JP2004292900A - Alloy powder having excellent sinterability - Google Patents
Alloy powder having excellent sinterability Download PDFInfo
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- JP2004292900A JP2004292900A JP2003087644A JP2003087644A JP2004292900A JP 2004292900 A JP2004292900 A JP 2004292900A JP 2003087644 A JP2003087644 A JP 2003087644A JP 2003087644 A JP2003087644 A JP 2003087644A JP 2004292900 A JP2004292900 A JP 2004292900A
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 45
- 239000000956 alloy Substances 0.000 title claims abstract description 45
- 239000000843 powder Substances 0.000 title claims abstract description 30
- 239000002245 particle Substances 0.000 claims abstract description 27
- 238000005245 sintering Methods 0.000 abstract description 16
- 238000000034 method Methods 0.000 description 5
- 239000010949 copper Substances 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 229910000997 High-speed steel Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000009689 gas atomisation Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
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- Powder Metallurgy (AREA)
Abstract
Description
【０００１】
【発明の属する技術分野】
本発明は、寸法精度の厳しい焼結部品に関し、例えば、ギヤ、軸受け、および電子部品等に使用される寸法精度の厳しい焼結部品に関するものである。
【０００２】
【従来の技術】
従来、ＯＡ、コンピューター関連分野さらには機械産業分野のメカトロニクス化に伴い、小型高性能な複雑形状部品のニーズが高まりつつある。このような要求を満たすために、粉末冶金法を応用して、成型と焼結により製造することが考えられている。この焼結のメカニズムは、一般に充填された粉末に熱を加えることで粉末同士が接した部分のネックが成長していき焼結体ができるものである。しかし、焼結材は、密度が上がりにくく、溶製材と比較して特性的に劣っているのが現状である。これを改善するために、例えば特開昭６２−１０３３４３号公報（特許文献１）においては、平均粒径６０〜２００μｍのガスアトマイズ球状粉末を圧縮成形した後、真空焼結し、Ｏ２ ０．０２％以下とする鉄−ニッケル系軟磁性焼結材料が提案されている。
【０００３】
また、特開平５−１１７７２１号公報（特許文献２）に開示しているように、ガスアトマイズ法により得られた８０〜９５重量％銅−５〜２０重量％クロム組成の合金粉体に、粒径が１５０μｍ以下の銅粉を５重量％以上５０重量％以下の割合で添加し、得られた混合粉末を加圧成形し、得られた成形体を不活性雰囲気で加熱して焼結させた電極材料の製造方法が提案されている。
【０００４】
（１）特許文献１（特開昭６２−１０３３４３号公報）
（２）特許文献２（特開平５−１１７７２１号公報）
【０００５】
【発明が解決しようとする課題】
上述した特許文献１または特許文献２のいずれも、粒度コントロールされていない粉末、または製造方法のために、粉末の粒度分布により焼結の進行に変化が生じたり、また収縮にバラツキが生じて焼結体の寸法コントロールが難しく、粉末の特性である収縮率が増大し、寸法精度が悪く、また焼結時間が長い等の問題がある。
