JPH0220683B2 - - Google Patents
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- Publication number
- JPH0220683B2 JPH0220683B2 JP59117928A JP11792884A JPH0220683B2 JP H0220683 B2 JPH0220683 B2 JP H0220683B2 JP 59117928 A JP59117928 A JP 59117928A JP 11792884 A JP11792884 A JP 11792884A JP H0220683 B2 JPH0220683 B2 JP H0220683B2
- Authority
- JP
- Japan
- Prior art keywords
- powder
- weight
- self
- sintered body
- metal
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
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Description
発明の目的
(1) 産業上の利用分野
本発明は金属焼結体の製造方法に関する。
(2) 従来の技術
従来、自溶性合金粉末、例えばNi−Ｂ−Si系
のNi自溶性合金粉末を用いて金属焼結体を得る
ことが知られている。この合金の固相線は1010〜
1020℃で、液相線は1075〜1085℃であり、固相線
より低温域で焼結すると形状維持性は良いが焼結
強度が弱くなり、また液相線を超えた高温域で焼
結すると全ての粉末が溶融して流動するため形状
維持が悪化する。
そこで固相線と液相線間の適当な温度、例えば
1050℃近傍で焼結を行つている。
(3) 発明が解決しようとする問題点
しかしながら、前記温度で焼結を行つた場合に
は、金属焼結体が収縮による寸法変化を示し寸法
精度が悪く、また焼結強度もそれ程高くない。
また自溶性合金は、硬度が高く、また耐摩耗性
に優れている反面、成形性が非常に悪いため、金
属焼結体に形態上の欠陥を生じ易く、また形態上
の制約が大きいという問題もある。
本発明は上記に鑑み、寸法精度が良好で、高強
度であり、その上、形態上の欠陥がなく、且つ形
態上の自由度の大きな金属焼結体を得ることので
きる前記製造方法を提供することを目的とする。
Ｂ 発明の構成
(1) 問題点を解決するための手段
本発明は、Ni自溶性合金粉末70〜90重量％と、
Mo粉末、Ｗ粉末およびステンレス鋼粉末から選
択される少なくとも一種の高融点金属粉末10〜30
重量％とを混合して混合粉末を得る工程と；該混
合粉末に１〜10重量％の合成樹脂バインダを混練
した物を用いて所定の形状を有する成形体を得る
工程と；該成形体を、1100〜1180℃にて焼結する
工程と；を用いることを第１の特徴とする。
また本発明は、Ni自溶性合金粉末70〜90重量
％と、Mo粉末、Ｗ粉末およびステンレス鋼粉末
から選択される少なくとも一種の高融点金属粉末
10〜30重量％とを混合して混合粉末を得る工程
と；該混合粉末に１〜10重量％の合成樹脂バイン
ダを混練した物を用いて所定の形状を有する成形
体を得る工程と；該成形体を、それの表面を微細
な連続気孔を持つ耐火物製シエル層よりなるバツ
クアツプにより覆つた状態で1100〜1180℃にて焼
結する工程と；を用いることを第２の特徴とす
る。
(2) 作用
第１の特徴によれば、前記高融点金属はNi自
溶性合金よりも融点が高く、したがつてNi自溶
性合金粉末に高融点金属粉末を特定量混合する
と、Ni自溶性合金粉末を1100〜1180℃、即ち、
その合金の液相線を超えた温度で焼結しても、
Ni自溶性合金の流動が高融点金属により妨げら
れて、形状維持性および寸法精度の良好な金属焼
結体を得ることができる。またNi自溶性合金相
互間の結合性が良好である上、前記のように特定
の高融点金属粉末を用いることによつて、その金
属とNi自溶性合金との絡み合いを十分に発生さ
せることができると共にそれらの密着性を向上さ
せることができ、これにより高強度な金属焼結体
を得ることができる。
またNi自溶性合金粉末と高融点金属粉末との
