JPH05117719A - Production of sintered body having high strength and ductility - Google Patents
Production of sintered body having high strength and ductilityInfo
- Publication number
- JPH05117719A JPH05117719A JP30384491A JP30384491A JPH05117719A JP H05117719 A JPH05117719 A JP H05117719A JP 30384491 A JP30384491 A JP 30384491A JP 30384491 A JP30384491 A JP 30384491A JP H05117719 A JPH05117719 A JP H05117719A
- Authority
- JP
- Japan
- Prior art keywords
- sintered body
- ductility
- strength
- particles
- alloy
- 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.)
- Granted
Links
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【0001】[0001]
【産業上の利用分野】この発明は、W−Fe−Ni合金な
どからなる焼結体を温間加工して、高強度で、しかも高
延性の性質を有する加工材を得る、高強度高延性焼結体
の製造方法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 and high-ductility product which is obtained by hot working a sintered body made of a W-Fe-Ni alloy or the like to obtain a processed material having high strength and high ductility. The present invention relates to a method for manufacturing a sintered body.
【0002】[0002]
【従来の技術】焼結体の一つであるW−Fe−Ni合金
は、Wの性質を利用して、高強度で、高延性の材料とし
て、重錘や放射線遮蔽などの用途に使用されている。こ
の焼結体を製造する際には、一般に、図4に示すよう
に、重量%で90%〜97%のW粉末と残量のFeおよ
びNi粉末とを調製・混合し、これをCIP(冷間等方
加工プレス)などを用いて、所定の形状に加圧成形して
圧粉体とし、次いで圧粉体をFe−Ni合金の液相線温度
以上に加熱して、W粉末をFe−Ni合金で結合する焼結
を行う(予備焼結および本焼結)。得られた焼結体に
は、熱処理後、機削りなどの機械加工を行い、さらに用
途によっては、所定の機械的特性(強度の向上など)を
与えるために、400〜600℃に予熱してスウェージ
加工などの温間加工を行う。その後は、後熱処理を行っ
て焼結体を得ている。2. Description of the Related Art A W-Fe-Ni alloy, which is one of the sintered bodies, is used as a high-strength, high-ductility material by utilizing the property of W for applications such as weights and radiation shielding. ing. When manufacturing this sintered body, generally, as shown in FIG. 4, 90% to 97% by weight of W powder and the remaining Fe and Ni powders are prepared and mixed, and this is mixed with CIP ( Using a cold isostatic press, etc., the green compact is pressed into a predetermined shape to obtain a green compact, and then the green compact is heated to the liquidus temperature of the Fe-Ni alloy or higher, and the W powder is converted into the Fe powder. -Sintering with Ni alloy bonding (pre-sintering and main sintering). After the heat treatment, the obtained sintered body is subjected to machining such as machining, and further preheated to 400 to 600 ° C. in order to give predetermined mechanical properties (improvement of strength, etc.) depending on the application. Perform warm processing such as swaging. After that, a post heat treatment is performed to obtain a sintered body.
【0003】[0003]
【発明が解決しようとする課題】しかし、上記したスウ
ェージ加工において、塑性加工率が20%を超えるよう
な加工を行うと、得られた焼結体の延性が急激に低下す
るという問題点がある。しかも、この現象は、予熱温度
が高いほど顕著になる傾向もある。したがって、良好な
延性が要求される材料では、焼結体に対し、20%を超
えるような加工率でスウェージ加工を行うことは困難で
あり、このため、スウェージ加工により、十分に機械的
特性を向上させることができないという問題点がある。However, in the above swaging, when the plastic working rate exceeds 20%, there is a problem that the ductility of the obtained sintered body sharply decreases. .. Moreover, this phenomenon tends to be more remarkable as the preheating temperature is higher. Therefore, it is difficult to perform swage processing on a sintered body with a processing rate of more than 20% with a material that requires good ductility. Therefore, swage processing provides sufficient mechanical properties. There is a problem that it cannot be improved.