【０００６】
【課題を解決するための手段】
上述した問題を解消するために、発明者らは鋭意開発を進めた結果、焼結の進行や収縮率に最適な粉末粒度を制御することにより、短い焼結時間で収縮率の小さい安定した品質の焼結体を得ることが出来る焼結性に優れた合金粉末を提供するものである。その発明の要旨とするところは、
（１）粒径８０〜２５０μｍ：１２〜１７％、粒径３０〜８０未満μｍ：２５〜３０％、粒径３０μｍ未満：４０〜４５％、残部２５０μｍ超に粒度調整されたことを特徴とする焼結性に優れた合金粉末。
【０００７】
（２）前記（１）記載の合金粉末の収縮率が２０％以下であることを特徴とする焼結性に優れた合金粉末。
（３）前記（１）または（２）記載の合金粉末が、Ｆｅ基合金、Ｎｉ基合金、Ｃｏ基合金、Ｃｕ基合金、Ｍｎ基合金のうち、１種以上であることを特徴とする焼結性に優れた合金粉末である。
【０００８】
【発明の実施の形態】
以下、本発明について詳細に説明する。
本発明において、粒径８０〜２５０μｍ：１２〜１７％、粒径３０〜８０未満μｍ：２５〜３０％、粒径３０μｍ未満：４０〜４５％、残部２５０μｍ超に粒度調整した粉末を加熱温度７００〜１５００℃の範囲で３〜７時間焼結した場合はネックの成長が最適に行われ、かつ収縮性を極めて小さくおさえることができる。この粒径粒径８０〜２５０μｍ：１２〜１７％、粒径３０〜８０未満μｍ：２５〜３０％、粒径３０μｍ未満：４０〜４５％、残部２５０μｍ超に粒度調整した理由は、この範囲を外れると、焼結時間が７時間を超え、生産性が著しく低下する。合金粉末の収縮率が２０％以下とした理由は、合金粉末の収縮率が２０％を超えると、焼結体の寸法コントロールが難しくなり、また、収縮率のバラツキも大きくなるため、寸法精度が悪くなる。
【０００９】
また、本発明に係る合金粉末としては、Ｆｅ基合金、Ｎｉ基合金、Ｃｏ基合金、Ｃｕ基合金、Ｍｎ基合金のうち１種以上である。具体的には、Ｆｅ基合金としては粉末ハイス（Ｆｅ−１．３Ｃ−４Ｃｒ−５Ｍｏ−３Ｖ−６Ｗ−８Ｃｏ）、ＳＵＳ３１６Ｌ（Ｆｅ−１３Ｎｉ−１７Ｃｒ−２Ｍｏ）等、Ｎｉ基合金としては、ＰＨＣ（Ｎｉ−１６Ｃｒ−１６Ｍｏ−３．５Ｗ−６．５Ｆｅ）等、Ｃｏ基合金としては、ＰＳ６（Ｃｏ−１．１Ｃ−２９Ｃｒ−５Ｗ）等、Ｃｕ基合金としては、ＢＣｕＰ２（Ｃｕ−７Ｐ）等、Ｍｎ基合金としては、ＭｎＡｌＣ（Ｍｎ−３０Ａｌ−０．５Ｃ）等を挙げることができる。
【００１０】
【実施例】
以下、本発明について実施例によって詳細に説明する。
表１に掲げる粉末ハイス、ＳＵＳ３１６Ｌ、ＰＨＣ、ＰＳ６、ＢＣｕＰ２、ＭｎＡｌＣの６種について、ガスアトマイズ法により製造し、篩分けし計量して粒度調整した後ブレード付混合機にて混合した後、梱包して出荷し、その合金粉末を焼結し、再び計量した後金型に充填してプレス加工し、加熱、保持後取り出し、検査工程で検査を行なった。その結果を表１に示す。
【００１１】
【表１】
表１に示すように、Ｎｏ．１〜１８は本発明例であり、Ｎｏ．１９〜３６は、比較例である。本発明でのＮｏ．１〜６、Ｎｏ．７〜１２、Ｎｏ．１３〜１８は６種の合金粉末を１０００〜７５０ｍｍ、７５０〜５００ｍｍ、５００〜２５０ｍｍ、２５０〜８０ｍｍ、８０〜３０ｍｍ、３０ｍｍ以下に区分してそれぞれの割合に混合して焼結後の収縮率を示している。いずれも収縮率が低いことが分かる。これに対し、比較例においても本発明例と同様にＮｏ．１９〜２４、Ｎｏ．２５〜３０、Ｎｏ．３１〜３６において６種の合金粉末を各粒度でそれぞれの混合割合で焼結した後の収縮率はいずれも焼結時間が長いにもかかわらず収縮率が２０％以上と本発明より高いことが分かる。
【００１３】
【発明の効果】
以上述べたように、本発明による粒度調整を行なうことにより、焼結時間が短縮され、かつ寸法精度に優れた焼結体を得ることが出来る極めて優れた効果を奏するものである。[0001]
TECHNICAL FIELD OF THE INVENTION
The present invention relates to a sintered part having strict dimensional accuracy, for example, a sintered part having strict dimensional accuracy used for gears, bearings, electronic components, and the like.
