JPS58130254A - Sintered fe alloy for sliding member - Google Patents
Sintered fe alloy for sliding memberInfo
- Publication number
- JPS58130254A JPS58130254A JP1041382A JP1041382A JPS58130254A JP S58130254 A JPS58130254 A JP S58130254A JP 1041382 A JP1041382 A JP 1041382A JP 1041382 A JP1041382 A JP 1041382A JP S58130254 A JPS58130254 A JP S58130254A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- ferrite
- sintered
- free graphite
- wear resistance
- 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.)
- Pending
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- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
この発明は、常温のみならず高温においてもすぐれた耐
摩耗性及び潤滑性を発揮し、特にパルプガイドやピスト
ンリング等のように、その機構上、あるいは温度環境等
のために給油が困難で、無潤滑で使用せざるを得ない摺
動部材の製造に供するのに適したＦｅ基焼結合金に関す
るものである。Detailed Description of the Invention This invention exhibits excellent wear resistance and lubricity not only at room temperature but also at high temperatures. The present invention relates to an Fe-based sintered alloy suitable for manufacturing sliding members that are difficult to lubricate and must be used without lubrication.
一般に、自動車等のエンジン部やその周辺部材は高温に
さらされるうえ、その機構構造上給油を施すことも困難
なために、このような個所に使用される摺動部材には、
格別な耐摩耗性能や潤滑性能を保有するものが必要とさ
れている。In general, the engine parts of automobiles and other surrounding parts are exposed to high temperatures, and it is difficult to lubricate them due to their mechanical structure.
There is a need for something with exceptional wear resistance and lubrication performance.
従来、このように、ある程度の高温域でも無潤滑で使用
できる耐摩耗特性や潤滑特性を備えた合金材料が各種提
案され、実用に供されているが、近年、ターボチャージ
ャー付エンジンの開発等によシ、上記のような摺動部材
のさらに高温域での使用が多くなってきており、これま
での摺動部材用材料では、このような苛酷な条件下にお
いて長時間無潤滑で使用するのに、その潤滑性能が十分
なものであるとはいえないのが現状である。In the past, various alloy materials with wear resistance and lubrication properties that can be used without lubrication even in a certain high temperature range have been proposed and put into practical use, but in recent years, in the development of turbocharged engines, etc. However, sliding parts such as those mentioned above are increasingly being used in higher temperature ranges, and conventional materials for sliding parts cannot be used without lubrication for long periods of time under such harsh conditions. However, at present, its lubrication performance cannot be said to be sufficient.
本発明者等は、上述のような観点から、無潤滑で使用せ
ざるを得ない内燃機関の摺動部材等として用いても、長
期間にわたって良好な潤滑性能を発揮し続ける、耐摩耗
性材料を得るべく研究を行なった結果、Ｆｅをベースと
して、これにＣｕ及びＳｎの焼結促進元素を加えるとと
もに、特定量のＣ及び窒化ホウ素を添加して焼結したと
ころの、素地フェライト中に遊離黒鉛が均一に分散した
組織を有するＦｅ基焼結合金が得られ、このＦｅ基焼結
合金においては、素地内に均一に分散した遊離黒鉛によ
って、常温ではもちろんのこと、高温域での使用におい
てもすぐれた耐摩耗性及び摺動特性を示し、さらに、上
記成分組成の焼結合金に、 Ｐｌ）−、二硫化モリブデ
ン、及び二硫化タングステンが含有されていると、これ
らの成分が素地の結晶粒界に均一に分散した組織が得ら
れるので、高温域での自己潤滑性が一段と向上するとい
う知見を得たのである。From the above-mentioned viewpoint, the present inventors have developed a wear-resistant material that continues to exhibit good lubrication performance over a long period of time even when used as a sliding member of an internal combustion engine that must be used without lubrication. As a result of conducting research to obtain ferrite, it was found that when sintering was performed using Fe as a base, adding sintering promoting elements of Cu and Sn, and adding a specific amount of C and boron nitride, free ferrite was found in the base ferrite. An Fe-based sintered alloy with a structure in which graphite is evenly dispersed is obtained, and in this Fe-based sintered alloy, the free graphite evenly dispersed within the matrix makes it possible to use it not only at room temperature but also in high-temperature ranges. It exhibits excellent wear resistance and sliding properties, and furthermore, when the sintered alloy with the above component composition contains Pl)-, molybdenum disulfide, and tungsten disulfide, these components cause the crystals of the base material to They found that since a structure uniformly dispersed at grain boundaries is obtained, self-lubricating properties at high temperatures are further improved.
