JP2003342700A - Sintered sliding material, sintered sliding member, and production method thereof - Google Patents

Sintered sliding material, sintered sliding member, and production method thereof

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Publication number
JP2003342700A
JP2003342700A JP2002152222A JP2002152222A JP2003342700A JP 2003342700 A JP2003342700 A JP 2003342700A JP 2002152222 A JP2002152222 A JP 2002152222A JP 2002152222 A JP2002152222 A JP 2002152222A JP 2003342700 A JP2003342700 A JP 2003342700A
Authority
JP
Japan
Prior art keywords
sintered
iron
sintered sliding
phase
sliding material
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
Application number
JP2002152222A
Other languages
Japanese (ja)
Inventor
Takemori Takayama
武盛 高山
Yoshikiyo Tanaka
義清 田中
Tetsuo Onishi
哲雄 大西
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Komatsu Ltd
Original Assignee
Komatsu Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Komatsu Ltd filed Critical Komatsu Ltd
Priority to JP2002152222A priority Critical patent/JP2003342700A/en
Publication of JP2003342700A publication Critical patent/JP2003342700A/en
Pending legal-status Critical Current

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Abstract

<P>PROBLEM TO BE SOLVED: To provide a sintered sliding material which improves the seizure resistance and/or the wear resistance of a bearing under high contact pressure, prevents the occurrence of abnormal sound, and extends the grease feeding interval; and a sintered sliding member prepared by uniting the sliding material to a backing metal and a production method for the member. <P>SOLUTION: This sliding material is an iron-based one containing at least 0.1 wt.% Al as an unavoidable component and 10-50 wt.% Cu. <P>COPYRIGHT: (C)2004,JPO

Description

【発明の詳細な説明】Detailed Description of the Invention

【０００１】[0001]

【発明の属する技術分野】本発明は、高面圧下での軸受
の耐焼付き性および／または耐摩耗性の向上、異音の発
生防止、給脂間隔の延長をねらいとした摺動材料並びに
焼結摺動部材およびそ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 sliding material and a burned material aiming at improving seizure resistance and / or wear resistance of a bearing under high surface pressure, preventing abnormal noise, and extending a greasing interval. The present invention relates to a binding slide member and a method for manufacturing the same.

【０００２】[0002]

【従来の技術】従来、建設機械の作業機ブッシュのよう
なより高面圧、低速の条件下で使用される軸受材とし
て、耐摩耗性を重視した浸炭もしくは高周波焼入れした
鋼製のブッシュがグリース潤滑下にて用いられている。
特に、この種の作業機では高面圧下で潤滑条件が厳しく
なることから、作業時に不快な異音が発生するのを防止
するために、前記鋼製ブッシュの摺動面に潤滑皮膜処理
を施したり、グリースの潤滑性を高めるために多数のグ
リース溝を形成することが行われている。2. Description of the Related Art Conventionally, as a bearing material used under conditions of higher surface pressure and lower speed, such as a working machine bush of a construction machine, a carburized or induction hardened steel bush with emphasis on wear resistance is grease. Used under lubrication.
In particular, in this type of working machine, the lubrication condition becomes severe under high surface pressure, so in order to prevent the generation of unpleasant noise during work, a lubricating film treatment is applied to the sliding surface of the steel bush. In addition, many grease grooves are formed in order to improve the lubricity of grease.

【０００３】また、前記グリースの給脂間隔を延ばすこ
とによるイージーメンテナンス化の関係から、例えばＦ
ｅ−Ｃ−Ｃｕを基本型とし、硬質なマルテンサイト基地
の鉄系焼結摺動材料の気孔に潤滑油を含浸させた含油焼
結軸受や、この鉄系焼結摺動材料に、より硬質な工具粉
末やセラミック粉末を添加した含油焼結軸受等も、軽負
荷の作業機部位において一部使用されている（「焼結機
械部品−その設計と製造−」、日本粉末冶金工業会偏
著、技術書院、昭和６２年発刊、Ｐ３３９参照）。Further, from the relationship of easy maintenance by extending the grease supply interval, for example, F
Harder than the oil-containing sintered bearing, which is made of e-C-Cu as the basic type, and in which the pores of the hard martensitic iron-based sintered sliding material are impregnated with lubricating oil, and this iron-based sintered sliding material. Oil-impregnated sintered bearings to which various tool powders and ceramic powders have been added are also used in some parts of light-duty working machines ("Sintered machine parts-design and manufacture-", Japan Powder Metallurgy Association , Tech. Shoin, published in 1987, see P339).

【０００４】また、銅系焼結軸受材についても、Ｃｕ−
Ｓｎ−Ｐｂ、Ｃｕ−Ｓｎ−Ｐｂ−Ｃ等の青銅系軸受が奨
励されている。Also, for the copper-based sintered bearing material, Cu-
Bronze-based bearings such as Sn-Pb and Cu-Sn-Pb-C are encouraged.

【０００５】作業機などの軸受部への給脂間隔を延ばす
ために、高力黄銅製ブッシュに、摺動部面積の３０％前
後の面積の機械加工穴を設け、その穴を摺動方向におい
てオーバーラップするように配置し、この穴に固体潤滑
剤の（多孔質）黒鉛を埋め込んだ軸受材料（例えばオイ
レス工業社製、５００ＳＰ）や、固体潤滑剤を多量に添
加した金属焼結体（例えば東芝タンガロイ社製、ＳＬ合
金）が利用されている場合もある。In order to extend the greasing interval to the bearing portion of a working machine or the like, a high-strength brass bush is provided with a machined hole having an area of about 30% of the sliding portion area, and the hole is slid in the sliding direction. Bearing materials (for example, 500SP manufactured by Oiles Industry Co., Ltd.), which are arranged so as to overlap and in which (porous) graphite as a solid lubricant is embedded in the hole, or a metal sintered body to which a large amount of the solid lubricant is added (for example, In some cases, Toshiba Tungaloy Co., Ltd., SL alloy) is used.

【０００６】また、高面圧条件下にて使用される複層焼
結摺動部材としては、鋼鉄裏金金属と、この鋼鉄裏金金
属に焼結と同時に接合される、銅１０〜３０重量部、黒
鉛０．１〜６．５重量部、二硫化モリブデン０．１〜７
重量部、残部が鉄からなる鉄系焼結合金層を含む滑りベ
アリングが、特開平１１−１１７９４０号公報において
開示されている。Further, as a multilayer sintered sliding member used under high surface pressure conditions, a steel back metal and 10 to 30 parts by weight of copper, which is joined to the steel back metal at the same time as sintering, Graphite 0.1-6.5 parts by weight, molybdenum disulfide 0.1-7
A sliding bearing including an iron-based sintered alloy layer in which the weight part and the balance are iron is disclosed in JP-A-11-117940.

【０００７】また、高面圧条件下で使用される銅系の複
層焼結摺動材としては、固体潤滑成分としての黒鉛が３
〜８重量％の範囲で分散含有された５〜１３重量％Ａ
ｌ、３〜６重量％Ｆｅ、０．１〜１．５ＴｉＨの組成範
囲のアルミ青銅系焼結摺動合金を燐合金板の接合層を介
して鋼板に一体接合してなる複層焼結摺動材およびその
製造方法が、特開平５−１５６３８８号公報において開
示されている。Further, as a copper-based multi-layer sintered sliding material used under high surface pressure conditions, graphite as a solid lubricating component is used.
5 to 13 wt% A dispersedly contained in the range of 8 wt%
1, a multi-layer sintered slide obtained by integrally joining an aluminum bronze-based sintered sliding alloy having a composition range of 3 to 6 wt% Fe and 0.1 to 1.5 TiH to a steel plate through a joining layer of a phosphorus alloy plate. A moving material and a method for manufacturing the same are disclosed in JP-A-5-156388.

【０００８】[0008]

【発明が解決しようとする課題】前述の作業機ブッシュ
のように、高面圧下で、かつ極めて遅い速度で摺動する
ものにおいては、潤滑膜形成条件が極めて厳しくなる。
前記鋼製ブッシュでは硬さの点で高荷重に対してへたる
ことはないが、容易に焼付いたり、不快な異音が発生し
易いことが重要な問題となっており、給脂間隔を短くし
てそれらの問題が発生しないように管理することが必要
となっている。The lubricant film forming condition becomes extremely strict in the above-mentioned working machine bushes that slide under a high surface pressure and at an extremely slow speed.
In terms of hardness, the steel bush does not sag under high loads, but it is an important issue that seizure easily and unpleasant noise are likely to occur. Then, it is necessary to manage so that those problems do not occur.

【０００９】前記作業機ブッシュとして、マルテンサイ
ト基地の含油鉄系焼結摺動材を使用するものにおいて
は、へたりがなく、鋼製ブッシュに比べて焼付き性の点
でかなり改善されるものであるが、作業機のように極め
て低速、かつ高荷重下で使用される場合には、潤滑切れ
状態が容易に起こるために、耐焼付き性の向上および異
音発生の防止を十分に図ることができないという問題点
がある。In the case where the martensite-based oil-impregnated iron-based sintered sliding material is used as the working machine bush, there is no settling and the seizure property is considerably improved as compared with the steel bush. However, when used at a very low speed and under a heavy load like a working machine, lubrication easily occurs, so seizure resistance should be improved and abnormal noise should be prevented sufficiently. There is a problem that you cannot do it.

【００１０】さらに、焼結摺動材中の空隙に潤滑油を多
量に含油させて摺動時の潤滑条件を改善するものにおい
ては、焼結体中に空隙が多く存在することによって逆に
潤滑的な条件が悪くなり、耐焼付き性の向上および異音
の発生を期待するほどに改善できないという問題点があ
る。Further, in the case where a large amount of lubricating oil is impregnated into the voids in the sintered sliding material to improve the lubrication condition at the time of sliding, conversely, there are many voids in the sintered body so that lubrication is adversely affected. However, there is a problem that it is not possible to improve the seizure resistance and the generation of abnormal noise as expected.

【００１１】また、鋼製の作業機ピンと作業機ブッシュ
との間の耐焼付き性を高めるために、異種材のＣｕ−Ｓ
ｎ、Ｃｕ−Ｐｂなど青銅系材料を用いるものでは、高面
圧下でへたってしまうという問題点と、潤滑条件が厳し
いために極めて簡単に摩耗するという問題点がある。Further, in order to enhance the seizure resistance between the steel work machine pin and the work machine bush, Cu-S of a different material is used.
In the case of using a bronze-based material such as n or Cu-Pb, there are problems that the material is worn out under a high surface pressure and that it is easily worn due to severe lubrication conditions.

【００１２】これに対し、作業機ブッシュに、より硬質
で、高強度の溶製された高力黄銅材を使用するもので
は、へたりはほぼなく、鋼製ブッシュに比べて異音の発
生がかなりの点で防止できるものの、前述のように潤滑
切れが容易に起こるために、耐焼付き性の向上および異
音発生の防止を十分に図ることができないという問題点
がある。On the other hand, when the working machine bush uses a harder, high-strength, high-strength, high-strength brass material, there is almost no settling, and noise is generated compared to a steel bush. Although it can be prevented from a considerable point, there is a problem that seizure easily occurs as described above, so that it is not possible to sufficiently improve the seizure resistance and prevent the generation of abnormal noise.

【００１３】また、より硬質で、高強度な溶製される高
力黄銅材に穴あけ加工を施し、この穴に自己潤滑性の高
い黒鉛を埋め込み、さらに黒鉛に潤滑油を含油させたブ
ッシュにおいても、前述のへたりに関する問題は解決さ
れるものの、黒鉛充填用の穴の面積率を通常２５〜３０
％に抑えて使用されるため、作業機のように揺動しなが
ら摺動する距離が短くなるに連れて潤滑の行き届かなく
なる個所ができ、局所的な焼付きが発生するとともに、
長時間にわたって十分な自己潤滑性が得られないという
問題点があり、また黒鉛埋め込み用の穴あけ加工と黒鉛
の充填等の工程がコストを顕著に引き上げるという問題
点がある。Further, in a bush which is made of a high-strength brass material which is harder and has a higher strength and which is manufactured by drilling, graphite having a high self-lubricating property is embedded in the hole, and the graphite is impregnated with lubricating oil. Although the above-mentioned problem regarding fatigue is solved, the area ratio of graphite filling holes is usually 25 to 30.
Since it is used while being suppressed to%, there are places where lubrication does not reach as the sliding distance decreases while swinging like a work machine, and local seizure occurs,
There is a problem that sufficient self-lubricating property cannot be obtained for a long time, and there is a problem that steps such as drilling for embedding graphite and filling with graphite significantly increase the cost.

【００１４】また、安価な作業機ブッシュとしてマルテ
ンサイト基地の含油鉄系焼結摺動材を使用するものにお
いては、へたりもなく、かつ前記鋼製ブッシュに比べて
耐焼付き性の点でかなり改善されるものの、まだ十分で
ないという問題点がある。Further, in the case of using an oil-containing ferrous sintered sliding material of martensite base as an inexpensive working machine bush, there is no settling, and in comparison with the steel bush, seizure resistance is considerably high. Although it is improved, there is a problem that it is not enough.

【００１５】一方、前記特開平１１−１１７９４０号公
報に開示されているものでは、多量の固体潤滑剤を分散
させていることから、耐焼付き性が改善されると考えら
れるが、多量の固体潤滑剤の分散および／または後述す
るその製造方法のために、鉄系焼結摺動材が極めて靭性
に乏しく、強度不足となってその耐摩耗性が問題とな
り、また例えば削岩作業中に容易に破損するといった問
題点がある。On the other hand, in the one disclosed in JP-A-11-117940, since a large amount of solid lubricant is dispersed, it is considered that seizure resistance is improved, but a large amount of solid lubricant is used. Due to the dispersion of the agent and / or its manufacturing method described later, the iron-based sintered sliding material has extremely poor toughness, insufficient strength, and its wear resistance becomes a problem. There is a problem such as damage.

【００１６】また、この特開平１１−１１７９４０号公
報に開示されている製造方法は、プレス金型中に鋼鉄製
裏金金属とその内周面に鉄系焼結材料の混合粉末を配し
て、この混合粉末を５０〜３００ｋｇｆ／ｃｍ２の圧力
で加圧成形した後に、金型から取り出して焼結する方法
であるが、このような方法によれば、焼結密度が極めて
低く、焼結時においてその鉄系焼結体が大きく収縮し
て、極めて不安定な焼結接合となること、焼結体強度が
十分でないことといった問題点がある。Further, according to the manufacturing method disclosed in Japanese Patent Laid-Open No. 11-117940, a steel metal backing metal and a mixed powder of an iron-based sintering material are arranged on the inner peripheral surface of the metal in a press die, This mixed powder is pressure-molded at a pressure of 50 to 300 kgf / cm 2 , and is then taken out of the mold and sintered. According to such a method, the sintering density is extremely low and In the above, there is a problem that the iron-based sintered body largely contracts, resulting in extremely unstable sinter bonding and insufficient strength of the sintered body.

【００１７】さらに、特開平５−１５６３８８号公報に
開示されている技術のように、耐焼付き性を高めるため
に、３〜８重量％（約１２〜３６体積％）に及ぶ多量の
固体潤滑剤の黒鉛を高強度なアルミ青銅焼結材料中に含
有させたものにおいても、Ｃｕ−Ａｌ焼結合金が軟質な
α相組織であるために十分な耐焼付き性を示さず、その
耐焼付き性を補う黒鉛を多量に含有することによる強度
的な弱さから、十分な高面圧下での摺動特性が確保され
ず、また耐摩耗性においても十分でないという問題点が
ある。Further, as in the technique disclosed in Japanese Patent Application Laid-Open No. 5-156388, a large amount of solid lubricant of 3 to 8% by weight (about 12 to 36% by volume) is added in order to enhance seizure resistance. Even when the graphite of No. 1 is contained in a high-strength aluminum bronze sintered material, the Cu-Al sintered alloy does not show sufficient seizure resistance because of its soft α-phase structure, and its seizure resistance is Due to the weakness in strength due to the inclusion of a large amount of supplementary graphite, there are problems in that the sliding characteristics under a sufficiently high surface pressure cannot be ensured and the wear resistance is also insufficient.