混合粉末に特定量の合成樹脂バインダを混練する
と、成形圧力が低くても形状維持性が良く、また
形態上の制約を大幅に低減した成形体を得ること
ができ、これにより形態上の欠陥がなく、且つ
種々の形態を有する金属焼結体を得ることができ
る。この合成樹脂バインダはNi自溶性合金粉末
の焼結温度で容易に熱分解されるので何等不都合
を生じない。
たヾし、高融点金属粉末の混合量が10重量％未
満では、金属焼結体の形状維持性が悪く、一方、
30重量％を上回ると、金属焼結体の焼結強度が低
下する。
また合成樹脂バインダの混合量が１重量％未満
では、成形体の形状維持性が悪く、一方、10重量
％を上回ると、金属焼結体の気孔率が高くなつ
て、その強度が低下する。
第２の特徴によれば、前記成形体を、その表面
を耐火物製シエル層よりなるバツクアツプにより
覆つた状態で焼結するので、そのバツクアツプに
より金属焼結体の寸法変化を抑制して、寸法精度
をさらに良好にすることができる。この場合、バ
ツクアツプは微細な連続気孔を持つているので、
合成樹脂バインダの分解に因る発生ガスは前記連
続気孔を通じて除去され、これにより残留ガスに
起因した金属焼結体の腐食といつた問題を回避し
てその品質を高めることができる。
(3) 実施例
〔実施例 〕
10〜60μmのNi自溶性合金粉末80重量％と10〜
53μmMo粉末20重量％とを混合して混合粉末を得
る。
四フツ化エチレン樹脂エマルジヨンとアクリル
樹脂エマルジヨンを１：１に混合した合成樹脂バ
インダを調整し、この合成樹脂バインダを前記混
合粉末に対して1.5重量％添加し、十分に混練し
て可塑性物を得る。この可塑性物を成形型に入れ
て0.5Kg／mm2の加圧力を以て成形し、直径20mm、
長さ20mmの円柱状成形体を得る。
この成形体を真空焼結炉に設置して、これに
Ni自溶性合金粉末の液相線を超えた温度である
120℃にて20分間の焼結処理を施し金属焼結体を
得る。
比較例として、前記Ni自溶性合金粉末91重
量％と前記Mo粉末９重量％とよりなる混合粉末
と、前記合成樹脂バインダ1.5重量％とを用いて
前記と同一寸法の円柱状成形体を成形し、前記と
同一焼結条件で金属焼結体を得る。また比較例
として、前記Ni自溶性合金粉末69重量％と前記
Mo粉末31重量％とよりなる混合粉末と、前記合
成樹脂バインダ1.5重量％とを用いて前記と同一
寸法の円柱状成形体を成形し、前記と同一焼結条
件で金属焼結体を得る。
各金属焼結体について、形状維持性、寸法変化
および焼結強度を調べたところ表の結果が得ら
れた。
Object of the Invention (1) Industrial Application Field The present invention relates to a method for producing a metal sintered body. (2) Prior Art Conventionally, it has been known to obtain a metal sintered body using a self-fusing alloy powder, for example, a Ni-B-Si based Ni self-fusing alloy powder. The solidus line of this alloy is 1010~
At 1020℃, the liquidus line is 1075 to 1085℃, and sintering at a temperature lower than the solidus line has good shape retention but weakens the sintering strength, while sintering at a temperature higher than the liquidus line Then, all the powder melts and flows, resulting in poor shape retention. Therefore, an appropriate temperature between the solidus line and the liquidus line, e.g.