したがって、この発明は上記知見に基いてなされたもの
であって、焼結合金を、Ｃｕ：１〜１５％（以下チは重
量％とする）、Ｓｎ：０．１〜５０係。Therefore, this invention was made based on the above knowledge, and the sintered alloy contains Cu: 1 to 15% (hereinafter, "ch" is weight %) and Sn: 0.1 to 50%.
Ｃ：１〜１０％、窒化ホウ素：０．０１〜３．０％を含
み、残シがＦｅと不可避不純物からなる成分組成とする
か、あるいはさらに、ｐｂ、二硫化モリブデン、及び二
硫化タングステンのうちの１種または２種以上を０５〜
ｌ Ｏ，Ｏ％含有せしめた成分組成とし、フェライト中
に遊離黒鉛が均一に分散した組織とすることによって、
すぐれた耐摩耗性と潤滑性とを付与せしめたことに特徴
を有するものである。C: 1 to 10%, boron nitride: 0.01 to 3.0%, with the remainder consisting of Fe and inevitable impurities, or in addition, PB, molybdenum disulfide, and tungsten disulfide. One or more of these from 05
By making the component composition contain 1 O, O% and creating a structure in which free graphite is uniformly dispersed in the ferrite,
It is characterized by having excellent wear resistance and lubricity.
ついで、この発明の摺動部材用Ｆｅ基焼結合金の成分組
成範囲を上記のとおりに限定した理由を説明する。Next, the reason why the composition range of the Fe-based sintered alloy for sliding members of the present invention is limited as described above will be explained.
（ａ） Ｃｕ
Ｃｕ成分には、合金製造時の焼結を促進し、かつ合金素
地の耐摩耗性及び耐酸化性を改善する作用があるが、そ
の含有量が１％未満では前記作用に所望の効果が得られ
ず、一方１５％を越えて含有させると合金自体の脆化が
著しくなることから、その含有量を１〜１５％と限定し
た。(a) Cu The Cu component has the effect of promoting sintering during alloy production and improving the wear resistance and oxidation resistance of the alloy matrix, but if its content is less than 1%, the desired effect may not be achieved. However, if the content exceeds 15%, the alloy itself becomes significantly brittle, so the content was limited to 1 to 15%.
（ｂｌ ５ｎ
Ｓｎ成分には、合金製造時にＣｕ成分と反応してＣｕ成
分の固溶を助長する作用があるが、その含有量が０１％
未満では前記作用に所望の効果が得られず、一方５０％
を越えて含有させると合金自体の脆化が著しくなること
から、その含有量を０．１〜５０％と限定した。(bl 5n The Sn component has the effect of reacting with the Cu component during alloy production and promoting solid solution of the Cu component, but the content is 0.1%.
If it is less than 50%, the desired effect cannot be obtained.
If the content exceeds 0.1%, the alloy itself will become significantly brittle, so the content was limited to 0.1% to 50%.
（Ｃ） Ｃ
Ｃ成分には、素地粒界に均一に分散して摺動特性を向上
させる作用があるが、その含有量が１％未満では所望の
摺動特性を確保することができず、一方ｌＯ％を越えて
含有させると合金の脆化が著しくなることから、その含
有量を１〜１０％と定めた。(C) C The C component has the effect of uniformly dispersing in the grain boundaries of the base material and improving the sliding properties, but if its content is less than 1%, the desired sliding properties cannot be ensured. On the other hand, if the content exceeds 10%, the embrittlement of the alloy becomes significant, so the content was set at 1 to 10%.
（ｄ） 窒化ホウ素
窒化ホウ素成分には、特に高温域での摺動特性を向上さ
せる作用と、Ｆｅ成分とＣ成分の反応を抑制する作用と
がある。つまシ、この成分は、合金の焼結中に一部分解
し、分解したＮ及び窒化ホウ素の両方の作用によってＦ
ｅ中へのＣの拡散を抑制して、Ｆｅ中に遊離黒鉛を析出
させる効果を有するのである。そして、その含有量が０
．０１ ％未満では遊離黒鉛の析出が少なくなって、前
記作用に所望の効果を得ることができず、一方３．０％
を越えて含有させても摺動特性のそれ以上の向上が認め
られないことから、経済性をも考慮してその含有量を０
．０１〜３．０％と限定した。(d) Boron nitride The boron nitride component has the effect of improving the sliding properties, especially in a high temperature range, and the effect of suppressing the reaction between the Fe component and the C component. This component partially decomposes during the sintering of the alloy and becomes F by the action of both decomposed N and boron nitride.