【００１８】また、この従来技術では、固体潤滑剤を多
量に含有し、かつＳｎ等の液相発生成分を含有しないこ
とから、金属焼結体では焼結性が困難となり、実用的な
強度を得るためには焼結時に加圧処理を必要としてい
る。例えば前記３〜８重量％黒鉛、８〜１０重量％Ａ
ｌ、４〜６重量％Ｆｅ、０．２〜１．０重量％Ｔｉを適
量として含有するＡｌ青銅系焼結摺動材料を燐青銅板の
接合層を介して裏金に一体化した複層焼結摺動部材は、
焼結時において加圧処理を必要としており、少なくとも
一体化する工程におけるコスト高が避けられないという
問題点がある。Further, in this prior art, since the solid lubricant is contained in a large amount and the liquid phase generating component such as Sn is not contained, it becomes difficult to sinter the metal sintered body and practical strength is obtained. In order to obtain it, pressure treatment is required at the time of sintering. For example, 3 to 8 wt% graphite, 8 to 10 wt% A
1. Multi-layer firing in which an Al bronze-based sintered sliding material containing appropriate amounts of 4 to 6% by weight Fe and 0.2 to 1.0% by weight Ti is integrated with a back metal through a bonding layer of a phosphor bronze plate. The binding sliding member is
There is a problem that pressure treatment is required at the time of sintering, and cost increase is unavoidable at least in the step of integrating.

【００１９】本発明は、このような問題点に鑑みてなさ
れたもので、高面圧下での軸受の耐焼付き性および／ま
たは耐摩耗性の向上と、異音の発生防止と、給脂間隔の
延長とをねらいとした焼結摺動材料と、この焼結摺動材
料を裏金に一体化させた焼結摺動部材およびその製造方
法を提供することを目的とするものである。The present invention has been made in view of the above problems, and improves the seizure resistance and / or wear resistance of a bearing under high surface pressure, prevents the generation of abnormal noise, and provides a greasing interval. It is an object of the present invention to provide a sintered sliding material aiming at extension of the above, a sintered sliding member in which the backing metal is integrated with the sintered sliding material, and a manufacturing method thereof.

【００２０】より詳細な目的は、Ａｌを含有するＦｅ
合金相とＣｕ合金相によって顕著な耐凝着性の改善を図
り、Ｆｅ合金相のマルテンサイト組織化による耐摩耗
性の向上を図り、摺動時の発熱をＦｅ合金相の二次変
態（規則−不規則変態および磁気変態）により吸熱して
潤滑面での昇温を遅らせ、硬質で、耐焼付き性に優れ
るＣｕ−Ａｌ系β相が、鉄系焼結摺動材料中に液相とし
て分散するＣｕ合金相および／または鉄合金相中に微細
に析出分散するＣｕ合金相となるようにし、気孔中へ
の潤滑油の含油と固体潤滑剤の分散による低速度の境界
潤滑でのスティック・スリップで発生し易い異音を防ぐ
ようにした鉄系焼結摺動材料を提供し、併せて、鉄系
焼結体を顕著に膨張させるＡｌと、収縮させるＣｕを含
有させ、円筒状または略円筒状鉄系材料の内径面に接合
させた複層焼結摺動部材およびその製造方法を提供する
ことにある。A more detailed object is Fe containing Al.
The alloy phase and the Cu alloy phase are used to significantly improve the anti-adhesion property, the martensite structure of the Fe alloy phase is used to improve the wear resistance, and the heat generated during sliding is changed to the secondary transformation of the Fe alloy phase (regular -Cu-Al-based β phase, which is hard and has excellent seizure resistance, is dispersed as a liquid phase in the iron-based sintered sliding material by absorbing heat due to irregular transformation and magnetic transformation) to delay the temperature rise on the lubricated surface. Stick slip in low-speed boundary lubrication due to impregnation of lubricating oil into pores and dispersion of solid lubricant by making Cu alloy phase finely precipitated and dispersed in Cu alloy phase and / or iron alloy phase The present invention provides an iron-based sintered sliding material that prevents abnormal noise that tends to occur at the same time, and also contains Al that causes the iron-based sintered body to significantly expand and Cu that causes the iron-based sintered body to contract, and has a cylindrical or substantially cylindrical shape. Multi-Layer Sintered Sliding Member Bonded to Inner Diameter Surface of Spheroidal Iron-Based Material and And to provide a manufacturing method.

【００２１】さらに、耐焼付き性、耐摩耗性に優れたＦ
ｅ合金相をＣｕ系焼結材料中に高濃度に分散させてなる
銅系焼結摺動材料並びに焼結摺動部材およびその製造方
法を提供することにある。Further, F which is excellent in seizure resistance and abrasion resistance
An object of the present invention is to provide a copper-based sintered sliding material obtained by dispersing an e-alloy phase in a Cu-based sintered material at a high concentration, a sintered sliding member, and a method for manufacturing the same.

【００２２】[0022]

【課題を解決するための手段および作用・効果】低速
で、かつ高面圧下の潤滑切れが起こり易い摺動条件下で
使用される作業機軸受材料は、適度の硬さを有しなが
ら、耐焼付き性および／または耐摩耗性に優れた特性を
持つことが必要であり、この結果として、異音の発生防
止、給脂間隔の延長が達成されるものである。このよう
な観点から、本発明では、このような特性を持つ材料と
して、Ｆｅ系合金規則相を形成し易いＡｌをＦｅ相中に
含有するＦｅ−Ａｌ−Ｃｕ系、Ｆｅ−Ａｌ−Ｃｕ−Ｃ系
合金相が優れていることを明らかにした点に特徴があ
る。とりわけ、炭素を含有させたＦｅ−Ａｌ−Ｃｕ−Ｃ
系合金相は、容易に焼結後の冷却段階でマルテンサイト
および／またはベイナイト組織に焼入れ硬化することが
できることから、その耐摩耗性の改善に安価に対応する
ことができる。[Means, Actions and Effects for Solving the Problems] A working machine bearing material used at a low speed and under a sliding condition where lubrication is likely to occur under a high surface pressure has a suitable hardness and is resistant to burning. It is necessary to have a property excellent in sticking property and / or wear resistance, and as a result, the prevention of abnormal noise and the extension of the greasing interval are achieved. From such a point of view, in the present invention, as a material having such characteristics, Fe-Al-Cu system and Fe-Al-Cu-C system containing Al which easily forms an Fe-based alloy ordered phase in the Fe phase. It is characterized in that it was clarified that the alloy phase was excellent. In particular, Fe-Al-Cu-C containing carbon
Since the alloy phase can be easily quench-hardened to the martensite and / or bainite structure in the cooling step after sintering, it is possible to cope with the improvement of the wear resistance at low cost.

【００２３】要するに、第１発明による焼結摺動材料
は、鉄系焼結摺動材料であって、少なくとも０．５重量
％以上のＡｌを不可避成分として含有するとともに、Ｃ
ｕを１０〜５０重量％含有してなることを特徴とするも
のである。In short, the sintered sliding material according to the first invention is an iron-based sintered sliding material, which contains at least 0.5% by weight or more of Al as an unavoidable component, and C
It is characterized by containing 10 to 50% by weight of u.

【００２４】ＨＡＮＳＥＮの状態図集を参照すれば、実
用的な軸受Ｆｅ系合金で規則相を示す系としては、Ｆｅ
−Ａｌ、Ｆｅ−Ｓｉ、Ｆｅ−Ｃｏ、Ｆｅ−Ｎｉが挙げら
れるが、コスト的な観点からは、Ｆｅ−Ａｌ系、Ｆｅ−
Ｓｉ系を主体に用いたものが極めて有効である。Referring to the HANSEN phase diagram collection, as a practical Fe-based alloy system showing a regular phase, Fe
-Al, Fe-Si, Fe-Co, Fe-Ni can be mentioned, but from the viewpoint of cost, Fe-Al-based, Fe-
It is extremely effective to mainly use Si.

【００２５】また、Ａｌ、Ｓｉはともに鉄系摺動材料表
面に酸化物層を形成し、耐食性、耐酸化性に優れる作用
があり、前述の過酷な摺動条件下では、これらの酸化物
層が金属同士の接触を防止して、その耐焼付き性を著し
く改善することも好都合である。Al and Si both form an oxide layer on the surface of the iron-based sliding material, and have the effect of excellent corrosion resistance and oxidation resistance. Under the severe sliding conditions described above, these oxide layers are It is also advantageous to prevent metal-to-metal contact and to significantly improve its seizure resistance.

【００２６】なお、Ｆｅ−Ａｌ系、Ｆｅ−Ｓｉ系の規則
相としては、Ｆｅ３Ａｌ、ＦｅＡｌ、Ｆｅ３Ｓｉ、Ｆｅ
Ｓｉがある。これらの結晶はいずれもＢＣＣ構造であ
り、Ｆｅ原子とＡｌ原子および／またはＳｉ原子が極め
て強力に引き付け合いながら、規則正しくそれら原子同
士が最近接距離に配置されることから、この規則相の硬
さは、規則度が高まるとともに、金属間化合物に近い硬
さを示すことが良く知られている。しかも、Ｎｉ、Ｃｏ
を添加したＦｅ−Ａｌ系合金ではＦｅ−ＡｌとＮｉ−Ａ
ｌもしくはＣｏ−Ａｌの２種の規則相への二相分離反応
も関与することから、例えば６００℃での時効処理を施
すか、焼結後の冷却速度を遅くすることによって、顕著
に硬化させることができ、耐摩耗性の付与に極めて有効
である。しかし、これらの規則相硬さがビッカース硬さ
Ｈｖ８００を越えることはなく、摺動材料として用いた
場合においては、前述の相手摺動材となる作業機ピン表
面が熱処理で硬化されているので、ブッシュによるアタ
ックがなく、かつ摺動材自身が耐摩耗性に優れることは
好ましいことである。The Fe-Al-based and Fe-Si-based ordered phases include Fe 3 Al, FeAl, Fe 3 Si, and Fe.
There is Si. All of these crystals have a BCC structure, and Fe atoms and Al atoms and / or Si atoms attract each other very strongly, and the atoms are regularly arranged at the closest distance to each other. It is well known that, with increasing ordering degree, exhibits hardness close to that of an intermetallic compound. Moreover, Ni, Co
Fe-Al alloys with addition of Fe-Al and Ni-A
Since the two-phase separation reaction of 1 or Co-Al into two ordered phases is also involved, it is significantly hardened by, for example, performing an aging treatment at 600 ° C. or slowing the cooling rate after sintering. And is extremely effective in imparting abrasion resistance. However, the ordered phase hardness does not exceed the Vickers hardness Hv800, and when used as a sliding material, the surface of the working machine pin that is the mating sliding material is hardened by heat treatment. It is preferable that there is no attack by the bush and that the sliding material itself has excellent wear resistance.

【００２７】規則相が金属間化合物に近い硬さをもつこ
とから類推されるように、Ｆｅ原子とＡｌ原子および／
またはＳｉ原子が規則配列すると極めて安定である。そ
の逆に、凝着によってその原子的配列が乱されると極め
て不安定な状態になる。したがって、化学的な意味合い
からして、鋼製の作業機ピンの凝着性を低減させること
は摺動材料としての特性に好ましいのは明らかである。As can be inferred from the fact that the ordered phase has a hardness close to that of an intermetallic compound, Fe atoms and Al atoms and / or
Alternatively, if Si atoms are regularly arranged, it is extremely stable. On the contrary, when the atomic arrangement is disturbed by adhesion, it becomes extremely unstable. Therefore, from the chemical point of view, it is apparent that reducing the cohesiveness of the steel work machine pin is preferable for the properties as a sliding material.

【００２８】さらに、規則的な原子配列が不規則化する
段階においては、顕著な吸熱反応を伴うことから、本発
明による摺動材料が摺動面における発熱を抑える作用を
示すことはより好ましい。また、顕著な凝着によるので
はなくても、摺動面が摩擦熱によって昇温する場合にお
いても、規則相から不規則相への二次変態的な広い温度
範囲での吸熱作用を持つことを利用することによって、
結果的には耐凝着性を改善することが好ましいのは明ら
かである。Further, since a remarkable endothermic reaction is accompanied at the stage where the regular atomic arrangement is disordered, it is more preferable that the sliding material according to the present invention has an action of suppressing heat generation on the sliding surface. Even if the sliding surface is heated by frictional heat, not by remarkable adhesion, it must have an endothermic action in a wide temperature range like a secondary transformation from ordered phase to disordered phase. By using
As a result, it is clear that it is preferable to improve the adhesion resistance.

【００２９】さらに、これら規則・不規則変態と同様な
吸熱反応は、強磁性体から常磁性体に二次的変態する磁
気変態によっても顕著に引き起こされるので、例えば規
則・不規則変態温度と磁気変態温度とを調整することに
よって、更なる二次変態的な広い温度範囲での極めて顕
著な吸熱作用を引き起こさせるように設計することが可
能であり、耐凝着性の向上を図ることができることも本
発明に係る摺動材料の特徴である。Further, the endothermic reaction similar to these ordered / disordered transformations is remarkably caused by the magnetic transformation which is a secondary transformation from a ferromagnetic material to a paramagnetic material. By adjusting the transformation temperature, it is possible to design so as to cause an extremely remarkable endothermic action in a wide temperature range that is further secondary transformation, and it is possible to improve the adhesion resistance. Is also a feature of the sliding material according to the present invention.

【００３０】Ｆｅ−Ａｌ系においては、ＨＡＮＳＥＮの
状態図を参照して、Ｆｅ３Ａｌ規則相を発現する組成範
囲を推定すると、一般の鉄系材料の摺動面が１００℃で
焼付き性が始まるとすれば、前記第１発明において、前
記Ｆｅ系合金相中のＡｌは少なくとも２〜３５重量％含
有するのが適量である（第２発明）。同様に、Ｆｅ−Ｓ
ｉ系でも、ほぼ同範囲の添加量が適当である。さらに、
ＳｉとＡｌと適当に混ぜて使用することも好ましいが、
その際の鉄系焼結摺動材料中のＦｅ系合金相におけるＡ
ｌ＋Ｓｉの組成範囲は２〜３５重量％が適当であること
は明らかである（第３発明）。In the Fe-Al system, when the composition range in which the Fe 3 Al ordered phase is developed is estimated with reference to the HANSEN phase diagram, the sliding surface of a general iron-based material has a seizure property at 100 ° C. If starting, in the first invention, it is appropriate that the Fe-based alloy phase contains at least 2 to 35% by weight of Al (second invention). Similarly, Fe-S
Even in the case of the i type, the addition amount in the substantially same range is suitable. further,
It is also preferable to use a mixture of Si and Al as appropriate,
A in the Fe-based alloy phase in the iron-based sintered sliding material at that time
It is clear that the appropriate composition range of l + Si is 2 to 35% by weight (third invention).

【００３１】前記各発明においては、Ｆｅ合金相におい
て、Ｃｏ、Ｎｉの一種以上を５〜４０重量％含有し、Ｆ
ｅ系規則相の硬さをＨｖ３００〜８００に調整するのが
好ましい（第４発明）。In each of the above inventions, the Fe alloy phase contains 5 to 40% by weight of one or more of Co and Ni, and F
It is preferable to adjust the hardness of the e-based ordered phase to Hv 300 to 800 (the fourth invention).

【００３２】なお、本発明のＡｌを高濃度に含有する鉄
系焼結摺動材料を製造する際において、金属Ａｌの素粉
末を添加する場合には極めて顕著な膨張性を示し、Ｆｅ
−Ａｌ系、Ｆｅ−Ａｌ−Ｃ系ではとても強度的な観点か
ら摺動材料としての使用に耐えられない問題がある。そ
こで、本発明では、燐（鉄）、Ｓｉ、Ｔｉの一種以上
を０．２５重量％以上添加し、還元性を高めると同時に
部分的な液相を出現させることによって焼結性を促進す
る、１０重量％以上のＣｕ粉末を添加して、焼結初期
においてＣｕ系の液相を発生させることによって焼結を
促進する、Ｃｕ粉末に固溶して融点を下げるＳｎ、Ｓ
ｉ、燐、Ｍｎ等の元素を１０重量％の範囲内で調整して
焼結性を促進する、という手段によって前述の顕著な膨
張性を制御することとし、Ｆｅ−Ａｌ系を主体とする規
則相焼結摺動材料および規則相がＣｕ系成分によって容
易に製造できるようにした。In the production of the iron-based sintered sliding material containing a high concentration of Al according to the present invention, when the elementary powder of metallic Al is added, it exhibits extremely remarkable expandability.
-Al type and Fe-Al-C type have a problem that they cannot withstand use as a sliding material from a very strong viewpoint. Therefore, in the present invention, one or more kinds of phosphorus (iron), Si, and Ti are added in an amount of 0.25% by weight or more to enhance the reducing property and at the same time to make the partial liquid phase appear to promote the sinterability. 10% by weight or more of Cu powder is added to promote sintering by generating a Cu-based liquid phase in the early stage of sintering. Sn, S which form a solid solution with Cu powder to lower the melting point
The above-mentioned remarkable expansion property is controlled by means of adjusting the elements such as i, phosphorus and Mn within the range of 10% by weight to promote the sinterability, and the rule mainly composed of Fe-Al system. The phase-sintered sliding material and the ordered phase were made to be easily manufactured by the Cu-based component.

