JP4532793B2 - Sintering aid for aluminum-containing copper-based alloy powder, and sintering alloy powder containing the same - Google Patents
Sintering aid for aluminum-containing copper-based alloy powder, and sintering alloy powder containing the same Download PDFInfo
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Description
【０００１】
【発明の属する技術分野】
本発明は、アルミニウム青銅やアルミニウム黄銅等のアルミニウム含有銅系合金粉を焼結するための焼結助剤に関する。また本発明は、この焼結助剤を含む焼結用のアルミニウム含有銅系合金粉に関する。
【０００２】
【従来の技術】
アルミニウム青銅やアルミニウム黄銅等のアルミニウム含有銅系合金は、優れた機械的特定および耐食性を有しており、種々の産業製品に用いられている。このアルミニウム含有銅系合金の加工方法の一つとして、従来より、合金粉を焼結する粉末冶金法が知られている。
しかしながら、一般的に、アルミニウム含有銅系合金粉は、焼結時にその表面に生成する酸化アルミニウムの皮膜が焼結を著しく阻害するので、十分な強度を有する焼結体を得ることができない。
そこで、従来より、アルミニウム含有銅系合金粉の焼結を促進するための焼結助剤が検討されてきた。
【０００３】
例えば、特公昭４８−２８２４６号には、アルカリ金属又はアルカリ土類金属のフッ化物から選ばれた１種又は２種以上から成るアルミニウム含有青銅合金粉のための焼結助剤が開示されている。
しかしながら、特公昭４８−２８２４６号に記載の焼結助剤のうち、アルカリ金属のフッ化物は、焼結時に合金粉の表面に生成する酸化アルミニウムの皮膜を分解して焼結を促進するが、アルカリ金属のフッ化物は腐食性が高く、焼結体や焼結炉を損傷させる。
【０００４】
一方、アルカリ土類金属のフッ化物は、極めて安定な化合物であり、その融点も高く、例えばフッ化カルシウムの融点は１３６０℃であり、またフッ化マグネシウムの融点は１２６０である。従って、アルカリ土類金属のフッ化物を単独でアルミニウム含有銅系合金粉の焼結助剤として添加しても、その焼結温度ではこれらのフッ化物は溶融することはないので、合金粉の表面に生成した酸化アルミニウムと反応し難く、その焼結を十分に促進することは困難である。さらに、上記のように、アルカリ土類金属のフッ化物は、融点も高く、酸化アルミニウムとの反応も進み難いので、製品である焼結体に焼結助剤が残存しやすい。
【０００５】
また、特許第２６８０８３２号には、Ｚｎを３０〜５０ｗｔ％含み残部がＣｕである−２８０メッシュのＣｕ−Ｚｎ合金粉と、Ａｌを３０〜５０ｗｔ％含み残部がＣｕである−２８０メッシュＣｕ−Ａｌ合金粉と−２５０メッシュのＣｕ粉とを所定の割合で配合し、それに焼結助剤としてフッ化物を０．０５〜１ｗｔ％混合し、得られた混合物を成形した圧粉体を８５０℃〜９５０℃で焼結し、ついで、得られた焼結部材を５００〜８５０℃に加熱後１０３℃／ｓ以上の冷却速度で急冷し、その後焼結部材に１〜３％の残留歪が生じる範囲で引張応力を加え、再度５００〜８５０℃に加熱後、１０３℃／ｓ以上の冷却速度で急冷することを特徴とするＣｕ−Ｚｎ−Ａｌ焼結超弾性合金の製造方法が記載されている。
【０００６】
しかしながら、特許第２６８０８３２号に記載のフッ化アルミニウムは、超弾性のアルミニウム含有黄銅合金を製造するために所定割合で混合された銅亜鉛合金粉と銅アルミニウム合金粉との混合粉に対しては有効な焼結助剤となり得るが、一般的には、フッ化アルミニウム単独ではアルミニウム含有銅系合金粉の焼結を十分に促進することはできない。