This has the effect of suppressing the diffusion of C into e and precipitating free graphite into Fe. And its content is 0
．． If the content is less than 0.01%, the precipitation of free graphite will be reduced, making it impossible to obtain the desired effect;
Since no further improvement in sliding properties is observed even if the content exceeds
．． It was limited to 01-3.0%.
（ｅ） Ｐｂ、二硫化モリブデン、二硫化タングステ
ン
ｐｂ、二硫化モリブデン、及び二硫化タングステン成分
には、素地粒界に均一に分散して摺動特性を向上させる
作用があるので、これらの特性が特に要求される場合に
必要に応じて含有せしめるものであるが、その含有量が
０５％未満では前記作用に所望の向上効果が得られず、
一方１０％を越えて含有させてもそれ以上の効果の向上
が認められず、強度の低下を招くことにもなり、また経
済的にも好ましくないことから、その含有量を０．５〜
１０．０チと限定した。(e) Pb, molybdenum disulfide, tungsten disulfide PB, molybdenum disulfide, and tungsten disulfide components have the effect of uniformly dispersing in the grain boundaries of the base material and improving the sliding properties. It is included as necessary when particularly required, but if the content is less than 0.5%, the desired effect of improving the above action cannot be obtained,
On the other hand, if the content exceeds 10%, no further improvement in the effect is observed, leading to a decrease in strength, and it is also economically unfavorable, so the content should be reduced from 0.5 to 10%.
It was limited to 10.0chi.
なお、この発明のＦｅ基焼結合金は通常の粉末冶金法に
よって通常の製造条件にて製造することができ、それに
よって、素地フェライト中に遊離黒鉛が均一に分散した
組織が得られるのである。The Fe-based sintered alloy of the present invention can be manufactured by a normal powder metallurgy method under normal manufacturing conditions, thereby providing a structure in which free graphite is uniformly dispersed in the base ferrite.
つぎに、この発明のＦｅ基焼結合金を実施例により比較
例と対比しながら説明する。Next, the Fe-based sintered alloy of the present invention will be explained using examples and comparing with comparative examples.
実施例
原料粉末として、粒度−１００ｍｅｓｈを有するＦｅ粉
末、それぞれ粒度−６０ｍｅｓｈを有する天然黒鉛粉末
１人造黒鉛粉末、及び電解Ｃ１１粉末２粒度−１００ｍ
ｅｓｈを有するＳｎ粉末９粒度−１００ｍｅｓｈを有す
る窒化ホウ素（ＢＮ ）粉末２粒度−１００ｍｅｓｈを
有するｐｂ粉末、そして、それぞれ粒度−６０＋ｎｔｓ
ｓｂを有する二硫化モリブデン（以下ＭｏＳ ２で示す
）及び二硫化タングステン（以下ＷＳ、で示す）粉末を
用意し、これらの原料粉末を第１表に示される最終成分
組成をもつように配合し、混合し、５ ｔｏｎ／ｃｒｌ
の圧力にて圧粉体に成形し、ついでとの圧粉体を中性ま
たは還元性雰囲気中、温度：１１００〜１１５０℃に１
時間保持の条件で焼結することによって、実質的に第１
表に示される成分組成をもった本発明焼結合金１〜１２
及び比較焼結合金１〜９をそれぞれ製造した。Example raw material powders include Fe powder with particle size -100mesh, natural graphite powder 1 artificial graphite powder each having particle size -60mesh, and electrolytic C11 powder 2 particle size -100m.
9 particle size of Sn powder with esh - 2 particle size of boron nitride (BN) powder with 100 mesh - PB powder with particle size of 100 mesh, and respectively particle size -60+nts
Molybdenum disulfide (hereinafter referred to as MoS 2) and tungsten disulfide (hereinafter referred to as WS) powder having sb are prepared, and these raw material powders are blended to have the final component composition shown in Table 1, Mixed, 5 ton/crl
The green compact is then molded into a compact at a pressure of 1,100 to 1,150°C in a neutral or reducing atmosphere.
By sintering under the conditions of time holding, substantially the first
Sintered alloys 1 to 12 of the present invention having the component compositions shown in the table
and Comparative Sintered Alloys 1 to 9 were manufactured, respectively.