Sintering is performed at around 1050℃. (3) Problems to be Solved by the Invention However, when sintering is performed at the above temperature, the metal sintered body undergoes dimensional changes due to shrinkage, resulting in poor dimensional accuracy and sintering strength is not very high. In addition, although self-fusing alloys have high hardness and excellent wear resistance, they have very poor formability, which tends to cause morphological defects in metal sintered bodies, and there are also major morphological restrictions. There is also. In view of the above, the present invention provides the above-mentioned manufacturing method capable of obtaining a metal sintered body with good dimensional accuracy, high strength, no morphological defects, and a large degree of morphological freedom. The purpose is to B. Structure of the Invention (1) Means for Solving the Problems The present invention comprises Ni self-fusing alloy powder of 70 to 90% by weight,
At least one high melting point metal powder selected from Mo powder, W powder and stainless steel powder 10-30
% by weight to obtain a mixed powder; a step of kneading the mixed powder with 1 to 10% by weight of a synthetic resin binder to obtain a molded body having a predetermined shape; The first feature is to use a step of sintering at 1100 to 1180°C. The present invention also provides 70 to 90% by weight of Ni self-fusing alloy powder and at least one high melting point metal powder selected from Mo powder, W powder, and stainless steel powder.
a step of mixing 10 to 30% by weight of a synthetic resin binder to obtain a mixed powder; a step of kneading the mixed powder with 1 to 10% of a synthetic resin binder to obtain a molded body having a predetermined shape; The second feature is that the molded body is sintered at 1100 to 1180° C. while the surface of the molded body is covered with a backup made of a refractory shell layer having fine continuous pores. (2) Effect According to the first feature, the high melting point metal has a higher melting point than the Ni self-fusing alloy, and therefore, when a specific amount of the high melting point metal powder is mixed with the Ni self-fusing alloy powder, the Ni self-fusing alloy powder Powder at 1100-1180℃, i.e.
Even if sintered at a temperature above the liquidus of the alloy,
The flow of the Ni self-fluxing alloy is hindered by the high melting point metal, making it possible to obtain a metal sintered body with good shape retention and dimensional accuracy. In addition, the bonding properties between the Ni self-fusing alloys are good, and by using a specific high-melting point metal powder as mentioned above, it is possible to sufficiently generate entanglement between the metal and the Ni self-fusing alloy. At the same time, it is possible to improve their adhesion, and as a result, a high-strength metal sintered body can be obtained. In addition, when a specific amount of synthetic resin binder is kneaded into a mixed powder of Ni self-fusing alloy powder and high-melting point metal powder, the molded product has good shape retention even at low molding pressure and has significantly reduced morphological constraints. This makes it possible to obtain metal sintered bodies that are free from morphological defects and have various morphologies. Since this synthetic resin binder is easily thermally decomposed at the sintering temperature of the Ni self-fusing alloy powder, it does not cause any inconvenience. However, if the amount of high melting point metal powder mixed is less than 10% by weight, the shape retention of the metal sintered body is poor;
When it exceeds 30% by weight, the sintering strength of the metal sintered body decreases. If the amount of the synthetic resin binder mixed is less than 1% by weight, the shaped body will have poor shape retention, while if it exceeds 10% by weight, the porosity of the metal sintered body will increase and its strength will decrease. According to the second feature, the molded body is sintered with its surface covered with a backup made of a refractory shell layer, so that the backup suppresses dimensional changes in the metal sintered body and reduces the size. Accuracy can be further improved. In this case, the backpack has fine continuous pores, so
Gas generated due to the decomposition of the synthetic resin binder is removed through the continuous pores, thereby avoiding problems such as corrosion of the metal sintered body caused by residual gas and improving its quality. (3) Example [Example] 80% by weight of Ni self-fusing alloy powder of 10 to 60 μm and 10 to 60 μm
A mixed powder is obtained by mixing with 20% by weight of 53 μm Mo powder. Prepare a synthetic resin binder by mixing a tetrafluoroethylene resin emulsion and an acrylic resin emulsion at a ratio of 1:1, add 1.5% by weight of this synthetic resin binder to the mixed powder, and thoroughly knead to obtain a plastic material. . This plastic material was put into a mold and molded with a pressure of 0.5Kg/ mm2 , with a diameter of 20mm.