即ち、フッ化アルミニウムもそれ自身は安定な化合物であるが、昇華性を有しているため、アルミニウム含有銅系合金粉に単独で添加されたフッ化アルミニウムは、その焼結時において昇華し、合金粉の表面を保護して酸化アルミニウムの生成を防止する役割を果たす。しかしながら蒸気圧が高いため、気化したフッ化アルミニウムは比較的早期に系外に排出されてしまう。従って、フッ化アルミニウム単独では、アルミニウム含有銅系合金粉の焼結を十分に促進することはできない。
【０００７】
【発明が解決しようとする課題】
そこで本発明は、焼結体や焼結炉を腐食することなく、アルミニウム含有銅系合金粉の焼結を更に促進することができる焼結助剤、並びにこれを含む焼結用合金粉を提供することを課題とする。
【０００８】
【課題を解決するための手段】
本発明者らは上記の課題を解決すべく種々検討を重ねた結果、フッ化アルミニウムに、フッ化カルシウムおよびフッ化マグネシウムから選択される少なくとも１種類を１〜７０重量％混合してなるアルミニウム含有銅系合金粉のための焼結助剤とすることによって解決されることを見出した。
特に、上記の焼結助剤を０．０２〜０．５重量％の範囲で含むアルミニウム含有銅系合金粉は、優れた機械的強度と耐腐食性とを備えた焼結体となる。
以下に、本発明を更に詳細に説明する。
【０００９】
【発明の実施の形態】
即ち、本発明の焼結助剤は、フッ化アルミニウムと、フッ化カルシウムおよびフッ化マグネシウムから選択される少なくとも１種類とから成る混合物である。このような混合物からなる焼結助剤は、８５０〜９００℃程度の融点を有することに加え、その蒸気圧もフッ化アルミニウム単体の場合に比べて低くなる。一般に、アルミニウム含有銅系合金粉の焼結温度は８５０〜９５０℃であるので、この焼結温度で本発明の焼結助剤は溶融しながら徐々に蒸発し、アルミニウム含有銅系合金粉の表面を保護して酸化アルミニウムの生成を抑制する。しかもフッ化アルミニウム単体の場合よりも蒸気圧が低いため、上記合金粉表面を保護する効果が持続する。これによって、合金粉は、その表面に生成する酸化アルミニウムの皮膜によって阻害されることなく、強固に焼結して、所定の機械的強度および耐腐食性を有する焼結体となる。しかも、本発明の焼結助剤は、最終的にはフッ化アルミニウム単独の場合と同様に、蒸発・揮散するので、製品としての焼結体中には焼結助剤は殆ど残存しない。
【００１０】
このように、本発明による焼結助剤は、合金粉の焼結温度においては液体となって合金紛との接触を向上するので、特公昭４８−２８２４６号に記載のアルカリ土類金属のフッ化物の単体からなる焼結助剤や、特許第２６８０８３２号に記載のフッ化アルミニウムの単体からなる焼結助剤よりも、合金粉の焼結を遥かに促進する。
【００１１】
本発明によると、フッ化アルミニウムとして、５０μｍを超えない粒径を有する粉末を使用することが好ましい。
また、フッ化カルシウムおよびフッ化マグネシウムとしても、同じく５０μｍを超えない粒径を有する粉末を使用することが好ましい。
【００１２】
フッ化アルミニウム中に含まれるフッ化カルシウムおよびフッ化マグネシウムの合計量は、１〜７０重量％、更には５〜５０重量％、最適には１０〜３０重量％である。上記の範囲で混合された本発明の焼結助剤は、酸化アルミニウムの生成抑制効果が大きく、８５０〜９００℃程度の融点を有するので、アルミニウム含有銅系合金粉の焼結助剤として特に好ましい。
【００１３】
本発明によると、アルミニウム含有銅系合金粉の組成については、特に限定されず、従来周知のアルミニウム青銅合金およびアルミニウム黄銅合金などの粉末の焼結に有用である。
合金中のアルミニウム含有量も特に限定されないが、高強度で高耐食性の焼結体を得るためには、合金中のアルミニウム含有量は１〜１３重量％になっていることが好ましい。
【００１４】
本発明で使用される粉末状の焼結用合金は、更なる他の金属成分を含んでいてもよい。
例えば、アルミニウム青銅合金は、１〜１３重量％のアルミニウム、および残部の銅から成る合金であるが、更に鉄、ニッケルおよびマンガンから選択される金属を、それぞれ１〜１０重量％含んでいてもよい。