なお、比較焼結合金１〜８はいずれも構成成分のうちの
いずれかの成分（第１表に壷印で表示）がこの発明の範
囲から外れた組成をもつものである。また、第１表に示
される比較焼結合金９は、従来主として用いられている
粉末冶金製の材料を別途用意したものである。さらに第
１表には、この結果得られた本発明焼結合金１〜１２．
比較焼結合金１〜９の密度、硬さくロックウェル硬さＢ
スケール）を示した。そして、上記本発明焼結合金９．
及び比較焼結合金７の顕微鏡による組織写真（倍率：
１００倍及び４００倍）を、第１図及び第２図にそれぞ
れ示した。It should be noted that each of Comparative Sintered Alloys 1 to 8 has a composition in which one of the constituent components (indicated by a pot in Table 1) is outside the scope of the present invention. Further, the comparative sintered alloy 9 shown in Table 1 is a separately prepared material made of powder metallurgy, which has been mainly used in the past. Furthermore, Table 1 shows the sintered alloys 1 to 12 of the present invention obtained as a result.
Density and hardness of comparative sintered alloys 1 to 9: Rockwell hardness B
scale). And the above-mentioned sintered alloy of the present invention 9.
and microscopic microstructure photographs of Comparative Sintered Alloy 7 (magnification:
(100x and 400x) are shown in Figures 1 and 2, respectively.
ついで、上記本発明焼結合金１−１２．及び比較焼結合
金１〜９よシ摺動試験用の試料を製造し、それぞれの材
料について摺動試験機を用いて摺動特性の試験を行なっ
た。この摺動試験は、円筒形の相手材料の端部の一定場
所に試料を一定圧で押付けながら、該相手材を回転させ
、試料及び相手材の摩耗深さを測定するものであって、
このときの試験条件は、相手材材質：５４５Ｃ材、相手
材内径’、 ９５５ ｍｍ＋相手材摺擦部幅（端部肉厚
）：５ｍｍ、相手材長さ：３ｍ、試料寸法：幅２５１Ｗ
ＷＸ長さ１００ｍｍＸ高さ１０ｍｍ＋ 試験速度： ０
．５ ｍ１ｓｅｃ。Next, the above-mentioned sintered alloy of the present invention 1-12. Samples for the sliding test were prepared from Comparative Sintered Alloys 1 to 9, and the sliding characteristics of each material were tested using a sliding testing machine. In this sliding test, the sample is pressed against a fixed position on the end of a cylindrical mating material under a constant pressure while the mating material is rotated, and the wear depth of the sample and the mating material is measured.
The test conditions at this time were: mating material: 545C material, mating material inner diameter', 955 mm + mating material sliding part width (end wall thickness): 5 mm, mating material length: 3 m, sample dimensions: width 251 W.
WX length 100mmX height 10mm+ Test speed: 0
．． 5 m1sec.
及び５ ｍ ／ ｓｅｃ 、試験時間：６時間であった
。この測定結果も併せて第１表に示した。and 5 m/sec, test time: 6 hours. The measurement results are also shown in Table 1.
第１表に示される結果からも、比較焼結合金１〜９にお
いては、自体の耐摩耗性、及び相手攻撃性のうちの少な
くともいずれかの性質が劣るものであるのに対して、本
発明焼結合金１〜１２では、いずれもすぐれた耐摩耗性
及び低い相手攻撃性を示しており、長期にわたってすぐ
れた摺動特性を発揮することが明らかである。The results shown in Table 1 also show that Comparative Sintered Alloys 1 to 9 are inferior in at least one of their own wear resistance and attack resistance, whereas the present invention All of the sintered alloys 1 to 12 exhibit excellent wear resistance and low aggressivity, and it is clear that they exhibit excellent sliding properties over a long period of time.
上述のように、この発明の摺動材料は、常温においても
高温においてもすぐれた耐摩耗性及び潤滑性を発揮する
特性を有するので、苛酷な高温雰囲気中や、給油でき彦
い個所等に使用することができることから、すぐれた性
能を生み出す機械装置の設計が可能となるなど工業上有
用な効果がもたらされるのである。As mentioned above, the sliding material of the present invention exhibits excellent wear resistance and lubricity both at room temperature and high temperature, so it can be used in harsh high-temperature atmospheres or in places where lubrication is not possible. This fact brings about industrially useful effects, such as making it possible to design mechanical devices that produce superior performance.
第１図はこの発明のＦｅ基焼結合金の顕微鏡による組織
写真であシ、第１図（ａ）はその倍率１００倍のもの、
第１図（ｂｌはその倍率４００倍のものであり、第２図
は比較Ｆｅ基焼結合金の顕微鏡による組織写真であって
、第２図ｆａ）はその倍率１００倍のもの、第２図ｆｂ
）はその倍率４００倍のものである。
ｌζミ亮ミ２図’ｐλFigure 1 is a microscopic micrograph of the Fe-based sintered alloy of the present invention, and Figure 1(a) is 100x magnification.