A cylindrical molded body with a length of 20 mm is obtained. This molded body is placed in a vacuum sintering furnace, and
The temperature exceeds the liquidus line of Ni self-fusing alloy powder.
A sintered metal body is obtained by sintering at 120°C for 20 minutes. As a comparative example, a cylindrical molded body having the same dimensions as above was molded using a mixed powder consisting of 91% by weight of the Ni self-fusing alloy powder and 9% by weight of the Mo powder, and 1.5% by weight of the synthetic resin binder. , a metal sintered body is obtained under the same sintering conditions as above. In addition, as a comparative example, 69% by weight of the Ni self-fusing alloy powder and the
A cylindrical molded body having the same dimensions as above is formed using a mixed powder consisting of 31% by weight of Mo powder and 1.5% by weight of the synthetic resin binder, and a metal sintered body is obtained under the same sintering conditions as above. Shape retention, dimensional change, and sintering strength of each metal sintered body were investigated, and the results shown in the table were obtained.
実施例と同様の手法により同一組成で同一形
状および同一寸法の成形体、即ち、Ni自溶性合
金粉末80重量％、Mo粉末20重量％およびそれら
の混合粉末に対して1.5重量％の前記合成樹脂バ
インダを含有し、直径20mm、長さ20mmの円柱状成
形体を複数個得る。
それらの成形体のうちいくつかのものの全表面
にはバツクアツプとして微細な連続気孔を持つ耐
火物製シエル層を形成する。このシエル層は、耐
火物としてのケイ酸ジルコニアの水懸濁液に無機
バインダとしてアルミナ粉末を添加して得られる
高粘度スラリに成形体を浸漬し、得られた付着膜
を自然乾燥後100℃にて１時間加熱乾燥すること
により形成される。
また比較のため、金属粉末としてNi自溶性合
金粉末のみを含有する同一形状および同一寸法の
成形体を得る。
第２図は、前記成形体を焼却処理した場合の焼
結温度と金属焼結体の寸法変化を示す。線a1は
Ni自溶性合金とMoよりなりシエル層を持たない
金属焼結体の場合に、線a2は同様の組成を有しシ
エル層を持つ金属焼結体の場合に、線ｂはNi自
溶性合金のみの金属焼結体の場合にそれぞれ該当
する。
図中、斜線で示す焼結温度1100〜1180℃の範囲
においてはNi自溶性合金相互間の結合性ならび
にそれとMoとの絡み合いおよび溶着性が良好
で、また前記温度範囲での寸法変化は線a1のシエ
ル層なしの焼結体の場合で＋１〜＋３％（膨脹）、
また線a2のシエル層を設けた金属焼結体の場合で
＋0.5％以下（膨脹）に抑制される。このように
シエル層を設けることにより金属焼結体の寸法変
化が抑制される理由は、本発明により得られる金
属焼結体が膨脹傾向にあり、その膨脹がシエル層
のバツクアツプ効果により妨げられるからであ
る。
またバツクアツプは微細な連続気孔を持つてい
るので、合成樹脂バインダの分解に因る発生ガス
は前記連続気孔を通じて除去され、これにより残
留ガスに起因した金属焼結体の腐食といつた問題
を回避してその品質を高めることができる。
一方、線ｂのNi自溶性合金のみの金属焼結体
の場合は、従来のように固有線と液相線間の温度
である1040℃で焼結すると、収縮による寸法変化
を示すことが明らかである。
〔実施例 〕
10〜60μmのNi自溶性合金粉末80重量％と10〜
53μmのステンレス鋼粉末20重量％とを混合して
混合粉末を得る。
四フツ化エチレン樹脂エマルジヨンとアクリル
樹脂エマルジヨンを１：１に混合した合成樹脂バ
インダを調整し、この合成樹脂バインダを前記混
合粉末に対して1.5重量％添加し、十分に混練し
て可塑性物を得る。この可塑性物を成形型に入れ
て0.5Kg／mm2の加圧力を以て成形し、直径20mm、
長さ20mmの円柱状成形体を得る。
この成形体を真空焼却炉に設置して、これに
Ni自溶性合金粉末の液相線を超えた温度である
1120℃にて20分間の焼結処理を施し金属焼結体を
得る。
比較例として、前記Ni自溶性合金粉末91重
量％と前記ステンレス鋼粉末９重量％とよりなる
混合粉末と、前記合成樹脂バインダ1.5重量％と
を用いて前記と同一寸法の円柱状成形体を成形
し、前記と同一焼結条件で金属焼結体を得る。ま
た比較例として、前記Ni自溶性合金粉末69重
量％と前記ステンレス鋼粉末31重量％とよりなる
混合粉末と、前記合成樹脂バインダ1.5重量％と
を用いて前記と同一寸法の円柱状成形体を成形
し、前記と同一焼結条件で金属焼結体を得る。
各金属焼結体について、形状維持性、寸法変化
および焼結強度を調べたところ表の結果が得ら
れた。