またアルミニウム黄銅合金は、１〜１３重量％のアルミニウム、１０〜４０重量％の亜鉛、および残部の銅からなる合金であるが、更に、鉄、ニッケル、マンガンおよび錫から選択される金属を、それぞれ０．５〜５重量％含んでいてもよい。
【００１５】
また、本発明において使用される焼結用合金は、単一組成を有する単一粉であっても、２種以上の合金粉を混合した混合粉であってもよい。なお、一般的に、機械部品のように高密度が要求される用途には単一粉が適している。また、軸受などの低密度の用途には、例えば電解法で調製された銅粉のような低見掛密度で成形性に優れた粉末を含む混合粉が適している。
【００１６】
本発明によると、焼結用合金紛中には、上記の焼結助剤が、０．０２〜０．５重量％添加されている。これによって、焼結時に、焼結助剤が合金粉の表面を覆って酸化アルミニウムの生成を阻害する。
【００１７】
更に、本発明において使用される焼結用合金粉の粒度も特に限定されないが、通常の粉末冶金におけるハンドリング性の見地より、−１５０〜−７５μｍ程度の粒度を有する合金粉の使用が好ましい。
【００１８】
本発明の焼結用合金粉は、一般的に、１００〜１０００ＭＰａで金型成型した後に、水素や窒素等の非酸化性雰囲気中での焼結により、優れた機械的特性および耐腐食性を有する焼結体となる。
【００１９】
焼結は、焼結助剤の融点よりも高く、基質である合金の融点よりも低い温度で実施される。
【００２０】
次に本発明を実施例に基づいて更に詳細に説明する。
【００２１】
（実施例１）
噴霧法で製造した粒度−１５０μｍの銅‐７重量％アルミニウム合金粉を用意した。この銅アルミニウム合金粉中に、表１に示す焼結助剤を添加して十分に混合した。なお、銅アルミニウム合金粉中に占める焼結助剤の割合は０．１重量％とした。
そして、この銅アルミニウム合金粉を、成型圧力５００ＭＰａで成型して、外径２０ｍｍ、内径１２ｍｍおよび高さ１０ｍｍの円筒形状の成型物を得た。この成型物を、ステンレス製ボートに載せて水素気流中にて９５０℃で３０ｍｉｎ間加熱して焼結体を得た。得られた焼結体について測定した密度、硬さおよび圧環強さを表１に併せて示す。
【００２２】
表１に示す結果より明らかなように、本発明に従う焼結助剤１〜２１を添加して焼結された焼結体は、本発明の範囲から外れる焼結助剤２２〜２７および３１〜３６を添加して焼結された焼結体に比べて、より高い密度、硬さおよび圧環強さを示している。従って、本発明による焼結助剤が、従来の焼結助剤よりも、銅アルミニウム合金粉の焼結を促進することが証明された。
【００２３】
また、焼結助剤１〜２７、および３１〜３４の場合には、ステンレス製ボートや得られた焼結体に目立った腐食は検出されなかったが、フッ化ナトリウムまたはフッ化カリウムからなる焼結助剤３５および３６を用いた場合には、ステンレス製ボートや焼結体に明らかな腐食が観察された。
【００２４】
【表１】
（実施例２）
電解法で製造した粒度−１５０μｍの銅粉と、搗砕法で製造した粒度−６３μｍの銅‐５０重量％アルミニウム合金粉との混合粉を用意した。この混合粉の混合比率は、重量比で、銅粉：銅アルミニウム合金粉＝８６：１４である。この混合粉中に表２に示す焼結助剤を添加して十分に混合した。なお、混合粉中に占める焼結助剤の割合は０．１重量％とした。
この混合粉を、成型圧力５００ＭＰａで成型して、外径２０ｍｍ、内径１２ｍｍおよび高さ１０ｍｍの円筒形状の成型物を得た。そして、この成型物を、ステンレス製ボートに載せて水素気流中にて９５０℃で３０ｍｉｎ間加熱して焼結体を得た。得られた焼結体について測定した密度、硬さおよび圧環強さを表２に併せて示す。
【００２６】
表２に示す結果より明らかなように、本発明に従う焼結助剤１〜２１を添加して焼結された焼結体は、本発明の範囲から外れる焼結助剤２２〜２７および３１〜３６を添加して焼結された焼結体に比べて、より高い密度、硬さおよび圧環強さを示している。従って、本発明による焼結助剤が、従来の焼結助剤よりも、銅粉と銅アルミニウム合金粉との混合粉に対する焼結を促進することが証明された。