[0002]
[Prior art]
2. Description of the Related Art Conventionally, with the development of mechatronics in the OA, computer-related fields, and the machine industry, there is a growing need for small-sized, high-performance, and complex-shaped components. In order to satisfy such requirements, it has been considered to apply powder metallurgy to manufacture by molding and sintering. The mechanism of this sintering is that, generally, by applying heat to the filled powder, the neck of the portion where the powders are in contact grows to form a sintered body. However, at present, sintered materials are hard to increase in density and are inferior in characteristics as compared with ingot materials. In order to improve this, for example, in Japanese Patent Application Laid-Open No. Sho 62-103343 (Patent Document 1), a gas atomized spherical powder having an average particle diameter of 60 to 200 μm is compression-molded, then vacuum-sintered, and O 2 0.02 % Iron-nickel-based soft magnetic sintering material has been proposed.
[0003]
As disclosed in JP-A-5-117721 (Patent Document 2), an alloy powder having a composition of 80 to 95% by weight of copper and 5 to 20% by weight of chromium obtained by a gas atomizing method has An electrode obtained by adding copper powder having a particle size of 150 μm or less at a ratio of 5% by weight or more and 50% by weight or less, pressing the obtained mixed powder under pressure, and heating and sintering the obtained molded body in an inert atmosphere. Methods for producing materials have been proposed.
[0004]
(1) Patent Document 1 (JP-A-62-103343)
(2) Patent Document 2 (JP-A-5-117721)
[0005]
[Problems to be solved by the invention]
In either of Patent Documents 1 and 2 described above, because of the powder whose particle size is not controlled, or the manufacturing method, the progress of sintering is changed due to the particle size distribution of the powder, or the shrinkage is varied, resulting in the firing. There are problems such as difficulty in controlling the size of the compact, increase in shrinkage, which is a characteristic of the powder, poor dimensional accuracy, and long sintering time.
[0006]
[Means for Solving the Problems]
In order to solve the above-mentioned problems, the inventors have made intensive developments, and as a result, by controlling the powder size optimal for the progress of sintering and shrinkage, a stable quality with a small shrinkage in a short sintering time. The present invention provides an alloy powder excellent in sinterability, which can obtain a sintered body of (1). The gist of the invention is that
(1) Particle size: 80 to 250 μm: 12 to 17%, particle size: less than 30 to 80 μm: 25 to 30%, particle size: less than 30 μm: 40 to 45%, and the balance is more than 250 μm. Alloy powder with excellent sinterability.
[0007]
(2) An alloy powder having excellent sinterability, wherein the alloy powder according to (1) has a shrinkage of 20% or less.
(3) The sintering method according to (1) or (2), wherein the alloy powder is at least one of an Fe-based alloy, a Ni-based alloy, a Co-based alloy, a Cu-based alloy, and a Mn-based alloy. It is an alloy powder with excellent binding properties.
[0008]
BEST MODE FOR CARRYING OUT THE INVENTION
Hereinafter, the present invention will be described in detail.
In the present invention, a powder having a particle size of 80 to 250 μm: 12 to 17%, a particle size of less than 30 to 80 μm: 25 to 30%, a particle size of less than 30 μm: 40 to 45%, and a balance of more than 250 μm is heated at a heating temperature of 700. When sintering is performed at a temperature in the range of １1500 ° C. for 3 to 7 hours, the growth of the neck is optimally performed, and the shrinkage can be extremely small. The reason why the particle size was adjusted to 80 to 250 μm: 12 to 17%, the particle size to less than 30 to 80 μm: 25 to 30%, the particle size to less than 30 μm: 40 to 45%, and the balance to more than 250 μm is as follows. If it is off, the sintering time exceeds 7 hours, and the productivity is significantly reduced. The reason why the shrinkage of the alloy powder is set to 20% or less is that if the shrinkage of the alloy powder exceeds 20%, the dimensional control of the sintered body becomes difficult, and the variation of the shrinkage also becomes large. become worse.