A molded body having the same composition, the same shape, and the same size by the same method as in the example, that is, 1.5% by weight of the above synthetic resin with respect to 80% by weight Ni self-fusing alloy powder, 20% by weight Mo powder, and a mixed powder thereof. A plurality of cylindrical molded bodies containing a binder and having a diameter of 20 mm and a length of 20 mm are obtained. A refractory shell layer with fine continuous pores is formed as a backup on the entire surface of some of these molded bodies. This shell layer is made by immersing the molded body in a high viscosity slurry obtained by adding alumina powder as an inorganic binder to an aqueous suspension of zirconia silicate as a refractory, and drying the resulting adhered film naturally at 100°C. It is formed by heating and drying for 1 hour. For comparison, a molded body of the same shape and size containing only Ni self-fusing alloy powder as the metal powder was obtained. FIG. 2 shows the sintering temperature and the dimensional change of the metal sintered body when the molded body is incinerated. line a 1 is
In the case of a metal sintered body made of Ni self-fusing alloy and Mo without a shell layer, line a 2 is a metal sintered body having a similar composition and a shell layer, and line b is a Ni self-fusing alloy. This applies to the case of only metal sintered bodies. In the sintering temperature range of 1,100 to 1,180°C, which is indicated by diagonal lines in the figure, the bonding properties between Ni self-fluxing alloys and the entanglement and welding properties between them and Mo are good, and the dimensional change in the temperature range is shown by line a. +1 to +3% (expansion) in case of sintered body without shell layer 1 ,
In addition, in the case of a metal sintered body provided with a shell layer of line a2 , the expansion is suppressed to +0.5% or less (expansion). The reason why the dimensional change of the metal sintered body is suppressed by providing the shell layer is that the metal sintered body obtained by the present invention tends to expand, and this expansion is prevented by the back-up effect of the shell layer. It is. In addition, since the backup has fine continuous pores, the gas generated due to the decomposition of the synthetic resin binder is removed through the continuous pores, thereby avoiding problems such as corrosion of the metal sintered body caused by residual gas. and improve its quality. On the other hand, in the case of a metal sintered body made only of Ni self-fluxing alloy shown in line b, it is clear that when sintered at 1040°C, which is the temperature between the characteristic line and the liquidus line, as in the conventional case, it shows dimensional changes due to shrinkage. It is. [Example] 80% by weight of 10-60 μm Ni self-fusing alloy powder and 10-60 μm
Mix with 20% by weight of 53μm stainless steel powder to obtain a mixed powder. Prepare a synthetic resin binder by mixing a tetrafluoroethylene resin emulsion and an acrylic resin emulsion at a ratio of 1:1, add 1.5% by weight of this synthetic resin binder to the mixed powder, and thoroughly knead to obtain a plastic material. . This plastic material was put into a mold and molded with a pressure of 0.5Kg/ mm2 , with a diameter of 20mm.