【００２７】
また、焼結助剤１〜２７、および３１〜３４の場合には、ステンレス製ボートや得られた焼結体に目立った腐食は検出されなかったが、フッ化ナトリウムまたはフッ化カリウムからなる焼結助剤３５および３６を用いた場合には、ステンレス製ボートや焼結体に明らかな腐食が観察された。
【００２８】
【表２】
（実施例３）
噴霧法で製造した粒度１００μｍの銅‐９重量％アルミニウム‐２重量％ニッケル‐３．５重量％鉄の合金粉を用意した。このアルミニウム青銅粉中に、表３に示す焼結助剤を添加して十分に混合した。なお、このアルミニウム青銅粉中に占める焼結助剤の割合は０．１重量％とした。
このアルミニウム青銅粉を、成型圧力５００ＭＰａで成型して、外径２０ｍｍ、内径１２ｍｍおよび高さ１０ｍｍの円筒形状の成型物を得た。この成型物を、ステンレス製ボートに載せて水素気流中にて９５０℃で３０ｍｉｎ間加熱して焼結体を得た。得られた焼結体について測定した密度、硬さおよび圧環強さを表３に併せて示す。
【００３０】
表３に示す結果より明らかなように、本発明に従う焼結助剤１〜２１を添加して焼結された焼結体は、本発明の範囲から外れる焼結助剤２２〜２７および３１〜３６を添加して焼結された焼結体に比べて、より高い密度、硬さおよび圧環強さを示している。従って、本発明による焼結助剤が、従来の焼結助剤よりも、アルミニウム青銅粉の焼結を促進することが証明された。
【００３１】
また、焼結助剤１〜２７、および３１〜３４の場合には、ステンレス製ボートや得られた焼結体に目立った腐食は検出されなかったが、フッ化ナトリウムまたはフッ化カリウムからなる焼結助剤３５および３６を用いた場合には、ステンレス製ボートや焼結体に明らかな腐食が観察された。
【００３２】
【表３】
（実施例４）
噴霧法で製造した粒度−１００μｍの銅‐３５重量％亜鉛‐３重量％アルミニウムの合金粉を用意した。このアルミニウム黄銅粉中に、表４に示す焼結助剤を添加して十分に混合した。なお、このアルミニウム黄銅粉中に占める焼結助剤の割合は０．１重量％とした。
焼結助剤を添加したアルミニウム黄銅粉を、成型圧力５００ＭＰａで成型して、外径２０ｍｍ、内径１２ｍｍおよび高さ１０ｍｍの円筒形状の成型物を得た。この成型物を、ステンレス製ボートに載せて水素気流中にて９００℃で３０ｍｉｎ間加熱して焼結体を得た。得られた焼結体について測定した密度、硬さおよび圧環強さを表４に併せて示す。
【００３４】
表４に示す結果より明らかなように、本発明に従う焼結助剤１〜２１を添加して焼結された焼結体は、本発明の範囲から外れる焼結助剤２２〜２７および３１〜３６を添加して焼結された焼結体に比べて、より高い密度、硬さおよび圧環強さを示している。従って、本発明による焼結助剤が、従来の焼結助剤よりも、アルミニウム黄銅粉の焼結を促進することが証明された。
【００３５】
また、焼結助剤１〜２７、および３１〜３４の場合には、ステンレス製ボートや得られた焼結体に目立った腐食は検出されなかったが、フッ化ナトリウムまたはフッ化カリウムからなる焼結助剤３５および３６を用いた場合には、ステンレス製ボートや焼結体に明らかな腐食が観察された。
【００３６】
【表４】
BACKGROUND OF THE INVENTION
The present invention relates to a sintering aid for sintering aluminum-containing copper-based alloy powders such as aluminum bronze and aluminum brass. The present invention also relates to an aluminum-containing copper-based alloy powder for sintering containing this sintering aid.
