994-10-25 | Method for producing solid-liquid coexisting metal for molding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28594794A JP3824670B2 (en) | 1994-10-25 | 1994-10-25 | Method for producing solid-liquid coexisting metal for molding |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08120301A true JPH08120301A (en) | 1996-05-14 |
| JP3824670B2 JP3824670B2 (en) | 2006-09-20 |
Family
ID=17698032
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP28594794A Expired - Lifetime JP3824670B2 (en) | 1994-10-25 | 1994-10-25 | Method for producing solid-liquid coexisting metal for molding |
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| Country | Link |
|---|---|
| JP (1) | JP3824670B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012201937A (en) * | 2011-03-25 | 2012-10-22 | National Institute For Materials Science | Inorganic-compound particles and process for producing same |
| US9340431B2 (en) | 2011-03-25 | 2016-05-17 | National Institute For Materials Science | Inorganic-compound particles and process for producing same |
| CN105583401A (en) * | 2015-12-25 | 2016-05-18 | 华中科技大学 | Method for preparing composite powder for 3D printing, product and application |
-
1994
- 1994-10-25 JP JP28594794A patent/JP3824670B2/en not_active Expired - Lifetime
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012201937A (en) * | 2011-03-25 | 2012-10-22 | National Institute For Materials Science | Inorganic-compound particles and process for producing same |
| US9340431B2 (en) | 2011-03-25 | 2016-05-17 | National Institute For Materials Science | Inorganic-compound particles and process for producing same |
| CN105583401A (en) * | 2015-12-25 | 2016-05-18 | 华中科技大学 | Method for preparing composite powder for 3D printing, product and application |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3824670B2 (en) | 2006-09-20 |
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