【0004】本願発明者らは、上記のスウェージ加工に
おける延性の低下について、種々、調査研究した結果、
スウェージ加工の際に、W粒子とバインダーになるFe
−Ni合金とが、様相の異なる塑性流動を起こすためで
はないかと考えた。 すなわち、W−Fe−Ni合金焼結
体は、W粒子の周囲に、高強度・高延性のNi /Fe 相
が溶け込んだ組織を有しており、これをスウェージ加工
すると、加工工具と焼結体との接触面における摩擦力に
より、W粒子とNi /Fe のいずれかが一方が優先的に
流動し、その結果、W粒子同士が接触する状態になるの
ではないかと考えた。特に20%を超える加工率で焼結
体を加工した際には、上記接触部が非常に多くなってい
ることが確認された。この接触部では、接触箇所が脆く
なっており、これが延性低下の原因になるのではないか
と考えられる。The inventors of the present invention have conducted various research studies on the reduction of ductility in the swaging process, and as a result,
Fe that becomes a binder with W particles during swaging
-It is thought that it may be because the Ni alloy causes plastic flow having a different aspect. That is, the W-Fe-Ni alloy sintered body has a structure in which a high-strength / high-ductility Ni / Fe phase is melted around W particles, and when this is swaged, it is sintered with a processing tool. It was considered that one of W particles and Ni / Fe would preferentially flow due to the frictional force on the contact surface with the body, resulting in the W particles contacting each other. In particular, it was confirmed that when the sintered body was processed at a processing rate of more than 20%, the number of contact portions was extremely large. At this contact portion, the contact portion is brittle, and it is considered that this may cause a decrease in ductility.
【0005】上記の点を、焼結体の硬度という点で検証
すると、図3に示すように、従来の方法で製造した加工
材(比較材)は、中心部に対し加工工具と接触する表層
側の硬度が高くなっており、これは、W粒子とFe−Ni
合金とで塑性流動が相違する結果、Fe−Ni合金の流動
が増加して硬度が増したものであり、延性の低下はそれ
に伴うW粒子同士の接触によると考えられる。本発明は
上記事情を背景としてなされたものであり、加工時にW
粒子同士の接触部分が発生するのを極力阻止して延性の
低下を防止することにより、高強度で高延性の焼結体を
得ることができる、高強度高延性焼結体の製造方法を提
供することを目的とする。When the above points are verified in terms of the hardness of the sintered body, as shown in FIG. 3, the processed material (comparative material) manufactured by the conventional method has a surface layer contacting the center part with the processing tool. The hardness of the side is higher, which is due to W particles and Fe-Ni.
As a result of the difference in plastic flow from the alloy, the flow of the Fe-Ni alloy increases and the hardness increases, and it is considered that the decrease in ductility is due to the contact between the W particles. The present invention has been made against the background of the above circumstances, and W
Provided is a method for producing a high-strength and high-ductility sintered body, which is capable of obtaining a high-strength and high-ductility sintered body by preventing generation of a contact portion between particles as much as possible and preventing a decrease in ductility. The purpose is to do.
【0006】[0006]
【課題を解決するための手段】上記課題を解決するため
本願発明の高強度高延性焼結体の製造方法は、高強度粉
末を焼結した焼結体の表面に、Cu を主体とする金属皮
膜を形成し、その後、前記焼結体を温間加工することを
特徴とする。In order to solve the above-mentioned problems, a method for producing a high-strength and high-ductility sintered body according to the present invention is such that a metal mainly containing Cu is formed on the surface of the sintered body obtained by sintering high-strength powder. A film is formed, and then the sintered body is warm-worked.
【0007】上記高強度粉末としては、例えばW粉末を
挙げることができるが、本願発明としてはこれに限定さ
れるものではなく、WCなどの他の高強度の粒子であっ
てもよい。この高強度粉末に対しては、上記W粒子で
は、Fe−Ni合金を用いるように、バインダーを添加
し、さらに、必要に応じてその他の添加剤を混合して、
焼結する。焼結体を得るまでの工程については本願発明
では特に限定するものではなく、常法などにより得られ
た焼結体が用いられる。Examples of the high-strength powder include W powder, but the present invention is not limited to this, and other high-strength particles such as WC may be used. With respect to the high-strength powder, in the W particles, a binder is added so that an Fe-Ni alloy is used, and further, if necessary, other additives are mixed,
Sinter. The process up to obtaining a sintered body is not particularly limited in the present invention, and a sintered body obtained by a conventional method or the like is used.