[0002]
[Prior art]
Aluminum-containing copper-based alloys such as aluminum bronze and aluminum brass have excellent mechanical identification and corrosion resistance, and are used in various industrial products. As one of processing methods for this aluminum-containing copper-based alloy, a powder metallurgy method for sintering an alloy powder has been conventionally known.
However, in general, the aluminum-containing copper-based alloy powder cannot obtain a sintered body having sufficient strength because the aluminum oxide film formed on the surface of the aluminum-containing copper powder significantly inhibits the sintering.
Therefore, conventionally, a sintering aid for promoting the sintering of the aluminum-containing copper-based alloy powder has been studied.
[0003]
For example, Japanese Patent Publication No. 48-28246 discloses a sintering aid for aluminum-containing bronze alloy powder composed of one or more selected from alkali metal or alkaline earth metal fluorides. .
However, among the sintering aids described in Japanese Patent Publication No. 48-28246, the alkali metal fluoride promotes the sintering by decomposing the aluminum oxide film formed on the surface of the alloy powder during sintering. Alkali metal fluorides are highly corrosive and damage sintered bodies and sintering furnaces.
[0004]
On the other hand, an alkaline earth metal fluoride is a very stable compound and has a high melting point. For example, calcium fluoride has a melting point of 1360 ° C., and magnesium fluoride has a melting point of 1260. Therefore, even if the alkaline earth metal fluoride is added alone as a sintering aid for the aluminum-containing copper-based alloy powder, the fluoride does not melt at the sintering temperature. It is difficult to react with the aluminum oxide produced in this, and it is difficult to sufficiently promote the sintering. Furthermore, as described above, the alkaline earth metal fluoride has a high melting point and does not easily react with aluminum oxide, so that the sintering aid tends to remain in the sintered product.
[0005]
Japanese Patent No. 2680832 discloses a -280 mesh Cu-Zn alloy powder containing 30 to 50 wt% Zn and the balance being Cu, and a -280 mesh Cu-Al powder containing 30 to 50 wt% Al and the balance being Cu. Alloy powder and -250 mesh Cu powder are blended at a predetermined ratio, and 0.05 to 1 wt% of fluoride is mixed as a sintering aid thereto, and a green compact obtained by molding the obtained mixture is 850 ° C to Sintered at 950 ° C., and then the obtained sintered member was heated to 500 to 850 ° C. and then rapidly cooled at a cooling rate of 103 ° C./s or more, and thereafter, a residual strain of 1 to 3% was generated in the sintered member A method for producing a Cu—Zn—Al sintered superelastic alloy is described, in which a tensile stress is applied and heated again to 500 to 850 ° C. and then rapidly cooled at a cooling rate of 103 ° C./s or more.
[0006]
However, the aluminum fluoride described in Japanese Patent No. 2680832 is effective for mixed powder of copper zinc alloy powder and copper aluminum alloy powder mixed at a predetermined ratio to produce a superelastic aluminum-containing brass alloy. In general, aluminum fluoride alone cannot sufficiently promote the sintering of aluminum-containing copper-based alloy powder.
That is, aluminum fluoride itself is a stable compound, but because it has sublimation properties, aluminum fluoride added alone to the aluminum-containing copper-based alloy powder sublimates during the sintering, It plays the role of protecting the surface of the alloy powder and preventing the formation of aluminum oxide. However, since the vapor pressure is high, the vaporized aluminum fluoride is discharged out of the system relatively early. Therefore, aluminum fluoride alone cannot sufficiently promote the sintering of the aluminum-containing copper-based alloy powder.
[0007]
[Problems to be solved by the invention]
Therefore, the present invention provides a sintering aid capable of further promoting the sintering of the aluminum-containing copper-based alloy powder without corroding the sintered body or the sintering furnace, and a sintering alloy powder containing the same. The task is to do.
[0008]
[Means for Solving the Problems]
As a result of various studies to solve the above-mentioned problems, the inventors of the present invention include aluminum containing 1 to 70% by weight of aluminum fluoride mixed with at least one selected from calcium fluoride and magnesium fluoride. It has been found that this problem can be solved by using a sintering aid for copper alloy powder.
In particular, the aluminum-containing copper-based alloy powder containing the above sintering aid in the range of 0.02 to 0.5% by weight is a sintered body having excellent mechanical strength and corrosion resistance.
Hereinafter, the present invention will be described in more detail.