A cylindrical molded body with a length of 20 mm is obtained. This molded body is placed in a vacuum incinerator, and
The temperature exceeds the liquidus line of Ni self-fusing alloy powder.
A sintered metal body is obtained by sintering at 1120°C for 20 minutes. As a comparative example, a cylindrical molded body having the same dimensions as above was molded using a mixed powder consisting of 91% by weight of the Ni self-fusing alloy powder and 9% by weight of the stainless steel powder, and 1.5% by weight of the synthetic resin binder. Then, a metal sintered body is obtained under the same sintering conditions as above. As a comparative example, a cylindrical molded body having the same dimensions as above was made using a mixed powder consisting of 69% by weight of the Ni self-fusing alloy powder and 31% by weight of the stainless steel powder, and 1.5% by weight of the synthetic resin binder. A metal sintered body is obtained by molding under the same sintering conditions as above. Shape retention, dimensional change, and sintering strength of each metal sintered body were investigated, and the results shown in the table were obtained.
10〜60μmのNi自溶性合金粉末80重量％と10〜
53μmのＷ粉末20重量％とを混合して混合粉末を
得る。
四フツ化エチレン樹脂エマルジヨンとアクリル
樹脂エマルジヨンを１：１に混合した合成樹脂バ
インダを調整し、この合成樹脂バインダを前記混
合粉末に対して1.5重量％添加し、十分に混練し
て可塑性物を得る。この可塑性物を成形型に入れ
て0.5Kg／mm2の加圧力を以て成形し、直径20mm、
長さ20mmの円柱状成形体を得る。
この成形体を真空焼結炉に設置して、これに
Ni自溶性合金粉末の液相線を超えた温度である
1120℃にて20分間の焼結処理を施し金属焼結体を
得る。
比較例として、前記Ni自溶性合金粉末91重
量％と前記Ｗ粉末９重量％とよりなる混合粉末
と、前記合成樹脂バインダ1.5重量％とを用いて
前記と同一寸法の円柱状成形体を成形し、前記と
同一焼結条件で金属焼結体を得る。また比較例
として、前記Ni自溶性合金粉末69重量％と前記
Ｗ粉末31重量％とよりなる混合粉末と、前記合成
樹脂バインダ1.5重量％とを用いて前記と同一寸
法の円柱状成形体を成形し、前記と同一焼結条件
で金属焼結体を得る。
各金属焼結体について、形状維持性、寸法変化
および焼結強度を調べたところ表の結果が得ら
れた。
10~60μm Ni self-fusing alloy powder 80wt% and 10~
A mixed powder is obtained by mixing with 20% by weight of 53 μm W powder. Prepare a synthetic resin binder by mixing a tetrafluoroethylene resin emulsion and an acrylic resin emulsion at a ratio of 1:1, add 1.5% by weight of this synthetic resin binder to the mixed powder, and thoroughly knead to obtain a plastic material. . This plastic material was put into a mold and molded with a pressure of 0.5Kg/ mm2 , with a diameter of 20mm.
A cylindrical molded body with a length of 20 mm is obtained. This molded body is placed in a vacuum sintering furnace, and
The temperature exceeds the liquidus line of Ni self-fusing alloy powder.
A sintered metal body is obtained by sintering at 1120°C for 20 minutes. As a comparative example, a cylindrical molded body having the same dimensions as above was molded using a mixed powder consisting of 91% by weight of the Ni self-fusing alloy powder and 9% by weight of the W powder, and 1.5% by weight of the synthetic resin binder. , a metal sintered body is obtained under the same sintering conditions as above. As a comparative example, a cylindrical molded body having the same dimensions as above was molded using a mixed powder consisting of 69% by weight of the Ni self-fusing alloy powder and 31% by weight of the W powder, and 1.5% by weight of the synthetic resin binder. Then, a metal sintered body is obtained under the same sintering conditions as above. Shape retention, dimensional change, and sintering strength of each metal sintered body were investigated, and the results shown in the table were obtained.