【００３３】とりわけ、軟質なＦｅ粉末とＡｌ粉末の混
合粉末を利用することによるその難焼結性を解決し、よ
り安価な軸受を製造するために、Ｃｕ添加量を極力低減
し、Ｓｎ、Ｔｉ、Ｐ、Ｓｉの一種以上を０．１〜５重量
％の範囲内で添加することによって焼結性を改善するこ
とが好ましい（第８発明）。In particular, in order to solve the difficulty of sintering due to the use of a mixed powder of soft Fe powder and Al powder and to manufacture a cheaper bearing, the amount of Cu added is reduced as much as possible, and Sn and Ti are added. It is preferable to improve the sinterability by adding one or more of P, Si and P in the range of 0.1 to 5% by weight (eighth invention).

【００３４】また、１０〜５０重量％のＣｕの添加は、
比較的低温側の焼結によってその材料の焼結性を高める
が、５０重量％以上の添加では焼結時の液相量が多くな
り過ぎ、焼結体の保形性が悪くなるとともに、コストが
高くなる。The addition of 10 to 50% by weight of Cu is
The sintering property of the material is improved by sintering at a relatively low temperature side, but if 50% by weight or more is added, the amount of liquid phase at the time of sintering becomes too large, the shape retention of the sintered body deteriorates, and the cost is reduced. Becomes higher.

【００３５】また、炭素を添加した場合には鉄合金相へ
のＣｕの固溶度が少なくなることによって同一Ｃｕ添加
量同士で焼結時の液相量を比較した場合には液相量が多
くなるので、Ｃ添加によってＣｕ添加を少なくすること
ができることもコストを下げるのに良い。Further, when carbon is added, the solid solubility of Cu in the iron alloy phase decreases, and when the amounts of liquid phase at the time of sintering are compared with each other with the same amount of Cu added, the amount of liquid phase is Since the amount increases, the addition of C can reduce the addition of Cu, which is also good for reducing the cost.

【００３６】前述のＡｌの添加による膨張は、Ａｌ添加
量が多いほど大きくなるために、それを抑えるためのＣ
ｕ添加量も多くなる問題がある場合には、金属Ａｌ粉末
の添加量を抑え、Ｆｅ−Ａｌ合金粉末を利用することが
極めて有効である。あるいは、Ｆｅ−Ａｌ合金粉末、Ｃ
ｕ−Ａｌ合金粉末などを利用することが、Ａｌの合金添
加方法として好ましいこともある。The expansion due to the addition of Al increases as the amount of Al added increases, so C for suppressing it increases.
When there is a problem that the added amount of u also increases, it is extremely effective to suppress the added amount of the metal Al powder and use the Fe—Al alloy powder. Alternatively, Fe-Al alloy powder, C
It may be preferable to use u-Al alloy powder as an Al alloy addition method.

【００３７】さらに、前記鉄系焼結摺動材料を製造する
際において、その摺動材料中のＦｅ合金相組成に近いＦ
ｅ系合金粉末とＣｕ粉末を混合成形して焼結すること
が、成形性の困難さを避けるため、また顕著な焼結時の
膨張性を抑えるために好ましいことであるが、Ｆｅ系合
金粉末の入手性と粉末コストが高いことが問題である。Further, in the production of the iron-based sintered sliding material, F which is close to the Fe alloy phase composition in the sliding material.
It is preferable to mix and mold the e-based alloy powder and the Cu powder and sinter to avoid the difficulty of formability and to suppress the expansive property during remarkable sintering. The problem is the availability and high cost of powder.

【００３８】前記Ｆｅ−Ａｌ−Ｃｕ−Ｃ系焼結摺動材料
における適正なＣ添加量は焼結後の冷却によって得られ
るＦｅ合金相硬さ（Ｈｖ＝２５０〜８５０）によって、
０．０５重量％以上が好ましく、その上限は、Ｆｅ合金
相中にセメンタイト粒子を分散させて耐摩耗性を向上さ
せる観点から１．５重量％とするのが好ましい（第５発
明）。ここで、前記Ｆｅ合金相は、マルテンサイト、ベ
イナイト、粒状セメンタイトの一種以上の組織からなっ
ているのが良い（第６発明）。The proper amount of C added in the Fe-Al-Cu-C type sintered sliding material depends on the Fe alloy phase hardness (Hv = 250 to 850) obtained by cooling after sintering.
The amount is preferably 0.05% by weight or more, and the upper limit is preferably 1.5% by weight from the viewpoint of improving the wear resistance by dispersing the cementite particles in the Fe alloy phase (fifth invention). Here, the Fe alloy phase is preferably composed of one or more structures of martensite, bainite, and granular cementite (sixth invention).

【００３９】なお、前記冷却によって鉄系焼結摺動材料
のＦｅ合金相がマルテンサイトおよび／またはベイナイ
ト組織となるようにＦｅ合金相の焼入れ硬化性および／
または時効硬化性を高めるためのＳｉ、Ｍｎ、Ｎｉ、Ｃ
ｒ、Ｍｏ、Ｖ、Ｐ、Ｔｉ、Ｗ、Ｃｏの一種以上の合金元
素を各々０．１〜５重量％で含有されているのが好まし
い（第７発明）。とりわけ、Ｎｉの添加は含有するＡ
ｌ、Ｓｉ、Ｔｉと顕著な時効硬化性を示すので、耐摩耗
性の観点からは好ましいが、コスト的な観点から５重量
％以下に制限した。Ｎｉと同じ作用はＣｏの添加によっ
ても認められる。このＣｏ添加量の上限についても同じ
理由から５重量％とするのが良い。The quenching and hardenability of the Fe alloy phase and / or the Fe alloy phase of the iron-based sintered sliding material becomes a martensite and / or bainite structure by the cooling.
Or Si, Mn, Ni, C for enhancing age hardening
It is preferable that each of one or more alloy elements of r, Mo, V, P, Ti, W, and Co is contained in an amount of 0.1 to 5% by weight (seventh invention). In particular, the addition of Ni contains A
Since it shows remarkable age hardening properties such as 1, Si and Ti, it is preferable from the viewpoint of wear resistance, but it is limited to 5% by weight or less from the viewpoint of cost. The same action as that of Ni is recognized even when Co is added. The upper limit of the amount of Co added is preferably 5% by weight for the same reason.

【００４０】なお、前述のようにＣの添加によって鉄系
焼結摺動材料を焼入れ硬化する機能は、Ｃを含まない鉄
系焼結摺動材料に浸炭処理を施して焼入れ硬化すること
によって実現させても良いことは明らかである。とりわ
け、Ａｌを含有する本鉄系焼結摺動材料は、窒化、ガス
軟窒化によって顕著に硬化されるので、耐摩耗性の改善
には有効である。As described above, the function of quenching and hardening the iron-based sintered sliding material by adding C is realized by carburizing the iron-based sintered sliding material not containing C and hardening it. Obviously, you can do that. Especially, since the iron-based sintered sliding material containing Al is significantly hardened by nitriding and gas soft nitriding, it is effective for improving wear resistance.

【００４１】さらに、前述のように前記鉄系焼結摺動材
料のＦｅ合金相組成に近いＦｅ−Ａｌ系合金粉末とＣｕ
粉末を混合成形して焼結することが、焼結時の顕著な膨
張を抑える上で好ましい手段であるが、Ａｌを除いたＦ
ｅ−ＣやＦｅ−Ｃ−Ｃｕ系焼結材料用混合粉末、または
その混合粉末にＡｌ添加量を最小限に抑えた混合粉末を
２０００ｋｇｆ／ｃｍ２以上で加圧したプレス成形体を
焼結すると同時に、Ｃｕ−Ａｌ系材料を溶融してその成
形体に溶浸するか、もしくは前記プレス成形体を一旦焼
結した後に、再度Ｃｕ−Ａｌ系材料を溶浸することによ
ってＦｅ−Ａｌ−Ｃｕ系、Ｆｅ−Ａｌ−Ｃｕ−Ｃ系焼結
摺動材料を製造することが好ましい（第９発明）。Further, as described above, the Fe-Al alloy powder and Cu which are close to the Fe alloy phase composition of the iron-based sintered sliding material are used.
Mixing and molding powders and sintering is a preferable means for suppressing remarkable expansion during sintering, but F without Al is used.
When a mixed powder for e-C or Fe-C-Cu based sintering material, or a mixed powder in which the added amount of Al is minimized to the mixed powder is pressed at 2000 kgf / cm 2 or more, a pressed compact is sintered. At the same time, the Fe-Al-Cu-based material is obtained by melting the Cu-Al-based material and infiltrating it into the formed body, or by once infiltrating the press-formed body and then infiltrating the Cu-Al-based material again. It is preferable to produce a Fe-Al-Cu-C based sintered sliding material (the ninth invention).

【００４２】前記各発明において、前記焼結摺動材料の
粒界に分散する元液相のＣｕ合金相および／または前記
焼結摺動材料のＦｅ合金相中に析出する微粒子のＣｕ合
金相が、Ｃｕ−Ａｌ状態図中に記載されるβ相および／
またはその変態相を含んでいるのが好ましい（第１０発
明）。In each of the above inventions, the Cu alloy phase of the original liquid phase dispersed in the grain boundaries of the sintered sliding material and / or the fine Cu alloy phase precipitated in the Fe alloy phase of the sintered sliding material are , Cu-Al phase diagram described in the phase diagram and /
Alternatively, it preferably contains the transformation phase thereof (the tenth invention).

【００４３】本発明では、Ｃｕ−Ａｌに固溶して融点を
下げるＳｎ、Ｓｉ、燐、Ｍｎ等の元素をＣｕに対して１
０重量％以下の範囲内で調整して溶浸温度を下げるとと
もに、顕著に膨張性を制御することとし、Ｆｅ−Ａｌ−
Ｃｕ−Ｃ系を主体とする鉄系焼結摺動材料を容易に製造
できるようにした。In the present invention, elements such as Sn, Si, phosphorus and Mn which form a solid solution in Cu-Al to lower the melting point are added to Cu.
The infiltration temperature is adjusted by adjusting it within the range of 0 wt% or less, and the expansivity is remarkably controlled.
An iron-based sintered sliding material mainly composed of a Cu-C system can be easily manufactured.

【００４４】ＳｎとＡｌは反発し合う性質を持ち、焼結
時や溶浸後の冷却時においてＳｎが焼結体から排出され
易い（発汗し易い）ことから、本発明では、ＳｎをＣｕ
添加量に対して１０重量％以下の範囲で添加することに
よってその発汗を防止した。また、ＴｉはＡｌとも反応
して本発明の鉄系焼結摺動材料中に分散するＣｕ合金相
を強化する働きをする。さらに、ＳｎはＣｕ−Ａｌ合金
系のβ相（ＨＡＮＳＥＮの状態図を参照）を安定化する
ことから、Ｔｉの添加はＳｎの発汗を防止してβ相を出
現し易くする働きをし、さらにそのβ相の出現によって
摺動時の耐焼付き性を改善する（特開２００１−２７１
１２９号公報参照）。また、Ｓｎが焼結体中に多く存在
し得ることは、後述する裏金との接合性によっても好ま
しいことである。Sn and Al have the property of repelling each other, and Sn is easily discharged from the sintered body during sintering or during cooling after infiltration (perspiration easily). Therefore, Sn is replaced by Cu in the present invention.
The perspiration was prevented by adding it in the range of 10% by weight or less based on the added amount. Ti also reacts with Al to strengthen the Cu alloy phase dispersed in the iron-based sintered sliding material of the present invention. Furthermore, since Sn stabilizes the β phase of the Cu-Al alloy system (see the phase diagram of HANSEN), addition of Ti serves to prevent sweating of Sn and facilitate the appearance of the β phase. The appearance of the β phase improves seizure resistance during sliding (Japanese Patent Laid-Open No. 2001-271).
129). It is also preferable that Sn is present in the sintered body in a large amount in view of the bondability with the back metal described later.

【００４５】また、Ｔｉの添加によって鉄系材料との接
合性が顕著に改善されることは後述するように、本発明
の鉄系焼結摺動材料を円筒状または略円筒状鉄系材料の
内径面に焼結接合または加熱接合した複層の鉄系焼結摺
動部材の製造に極めて重要である。As will be described later, the addition of Ti remarkably improves the bondability with the iron-based material. As described later, the iron-based sintered sliding material of the present invention can be used as a cylindrical or substantially cylindrical iron-based material. It is extremely important for manufacturing a multi-layered iron-based sintered sliding member that is sintered or heat-bonded to the inner diameter surface.

【００４６】さらに、後述するように固体潤滑剤として
黒鉛を分散させた本発明の鉄系焼結摺動材料において
は、Ｃｕ−Ａｌ、Ｃｕ−Ｓｎ系合金液相と黒鉛の濡れ性
が悪い問題があるが、Ｔｉの添加によって黒鉛表面にＴ
ｉＣを形成させることによって濡れ性を顕著に改善する
ことができる。Further, as described later, in the iron-based sintered sliding material of the present invention in which graphite is dispersed as a solid lubricant, the wettability between the Cu-Al, Cu-Sn alloy liquid phase and graphite is poor. However, the addition of Ti causes T on the graphite surface.
The wettability can be significantly improved by forming iC.

【００４７】なお、後述するように、Ｆｅ−Ａｌ−Ｃｕ
系焼結摺動材料中の各相のＥＰＭＡ組成分析（Ｘ線マイ
クロアナライザー分析）を行った結果、Ａｌ、ＴｉはＣ
ｕ合金相よりもＦｅ規則相中へ濃化するのに対して、Ｓ
ｎはＣｕ系相へ濃化し、Ｐはほぼ均等に固溶することが
明らかとなっている。また、Ｆｅ合金相中へ固溶するＣ
ｕ濃度は約２５重量％、Ｃｕ合金相へ固溶するＦｅ濃度
は約５重量％にまで及ぶことが明らかとなっている。As will be described later, Fe-Al-Cu
As a result of an EPMA composition analysis (X-ray microanalyzer analysis) of each phase in the sintered sintered sliding material, Al and Ti are C
While it concentrates in the Fe ordered phase rather than the u alloy phase, S
It has been clarified that n is concentrated in the Cu-based phase and P is almost uniformly solid-dissolved. In addition, C which forms a solid solution in the Fe alloy phase
It has been clarified that the u concentration is about 25% by weight, and the concentration of Fe dissolved in the Cu alloy phase is about 5% by weight.

【００４８】したがって、１０重量％以上のＣｕを含有
するＦｅ−Ａｌ−ＣｕおよびＦｅ−Ａｌ−Ｃｕ−Ｃ系焼
結摺動材料は、Ｆｅ合金相中には焼結時に最大でも約２
５重量％のＣｕを固溶しているため、焼結温度からの冷
却時や、低温度における時効処理によって、Ｆｅ合金相
内部に微細なＣｕ合金相が析出することが予想される。
とりわけ、析出するＣｕ合金相が前述の耐焼付き性に優
れ（特開２００１−２７１１２９号公報参照）、かつ高
硬度なβ相である場合には、Ｆｅ合金相自身の耐焼付き
性向上に寄与することは明らかである。Therefore, the Fe-Al-Cu and Fe-Al-Cu-C sintered sliding materials containing 10% by weight or more of Cu are contained in the Fe alloy phase at a maximum of about 2 at the time of sintering.
Since 5 wt% of Cu is solid-dissolved, it is expected that a fine Cu alloy phase will precipitate inside the Fe alloy phase during cooling from the sintering temperature or by aging treatment at a low temperature.
In particular, when the precipitated Cu alloy phase is a β phase having excellent seizure resistance (see JP 2001-271129 A) and high hardness, it contributes to improvement in seizure resistance of the Fe alloy phase itself. That is clear.

【００４９】また、Ｓｎは、Ｆｅ規則相へほとんど固溶
せずにＣｕ系相に濃化して、Ｃｕ合金相の摺動特性を高
めることが容易に理解できるが、本出願人が特開２００
１−２７１１２９号公報において開示しているように、
このＳｎは、Ｃｕ−Ａｌ系β相を顕著に安定化してβ相
を出現し易くすると同時に、Ｃｕ合金相の融点を下げて
易焼結性を高める働きをするが、Ａｌ共存下でＳｎが多
量に添加された場合には、金属間化合物を多量に析出し
て顕著に脆化するので、このＳｎの添加量をＣｕ添加量
の１０重量％以下とした。Further, it can be easily understood that Sn is concentrated in the Cu phase with almost no solid solution in the Fe ordered phase to enhance the sliding characteristics of the Cu alloy phase.
As disclosed in JP-A 1-271129,
This Sn remarkably stabilizes the Cu-Al-based β phase to facilitate the appearance of the β phase, and at the same time, lowers the melting point of the Cu alloy phase to enhance the easy sinterability, but Sn coexists in the presence of Al. When added in a large amount, a large amount of intermetallic compound is precipitated and remarkably embrittles, so the amount of Sn added is set to 10% by weight or less of the amount of Cu added.