[0009]
DETAILED DESCRIPTION OF THE INVENTION
That is, the sintering aid of the present invention is a mixture composed of aluminum fluoride and at least one selected from calcium fluoride and magnesium fluoride. In addition to having a melting point of about 850 to 900 ° C., the sintering aid made of such a mixture has a lower vapor pressure than that of a single aluminum fluoride. In general, since the sintering temperature of the aluminum-containing copper-based alloy powder is 850 to 950 ° C., the sintering aid of the present invention gradually evaporates while melting, and the surface of the aluminum-containing copper-based alloy powder To prevent the formation of aluminum oxide. Moreover, since the vapor pressure is lower than in the case of aluminum fluoride alone, the effect of protecting the alloy powder surface is sustained. Thus, the alloy powder is strongly sintered without being inhibited by the aluminum oxide film formed on the surface thereof, and becomes a sintered body having a predetermined mechanical strength and corrosion resistance. In addition, since the sintering aid of the present invention finally evaporates and volatilizes as in the case of aluminum fluoride alone, almost no sintering aid remains in the sintered product as a product.
[0010]
Thus, since the sintering aid according to the present invention becomes liquid at the sintering temperature of the alloy powder and improves the contact with the alloy powder, the alkaline earth metal foot described in Japanese Patent Publication No. 48-28246. The sintering of the alloy powder is further promoted than the sintering aid made of a simple substance of a chemical compound or the sintering aid made of a simple substance of aluminum fluoride described in Japanese Patent No. 2680832.
[0011]
According to the invention, it is preferable to use a powder having a particle size not exceeding 50 μm as aluminum fluoride.
Moreover, it is preferable to use the powder which has a particle size which does not exceed 50 micrometers similarly as calcium fluoride and magnesium fluoride.
[0012]
The total amount of calcium fluoride and magnesium fluoride contained in the aluminum fluoride is 1 to 70% by weight, more preferably 5 to 50% by weight, and most preferably 10 to 30% by weight. The sintering aid of the present invention mixed in the above range has a great effect of suppressing the formation of aluminum oxide and has a melting point of about 850 to 900 ° C., and thus is particularly preferable as a sintering aid for aluminum-containing copper-based alloy powders. .
[0013]
According to the present invention, the composition of the aluminum-containing copper-based alloy powder is not particularly limited, and is useful for sintering powders such as conventionally known aluminum bronze alloys and aluminum brass alloys.
The aluminum content in the alloy is not particularly limited, but in order to obtain a sintered body having high strength and high corrosion resistance, the aluminum content in the alloy is preferably 1 to 13% by weight.
[0014]
The powdery sintering alloy used in the present invention may further contain other metal components.
For example, the aluminum bronze alloy is an alloy composed of 1 to 13% by weight of aluminum and the balance of copper, but may further contain 1 to 10% by weight of a metal selected from iron, nickel and manganese, respectively. .
The aluminum brass alloy is an alloy composed of 1 to 13% by weight of aluminum, 10 to 40% by weight of zinc, and the balance of copper, and further, a metal selected from iron, nickel, manganese and tin, You may contain 0.5 to 5weight%.
[0015]
The sintering alloy used in the present invention may be a single powder having a single composition or a mixed powder in which two or more kinds of alloy powders are mixed. In general, a single powder is suitable for applications where high density is required, such as mechanical parts. For low-density applications such as bearings, mixed powder containing powder with low apparent density and excellent moldability, such as copper powder prepared by electrolysis, is suitable.
[0016]
According to the present invention, 0.02 to 0.5% by weight of the sintering aid is added to the sintering alloy powder. As a result, during sintering, the sintering aid covers the surface of the alloy powder and inhibits the production of aluminum oxide.
[0017]
Furthermore, although the particle size of the sintering alloy powder used in the present invention is not particularly limited, the use of alloy powder having a particle size of about -150 to -75 μm is preferred from the viewpoint of handling properties in ordinary powder metallurgy.
[0018]
The alloy powder for sintering of the present invention generally exhibits excellent mechanical properties and corrosion resistance by being molded in a non-oxidizing atmosphere such as hydrogen and nitrogen after being molded at 100 to 1000 MPa. It becomes the sintered compact which has.