【0008】上記焼結体の表面に形成する金属皮膜は、
メッキや金属溶射などにより行うことができ、さらに、
これら方法に限定されるものではなく、要は、必要な金
属皮膜が形成されるものであればよく、その形成方法が
限定されるものではない。上記金属皮膜は、Cu を主体
とするものであればよく、さらには純銅が望ましい。ま
た、金属皮膜は、必ずしも焼結体の表面全面に形成する
必要はなく、少なくとも加工工具との接触面の必要な面
に形成するものであればよい。皮膜の厚さについては、
薄すぎては膜が破断する可能性があり、厚すぎては潤滑
性能が低下するので、5μm〜50μmの厚さが望まし
い。The metal coating formed on the surface of the sintered body is
It can be done by plating, metal spraying, etc.
The method is not limited to these methods, and the point is that the required metal film can be formed, and the forming method is not limited. The above-mentioned metal film may be mainly composed of Cu, and more preferably pure copper. Further, the metal film does not necessarily have to be formed on the entire surface of the sintered body, and may be formed on at least the necessary surface of the contact surface with the processing tool. For the film thickness,
If it is too thin, the film may break, and if it is too thick, the lubrication performance deteriorates, so a thickness of 5 μm to 50 μm is desirable.
【0009】皮膜形成後には、温間加工を行うべく焼結
体を予熱する。予熱温度は特に限定されるものではない
が、従来の方法よりも高い温度に加熱することができ、
その温度としては、450〜650℃が望ましい。その
理由は、450℃未満では、焼結体の変形能が低下し、
加工割れが発生する危険性があり、また650℃を超え
ると、焼結体に変態が生じ、延性が低下するためであ
る。また、温間加工の種別としても特に限定されない
が、一般には、スウェージ加工が行われる。この温間加
工後には、必要に応じて後熱処理を行う。After the film is formed, the sintered body is preheated for warm working. The preheating temperature is not particularly limited, but it can be heated to a higher temperature than the conventional method,
The temperature is preferably 450 to 650 ° C. The reason is that if the temperature is lower than 450 ° C., the deformability of the sintered body decreases,
This is because there is a risk that work cracking will occur, and if the temperature exceeds 650 ° C., transformation will occur in the sintered body and ductility will decrease. The type of warm working is not particularly limited, but generally swaging is performed. After the warm working, a post heat treatment is performed if necessary.
【0010】[0010]
【作用】すなわち、本願発明によれば、焼結体の表面に
形成された金属皮膜は、Cu 系金属特有の潤滑性能を有
しており、この状態で焼結体を温間加工することによ
り、加工工具と焼結体表面との潤滑性が向上し、両者間
の摩擦力が減少する。この結果、焼結体組織中の高強度
粒子やバインダーが均等に塑性流動し、高強度粒子の凝
集や高強度粒子同士による接触部の増加を極力阻止し
て、延性の低下を防止する。得られた焼結体は、十分に
加工されて強度が増し、また、延性の低下が防止される
ので、高強度で高延性の焼結体が得られる。In other words, according to the present invention, the metal coating formed on the surface of the sintered body has the lubrication performance peculiar to Cu-based metal, and the sintered body is warm-worked in this state. The lubricity between the processing tool and the surface of the sintered body is improved, and the frictional force between them is reduced. As a result, the high-strength particles and binder in the structure of the sintered body uniformly plastically flow, and the aggregation of the high-strength particles and the increase in the contact portion between the high-strength particles are prevented as much as possible, and the decrease in ductility is prevented. The obtained sintered body is sufficiently processed to increase its strength and is prevented from being reduced in ductility, so that a high-strength and highly ductile sintered body can be obtained.