【００５０】さらに、前記β相のＣｕ合金相の摺動特性
を高める、Ｓｎ、Ｔｉ、Ｎｉ、Ｍｎ、Ｓｉ、Ｐの一種以
上の元素が共存することが望ましいことは明らかであ
る。Further, it is clear that it is desirable that one or more elements of Sn, Ti, Ni, Mn, Si and P coexist to enhance the sliding characteristics of the β-phase Cu alloy phase.

【００５１】なお、前記鉄系焼結摺動材料中のＣｕ合金
相の分布や大きさ、後述する気孔の分散性や固体潤滑剤
の分散性はその摺動材料の摺動特性や強度に深く関係す
ることが良く知られており、鉄系焼結摺動材料に使用す
る鉄系粉末を６０μｍ（２５０メッシュ以下）で、より
好ましくは４５μｍ（３２５メッシュ以下）の微細なも
のにすることが好ましい（第１１発明）。The distribution and size of the Cu alloy phase in the iron-based sintered sliding material, the dispersibility of pores and the dispersibility of the solid lubricant described later are deeply related to the sliding characteristics and strength of the sliding material. It is well known that the iron-based powder used for the iron-based sintered sliding material has a fine particle size of 60 μm (250 mesh or less), more preferably 45 μm (325 mesh or less). (Eleventh invention).

【００５２】前述のように、本発明の鉄系焼結摺動材料
の優れた摺動特性および耐摩耗性は、その摺動材料中の
Ｆｅ合金相にあることは明らかであることから、本発明
では、更に、Ｆｅ合金相成分範囲の粒子をＣｕ系合金マ
トリックスに分散させた銅系焼結摺動材料を開発した。As described above, it is clear that the excellent sliding characteristics and wear resistance of the iron-based sintered sliding material of the present invention are in the Fe alloy phase in the sliding material. The invention further developed a copper-based sintered sliding material in which particles in the Fe alloy phase component range are dispersed in a Cu-based alloy matrix.

【００５３】要するに、第１２発明による焼結摺動材料
は、銅系焼結摺動材料であって、少なくとも２．０〜３
５重量％のＡｌを含有し、２５重量％以下のＣｕと、
０．０５〜１．５重量％のＣと、５〜４０重量％のＣｏ
と、５〜４０重量％のＮｉと、０．０５〜５．０重量％
のＳｉ、Ｍｎ、Ｎｉ、Ｃｒ、Ｍｏ、Ｖ、Ｔｉ、Ｐ、Ｃ
ｏ、Ｓｎの一種以上を含有する鉄合金相が、５〜５０重
量％分散されてなることを特徴とするものである。In summary, the sintered sliding material according to the twelfth invention is a copper-based sintered sliding material, and is at least 2.0-3.
Cu containing 5% by weight of Al and 25% by weight or less,
0.05-1.5 wt% C and 5-40 wt% Co
And 5 to 40 wt% Ni and 0.05 to 5.0 wt%
Si, Mn, Ni, Cr, Mo, V, Ti, P, C
The iron alloy phase containing one or more of o and Sn is dispersed in an amount of 5 to 50% by weight.

【００５４】ここで、Ｃｕ合金相において、少なくとも
Ａｌ、Ｓｎ、Ｔｉの一種以上を含有し、Ｃｕ−Ａｌ状態
図中に記載されるβ相および／またはその変態相を含ん
でいるのが好ましい（第１３発明）。Here, it is preferable that the Cu alloy phase contains at least one or more of Al, Sn and Ti, and contains the β phase and / or its transformation phase described in the Cu-Al phase diagram ( 13th invention).

【００５５】また、前記焼結摺動材料中に分散するＦｅ
合金相が、マルテンサイト、ベイナイト、粒状セメンタ
イトの一種以上の組織からなっており（第１４発明）、
硬さがＨｖ＝２５０〜８５０の銅系焼結摺動材料とする
のが好ましい。Further, Fe dispersed in the sintered sliding material
The alloy phase is composed of one or more structures of martensite, bainite, granular cementite (the fourteenth invention),
It is preferable to use a copper-based sintered sliding material having a hardness of Hv = 250 to 850.

【００５６】さらに、潤滑油の軸受摺動面への均一供給
を図る目的で、Ｆｅ系焼結摺動材料中に潤滑油を含有さ
せる気孔を分散させることは、軸受の耐焼付き性を高め
るだけでなく、軸受への給脂間隔を顕著に延長する効果
があるので、本発明では、前述の軸受用鉄系および／ま
たは銅系焼結摺動材料中の気孔を規定した。Further, for the purpose of uniformly supplying the lubricating oil to the sliding surface of the bearing, dispersing pores containing the lubricating oil in the Fe-based sintered sliding material only enhances the seizure resistance of the bearing. In addition, the present invention defines the pores in the above-mentioned iron-based and / or copper-based sintered sliding material for bearings because it has the effect of significantly extending the greasing interval to the bearings.

【００５７】通常、鉄系および／または銅系焼結摺動材
料は、０．５〜３０体積％の気孔を含有しているが、摺
動材料としては気孔が通気孔である３体積％以上が望ま
しく、またその上限は焼結体強度の観点から３０体積％
を越えないことが望ましい（第１５発明）。Usually, the iron-based and / or copper-based sintered sliding material contains 0.5 to 30% by volume of pores, but as the sliding material, 3% by volume or more in which the pores are ventilation holes. Is desirable, and the upper limit is 30% by volume from the viewpoint of the strength of the sintered body.
It is desirable not to exceed (15th invention).

【００５８】また、気孔中に含油する潤滑油の粘性は、
使用条件によって種々変えることができる（例えばＩＳ
Ｏ粘度等級１００〜１５００）が、例えば作業機ブッシ
ュのような高面圧、低摺動特性で使用する場合にはより
高粘度な潤滑油を含浸することが好ましく、また耐熱性
の高い合成潤滑油やそれと２〜１０重量％のワックス類
を溶融させたもの等を含油しても良い。The viscosity of the lubricating oil contained in the pores is
It can be changed variously depending on the use conditions (eg IS
O viscosity grade 100 to 1500) is preferably impregnated with higher viscosity lubricating oil when it is used with high surface pressure and low sliding characteristics such as in working machine bushing, and synthetic lubrication with high heat resistance. The oil may be impregnated with oil or a mixture of wax and 2 to 10% by weight of wax.

【００５９】また、前記多量の気孔を含有させる場合に
おいては、潤滑性の優れたＰＡ（ポリアミド）等の樹脂
やワックスを含浸させることも効果的である。In addition, in the case of containing a large amount of pores, it is also effective to impregnate a resin such as PA (polyamide) having excellent lubricity or a wax.

【００６０】さらに、前記鉄系および／または銅系焼結
摺動材料において、その耐焼付き性と耐摩耗性を改善す
るために、従来から良く知られている固体潤滑性の高
い、黒鉛、ＭｏＳ２、ＷＳ２、ＭｎＳ、ＣａＦ２等の固
体潤滑剤（３〜９重量％）を添加するのが好ましい（第
１６発明）。Further, in order to improve the seizure resistance and wear resistance of the iron-based and / or copper-based sintered sliding material, graphite, MoS, which is well known in the art and has high solid lubricity, is used. It is preferable to add a solid lubricant (3 to 9% by weight) such as 2 , WS 2 , MnS, and CaF 2 (sixteenth invention).

【００６１】なお、固体潤滑剤である黒鉛を鉄系焼結摺
動材料中に分散させた場合には、０．０６〜１ｍｍの粒
径が主体となる黒鉛に対して、前述の４５μｍ以下の微
細な鉄系粉末を用いて黒鉛粒子を取り囲むことが好まし
い。また、固体潤滑剤となる黒鉛は造粒等の手段で粒状
に調整されることが好ましい。なお、銅系焼結摺動材料
においてもこれと同じことが言える。When graphite, which is a solid lubricant, is dispersed in the iron-based sintered sliding material, the above-mentioned 45 μm or less is used for the graphite whose particle size is 0.06 to 1 mm. It is preferable to surround the graphite particles with a fine iron-based powder. Further, it is preferable that graphite serving as a solid lubricant is adjusted to be granular by means such as granulation. The same can be said for the copper-based sintered sliding material.

【００６２】さらに、前記黒鉛粒子周辺に不定形な気孔
が多く存在すると、その位置での切欠き作用による強度
低下が著しくなるために、後述するような溶浸方法を用
い、その気孔を低減した鉄系焼結摺動材料が好ましく、
またより多量の黒鉛を含有する際の鉄系焼結摺動材料の
気孔率は、例えば０．１〜１０体積％のように、できる
だけ少ない方が強度的な観点から好ましい。Further, if a large number of irregular pores exist around the graphite particles, the strength is significantly reduced due to the notch action at that position, so the pores are reduced by the infiltration method described below. Iron-based sintered sliding materials are preferred,
The porosity of the iron-based sintered sliding material when it contains a larger amount of graphite is preferably as small as possible, for example, 0.1 to 10% by volume, from the viewpoint of strength.

【００６３】また、黒鉛が鉄系マトリックス中に固溶し
ていき、黒鉛周辺にセメンタイトなどの大きな炭化物を
形成し、摺動時において相手材料を強烈に摩耗させる場
合が多く、またＭｏＳ２、ＷＳ２においても、反応して
硫化鉄や硫化銅を形成するので、固体潤滑材として、黒
鉛、ＭｏＳ２、ＷＳ２などを分散焼結する場合には、固
体潤滑材の表面に鉄との反応を防止するためのガラス系
材料をコーティングした状態にすることが望ましい（特
開平４−２５４５５６号公報参照）。なお、銅系焼結摺
動材料についても、ＭｏＳ２、ＷＳ２の分解、反応を防
止する観点からこれと同じことが言える。In addition, graphite often forms a solid solution in the iron-based matrix and forms large carbides such as cementite around the graphite, which often abrades the mating material strongly during sliding. In addition, MoS 2 , WS 2 also reacts to form iron sulfide or copper sulfide, so when graphite, MoS 2 , WS 2 or the like is dispersed and sintered as a solid lubricant, the reaction with iron is performed on the surface of the solid lubricant. It is desirable that the glass-based material for prevention is coated (see Japanese Patent Laid-Open No. 4-254556). The same applies to the copper-based sintered sliding material from the viewpoint of preventing decomposition and reaction of MoS 2 and WS 2 .

【００６４】さらに、硬質分散粒子による耐焼付き性お
よび耐摩耗性を改善する手段として、Ｍｏ（０．２〜１
０重量％）、Ｗ等の金属粒子、酸化物、炭化物、窒化物
等のセラミックス、超硬（Ｃｏ−ＷＣ系）、サーメット
（Ｎｉ−ＴｉＣ系）、高速度鋼粉末等の炭化物、窒化物
を含有する硬質分散材、さらにはＦｅＣｏ、ＮｉＡｌ、
ＴｉＡｌ、ＮｉＳｉ、ＮｉＴｉ等の金属間化合物の一種
以上が含有されているのが好ましい（第１６発明）。Further, as a means for improving the seizure resistance and wear resistance of the hard dispersed particles, Mo (0.2 to 1)
0% by weight), metal particles such as W, oxides, carbides, ceramics such as nitrides, carbide (Co-WC type), cermet (Ni-TiC type), carbides such as high speed steel powder, and nitrides. Hard dispersant containing, further FeCo, NiAl,
It is preferable that one or more intermetallic compounds such as TiAl, NiSi, and NiTi are contained (sixteenth invention).

【００６５】前記第１６発明においては、少なくとも２
〜９重量％の造粒された黒鉛が分散され、さらに０．１
〜５重量％のＭｏＳ２、ＷＳ２、ＭｎＳが分散されてい
るのが良い（第１７発明）。In the sixteenth invention, at least 2
~ 9% by weight of granulated graphite is dispersed,
5% by weight of MoS 2, WS 2, is good MnS is dispersed (seventeenth aspect).

【００６６】次に、固体潤滑剤を多く含有する強度の弱
い本発明の鉄系焼結摺動材料を補強する目的、本発明の
鉄系焼結摺動材料の使用量を少なくする目的等のため
に、本発明では、前述の鉄系または銅系焼結摺動材料を
裏金に一体化して複層焼結摺動部材として利用すること
が好ましい。ここで、一体化方法としては、前記摺動材
料をロウ付け、接着の各種方法や、この摺動材料を焼結
する時に接合する焼結接合法による方法がある。Next, for the purpose of reinforcing the iron-based sintered sliding material of the present invention containing a large amount of solid lubricant and having low strength, and for reducing the amount of use of the iron-based sintered sliding material of the present invention. Therefore, in the present invention, it is preferable that the above-mentioned iron-based or copper-based sintered sliding material is integrated with the back metal and used as a multilayer sintered sliding member. Here, as an integration method, there are various methods of brazing and adhering the sliding material, and a method by a sintering joining method of joining when sliding the sliding material.

【００６７】とりわけ、前述の銅系焼結摺動材料を裏金
に焼結接合する方法としては、Ｃｕ−Ｓｎ、Ｃｕ−Ｓｎ
−Ｐｂ系焼結摺動材料を裏金鋼板に焼結接合する従来か
らの方法が簡便に適用される。この方法は、前記Ｆｅ合
金相成分の粉末を青銅系のＣｕ−Ｓｎ、Ｃｕ−Ｓｎ−Ｐ
ｂ系粉末に混合した混合粉末や金属Ｃｕ、Ｓｎ、Ｐｂ粉
末やそれらの合金粉末で調整した粉末との混合粉末を裏
金となる鋼板上に散布し、７００℃以上の温度で一旦仮
焼結接合した後、圧延機などの機械的手段でその仮焼結
体を加圧成形して再度焼結して製造する方法であり、よ
り高密度な焼結層を得るには、加圧成形と焼結とを繰り
返すこととなる。Above all, as a method of sinter-bonding the above-mentioned copper-based sintered sliding material to the back metal, Cu-Sn, Cu-Sn
A conventional method of sinter-bonding a Pb-based sintered sliding material to a backing steel plate is simply applied. According to this method, the powder of the Fe alloy phase component is bronze-based Cu-Sn, Cu-Sn-P.
Disperse the mixed powder mixed with b-type powder or the mixed powder of metal Cu, Sn, Pb powder or the powder prepared by alloy powder thereof onto the steel plate as the backing metal, and temporarily sinter and join at a temperature of 700 ° C or more. After that, the pre-sintered body is pressure-molded by a mechanical means such as a rolling mill and then sintered again to be manufactured. The conclusion will be repeated.

【００６８】円筒状もしくは略円筒状の焼結摺動部材を
得る場合には、焼結摺動材料を円筒状、略円筒状もしく
は板状に成形・加工し、鉄系材料よりなる裏金に一体化
するのが好ましい（第１８発明）。In the case of obtaining a cylindrical or substantially cylindrical sintered sliding member, the sintered sliding material is molded and processed into a cylindrical shape, a substantially cylindrical shape or a plate shape, and integrated with a backing metal made of an iron-based material. It is preferable to convert it (the eighteenth invention).

【００６９】前記第１８発明において、前記裏金となる
鉄系材料の焼入れ性がＤＩ値＝２．０以下で、ガス急冷
もしくは油焼入れによってもフェライト、パーライト、
ベイナイトのいずれかの組織を示し、この裏金に焼結接
合する鉄系焼結摺動材料中のＦｅ合金相の一部以上をマ
ルテンサイト化することによって、この鉄系焼結摺動材
料に圧縮残留応力が働くようにするのが好ましい（第１
９発明）。この場合、前記裏金となる鉄系材料の気孔率
が３〜２０体積％に調整され、各気孔に潤滑油が含浸さ
れているのが良い（第２０発明）。In the eighteenth aspect of the invention, the hardenability of the iron-based material as the back metal is DI value = 2.0 or less, and ferrite, pearlite,
The iron-based sintered sliding material is compressed into this iron-based sintered sliding material by showing a structure of bainite and converting a part or more of the Fe alloy phase in the iron-based sintered sliding material to be sintered and joined to this back metal into martensite. It is preferable that residual stress is exerted (first
9 invention). In this case, it is preferable that the porosity of the iron-based material that serves as the back metal is adjusted to 3 to 20% by volume and that each pore is impregnated with lubricating oil (twentieth invention).

【００７０】また、円筒状もしくは略円筒状に成形され
て複層焼結ブッシュとされた複層焼結摺動部材において
は、両端面部の外周面の面取りが内周面の面取りよりも
小さくされているのが好ましい（第２１発明）。Further, in the multilayer sintered sliding member formed into a cylindrical shape or a substantially cylindrical shape to form a multilayer sintered bush, the chamfer of the outer peripheral surface of both end surfaces is made smaller than the chamfer of the inner peripheral surface. Is preferable (21st invention).