[0019]
Sintering is performed at a temperature higher than the melting point of the sintering aid and lower than the melting point of the alloy that is the substrate.
[0020]
Next, the present invention will be described in more detail based on examples.
[0021]
Example 1
A copper-7 wt% aluminum alloy powder having a particle size of −150 μm produced by a spraying method was prepared. In this copper aluminum alloy powder, the sintering aid shown in Table 1 was added and mixed well. The proportion of the sintering aid in the copper aluminum alloy powder was 0.1% by weight.
The copper aluminum alloy powder was molded at a molding pressure of 500 MPa to obtain a cylindrical molded product having an outer diameter of 20 mm, an inner diameter of 12 mm, and a height of 10 mm. This molded product was placed on a stainless steel boat and heated in a hydrogen stream at 950 ° C. for 30 minutes to obtain a sintered body. The density, hardness, and crushing strength measured for the obtained sintered body are also shown in Table 1.
[0022]
As is apparent from the results shown in Table 1, the sintered bodies sintered by adding the sintering aids 1 to 21 according to the present invention are sintered aids 22 to 27 and 31 to 31 which are out of the scope of the present invention. Compared with the sintered body sintered by adding 36, higher density, hardness and crushing strength are shown. Therefore, it has been proved that the sintering aid according to the present invention accelerates the sintering of the copper aluminum alloy powder than the conventional sintering aid.
[0023]
In the case of sintering aids 1-27 and 31-34, no noticeable corrosion was detected in the stainless steel boat or the obtained sintered body, but the sintering was made of sodium fluoride or potassium fluoride. When the binders 35 and 36 were used, obvious corrosion was observed on the stainless steel boat and the sintered body.
[0024]
[Table 1]
(Example 2)
A mixed powder of a copper powder having a particle size of −150 μm produced by an electrolytic method and a copper-50 wt% aluminum alloy powder having a particle size of −63 μm produced by a grinding method was prepared. The mixing ratio of the mixed powder is copper powder: copper aluminum alloy powder = 86: 14 in weight ratio. A sintering aid shown in Table 2 was added to the mixed powder and mixed thoroughly. The proportion of the sintering aid in the mixed powder was 0.1% by weight.
The mixed powder was molded at a molding pressure of 500 MPa to obtain a cylindrical molded product having an outer diameter of 20 mm, an inner diameter of 12 mm, and a height of 10 mm. Then, this molded product was placed on a stainless steel boat and heated in a hydrogen stream at 950 ° C. for 30 minutes to obtain a sintered body. Table 2 shows the density, hardness, and crushing strength measured for the obtained sintered body.
[0026]
As is clear from the results shown in Table 2, the sintered bodies sintered by adding the sintering aids 1 to 21 according to the present invention are sintered aids 22 to 27 and 31 to 31 which are out of the scope of the present invention. Compared with the sintered body sintered by adding 36, higher density, hardness and crushing strength are shown. Therefore, it was proved that the sintering aid according to the present invention promotes the sintering of the mixed powder of the copper powder and the copper aluminum alloy powder as compared with the conventional sintering aid.
[0027]
In the case of sintering aids 1-27 and 31-34, no noticeable corrosion was detected in the stainless steel boat or the obtained sintered body, but the sintering was made of sodium fluoride or potassium fluoride. When the binders 35 and 36 were used, obvious corrosion was observed on the stainless steel boat and the sintered body.
[0028]
[Table 2]
(Example 3)
An alloy powder of copper-9 wt% aluminum-2 wt% nickel-3.5 wt% iron with a particle size of 100 μm produced by the spray method was prepared. In this aluminum bronze powder, the sintering aid shown in Table 3 was added and mixed thoroughly. The proportion of the sintering aid in the aluminum bronze powder was 0.1% by weight.
This aluminum bronze powder was molded at a molding pressure of 500 MPa to obtain a cylindrical molded product having an outer diameter of 20 mm, an inner diameter of 12 mm, and a height of 10 mm. This molded product was placed on a stainless steel boat and heated in a hydrogen stream at 950 ° C. for 30 minutes to obtain a sintered body. The density, hardness and crushing strength measured for the obtained sintered body are also shown in Table 3.