【表】
上記表から明らかなように、本発明により得ら
れる焼結体は、前記実施例同様に僅かな膨脹量
を示すのみで寸法精度および形状維持性が良好で
ある。
Ｃ 発明の効果
第１発明によれば、Ni自溶性合金粉末に、そ
れよりも融点の高い特定の高融点金属粉末を特定
量混合するので、Ni自溶性合金粉末を1100〜
1180℃、即ち、その合金の液相線を超えた温度で
焼結しても、Ni自溶性合金の流特が高融点金属
粉末により妨げられて、形状維持性および寸法精
度の良好な金属焼結体を得ることができる。また
Ni自溶性合金相互間の結合性が良好である上、
前記のように特定の高融点金属粉末を用いること
によつて、その金属とNi自溶性合金との絡み合
いを十分に発生させることができると共にそれら
の溶着性を向上させることができ、これにより高
強度な金属焼結体を得ることができる。
さらに、Ni自溶性合金粉末と高融点金属粉末
との混合粉末に特定量の合成樹脂バインダを混練
するので、成形圧力が低くても形状維持性の良い
成形体を得ることができ、延いては形態上の欠陥
がなく、且つ種々の形態を有する金属焼結体を得
ることができる。
第２発明によれば、前記効果に加え、耐火物製
シエル層よりなるバツクアツプにより金属焼結体
の寸法変化を抑制して、寸法精度をさらに良好に
することができる。また残留ガスに起因した金属
焼結体の腐食といつた問題を回避して高品質な金
属焼結体を得ることができる。[Table] As is clear from the above table, the sintered body obtained according to the present invention exhibits only a small amount of expansion and has good dimensional accuracy and shape retention, similar to the examples described above. C. Effects of the Invention According to the first invention, since a specific amount of a specific high-melting point metal powder having a higher melting point than Ni self-fusing alloy powder is mixed with the Ni self-fusing alloy powder, Ni self-fusing alloy powder is
Even when sintered at 1180°C, that is, above the liquidus line of the alloy, the flow characteristics of the Ni self-fusing alloy are hindered by the high melting point metal powder, resulting in metal sintering with good shape retention and dimensional accuracy. You can get a solid body. Also
In addition to having good bonding properties between Ni self-fusing alloys,
As mentioned above, by using a specific high-melting point metal powder, it is possible to sufficiently generate entanglement between the metal and the Ni self-fluxing alloy, and to improve their weldability. A strong metal sintered body can be obtained. Furthermore, since a specific amount of synthetic resin binder is kneaded into the mixed powder of Ni self-fusing alloy powder and high melting point metal powder, it is possible to obtain a molded body with good shape retention even at low molding pressure. Metal sintered bodies with no morphological defects and having various morphologies can be obtained. According to the second invention, in addition to the above-mentioned effects, dimensional changes in the metal sintered body can be suppressed by the backup made of the refractory shell layer, and dimensional accuracy can be further improved. Further, problems such as corrosion of the metal sintered body caused by residual gas can be avoided, and a high quality metal sintered body can be obtained.
第１図は本発明により得られた金属焼結体の金
属組織を示す顕微鏡写真図、第２図は焼結温度と
寸法変化の関係を示すグラフである。
FIG. 1 is a microscopic photograph showing the metal structure of a metal sintered body obtained according to the present invention, and FIG. 2 is a graph showing the relationship between sintering temperature and dimensional change.