【００７１】さらに、前記第１８発明〜第２１発明にお
いては、円筒状もしくは略円筒状に成形された複層焼結
摺動部材であって、スラスト荷重を受けて摺動するよう
に前記裏金に鍔部が設けられ、この鍔部摺動面に焼入れ
硬化処理が施されているか、もしくは耐摩耗材料および
／または摺動材料が配されているのが好ましい（第２２
発明）。ここで、前記耐摩耗材料もしくは摺動材料は、
超硬、ステライト、鉄系耐摩耗材料、セラミックス、Ｃ
ｕ系耐摩耗材料のうちの一種であり、これらが溶射、ロ
ウ付け、焼結接合、溶浸接合、接着のうちのいずれかの
手段で一体化されるのが良い（第２３発明）。Further, in the eighteenth to twenty-first inventions, there is provided a multilayer sintered sliding member formed in a cylindrical shape or a substantially cylindrical shape, wherein the backing metal is slid on receiving a thrust load. It is preferable that a collar portion is provided, and that the sliding surface of the collar portion is subjected to quench hardening treatment, or is provided with an abrasion resistant material and / or a sliding material (22nd aspect).
invention). Here, the wear resistant material or the sliding material,
Carbide, stellite, iron-based wear resistant material, ceramics, C
It is a kind of u-based wear resistant material, and it is preferable that these materials are integrated by any one of thermal spraying, brazing, sinter bonding, infiltration bonding, and bonding (23rd invention).

【００７２】さらに、前記各発明における焼結摺動材料
が前記鍔部摺動面において一体化されているのが好まし
い（第２４発明）。Furthermore, it is preferable that the sintered sliding material in each of the above inventions be integrated on the flange sliding surface (the twenty-fourth invention).

【００７３】次に、円筒状もしくは略円筒状に成形され
た複層焼結摺動部材を製造するための製造方法は、予め
成分調整された鉄系焼結材料の成形体もしくは焼結体
を、円筒状もしくは略円筒状の鉄系材料よりなる裏金の
内径面に略内接するように配置し、前記鉄系焼結材料よ
り低融点に成分調整された銅系または銅アルミニウム系
材料を前記鉄系焼結材料の成形体もしくは焼結体に加熱
しながら溶浸することによってその鉄系焼結材料を膨張
させながら前記裏金に接合することを特徴とするもので
ある（第２５発明）。Next, a manufacturing method for manufacturing a multilayer sintered sliding member formed into a cylindrical shape or a substantially cylindrical shape is performed by forming a molded body or a sintered body of an iron-based sintered material whose components are adjusted in advance. A copper-based or copper-aluminum-based material whose component is adjusted to have a lower melting point than that of the iron-based sintered material and which is disposed so as to be substantially inscribed on the inner diameter surface of the backing made of a cylindrical or substantially cylindrical iron-based material The invention is characterized in that the iron-based sintered material is infiltrated while being heated and infiltrated into a molded body or a sintered body of a system-based sintered material to be bonded to the backing metal while expanding the iron-based sintered material (25th invention).

【００７４】なお、前記銅系焼結摺動材料中のＦｅ合金
相を焼入れ硬化させるためには、少なくとも８５０℃以
上の温度から冷却する必要があるので、焼結温度は８５
０℃以上であって、焼結後の冷却速度によって焼入れ硬
化するように、Ｎｉ、Ｃｒ、Ｍｎ、Ｍｏなどの合金元素
が調整されているのが好ましい。ただし、裏金鋼板は、
その冷却速度において焼入れ硬化しないような、例えば
ＳＰＣＣや炭素鋼鋼板ならなるのが好ましい。In order to quench-harden the Fe alloy phase in the copper-based sintered sliding material, it is necessary to cool it from a temperature of at least 850 ° C. or higher, so the sintering temperature is 85.
It is preferable that the alloying elements such as Ni, Cr, Mn, and Mo are adjusted so that the temperature is 0 ° C. or higher and the material is hardened by quenching at the cooling rate after sintering. However, the backing steel plate is
It is preferable to use, for example, SPCC or a carbon steel sheet that does not quench harden at the cooling rate.

【００７５】また、前述の鉄系焼結摺動材料を同様の方
法で複層焼結摺動部材とするには、Ｆｅ合金相粉末の添
加量をより増大させると良いので、前述の基本的な製造
方法は変わらない。Further, in order to make the above-mentioned iron-based sintered sliding material into a multilayer sintered sliding member by the same method, it is better to increase the addition amount of the Fe alloy phase powder. The manufacturing method does not change.

【００７６】前記複層の鉄系焼結摺動部材の製造方法に
おいては、円筒状もしくは略円筒状の鉄系材料の内径面
に、その内径とほぼ同じか僅かに小さい外径をもつとと
もに、Ａｌを除いたＦｅ−ＣやＦｅ−Ｃ−Ｃｕ系焼結材
料用混合粉末、またはその混合粉末にＡｌ添加量を最小
限に抑えた混合粉末を、２０００ｋｇｆ／ｃｍ２以上で
加圧成形した成形体を配置し、この成形体を焼結すると
同時に、Ｃｕ−Ａｌ系材料を溶融してその成形体に溶浸
することによって、その成形体内での焼結とＡｌ成分の
拡散によって膨張が始まり、鉄系焼結摺動材料を鉄系材
料の内径面に押し付けながら接合することができる。In the method for producing a multi-layered iron-based sintered sliding member, the inner diameter surface of a cylindrical or substantially cylindrical iron-based material has an outer diameter that is substantially the same as or slightly smaller than the inner diameter. Fe-C or Fe-C-Cu-based mixed material powder excluding Al, or a mixed powder in which the amount of Al added to the mixed powder is minimized, is compacted at 2000 kgf / cm 2 or more. By arranging the body and sintering the compact, at the same time when the Cu-Al-based material is melted and infiltrated into the compact, expansion starts due to sintering in the compact and diffusion of the Al component. The iron-based sintered sliding material can be joined while being pressed against the inner diameter surface of the iron-based material.

【００７７】なお、前記溶浸するＦｅ−ＣやＦｅ−Ｃ−
Ｃｕ系のプレス成形体は、一旦焼結した後に、鉄系材料
の内径面に配置して溶浸する方法であっても良いのは明
らかである。The infiltrating Fe-C or Fe-C-
It is obvious that the Cu-based press-molded body may be sintered and then placed on the inner diameter surface of the iron-based material and infiltrated.

【００７８】さらに、前記溶浸方法で作った鉄系摺動材
料においても、溶浸後に再加熱することによってＡｌの
合金化がより進行して更なる膨張性が出現することが容
易に想定されることから、溶浸法で作った鉄系焼結摺動
材料を鉄系材料内径面に配置して、再加熱して接合する
方法を用いるのが良く、また、接合面に予め適正なロウ
剤を配置し、その接合性を改善することも好ましい。Further, even in the iron-based sliding material produced by the infiltration method, it is easily assumed that Al is further alloyed and further expandability appears by reheating after infiltration. Therefore, it is better to use a method in which an iron-based sintered sliding material made by the infiltration method is placed on the inner diameter surface of the iron-based material and reheated to join it. It is also preferred to place the agent to improve its bondability.

【００７９】円筒状および／または鍔付き円筒形状の鉄
系裏金材料の内径部に、前記鉄系焼結摺動材料を焼結接
合してなる複層焼結摺動部材の製造原理は、その前記鉄
系焼結摺動材料の焼結時に添加したＡｌが８００℃以上
の低温側において顕著に拡散し始めることによって大き
な膨張を引き起こし、その膨張によってその鉄系焼結摺
動材料を鉄系裏金材料の内径面に押し付けながら焼結接
合し、さらに昇温しながら８５０℃以上の温度で接合の
主体となるＣｕ合金成分が溶融してその焼結性を高め、
より高強度化させる点にある。The manufacturing principle of the multilayer sintered sliding member obtained by sintering and joining the above-mentioned iron-based sintered sliding material to the inner diameter of the cylindrical and / or flanged iron-based backing metal material is as follows. Al added at the time of sintering of the iron-based sintered sliding material begins to diffuse remarkably on the low temperature side of 800 ° C. or more to cause a large expansion, and the expansion causes the iron-based sintered sliding material to be transferred to the iron-based backing metal. Sintering is performed while pressing against the inner diameter surface of the material, and the Cu alloy component, which is the main component of the welding, is melted at a temperature of 850 ° C. or higher while further raising the temperature, and the sinterability is increased
There is a point to make it stronger.

【００８０】円筒状もしくは略円筒状にした前記鉄系ま
たは銅系焼結摺動材料を円筒状もしくは略円筒状の鉄系
材料の内径面にロウ付けする方法として、円筒状もしく
は略円筒状に成形された複層焼結摺動部材の製造方法で
あって、鉄系または銅系焼結摺動材料を、円筒状もしく
は略円筒状の鉄系材料よりなる裏金の内径面に略内接す
るように配置するとともに、それら焼結摺動材料と裏金
との間にロウ剤を配置し、前記焼結摺動材料の内周面か
らの高周波加熱によってその焼結摺動材料を前記裏金に
押し付けながらロウ付けすることが好ましい（第２６発
明）。なお、前記ロウ付け後に前記鉄系または銅系焼結
摺動材料中のＦｅ合金相を焼入れ硬化させるには、ロウ
付け温度が８５０℃以上であるのが好ましい。As a method of brazing the cylindrical or substantially cylindrical iron-based or copper-based sintered sliding material onto the inner diameter surface of the cylindrical or substantially cylindrical iron-based material, a cylindrical or substantially cylindrical shape is used. A method for manufacturing a formed multilayer sintered sliding member, wherein an iron-based or copper-based sintered sliding material is inscribed substantially on the inner diameter surface of a backing made of a cylindrical or substantially cylindrical iron-based material. While placing a brazing agent between the sintered sliding material and the back metal, and pressing the sintered sliding material against the back metal by high frequency heating from the inner peripheral surface of the sintered sliding material. It is preferable to braze (the twenty-sixth invention). In order to quench-harden the Fe alloy phase in the iron-based or copper-based sintered sliding material after the brazing, the brazing temperature is preferably 850 ° C. or higher.

【００８１】前記鉄系焼結材料を焼入れ硬化させるため
に、炭素量はその必要硬さに応じて自在に調整される
が、通常は０．０５〜１．０重量％の範囲とするのが好
ましい。さらに、本発明では、焼結接合後の冷却過程に
おいて、マルテンサイトおよび／またはベイナイトの一
種以上が形成されて硬化するように、Ｎｉ、Ｍｏ、Ｃ
ｒ、Ｗ等の一種以上の元素によって焼入れ性が調整さ
れ、かつ裏金の鉄系材料が焼入れ硬化されないようにし
て、冷却完了時点では鉄系焼結体が焼入れ変態によって
膨張し、裏金によって圧縮応力が残留するように調整
し、焼入れ時の裏金との剥離や焼結層の割れが発生しな
いようにするのが好ましい。In order to quench-harden the iron-based sintered material, the amount of carbon is freely adjusted according to the required hardness, but usually it is in the range of 0.05 to 1.0% by weight. preferable. Further, in the present invention, Ni, Mo, C are added so that one or more of martensite and / or bainite is formed and hardened in the cooling process after sinter bonding.
The hardenability is adjusted by one or more elements such as r and W, and the iron-based material of the backing metal is prevented from quenching and hardening.When the cooling is completed, the iron-based sintered body expands by quenching transformation, and the backing metal causes compressive stress. It is preferable to adjust so as to remain so that peeling from the back metal and cracks in the sintered layer do not occur during quenching.

【００８２】また、円筒形の軸方向への膨張収縮により
割れが発生する場合には、その防止手段として、鉄系焼
結材料の成形体を２つ以上多段積みに分けて焼結接合す
ることが好ましい。When cracking occurs due to expansion and contraction in the axial direction of the cylindrical shape, as a means for preventing cracking, two or more iron-based sintered material compacts are divided into multi-tiered layers and sintered and joined. Is preferred.

【００８３】前記円筒状、略円筒状または板状の鉄系裏
金材料としては、鋼、鋳鉄、焼結材料等が適用できるこ
とは明らかである。前記鉄系または銅系焼結摺動材料を
一体化した複層の焼結摺動部材においては、より潤滑油
を多く含有し、より長時間の給脂間隔を達成するため
に、鉄系の焼結材料を裏金に利用し、この裏金中におい
ても潤滑油を多量に含有させることが好ましい。It is obvious that steel, cast iron, sintered material, etc. can be applied as the above-mentioned cylindrical, substantially cylindrical or plate-shaped iron-based backing metal material. In the multi-layered sintered sliding member in which the iron-based or copper-based sintered sliding material is integrated, the iron-based sintered sliding member contains more lubricating oil and is made to achieve a longer lubrication interval. It is preferable that a sintered material is used for the back metal and a large amount of lubricating oil is contained in the back metal.

【００８４】また、前記複層焼結摺動部材の製造方法
は、鉄系または銅系焼結材料を膨張させる金属であるＡ
ｌを添加する鉄系焼結体においては、Ａｌを少なくとも
０．１重量％以上含有することによって膨張性が顕著に
確認されるので、鉄系または銅系焼結材料を膨張させる
金属であるＡｌを少なくとも０．１重量％以上含有する
とともに、高温度側で液相を発生させて焼結体強度と焼
結接合性を確保するために、１０〜５０重量％のＣｕ、
０．１〜１０重量％のＳｎおよび０．１〜１０重量％の
Ｔｉのいずれか一種以上を含有してなり、円筒状もしく
は略円筒状の鉄系材料よりなる裏金の内径と略同じか、
または僅かに小さい外径を有する鉄系または銅系焼結材
料よりなる円筒状の成形体を、前記裏金の内径面に挿入
・配置し、（ａ）７００℃以上の温度で所定時間加熱す
ることによって、前記焼結材料を膨張させて前記裏金に
焼結接合させ、（ｂ）さらに昇温して８２０℃以上の温
度で加熱することによりＣｕ系合金液相を発生させるこ
とによって、前記焼結材料を緻密化させることを特徴と
するものである（第２７発明）。In the method for manufacturing the multilayer sintered sliding member, the metal A which expands the iron-based or copper-based sintered material is used.
In the iron-based sintered body to which 1 is added, since the expansiveness is remarkably confirmed by containing at least 0.1% by weight of Al, Al which is a metal that expands the iron-based or copper-based sintered material. In an amount of at least 0.1% by weight, and in order to generate a liquid phase on the high temperature side to secure the strength and sinter bondability of the sintered body, 10 to 50% by weight of Cu,
0.1 to 10 wt% of Sn and 0.1 to 10 wt% of Ti, and at least one of the inner diameter of the back metal made of a cylindrical or substantially cylindrical iron-based material,
Alternatively, a cylindrical compact made of an iron-based or copper-based sintered material having a slightly smaller outer diameter is inserted and placed on the inner diameter surface of the back metal, and (a) heated at a temperature of 700 ° C. or higher for a predetermined time. The sinter material is expanded and sinter-bonded to the back metal, and (b) the temperature is further raised and heated at a temperature of 820 ° C. or more to generate a Cu-based alloy liquid phase, whereby the sintering is performed. It is characterized in that the material is densified (the twenty-seventh invention).

【００８５】Ａｌの添加による膨張性は合金の拡散性が
活発になる８００℃以上の温度域で顕著に現れ始め、Ｃ
ｕが共存しない場合には１１００℃においても更に膨張
し続けるが、例えばＣｕを１５重量％以上添加した場合
には１０５０℃前後での液相の発生とともに収縮し始め
ることがわかる。The expandability due to the addition of Al begins to appear remarkably in the temperature range of 800 ° C. or higher where the diffusivity of the alloy becomes active, and C
It can be seen that when u does not coexist, it continues to expand even at 1100 ° C., but when Cu is added in an amount of 15 wt% or more, for example, it begins to contract with the generation of a liquid phase at around 1050 ° C.

【００８６】また、炭素を添加することによって、Ｆｅ
合金相へのＣｕの固溶度を減じることになり、焼結時の
Ｃｕの液相量が多くなり、より焼結性が促進される。Further, by adding carbon, Fe
The solid solubility of Cu in the alloy phase is reduced, the amount of Cu liquid phase during sintering is increased, and the sinterability is further promoted.