[0030]
As is apparent from the results shown in Table 3, the sintered bodies sintered by adding the sintering aids 1 to 21 according to the present invention are sintered auxiliary materials 22 to 27 and 31 to 31 which are out of the scope of the present invention. Compared with the sintered body sintered by adding 36, higher density, hardness and crushing strength are shown. Therefore, it was proved that the sintering aid according to the present invention accelerates the sintering of aluminum bronze powder than the conventional sintering aid.
[0031]
In the case of sintering aids 1-27 and 31-34, no noticeable corrosion was detected in the stainless steel boat or the obtained sintered body, but the sintering was made of sodium fluoride or potassium fluoride. When the binders 35 and 36 were used, obvious corrosion was observed on the stainless steel boat and the sintered body.
[0032]
[Table 3]
Example 4
An alloy powder of copper-35 wt% zinc-3 wt% aluminum having a particle size of −100 μm and prepared by a spray method was prepared. A sintering aid shown in Table 4 was added to the aluminum brass powder and mixed thoroughly. The proportion of the sintering aid in the aluminum brass powder was 0.1% by weight.
Aluminum brass powder to which a sintering aid was added was molded at a molding pressure of 500 MPa to obtain a cylindrical molded product having an outer diameter of 20 mm, an inner diameter of 12 mm, and a height of 10 mm. This molded product was placed on a stainless steel boat and heated in a hydrogen stream at 900 ° C. for 30 minutes to obtain a sintered body. The density, hardness and crushing strength measured for the obtained sintered body are also shown in Table 4.
[0034]
As is apparent from the results shown in Table 4, the sintered bodies sintered by adding the sintering aids 1 to 21 according to the present invention are sintered aids 22 to 27 and 31 to 31 which are out of the scope of the present invention. Compared with the sintered body sintered by adding 36, higher density, hardness and crushing strength are shown. Therefore, it has been proved that the sintering aid according to the present invention promotes the sintering of aluminum brass powder than the conventional sintering aid.
[0035]
In the case of sintering aids 1-27 and 31-34, no noticeable corrosion was detected in the stainless steel boat or the obtained sintered body, but the sintering was made of sodium fluoride or potassium fluoride. When the binders 35 and 36 were used, obvious corrosion was observed on the stainless steel boat and the sintered body.
[0036]
[Table 4]
Claims (2)
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| Application Number | Priority Date | Filing Date | Title |
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| JP2001239184A JP4532793B2 (en) | 2001-08-07 | 2001-08-07 | Sintering aid for aluminum-containing copper-based alloy powder, and sintering alloy powder containing the same |
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| JP2001239184A JP4532793B2 (en) | 2001-08-07 | 2001-08-07 | Sintering aid for aluminum-containing copper-based alloy powder, and sintering alloy powder containing the same |
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS497106A (en) * | 1972-05-14 | 1974-01-22 | ||
| JPS52115708A (en) * | 1976-09-17 | 1977-09-28 | Fukuda Metal Foil Powder | Powder for production of sintered copper alloy |
| JPH01219062A (en) * | 1988-02-29 | 1989-09-01 | Toyota Motor Corp | Production of silicon nitride sintered body |
| JPH05286762A (en) * | 1992-04-10 | 1993-11-02 | Kurosaki Refract Co Ltd | Manufacture of polycrystalline transparent yag ceramic for solid laser |
| JPH05294724A (en) * | 1992-04-10 | 1993-11-09 | Kurosaki Refract Co Ltd | Production of polycrystalline transparent yag ceramic for solid laser |
-
2001
- 2001-08-07 JP JP2001239184A patent/JP4532793B2/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS497106A (en) * | 1972-05-14 | 1974-01-22 | ||
| JPS52115708A (en) * | 1976-09-17 | 1977-09-28 | Fukuda Metal Foil Powder | Powder for production of sintered copper alloy |
| JPH01219062A (en) * | 1988-02-29 | 1989-09-01 | Toyota Motor Corp | Production of silicon nitride sintered body |
| JPH05286762A (en) * | 1992-04-10 | 1993-11-02 | Kurosaki Refract Co Ltd | Manufacture of polycrystalline transparent yag ceramic for solid laser |
| JPH05294724A (en) * | 1992-04-10 | 1993-11-09 | Kurosaki Refract Co Ltd | Production of polycrystalline transparent yag ceramic for solid laser |
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