Claims (1)
末、Ｗ粉末およびステンレス鋼粉末から選択され
る少なくとも一種の高融点金属粉末10〜30重量％
とを混合して混合粉末を得る工程と；該混合粉末
に１〜10重量％の合成樹脂バインダを混練した物
を用いて所定の形状を有する成形体を得る工程
と；該成形体を、1100〜1180℃にて焼結する工程
と；を用いることを特徴とする金属焼結体の製造
方法。 ２ Ni自溶性合金粉末70〜90重量％と、Mo粉
末、Ｗ粉末およびステンレス鋼粉末から選択され
る少なくとも一種の高融点金属粉末10〜30重量％
とを混合して混合粉末を得る工程と；該混合粉末
に１〜10重量％の合成樹脂バインダを混練した物
を用いて所定の形状を有する成形体を得る工程
と；該成形体を、それの全表面を微細な連続気孔
を持つ耐火物製シエル層よりなるバツクアツプに
より覆つた状態で1100〜1180℃にて焼結する工程
と；を用いることを特徴とする金属焼結体の製造
方法。[Claims] 1 Ni self-fusing alloy powder, 70 to 90% by weight, and at least one high melting point metal powder selected from Mo powder, W powder, and stainless steel powder, 10 to 30% by weight
A step of kneading the mixed powder with 1 to 10% by weight of a synthetic resin binder to obtain a molded body having a predetermined shape; A method for producing a metal sintered body, comprising: sintering at ~1180°C. 2 70 to 90% by weight of Ni self-fusing alloy powder and 10 to 30% by weight of at least one kind of high melting point metal powder selected from Mo powder, W powder, and stainless steel powder
A step of kneading the mixed powder with 1 to 10% by weight of a synthetic resin binder to obtain a molded body having a predetermined shape; A method for producing a metal sintered body, comprising the steps of: sintering at 1100 to 1180°C while the entire surface of the metal sintered body is covered with a backup made of a refractory shell layer having fine continuous pores.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11792884A JPS60262904A (en) | 1984-06-08 | 1984-06-08 | Manufacture of metallic sintered body |
| US06/723,030 US4608317A (en) | 1984-04-17 | 1985-04-15 | Material sheet for metal sintered body and method for manufacturing the same and method for manufacturing metal sintered body |
| BR8501806A BR8501806A (en) | 1984-04-17 | 1985-04-16 | PROCESS FOR THE MANUFACTURE OF A SINTERIZED METAL BODY AND MATERIAL SHEET FOR A SINTERIZED METAL BODY AND PROCESS FOR THE MANUFACTURE OF A MATERIAL SHEET FOR A SINTERIZED METAL BODY |
| BE2/60665A BE902203A (en) | 1984-04-17 | 1985-04-16 | MATERIAL LAYER FOR SINTERED METAL BODY AND METHOD FOR MANUFACTURING IT AND METHOD FOR MANUFACTURING A SINTERED METAL BODY |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11792884A JPS60262904A (en) | 1984-06-08 | 1984-06-08 | Manufacture of metallic sintered body |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS60262904A JPS60262904A (en) | 1985-12-26 |
| JPH0220683B2 true JPH0220683B2 (en) | 1990-05-10 |
Family
ID=14723667
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11792884A Granted JPS60262904A (en) | 1984-04-17 | 1984-06-08 | Manufacture of metallic sintered body |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS60262904A (en) |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5092209A (en) * | 1973-12-19 | 1975-07-23 | ||
| JPS5228090A (en) * | 1975-08-26 | 1977-03-02 | Tei Kitsushiyu Isutoban | Method of trueing diamond grinding wheel |
| JPS5435564A (en) * | 1977-08-26 | 1979-03-15 | Iseki & Co Ltd | Brake device for winding transmission mechanism |
| AU561663B2 (en) * | 1982-05-28 | 1987-05-14 | General Electric Company | Homogeneous superalloy powder mixture for the repair of nickel and cobalt superalloy articles |
| JPS6089503A (en) * | 1983-10-21 | 1985-05-20 | Toshiba Mach Co Ltd | Coating method of wear resistant material |
-
1984
- 1984-06-08 JP JP11792884A patent/JPS60262904A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS60262904A (en) | 1985-12-26 |
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