【００８７】本発明では、Ｆｅ−Ａｌ−Ｃｕの膨張収縮
特性を利用して、８００℃以上で、かつ最大膨張を示す
１０５０℃以下の温度域において収縮性にあまり寄与し
ない第三の合金元素を添加して液相を発生させることに
よって接合性を確保し、１０５０℃以上の温度での加熱
によって鉄系焼結体の緻密化と焼結体強度の確保を図る
ようにした。なお、前記Ｆｅ−Ａｌ−Ｃｕ系焼結摺動材
料において、円筒状もしくは略円筒状の鉄系材料との焼
結接合性を改善するための第三元素としては、少なくと
もＳｎ、Ｐ、Ｔｉ、Ｓｉの一種以上が選ばれる。例えば
ＳｎやＴｉを添加した場合においては大きな膨張性が発
現されるが、Ｃｕと合金化されることによって、低融点
化される特性を持つものである。各々の添加量として
は、１〜１０重量％の範囲で調整されるが、作用効果と
コスト的な観点からは５重量％以下とするのが好まし
い。In the present invention, by utilizing the expansion / contraction characteristics of Fe-Al-Cu, a third alloying element which does not contribute much to the contractibility in the temperature range of 800 ° C or higher and 1050 ° C or lower showing the maximum expansion is selected. By adding it to generate a liquid phase, the bondability is secured, and by heating at a temperature of 1050 ° C. or higher, the iron-based sintered body is densified and the sintered body strength is secured. In the Fe-Al-Cu based sintered sliding material, at least Sn, P, Ti, as the third element for improving the sinter bondability with the cylindrical or substantially cylindrical iron-based material, One or more types of Si are selected. For example, when Sn or Ti is added, great expandability is exhibited, but when alloyed with Cu, it has a characteristic of lowering the melting point. The addition amount of each is adjusted in the range of 1 to 10% by weight, but it is preferably 5% by weight or less from the viewpoints of working effects and cost.

【００８８】とりわけ、Ｔｉは微量添加によっても、炭
素を含む鉄相とＣｕ相の界面に炭化物を形成して、Ｃｕ
液相との濡れ性を顕著に改善するので、添加量としては
０．１重量％以上とするのが効果的である。In particular, even if a small amount of Ti is added, a carbide is formed at the interface between the iron phase containing carbon and the Cu phase to form Cu.
Since the wettability with the liquid phase is remarkably improved, it is effective that the addition amount is 0.1% by weight or more.

【００８９】また、Ｐは燐鉄として炭素を含有する鉄系
焼結体に添加した場合において膨張性を与えることは良
く知られている。また、Ｃｕとの合金化では強力な還元
作用を示し、内径面焼結接合技術においては極めて好ま
しい添加元素であり、燐鉄添加量としては、Ｆｅ−Ｃ固
溶体に対するＰの固溶度が約１．２重量％であるので、
Ｐ量として１．２重量％以下に抑えるのが好ましい。It is well known that P imparts expandability when added to an iron-based sintered body containing carbon as phosphorus iron. Further, when alloyed with Cu, it exhibits a strong reducing action, and is an extremely preferable additive element in the inner diameter surface sinter bonding technique. As the additive amount of phosphorus iron, the solid solubility of P to the Fe—C solid solution is about 1 .2% by weight,
It is preferable that the amount of P is 1.2% by weight or less.

【００９０】前記第２５発明〜第２７発明においては、
焼結接合後の冷却過程において、炭素を含有するＦｅ合
金相をマルテンサイト変態によって硬化させるとともに
膨張させ、同時に前記裏金は焼入れ硬化させないように
焼入れ性を調整することによって、前記焼結材料および
焼結接合を強化する圧縮残留応力を作用させるようにす
るのが好ましい（第２８発明）。In the twenty-fifth invention to the twenty-seventh invention,
In the cooling process after sinter-bonding, the Fe alloy phase containing carbon is hardened and expanded by martensitic transformation, and at the same time, the backing metal is adjusted for hardenability so as not to be hardened by quenching. It is preferable that a compressive residual stress that strengthens the bond is applied (the twenty-eighth invention).

【００９１】次に、第２９発明に係る焼結摺動部材の製
造方法は、円筒状もしくは略円筒状に成形された複層焼
結摺動部材の製造方法であって、円筒状もしくは略円筒
状の鉄系材料よりなる裏金にスラスト荷重を受けて摺動
するように鍔部が設けられ、この裏金の内径面に鉄系ま
たは銅系焼結摺動材料を焼結接合すると同時に、前記鍔
部摺動面に耐摩耗材料および／または摺動材料を接合す
ることを特徴とするものである。Next, a method for producing a sintered sliding member according to the twenty-ninth aspect of the present invention is a method for producing a multilayer sintered sliding member formed into a cylindrical shape or a substantially cylindrical shape, which has a cylindrical shape or a substantially cylindrical shape. -Shaped backing material made of iron-based material is provided with a flange so as to slide under a thrust load, and at the same time when the iron-based or copper-based sintered sliding material is sinter-bonded to the inner diameter surface of this backing material, The wear resistant material and / or the sliding material is joined to the sliding surface of the section.

【００９２】ここで、前記耐摩耗材料および／または摺
動材料は、少なくとも炭素１．５〜３．５重量％、Ｃｒ
５〜１７重量％を含有する高炭素高Ｃｒ鉄合金焼結材料
であるのが良い（第３０発明）。Here, the wear resistant material and / or the sliding material is at least 1.5 to 3.5% by weight of carbon and Cr.
A high carbon high Cr iron alloy sintered material containing 5 to 17% by weight is preferable (30th invention).

【００９３】また、本発明では、前記円筒状および／ま
たは鍔付き円筒形状複合焼結摺動部材において、焼結材
料と焼結接合する裏金面に潤滑油の溜り溝部を予め形成
しておき、前記方法によって内径面に焼結接合すること
によって潤滑油を貯蔵できるようにし、含油工程におい
て複合焼結摺動部材の含油量を増すようにした。また、
このような潤滑油溜りを持つ軸受では、焼結層自身に強
度を極端に低下させる気孔を、従来の含油軸受のように
１５体積％と多量に形成する必要がなく、潤滑油溜りに
ある潤滑油が焼結層中に気孔を通じて摺動面に供給され
る程度の開気孔率が保証されれば良いので、焼結層中の
開気孔率が十分に保証される気孔率である５体積％程度
にまで焼結層を緻密化できることになり、高強度な含油
焼結軸受が提供できるようになった。Further, in the present invention, in the cylindrical and / or flanged cylindrical composite sintered sliding member, a lubricating oil reservoir groove is formed in advance on the back metal surface which is sintered and joined to the sintered material, The lubricating oil can be stored by sintering and joining to the inner diameter surface by the above method, and the oil content of the composite sintered sliding member is increased in the oil impregnation step. Also,
In a bearing having such a lubricating oil sump, it is not necessary to form as many pores as 15 vol% in the sintered layer itself, which extremely lowers the strength, as in the conventional oil-impregnated bearing. It is sufficient that the open porosity is such that oil is supplied to the sliding surface through the pores in the sintered layer, so that the open porosity in the sintered layer is 5% by volume, which is a porosity that is sufficiently guaranteed. The sintered layer can be densified to a certain degree, and a high-strength oil-impregnated sintered bearing can be provided.

【００９４】また、本発明では、衝撃力による高面圧だ
けでなく、スラスト荷重のかかる状態での回転および／
または揺動摺動時においても耐焼付き性に優れ、土砂の
侵入に対する耐摩耗性とシール機能を付加した鍔付き作
業機ブッシュを提供することができる。とりわけ、コス
ト的には前記鍔付き円筒形状の複層鉄系焼結部材の円筒
状内径面に鉄系焼結摺動材料を焼結接合する際に、鍔部
のスラスト部摺動環境に応じて、超硬、ステライト、鉄
系耐摩耗材料、セラミックス、Ｃｕ系耐摩耗材料等の各
種の摺動材料および耐摩耗材料を裏金になる鉄系材料に
ロウ付け、焼結接合、溶浸接合することが好ましい。Further, in the present invention, not only the high surface pressure due to the impact force but also the rotation and / or the rotation under the thrust load are applied.
Alternatively, it is possible to provide a work implement bush with a collar, which is excellent in seizure resistance even when swinging and sliding, and has added wear resistance against the intrusion of earth and sand and a sealing function. Particularly, in terms of cost, when the iron-based sintered sliding material is sinter-bonded to the cylindrical inner diameter surface of the multi-layered iron-based sintered member with the flange, depending on the thrust part sliding environment of the flange part. Then, various sliding materials and wear-resistant materials such as cemented carbide, stellite, iron-based wear-resistant materials, ceramics, and Cu-based wear-resistant materials are brazed to the iron-based material serving as the backing metal, sintered, and infiltration-bonded. It is preferable.

【００９５】なお、後述する実施例においては、Ｆｅ−
３重量％Ｃ−１５重量％Ｃｒ−２．３重量％Ｍｏ−２．
１重量％Ｎｉ−０．２重量％Ｐの高炭素高Ｃｒ鉄系耐摩
耗焼結材料を焼結接合したが、その焼結材料は建設機械
の下転輪ローラ部のフローティングシール用材料として
耐久性に優れた材料である。In the examples described later, Fe-
3 wt% C-15 wt% Cr-2.3 wt% Mo-2.
A high carbon, high Cr iron-based wear-resistant sintered material of 1 wt% Ni-0.2 wt% P was sinter-bonded, and the sinter material was durable as a material for the floating seal of the lower wheel roller of construction machinery. It is a material with excellent properties.

【００９６】[0096]

【実施例】次に、本発明による焼結摺動材料並びに焼結
摺動部材およびその製造方法の具体的な実施例につい
て、図面を参照しつつ説明する。EXAMPLES Specific examples of the sintered sliding material, the sintered sliding member and the method for producing the same according to the present invention will be described with reference to the drawings.

【００９７】（実施例１）電解鉄（９９．９５重量％）
とＡｌ、Ｃｏとを用いて、各種組成の合金を真空雰囲気
下で溶解、製造し、鍛造後、小試験片に切り出し、それ
ら合金の磁気変態温度（キュリー点、℃）と、硬さと熱
処理との関係を調べた。Example 1 Electrolytic iron (99.95% by weight)
And Al and Co, alloys of various compositions are melted and manufactured in a vacuum atmosphere, forged, and then cut into small test pieces, and the magnetic transformation temperature (Curie point, ° C), hardness and heat treatment of these alloys I investigated the relationship.

【００９８】図１（ａ）（ｂ）には、０〜４０原子％Ｃ
ｏ、０〜４０原子％Ａｌの組成のＦｅ−Ａｌ−Ｃｏ三元
合金を１２００℃に加熱後急冷したもの（ａ）と、この
急冷後に６００℃で１０時間時効処理したもの（ｂ）の
それぞれのビッカース硬さ分布が示されている。これら
の図から、急冷したもの（図１（ａ））においても２５
〜４０原子％Ａｌ、１５〜３０原子％Ｃｏの範囲におい
てわずかな硬化傾向が認められるが、６００℃で時効処
理したもの（図１（ｂ））では、１５〜４０原子％Ａ
ｌ、１０〜４０原子％Ｃｏの範囲において顕著に硬化す
る領域が存在することがわかる。1 (a) and 1 (b), 0-40 atomic% C
o, a Fe-Al-Co ternary alloy having a composition of 0 to 40 atomic% Al, heated to 1200 ° C and then rapidly cooled (a), and this rapidly cooled and aged at 600 ° C for 10 hours, respectively (b). The Vickers hardness distribution of is shown. From these figures, even the rapidly cooled one (Fig. 1 (a)) has 25
A slight hardening tendency is observed in the range of ˜40 atomic% Al and 15-30 atomic% Co, but in the case of aging treatment at 600 ° C. (FIG. 1 (b)), 15-40 atomic% A
It can be seen that there is a region that is significantly hardened in the range of 1 and 10 to 40 atomic% Co.

【００９９】次に、図２には、図１（ｂ）において、
０、１０、１５、２０、３０、４０原子％Ｃｏ断面にお
けるＡｌ濃度（原子％）と硬さとの関係が示されてい
る。この図から、次のことがわかる。すなわち、０原子
％Ｃｏ（Ｃｏを添加しない場合）においては、Ａｌ濃度
の増加に伴って硬化している。この硬化割合は、急冷合
金で観察された増加の程度にほぼ等しいため、６００℃
での時効硬化現象がほとんど観察されていない。これに
対して、１０原子％Ｃｏにおいては、１５原子％Ａｌ
（約８重量％Ａｌ）において顕著に硬化し、２０原子％
Ａｌにて最大硬さ（Ｈｖ＝６２０）に達した後、３０原
子％Ａｌで時効硬化性が消失する。また、２０原子％Ｃ
ｏでのＡｌ添加の影響は、１０原子％Ａｌから時効硬化
性が確認され、３０原子％Ａｌで最大硬さ（Ｈｖ＝７７
０）に達した後、４０原子％Ａｌでほぼ時効硬化性が消
失する。さらに、３０原子％Ｃｏにおいては、４０原子
％Ａｌまで時効硬化性が確認されるが、４０原子％Ａｌ
に至ると顕著な時効硬化性はなくなる。Next, referring to FIG. 2, in FIG.
The relationship between the Al concentration (atomic%) and hardness in the 0, 10, 15, 20, 30, 40 atomic% Co cross section is shown. From this figure, the following can be seen. That is, in 0 atomic% Co (when Co is not added), it hardens as the Al concentration increases. This hardening rate is approximately equal to the degree of increase observed in the quenched alloys, so 600 ° C
Almost no age hardening phenomenon was observed. On the other hand, in 10 atom% Co, 15 atom% Al
Remarkably hardened at (about 8% by weight Al), 20 atom%
After reaching the maximum hardness (Hv = 620) with Al, the age hardenability disappears with 30 atomic% Al. Also, 20 atom% C
As for the effect of Al addition at 0, age hardening was confirmed from 10 atomic% Al, and the maximum hardness (Hv = 77) at 30 atomic% Al.
After reaching 0), the age hardenability disappears at 40 atomic% Al. Furthermore, in 30 at% Co, age hardening is confirmed up to 40 at% Al.
However, the marked age-hardening property disappears.

【０１００】上述の結果からすれば、Ｃｏ添加による時
効硬化性を効率的に発揮するには、１０〜３０原子％Ｃ
ｏおよび１０〜５０原子％Ａｌの範囲で調整されるのが
好ましく、より低温度側での時効硬化性はさらに、例え
ば５原子％程度の低Ａｌ、低Ｃｏ濃度側においても現れ
ることは明らかである。なお、上述のようなＣｏの添加
による顕著な時効硬化現象は、Ｆｅ系規則相の二相分離
反応に由来することは明らかであり、同様の現象はＦｅ
−Ａｌ−Ｎｉ系合金においても確認されている。さら
に、同様の現象がＡｌの代わりにＳｉおよびＣｏ、Ｎｉ
の代わりにＭｎの合金元素を用いることにより得られる
のは、熱力学的に予測される。From the above results, in order to effectively exhibit the age hardenability by the addition of Co, 10 to 30 atomic% C
It is preferable to adjust in the range of 0 and 10 to 50 atomic% Al, and it is clear that the age hardenability at the lower temperature side also appears on the low Al and low Co concentration side of, for example, about 5 atomic%. is there. It is clear that the remarkable age hardening phenomenon due to the addition of Co as described above originates from the two-phase separation reaction of the Fe-based ordered phase.
It has also been confirmed in -Al-Ni alloys. Furthermore, a similar phenomenon occurs when Si, Co, and Ni are used instead of Al.
What is obtained by using an alloying element of Mn instead of is predicted thermodynamically.