【0011】[0011]
【実施例】図1の工程に従って、平均粒径約5μmのW
粉末93重量%と、平均粒径約5μmのNiおよびFe粉
末7重量%(ただし、Ni:Fe 重量比が7/3)とを
混合し、これを所定形状のゴム袋に充填して、靜水圧成
型によって圧縮して、50mm径の棒状圧粉体を得た。
この圧粉体には必要に応じて機械加工を施し、次いで、
予備焼結、本焼結を行った。予備焼結は、圧粉体を13
00〜1400℃に加熱し、4時間保持することにより
行い、本焼結は、予備焼結後の圧粉体を1460〜15
50℃に加熱し、1時間保持して行った。得られた焼結
体には、1100℃×10時間の熱処理を行い、その
後、必要な機削りを冷間で行った。EXAMPLE According to the process of FIG. 1, W having an average particle size of about 5 μm
93% by weight of the powder and 7% by weight of Ni and Fe powder having an average particle size of about 5 μm (however, the Ni: Fe weight ratio is 7/3) are mixed and filled in a rubber bag of a predetermined shape, It was compressed by hydraulic molding to obtain a rod-shaped green compact with a diameter of 50 mm.
If necessary, this green compact is machined, and then
Pre-sintering and main sintering were performed. For pre-sintering, 13
The sintering is performed by heating to 00 to 1400 ° C. and holding for 4 hours. The main sintering is 1460 to 15 for the pre-sintered green compact.
It heated at 50 degreeC and hold | maintained for 1 hour, and performed. The obtained sintered body was heat-treated at 1100 ° C. for 10 hours, and then subjected to necessary milling in the cold.
【0012】次いで、上記焼結体の側面全面に5μm以
上の厚さで純銅をメッキした。さらに、この焼結体の表
面に二硫化モリブデン系潤滑剤を塗布した後、550〜
600℃に加熱する予熱を行い、焼結体側面を圧縮する
スウェージ加工を、加工率10%、20%、25%でそ
れぞれ行って発明材を得た。また、比較例として、上記
した潤滑剤塗布焼結体に純銅のメッキを行うことをな
く、550〜600℃に加熱し、上記と同様にしてスウ
ェージ加工を行って比較材を得た。上記発明材および比
較材に、400〜600℃の後熱処理を行った。 上記
発明材および比較材に対し、引張り試験を行い、その試
験結果である、伸びおよび引張強さを図2に示した。ま
た、上記焼結体と同一の焼結体を用いて、これに油性黒
鉛系潤滑剤を塗布し、上記と同様にして発明法、比較例
について、加工率10%のスウェージ加工を行った。得
られた発明材および比較材について、径方向の深度を変
えてロックウェル硬さを測定し、その結果を図3に示し
た。Then, pure copper was plated on the entire side surface of the sintered body to a thickness of 5 μm or more. Further, after applying a molybdenum disulfide-based lubricant to the surface of this sintered body,
The invention material was obtained by performing pre-heating by heating to 600 ° C. and swaging for compressing the side surface of the sintered body at processing rates of 10%, 20%, and 25%, respectively. Further, as a comparative example, a comparative material was obtained by heating the above lubricant-coated sintered body to 550 to 600 ° C. without performing plating with pure copper and performing swaging in the same manner as above. The above-mentioned invention material and comparative material were post-heat-treated at 400 to 600 ° C. A tensile test was conducted on the above-mentioned invention material and comparative material, and the test results, elongation and tensile strength, are shown in FIG. Further, the same sintered body as the above-mentioned sintered body was used, and an oily graphite lubricant was applied thereto, and in the same manner as above, the invention method and the comparative example were swaged at a processing rate of 10%. The Rockwell hardness of each of the obtained invention material and comparative material was measured while changing the radial depth, and the results are shown in FIG.
【0013】図2から明らかなように、発明材は優れた
延性を有しているのに対し、比較材は、20%を超える
加工率では伸びが急激に低下しており、十分な延性が得
られなかった。また、図3から明らかなように、発明材
では、深度に拘らず、ほぼ均等な硬度が得られたが、比
較材では、表層部の硬度が特に高くなっており、この焼
結体では、表層部でW粒子の凝縮が生じているものと思
われる。なお、この発明材でも、延性について、優れた
性質を有していた。なお、上記実施例では、潤滑剤とし
て二硫化モリブデン系潤滑剤、油性黒鉛系潤滑剤を使用
したが、これらに限定されるものではなく、その他の潤
滑剤を用いることも可能である。As is clear from FIG. 2, the invention material has excellent ductility, whereas the comparative material has a sharp decrease in elongation at a processing rate of more than 20%, and thus has sufficient ductility. I couldn't get it. Further, as is clear from FIG. 3, the invention material obtained almost uniform hardness irrespective of the depth, but the comparative material had a particularly high hardness in the surface layer portion. It seems that W particles are condensed at the surface layer. The invention material also had excellent ductility. Although molybdenum disulfide-based lubricants and oil-based graphite-based lubricants are used as the lubricants in the above-described examples, the lubricants are not limited to these, and other lubricants may be used.