[0009]
Further, the alloy powder according to the present invention is at least one of an Fe-based alloy, a Ni-based alloy, a Co-based alloy, a Cu-based alloy, and a Mn-based alloy. Specifically, powdered high-speed steel (Fe-1.3C-4Cr-5Mo-3V-6W-8Co), SUS316L (Fe-13Ni-17Cr-2Mo), etc. as the Fe-based alloy, and PHC ( Ni-16Cr-16Mo-3.5W-6.5Fe) and the like, such as PS6 (Co-1.1C-29Cr-5W) as a Co-based alloy, and BCuP2 (Cu-7P) as a Cu-based alloy. Examples of the Mn-based alloy include MnAlC (Mn-30Al-0.5C).
[0010]
【Example】
Hereinafter, the present invention will be described in detail with reference to examples.
The six types of powdered high-speed steel, SUS316L, PHC, PS6, BCuP2, and MnAlC listed in Table 1 were produced by a gas atomizing method, sieved, weighed, adjusted for particle size, mixed with a mixer with a blade, and packed. After shipping, the alloy powder was sintered, weighed again, filled in a mold, pressed, heated, held, taken out, and inspected in an inspection process. Table 1 shows the results.
[0011]
[Table 1]
As shown in Table 1, Nos. 1 to 18 are examples of the present invention. 19 to 36 are comparative examples. No. in the present invention. Nos. 1 to 6; Nos. 7 to 12; 13 to 18 are divided into 1000 to 750 mm, 750 to 500 mm, 500 to 250 mm, 250 to 80 mm, 80 to 30 mm, and 30 mm or less in the six kinds of alloy powders, and mixed in respective proportions to reduce the shrinkage after sintering. Is shown. It can be seen that the shrinkage rate is low in each case. On the other hand, in the comparative example as well as in the present invention example, 19 to 24; 25-30, No. Regarding 31 to 36, the shrinkage rate after sintering the six kinds of alloy powders at the respective particle sizes and the respective mixing ratios is that the shrinkage rate is 20% or more, which is higher than the present invention, despite the long sintering time. I understand.
[0013]
【The invention's effect】
As described above, by performing the grain size adjustment according to the present invention, the sintering time is shortened, and an extremely excellent effect that a sintered body having excellent dimensional accuracy can be obtained can be obtained.
Claims (3)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2003087644A JP4275438B2 (en) | 2003-03-27 | 2003-03-27 | Alloy powder with excellent sinterability |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2003087644A JP4275438B2 (en) | 2003-03-27 | 2003-03-27 | Alloy powder with excellent sinterability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2004292900A true JP2004292900A (en) | 2004-10-21 |
| JP4275438B2 JP4275438B2 (en) | 2009-06-10 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2003087644A Expired - Lifetime JP4275438B2 (en) | 2003-03-27 | 2003-03-27 | Alloy powder with excellent sinterability |
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| Country | Link |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107824778A (en) * | 2017-10-20 | 2018-03-23 | 广西银英生物质能源科技开发股份有限公司 | Powder metallurgy material for gear and preparation method thereof |
-
2003
- 2003-03-27 JP JP2003087644A patent/JP4275438B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107824778A (en) * | 2017-10-20 | 2018-03-23 | 广西银英生物质能源科技开发股份有限公司 | Powder metallurgy material for gear and preparation method thereof |
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| JP4275438B2 (en) | 2009-06-10 |
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| EXPY | Cancellation because of completion of term |