【０１０１】図３には、１０原子％Ｃｏを添加したＦｅ
−Ａｌ−Ｃｏ三元合金を、５℃／ｍｉｎの昇温、降温速
度で測定した磁化曲線から求めた磁気変態温度（キュリ
ー温度）とＡｌ原子％濃度との関係が示されている。な
お、図中には、ＨＡＮＳＥＮの状態図に記載のＦｅ３Ａ
ｌの規則不規則変態温度を熱分析、比熱、電気抵抗およ
び磁気変態法等の測定方法によって調査した結果が併せ
て示されている。一般に、磁気変態測定からの規則不規
則変態温度の測定方法は感度が低いものであるが、その
他の測定方法による結果を総合すると、Ｆｅ−Ａｌ合金
系におけるＦｅ ３Ａｌの規則不規則変態が５００℃で起
こるＡｌ濃度限界は１０原子％（約５重量％）であり、
前述のように室温においても規則不規則変態が起こるこ
と、および摺動面温度が１００〜２００℃にすぐに達成
することを考え合わせると、図３中の破線で示されるよ
うに、規則不規則変態が生じるＡｌ濃度限界は約４原子
％（約２重量％）であることが明らかである。したがっ
て、明確な規則不規則変態性を有効に利用するために
は、少なくとも４重量％以上の添加が好ましいことが分
かる。In FIG. 3, Fe containing 10 at% Co is added.
-Al-Co ternary alloy, temperature rise / fall rate of 5 ° C / min
Magnetic transformation temperature (curie
Temperature) and the Al atomic% concentration. Na
In the figure, Fe in the state diagram of HANSENThreeA
The orderly disordered transformation temperature of 1 was analyzed by thermal analysis, specific heat, electrical resistance
And the results of investigations by measurement methods such as magnetic transformation
Is shown. In general, the rule irregularities from magnetic transformation measurements
Although the method of measuring the law transformation temperature has low sensitivity,
Fe-Al alloy is a summary of the results of other measurement methods.
Fe in the system ThreeA disordered Al transformation occurs at 500 ° C.
The Al concentration limit is 10 atomic% (about 5% by weight),
As mentioned above, ordered disorder occurs even at room temperature.
And, the temperature of the sliding surface quickly reached 100-200 ℃
Considering what you do, it is shown by the broken line in FIG.
As described above, the Al concentration limit at which the ordered disorder occurs is about 4 atoms.
% (About 2% by weight). According to
In order to effectively utilize the distinct regular irregular transformation property
Is preferable to be added at least 4% by weight or more.
Light

【０１０２】さらに、Ｆｅ−１０原子％Ｃｏ−１５原子
％Ａｌでは、複数の磁気変態点が出現し、Ｆｅ−１０原
子％Ｃｏ−２０原子％Ａｌ合金では三段の磁気変態温度
が確認される。このことから、不規則状態、Ｆｅ３Ａｌ
型およびＦｅＡｌ型の３種類の原子配列が存在している
ことが確認されるとともに、規則相による複数の磁気変
態点出現域が、より高温度側とＡｌのより低濃度側に推
移して発現されることから、１０原子％Ｃｏの添加によ
ってＦｅ−Ａｌ系の規則相がより安定化され、この場合
の前述のＡｌ添加の適正量は１重量％以上で、さらなる
Ｃｏの添加（〜４０原子％）によって、Ａｌ添加の適正
量は０．５重量％にさがることが明らかである。Further, in Fe-10 atomic% Co-15 atomic% Al, a plurality of magnetic transformation points appear, and in Fe-10 atomic% Co-20 atomic% Al alloy, three-step magnetic transformation temperatures are confirmed. . From this, the disordered state, Fe 3 Al
-Type and FeAl-type atomic arrangements are confirmed to exist, and multiple magnetic transformation point appearance regions due to the ordered phase shift to the higher temperature side and the lower Al concentration side and appear. Therefore, the Fe-Al-based ordered phase is further stabilized by the addition of 10 atomic% Co. In this case, the appropriate amount of the above Al addition is 1% by weight or more, and further addition of Co (up to 40 atomic %), It is clear that the appropriate amount of Al addition is 0.5% by weight.

【０１０３】（実施例２）本実施例では、Ｆｅ規則相単
味の耐摩耗性を評価するために、表１に示される組成の
溶製材料よりなる直径１０ｍｍ、長さ５０ｍｍの円柱状
試験片を用いて、５００℃と６００℃での前記時効処理
時間を調整することによって各種の硬さを調整した後、
油潤滑下で、ＳｉＣを２０重量％含有したポルトランド
セメント円盤に摺動材料を押し付けたときの土砂摩耗性
を評価した。Example 2 In this example, in order to evaluate the wear resistance of the Fe ordered phase alone, a columnar test with a diameter of 10 mm and a length of 50 mm made of a molten material having the composition shown in Table 1 was carried out. After adjusting various hardness by adjusting the aging treatment time at 500 ° C. and 600 ° C. using a piece,
Under oil lubrication, earth and sand abrasion resistance when a sliding material was pressed against a Portland cement disk containing 20% by weight of SiC was evaluated.

【０１０４】[0104]

【表１】 [Table 1]

【０１０５】図４には、試験装置の概念図と試験条件と
が示されている。この試験においては、ビッカース硬さ
がＨｖ＝５００となるように焼入れ焼戻しされたＳ４５
基準材を試験材と同時に装置に取り付けて、試験材の摩
耗性を基準材の摩耗量に対する摩耗量の比で評価した。
図５に、本発明によるＦｅ系規則相材料の硬さを、比較
材とともに示す試験結果が示されている。この図から明
らかに、Ｆｅ系規則相の耐摩耗性が硬さの割に極めて優
れていることがわかる。これらの結果は、各合金を０．
１体積％以上の気孔率を含有する焼結材料として製造し
た場合においても同じであることは明らかである。FIG. 4 shows a conceptual diagram of the test apparatus and test conditions. In this test, S45 was quenched and tempered so that the Vickers hardness was Hv = 500.
The reference material was attached to the apparatus simultaneously with the test material, and the wear resistance of the test material was evaluated by the ratio of the wear amount to the wear amount of the reference material.
FIG. 5 shows the test results showing the hardness of the Fe-based ordered phase material according to the present invention together with the comparative material. From this figure, it is clear that the wear resistance of the Fe-based ordered phase is extremely excellent for its hardness. These results show that for each alloy
It is clear that the same is true when manufactured as a sintered material containing a porosity of 1% by volume or more.

【０１０６】（実施例３）本実施例では、表２に示され
る合金を真空溶解して、１０００〜１１５０℃での熱間
鍛造、熱間圧延で板状に加工した後、切断・丸曲げし、
図６に示される形状に機械加工したブッシュを摺動試験
片とし、６００℃での前記時効処理時間を調整すること
によって各種の硬さになるように調整した。比較材とし
ては、ＳＣＭ４２０肌焼き鋼に表面炭素濃度を約０．８
重量％に調整した浸炭処理ブッシュ（比較材１）、Ｓ４
３Ｃ焼入れ焼戻しブッシュ（比較材２）および高力黄銅
４種材（Ｃｕ−２５重量％Ｚｎ−５重量％Ａｌ−３重量
％Ｍｎ−２．５重量％Ｆｅ）（比較材３）を用いた。(Embodiment 3) In this embodiment, the alloys shown in Table 2 are melted in vacuum, hot forged at 1000 to 1150 ° C., processed into a plate shape by hot rolling, and then cut and bent. Then
Bushings machined into the shape shown in FIG. 6 were used as sliding test pieces and adjusted to various hardnesses by adjusting the aging treatment time at 600 ° C. As a comparative material, SCM420 case-hardened steel with a surface carbon concentration of about 0.8
Carburized bush adjusted to weight% (Comparative material 1), S4
A 3C quenched and tempered bush (comparative material 2) and a high-strength brass type 4 material (Cu-25 wt% Zn-5 wt% Al-3 wt% Mn-2.5 wt% Fe) (comparative material 3) were used.

【０１０７】[0107]

【表２】 [Table 2]

【０１０８】図７には、摺動試験装置の概念図と試験条
件が示されている。この摺動試験においては、供試ブッ
シュの投影面積に対して１０００ｋｇ／ｃｍ２まで１０
０ｋｇ／ｃｍ２毎に１００００回の往復摺動を行いなが
ら摺動面圧を段階的に高めて行き、焼付いて摩擦係数が
急増したり、急進的な摩耗や異音が発生した時点で試験
を中断して評価を行った。FIG. 7 shows a conceptual diagram of the sliding test device and test conditions. In this sliding test, up to 1000 kg / cm 2 was applied to the projected area of the bush under test up to 10 kg.
While sliding back and forth 10,000 times every 0 kg / cm 2, the sliding surface pressure is gradually increased, and the test is conducted when seizure causes a sharp increase in the friction coefficient, or sudden wear or abnormal noise. It was interrupted and evaluated.

【０１０９】図８には摺動摩擦係数の推移、図９には摺
動摩耗量の推移がそれぞれ示されている。これらの試験
結果から、本発明材が比較材に比べて極めて良好な耐焼
付き性を発揮するとともに、Ｆｅ規則相を時効硬化させ
た場合において耐摩耗性が改善されるのが明らかであ
る。この結果は、気孔率を極力少なくした高密度焼結摺
動材料においても適用されることは明らかである。FIG. 8 shows the change of sliding friction coefficient, and FIG. 9 shows the change of sliding wear amount. From these test results, it is apparent that the material of the present invention exhibits extremely good seizure resistance as compared with the comparative material, and the wear resistance is improved when the Fe ordered phase is age hardened. It is clear that this result is also applied to the high-density sintered sliding material whose porosity is minimized.

【０１１０】（実施例４）３００メッシュ以下のＦｅア
トマイズ粉末、Ｆｅ１０重量％Ａｌ、Ｆｅ１７重量％Ａ
ｌアトマイズ粉末、Ａｌアトマイズ粉末、Ｓｎアトマイ
ズ粉末、Ｎｉ１０Ｐアトマイズ粉末、Ｃｕ８Ｐアトマイ
ズ粉末、３００メッシュ以下のＴｉＨ粉末、燐鉄（２５
重量％Ｐ）、Ｓｉ粉末、Ｍｎ粉末、５μｍのカーボニル
Ｎｉ粉末、平均粒径６μｍの黒鉛等を用いて、表３、表
４に示される配合成分の混合粉末を作成し、図１０に示
される引張試験片（形状ブッシュ摺動試験片）を成形圧
力４ｔｏｎ／ｃｍ２で成形した。なお、これら成形体
は、１０−１ｔｏｒｒ以下の真空状態にて９５０〜１２
５０℃の範囲で１０分〜１ｈｒ焼結して、６００ｔｏｒ
ｒのＮ２ガス冷却後にそれらの寸法、組織を調査した。(Example 4) Fe atomized powder of 300 mesh or less, Fe 10 wt% Al, Fe 17 wt% A
l atomized powder, Al atomized powder, Sn atomized powder, Ni10P atomized powder, Cu8P atomized powder, TiH powder of 300 mesh or less, iron phosphate (25
% P), Si powder, Mn powder, 5 μm carbonyl Ni powder, graphite having an average particle size of 6 μm, etc. to prepare mixed powders of the compounding components shown in Tables 3 and 4 and shown in FIG. A tensile test piece (shape bush sliding test piece) was molded at a molding pressure of 4 ton / cm 2 . It should be noted that these molded products are 950 to 12 in a vacuum state of 10 -1 torr or less.
Sintered for 10 minutes to 1 hour in the range of 50 ° C, 600 torr
After cooling with r 2 N 2 gas, their size and texture were investigated.

【０１１１】[0111]

【表３】 [Table 3]

【表４】 [Table 4]

【０１１２】図１１〜図１３は、１１４０℃、１２００
℃、１２５０℃で各１ｈｒ真空焼結した時の前記引張試
験片長さを示したものである。なお、その他の詳細な寸
法測定結果は表３、表４中に合わせて示した。この結果
から明らかなように、図中に破線にて示される成形体長
さ（約９６．５５ｍｍ）に対して、Ｆｅ−Ａｌ二元系焼
結合金において、ＦｅとＡｌの素粉末を配合した焼結合
金では、１２５０℃までの高温度においても焼結収縮す
ることはなく、従来からの報告（例えばＤ．Ｊ．ＬＥＥ
ＡＮＤ Ｒ．Ｍ．Ｇｅｒｍａｎ、Ａｍｅｒｉｃａｎ
Ｐｏｗｅｒ Ｍｅｔａｌｌｕｒｇｙ Ｉｎｓｔｉｔｕｔ
ｅ，２１（１９８５．９））の通りに、顕著な膨張性を
示すことがわかった。また、Ａｌに対して熱力学的反発
性を有するＳｉ、Ｓｎ、Ｃを単独に添加した焼結合金に
おいても、顕著な膨張性を抑えることはなく、燐鉄（Ｆ
ｅ２５重量％Ｐ）を単独に添加した場合においてのみ１
２５０℃において焼結収縮性が認められた。したがっ
て、緻密なＦｅ−Ａｌ二元系焼結合金を得るためにはＦ
ｅ−Ａｌ二元合金粉末や二元合金粉末に少量のＡｌ素粉
末を添加することが望ましいのは明らかである（表３、
表４のＮｏ．３２参照）。11 to 13 show 1140 ° C. and 1200
The lengths of the tensile test pieces when vacuum-sintered at 1 ° C. and 1250 ° C. for 1 hour are shown. Other detailed dimensional measurement results are also shown in Tables 3 and 4. As is clear from this result, in the Fe-Al binary sintered alloy, a sintered body was prepared by mixing elementary powders of Fe and Al with respect to the compact length (about 96.55 mm) shown by the broken line in the figure. Bonded gold does not undergo sinter shrinkage even at high temperatures up to 1250 ° C, and has been reported in the past (for example, DJ LEE).
AND R. M. German, American
Power Metallurgy Institute
e, 21 (1985.9)). In addition, even in a sintered alloy in which Si, Sn, and C, which have thermodynamic repulsion with respect to Al, are added alone, remarkable expansion is not suppressed, and phosphorus iron (F
e 25 wt% P) only when added alone 1
Sintering shrinkage was observed at 250 ° C. Therefore, in order to obtain a dense Fe-Al binary sintered alloy, F
It is clear that it is desirable to add a small amount of Al elemental powder to the e-Al binary alloy powder or the binary alloy powder (Table 3,
No. of Table 4 32).

【０１１３】しかし、素粉末を用いたＦｅ−Ａｌ焼結合
金の難焼結性を改善するためのＣｕ添加の影響を調査し
た結果、Ｃｕ単独の添加では１０重量％未満では焼結収
縮性の改善がほとんどないが、１０重量％以上の添加に
よって焼結収縮性が認められるようになり、好ましくは
約２０重量％Ｃｕによって十分な焼結収縮性が確保され
ることがわかった。この原因は、図１４に示されるＦｅ
−１２重量％Ａｌ−２０重量％Ｃｕ焼結合金の組織観察
写真からわかるように、Ｆｅ−Ａｌ合金相中にＣｕを多
量に固溶して、Ｆｅ−Ａｌ合金相粒子間にＣｕ−Ａｌ系
合金が液相として残留する量が少なくなるためである。
したがって、Ｆｅ−Ａｌ系焼結合金の焼結性を高めるた
めには、１０重量％以上のＣｕの添加が必要であり、よ
り好ましくは２０重量％以上であることがわかった。However, as a result of investigating the influence of Cu addition for improving the sintering resistance of the Fe—Al sintered alloy using the elementary powder, the addition of Cu alone causes the sintering shrinkage to be less than 10% by weight. Although there was almost no improvement, it was found that the addition of 10% by weight or more allows the sintering shrinkage to be recognized, and preferably about 20% by weight Cu secures sufficient sintering shrinkage. The cause of this is Fe shown in FIG.
As can be seen from the microstructure observation photograph of the -12 wt% Al-20 wt% Cu sintered alloy, a large amount of Cu was solid-solved in the Fe-Al alloy phase, and the Cu-Al-based alloy was formed between the Fe-Al alloy phase particles. This is because the amount of the alloy remaining as a liquid phase is reduced.
Therefore, it was found that in order to improve the sinterability of the Fe-Al based sintered alloy, it is necessary to add 10 wt% or more of Cu, and more preferably 20 wt% or more.

【０１１４】さらに、ＣｕとともにＳｉ，Ｓｎ，Ｐ，Ｔ
ｉ等のＣｕ合金の融点を下げる合金元素を複合添加する
ことによって、その焼結収縮性はさらに改善され、より
低温度側からの焼結収縮性が確保されることがわかる。
また、炭素を固溶させた焼結合金においては、より焼結
性が高められているが、これはＦｅ合金相へのＣｕの固
溶度が減じることによって、液相を発生させるＣｕが多
くなったためである。Furthermore, together with Cu, Si, Sn, P, T
It can be seen that the composite addition of alloying elements such as i that lowers the melting point of the Cu alloy further improves the sintering shrinkage and secures the sintering shrinkage from the lower temperature side.
Further, in a sintered alloy in which carbon is dissolved as a solid solution, the sinterability is further improved. This is because the solid solubility of Cu in the Fe alloy phase is reduced, so that a large amount of Cu is generated in the liquid phase. This is because

【０１１５】表５は、表３、表４中のＮｏ．２３〜２７
の焼結合金を１２００℃で０．５ｈｒ真空焼結・ガス冷
却したＦｅ−Ａｌ系規則相およびＦｅ−Ａｌ規則相を繋
ぐＣｕ−Ａｌ系相の化学組成をＸ線マイクロアナライザ
ー（ＥＰＭＡ分析）によって調べた結果を示したもので
ある。Table 5 shows the numbers in Tables 3 and 4. 23-27
X-ray microanalyzer (EPMA analysis) was performed to analyze the chemical composition of the Fe-Al ordered phase and the Cu-Al ordered phase connecting the Fe-Al ordered phases, which were obtained by vacuum sintering and sintering the sintered alloy of No. 1 at 1200 ° C for 0.5 hr. It shows the results of the examination.