【0014】[0014]
【発明の効果】以上説明したように、本願発明の高強度
高延性焼結体の製造方法は、高強度粉末を焼結したW−
Fe−Ni合金などの焼結体の表面に、Cu を主体とする
金属皮膜をメッキなどにより形成し、その後に、前記焼
結体を温間加工するので、温間加工時の延性の低下を防
止して、十分な加工率による加工を可能とし、その結
果、高強度で高延性の焼結体が得られる効果がある。As described above, the method for producing a high-strength and high-ductility sintered body of the present invention is the W-
Since a metal film mainly composed of Cu is formed on the surface of a sintered body such as an Fe-Ni alloy by plating, and then the sintered body is warm-worked, the ductility during warm-working is reduced. It is possible to prevent this and to perform processing with a sufficient processing rate, and as a result, it is possible to obtain a sintered body having high strength and high ductility.
【図1】図1は、実施例の製造方法の工程を示すチャー
ト図である。FIG. 1 is a chart showing steps of a manufacturing method of an example.
【図2】図2は、実施例および比較例の焼結体の引張強
さ−伸び関係を示すグラフである。FIG. 2 is a graph showing a tensile strength-elongation relationship of sintered bodies of Examples and Comparative Examples.
【図3】図3は、実施例および比較例の焼結体の径方向
深度における硬さ分布を示すグラフである。FIG. 3 is a graph showing hardness distributions in radial depths of sintered bodies of Examples and Comparative Examples.
【図4】図4は、従来の製造方法の工程を示すチャート
図である。FIG. 4 is a chart showing steps of a conventional manufacturing method.
Claims (2)
Cu を主体とする金属皮膜を形成し、その後、前記焼結
体を温間加工することを特徴とする高強度高延性焼結体
の製造方法1. A surface of a sintered body obtained by sintering high-strength powder,
A method for producing a high-strength and high-ductility sintered body, which comprises forming a metal film mainly composed of Cu and then hot working the sintered body.
この焼結体表面に純銅をメッキして金属皮膜を形成した
ことを特徴とする請求項1記載の高強度高延性焼結体の
製造方法2. The sintered body is made of a W—Fe—Ni alloy,
The method for producing a high-strength and high-ductility sintered body according to claim 1, wherein pure copper is plated on the surface of the sintered body to form a metal film.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3303844A JPH0768568B2 (en) | 1991-10-24 | 1991-10-24 | Method for manufacturing high strength and high ductility sintered body |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3303844A JPH0768568B2 (en) | 1991-10-24 | 1991-10-24 | Method for manufacturing high strength and high ductility sintered body |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH05117719A true JPH05117719A (en) | 1993-05-14 |
JPH0768568B2 JPH0768568B2 (en) | 1995-07-26 |
Family
ID=17925987
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP3303844A Expired - Lifetime JPH0768568B2 (en) | 1991-10-24 | 1991-10-24 | Method for manufacturing high strength and high ductility sintered body |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH0768568B2 (en) |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS58145302A (en) * | 1982-02-24 | 1983-08-30 | Toshiba Corp | Production of thin metallic sheet having high melting point |
JPH0297652A (en) * | 1988-06-22 | 1990-04-10 | Cime Bocuze | Method for molding piercing type projectile |
-
1991
- 1991-10-24 JP JP3303844A patent/JPH0768568B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS58145302A (en) * | 1982-02-24 | 1983-08-30 | Toshiba Corp | Production of thin metallic sheet having high melting point |
JPH0297652A (en) * | 1988-06-22 | 1990-04-10 | Cime Bocuze | Method for molding piercing type projectile |
Also Published As
Publication number | Publication date |
---|---|
JPH0768568B2 (en) | 1995-07-26 |
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