Figure 1 (bl is a photograph taken at a magnification of 400 times, Figure 2 is a photograph of the microstructure of a comparison Fe-based sintered alloy, and Figure 2 fa) is taken at a magnification of 100 times. fb
) is a magnification of 400 times. lζmi ryomi 2 figure'pλ
Claims (1)
イト中に遊離黒鉛が均一に分散した組織を有することを
特徴とする耐摩耗性にすぐれた摺動部材用Ｆｅ基焼結合
金。 （２） Ｃｕ： １〜１５％、 Ｓｎ：０．１〜５ｏ％、 Ｃ：１〜１０％、 窒化ホウ素二〇０１〜３．０％、 を含有し、さらに、 Ｐｂ、二硫化モリブデン、及び二硫化タングステンのう
ちの１種または２種以上：０．５〜１０． （１％ 。 を含み、 Ｆｅ及び不可避不純物：残り、 （以上重量％）からなる組成を有するとともに、フェラ
イト中に遊離黒鉛が均一に分散した組織を有することを
特徴とす・る耐摩耗性にすぐれた摺動部材用Ｆｅ基焼結
合金。[Claims] (11Cu: 1-15%, Sn: 0.1-5.0%, C: 1-10%, boron nitride: 001-3.0%, Fe and inevitable impurities: remainder, An Fe-based sintered alloy for sliding members with excellent wear resistance, characterized by having a composition consisting of (more than % by weight) and a structure in which free graphite is uniformly dispersed in ferrite. (2) Cu : 1 to 15%, Sn: 0.1 to 5o%, C: 1 to 10%, boron nitride 2001 to 3.0%, and further contains Pb, molybdenum disulfide, and tungsten disulfide. One or more of these: 0.5 to 10. (1%), Fe and unavoidable impurities: the rest (more than 1% by weight), and free graphite is uniformly dispersed in the ferrite. An Fe-based sintered alloy for sliding members with excellent wear resistance, which is characterized by having a microstructure.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1041382A JPS58130254A (en) | 1982-01-26 | 1982-01-26 | Sintered fe alloy for sliding member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1041382A JPS58130254A (en) | 1982-01-26 | 1982-01-26 | Sintered fe alloy for sliding member |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS58130254A true JPS58130254A (en) | 1983-08-03 |
Family
ID=11749457
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1041382A Pending JPS58130254A (en) | 1982-01-26 | 1982-01-26 | Sintered fe alloy for sliding member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS58130254A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100253920B1 (en) * | 1996-07-10 | 2000-04-15 | 셈보쿠야 아키오 | The manufacturing method for valve guide and same goods |
| FR2813317A1 (en) * | 2000-08-31 | 2002-03-01 | Hitachi Powdered Metals | SINTERED ALLOY MATERIAL FOR VALVE GUIDES |
| WO2010028470A2 (en) | 2008-09-12 | 2010-03-18 | Whirlpool S.A. | Metallurgical composition of particulate materials, self-lubricating sintered product and process for obtaining self-lubricating sintered products |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5114804A (en) * | 1974-07-27 | 1976-02-05 | Yamada Seisakusho Jugen | Jidoshayonadono ketsugobuhin oyobi sono seizohoho |
-
1982
- 1982-01-26 JP JP1041382A patent/JPS58130254A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5114804A (en) * | 1974-07-27 | 1976-02-05 | Yamada Seisakusho Jugen | Jidoshayonadono ketsugobuhin oyobi sono seizohoho |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100253920B1 (en) * | 1996-07-10 | 2000-04-15 | 셈보쿠야 아키오 | The manufacturing method for valve guide and same goods |
| FR2813317A1 (en) * | 2000-08-31 | 2002-03-01 | Hitachi Powdered Metals | SINTERED ALLOY MATERIAL FOR VALVE GUIDES |
| WO2010028470A2 (en) | 2008-09-12 | 2010-03-18 | Whirlpool S.A. | Metallurgical composition of particulate materials, self-lubricating sintered product and process for obtaining self-lubricating sintered products |
| EP2331279B1 (en) * | 2008-09-12 | 2014-11-05 | Whirlpool S.A. | Metallurgical composition of particulate materials, self-lubricating sintered product and process for obtaining self-lubricating sintered products |
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