【０１１６】[0116]

【表５】 [Table 5]

【０１１７】この表５から明らかなように、Ａｌ、Ｔｉ
はＣｕ−Ａｌ相よりもＦｅ−Ａｌ規則相中に顕著に濃縮
して存在しており、ＳｎはＣｕ−Ａｌ相中に濃縮すると
ともに、Ｆｅが３〜５重量％程度固溶することがわかっ
た。また、ＨＡＮＳＥＮの状態図を参考にした場合、Ｃ
ｕ−Ａｌ相には約９重量％のＡｌが含有され、さらにＳ
ｎ，Ｆｅなどのβ相を安定化する元素が含有されている
ことから、Ｃｕ−Ａｌ相がほぼβ相に相当すると考えら
れることがわかった。As is clear from Table 5, Al, Ti
Is significantly concentrated and present in the Fe-Al ordered phase rather than the Cu-Al phase, and it is understood that Sn is concentrated in the Cu-Al phase and Fe is solid-dissolved by about 3 to 5% by weight. It was When referring to the HANSEN state diagram, C
The u-Al phase contains about 9% by weight of Al and further contains S
It was found that the Cu-Al phase is considered to be almost equivalent to the β phase because it contains an element that stabilizes the β phase such as n and Fe.

【０１１８】さらに、Ｆｅ−Ａｌ合金相には焼結温度に
よって最大２５重量％のＣｕも固溶しており、焼結後の
冷却過程や焼結温度以下の低温側での再加熱によってＦ
ｅ−Ａｌ合金相中においてもβ相に相当する微細なＣｕ
合金相が析出することは明らかである。Further, up to 25% by weight of Cu is solid-dissolved in the Fe-Al alloy phase depending on the sintering temperature, and F is generated by the cooling process after sintering and reheating on the low temperature side below the sintering temperature.
Fine Cu corresponding to the β phase even in the e-Al alloy phase
It is clear that the alloy phase precipitates.

【０１１９】このことは、本出願人が既に特開２００１
−２７１１２９号公報において開示しているように、β
相Ｃｕ−Ａｌ合金が高面圧、低摺動速度の極めて厳しい
油潤滑条件下で使用する合金として優れた摺動特性と耐
摩耗性を発揮することから、極めて好ましいことである
ことは明らかである。This is already known by the present applicant from Japanese Patent Laid-Open No. 2001.
As disclosed in Japanese Patent Publication No. 2711129, β
It is clear that the phase Cu-Al alloy is extremely preferable because it exhibits excellent sliding characteristics and wear resistance as an alloy used under extremely severe oil lubrication conditions of high surface pressure and low sliding speed. is there.

【０１２０】なお、前記特開２００１−２７１１２９号
公報においても既に開示しているように、Ｓｉ，Ｓｎ，
Ｔｉの添加はβ相Ｃｕ−Ａｌ合金の焼結性をも顕著に高
めると同時に、顕著に硬化させるために、その添加量は
Ｃｕ添加量に対して１０重量％以下に抑えて使用するこ
とが好ましい。As already disclosed in Japanese Patent Laid-Open No. 2001-271129, Si, Sn,
The addition of Ti remarkably enhances the sinterability of the β-phase Cu-Al alloy and, at the same time, remarkably hardens it. Therefore, the addition amount of Ti should be 10% by weight or less based on the addition amount of Cu. preferable.

【０１２１】図１５は、Ｆｅ，Ａｌ素粉末を用いたＦｅ
−Ａｌ系焼結合金の焼結収縮性に対するＳｉ，Ｃｏ，Ｎ
ｉの影響を示したものである。この図から、前記時効硬
化性を顕著にするＮｉ，Ｃｏの添加によっても十分な焼
結収縮性が得られること、およびＳｉの添加によって焼
結収縮性がより改善されることがわかる。ＳｉはＡｌと
同結晶構造のＦｅ−Ｓｉ系規則相を形成する元素である
ことから、Ａｌとの複合添加は規則相を形成させる観点
から極めて望ましい元素である。FIG. 15 shows Fe containing Al and Fe powders.
-Si, Co, N for sintering shrinkage of Al-based sintered alloy
It shows the effect of i. From this figure, it can be seen that sufficient sintering shrinkage can be obtained even by adding Ni and Co that make the age-hardening property remarkable, and that sintering shrinkage can be further improved by adding Si. Since Si is an element that forms an Fe—Si-based ordered phase having the same crystal structure as Al, composite addition with Al is an extremely desirable element from the viewpoint of forming an ordered phase.

【０１２２】さらに、図１５中にはＦｅ１０重量％Ａｌ
合金粉末を利用して、Ａｌ素粉末添加量を抑えた規則相
焼結合金（表３、表４中のＮｏ．３２）の焼結収縮性が
示されているが、素粉末だけの焼結合金に比べ、良好な
収縮性を示すとともに、例えばＦｅ−Ａｌ、Ｆｅ−Ｃｏ
−Ａｌ、Ｆｅ−Ｎｉ−Ａｌ、Ｆｅ−Ａｌ−Ｓｉ等の合金
粉末の入手性が良い場合には、これらの合金粉末にＣｕ
もしくはＣｕ合金粉末を添加配合することによって焼結
収縮性の良い各種Ｆｅ−Ａｌ系焼結合金が得られること
が明らかである。Further, in FIG. 15, Fe 10 wt% Al
Sintering shrinkage of an ordered phase sintered alloy (No. 32 in Tables 3 and 4) in which the addition amount of Al elementary powder is suppressed by using alloy powder is shown, but only the elementary powder is fired and bonded. Compared with gold, it shows good shrinkability, and Fe-Al, Fe-Co, for example
-Al, Fe-Ni-Al, Fe-Al-Si and other alloy powders have good availability, Cu is added to these alloy powders.
Alternatively, it is clear that various Fe—Al based sintered alloys having good sintering shrinkage can be obtained by adding and blending Cu alloy powder.

【０１２３】（実施例５）本実施例は、実施例４に示さ
れる表３、表４中の代表的なＦｅ−Ａｌ焼結合金と、表
６に示されるようなＣｕ合金マトリックスに＃１００メ
ッシュ以下のＦｅ１５Ａｌ、Ｆｅ１０Ａｌ１０Ｃｏ、Ｆ
ｅ０．６Ｃ４Ａｌ０．７４Ｍｎ１．５１Ｃｒ０．３８Ｍ
ｏ合金粉を分散させるように焼結した材料の摺動特性の
調査を行ったものである。なお、比較材として、高力黄
銅４種材（Ｃｕ−２５重量％Ｚｎ−５重量％Ａｌ−３重
量％Ｍｎ−２．５重量％Ｆｅ）および表６中のＮｏ．５
３組成の鉄系含油軸受を用いた。(Example 5) In this example, the representative Fe-Al sintered alloys in Tables 3 and 4 shown in Example 4 and the Cu alloy matrix as shown in Table 6 were added to # 100. Fe15Al, Fe10Al10Co, F below mesh
e0.6C4Al0.74Mn1.51Cr0.38M
The sliding characteristics of the material sintered so that the o alloy powder was dispersed were investigated. As comparative materials, high-strength brass type 4 material (Cu-25 wt% Zn-5 wt% Al-3 wt% Mn-2.5 wt% Fe) and No. 6 in Table 6 were used. 5
An iron-based oil-impregnated bearing having three compositions was used.

【０１２４】[0124]

【表６】 [Table 6]

【０１２５】プレス成形体は、外径６６ｍｍ、内径４７
ｍｍ、高さ３５ｍｍの円筒体を４ｔｏｎ／ｃｍ２の加圧
力で成形した後に、気孔率が１０体積％、２０体積％程
度になるように真空焼結、Ｎ２ガス冷却したものを前述
の図６に示される形状にブッシュ加工したもの、および
６００℃で１ｈｒの加熱処理を行ったものに＃３０の潤
滑オイルを含浸させて摺動試験に供した。また、摺動試
験装置およびその試験条件は前述の図７に示されている
とおりである。摺動面圧は供試ブッシュの投影面積に対
して１０００ｋｇ／ｃｍ２まで５０ｋｇ／ｃｍ２毎に１
００００回の往復摺動を行いながら面圧を段階的に高
め、焼付いて摩擦係数が急増したり、急進的な摩耗や異
音が発生した時点で試験を中断して評価した。The press molded product has an outer diameter of 66 mm and an inner diameter of 47 mm.
After molding a cylindrical body having a size of 35 mm and a height of 35 mm with a pressurizing force of 4 ton / cm 2 , vacuum sintering and N 2 gas cooling so that the porosity becomes about 10% by volume and 20% by volume, respectively. A bushing processed into the shape shown in No. 6 and one heat-treated at 600 ° C. for 1 hr were impregnated with # 30 lubricating oil and subjected to a sliding test. The sliding test device and its test conditions are as shown in FIG. Suridomen圧1 per 50 kg / cm 2 to 1000 kg / cm 2 with respect to the projected area of the test bushing
The surface pressure was increased stepwise while performing reciprocal sliding of 0000 times, and the test was interrupted and evaluated when seizure resulted in a sharp increase in the friction coefficient, or when sudden wear or abnormal noise occurred.

【０１２６】図１６には、気孔率を約１０体積％に調整
した場合の試験結果が示されている。この結果から明ら
かなように、本発明材の多くが高力黄銅材に比べて明ら
かに高い耐焼付き面圧を示していることがわかる。とり
わけ、Ｃｏ，Ｎｉ等を含有しないＦｅ−Ａｌ−Ｃｕ、Ｆ
ｅ−Ｃ−Ａｌ−Ｃｕにおいて、前記図８に示されるもの
に比べて優れた耐焼付き性を有している。この原因は、
焼結体中に含浸させた潤滑油に起因することは明らかで
あり、少なくとも開気孔性が維持される５体積％以上の
気孔率が望ましいことは明らかである。また、Ｎｏ．４
７〜５７の結果からは、Ｆｅ−Ａｌ規則相をＣｕマトリ
ックス中に分散させた摺動材料においてもその耐焼付き
性は顕著に改善され、Ｆｅ系規則相がほぼ５重量％以上
でその改善効果が認められるが、１０重量％以上（近似
的には１０体積％以上）含有されるのが望ましいことが
わかる。FIG. 16 shows the test result when the porosity was adjusted to about 10% by volume. As is clear from these results, it can be seen that most of the materials of the present invention exhibit a significantly higher seizure resistance than the high strength brass materials. In particular, Fe-Al-Cu and F containing no Co or Ni
e-C-Al-Cu has excellent seizure resistance as compared with that shown in FIG. The cause is
It is clear that this is due to the lubricating oil impregnated into the sintered body, and it is clear that a porosity of at least 5% by volume that maintains open porosity is desirable. In addition, No. Four
From the results of 7 to 57, the seizure resistance is remarkably improved even in the sliding material in which the Fe-Al ordered phase is dispersed in the Cu matrix, and the improvement effect is obtained when the Fe-based ordered phase is approximately 5% by weight or more. However, it can be seen that it is desirable to contain 10% by weight or more (approximately 10% by volume or more).

【０１２７】また、Ｎｏ．５３〜５５のＦｅ−Ｃ−Ａｌ
規則相合金は、Ａｌ濃度が４重量％と低いが、焼結後の
ガス冷却で焼入れ硬化され、その硬さがＨｖ４５０以上
になっていることによって、耐焼付き性が改善されてい
ることがわかる。No. Fe-C-Al of 53-55
Although the ordered phase alloy has a low Al concentration of 4% by weight, it can be seen that the seizure resistance is improved by quenching and hardening by gas cooling after sintering and the hardness being Hv 450 or more. .

【０１２８】さらに、Ｎｏ．５７は、銅焼結マトリック
ス組成をβ相Ｃｕ−Ａｌ合金になるようにしたものであ
るが、極めて優れた摺動特性を示すことがわかる。Further, in No. No. 57 has a copper-sintered matrix composition of β-phase Cu-Al alloy, and it is understood that it exhibits extremely excellent sliding characteristics.

【０１２９】また、図１７には気孔率を約２０体積％に
調整した場合の摺動試験結果が示されているが、耐焼付
き性がより改善されていることがわかる。現実的には２
５体積％以上の気孔率を維持した場合には、軸受材料と
しての強度不足が問題になるものと考えられる。Further, FIG. 17 shows the results of the sliding test when the porosity was adjusted to about 20% by volume, and it can be seen that the seizure resistance is further improved. 2 in reality
When the porosity of 5% by volume or more is maintained, it is considered that insufficient strength as a bearing material poses a problem.

【０１３０】以上の実施例の結果から、Ｆｅ合金相自身
に極めて優れた耐焼付き性および耐摩耗性等の摺動、耐
摩耗特性が備わっていることが明らかになったが、Ｆｅ
系焼結合金にようにＣｕを多量に添加して、Ｆｅ規則相
をＣｕ相で繋ぐような組織や、Ｃｕ量をより多くしてＣ
ｕ相中にＦｅ合金相が分散するような組織を持つ銅系焼
結摺動材料を開発することが可能である。この場合、銅
系焼結摺動材料中に分散させるＦｅ−Ａｌ系合金相の量
は、１０体積％以上であると考えられるが、より好まし
くは２０体積％以上で５０体積％以下であることは明ら
かである。From the results of the above examples, it was revealed that the Fe alloy phase itself has extremely excellent seizure resistance and abrasion resistance, and sliding and abrasion resistance characteristics.
A large amount of Cu is added as in the case of sintered alloys, the structure is such that the Fe ordered phase is connected by the Cu phase, and the amount of Cu is increased to C.
It is possible to develop a copper-based sintered sliding material having a structure in which the Fe alloy phase is dispersed in the u phase. In this case, the amount of the Fe-Al alloy phase dispersed in the copper-based sintered sliding material is considered to be 10% by volume or more, but more preferably 20% by volume or more and 50% by volume or less. Is clear.

【０１３１】（実施例６）表７には本実施例で使用した
Ｆｅ系規則相焼結合金組成が示されている。混合粉末の
成形は、外径５３ｍｍ、内径４７ｍｍ、高さ３５ｍｍの
円筒体を２ｔｏｎ／ｃｍ２の加圧力で成形した後に、外
径６６ｍｍ、内径５３ｍｍ、高さ４０ｍｍの鋼管（Ｓ４
５Ｃ）の内径部にセットして１１５０℃、１ｈｒ真空焼
結した後、Ｎ２ガス冷却した。(Example 6) Table 7 shows the composition of the Fe-based ordered phase sintered alloy used in this example. The mixed powder is molded by molding a cylindrical body having an outer diameter of 53 mm, an inner diameter of 47 mm, and a height of 35 mm with a pressing force of 2 ton / cm 2 , and then forming a steel pipe having an outer diameter of 66 mm, an inner diameter of 53 mm, and a height of 40 mm (S4
5C) was set in the inner diameter portion, vacuum-sintered at 1150 ° C. for 1 hr, and then cooled with N 2 gas.

【０１３２】[0132]

【表７】 [Table 7]

【０１３３】なお、表７中には、超音波検査装置にて評
価した鋼管と焼結層との接合率が合わせて示されてい
る。この表から明らかなように、内径焼結接合にとって
もＳｎの添加が極めて効果的であり、０．２重量％以
上、好ましくは０．５重量％以上の添加が必要であるこ
とがわかる。また、燐鉄，Ｔｉ，Ｃｒ，Ｎｉの添加によ
って接合率が顕著に改善されているのがわかる。これ
は、これらの元素が焼結の際に発生する液相と外接する
鋼管表面の濡れ性を改善するためであることは明らかで
ある。また、黒鉛の単独添加による接合率の低下が大き
く認められなかったのは、黒鉛とＳｎを多量に含有する
液相が濡れにくいことから、焼結体内に発生する液相が
鋼管との接合界面に排出され易くなるためと考えられる
が、黒鉛と、Ｔｉ，Ｃｒ等の黒鉛との反応性に富んだ合
金元素とを複合添加した場合には、低融点のＳｎに対す
る黒鉛の影響が先行して作用し、さらにＴｉ，Ｃｒの作
用が重複することによって、接合性がより改善されるこ
とがわかった。Table 7 also shows the joining rates of the steel pipe and the sintered layer evaluated by the ultrasonic inspection apparatus. As is clear from this table, the addition of Sn is extremely effective also for the inner diameter sintering bonding, and it is necessary to add 0.2 wt% or more, preferably 0.5 wt% or more. Also, it can be seen that the bonding rate is remarkably improved by adding phosphorus iron, Ti, Cr and Ni. It is clear that this is because these elements improve the wettability of the surface of the steel pipe in contact with the liquid phase generated during sintering. Further, the decrease in the bonding rate due to the addition of graphite alone was not recognized to be large because the liquid phase containing a large amount of graphite and Sn is difficult to wet, and the liquid phase generated in the sintered body is the bonding interface with the steel pipe. It is considered that the effect of graphite on Sn having a low melting point precedes when graphite and an alloy element having high reactivity with graphite such as Ti and Cr are added in combination. It was found that the bondability is further improved by the action and the overlapping actions of Ti and Cr.

【０１３４】また、Ｂ１２，１３，１４，１５には、固
体潤滑用として水ガラスでＳＧＯ黒鉛を直径０．０５〜
０．８５ｍｍに造粒した黒鉛粒子を添加した鉄系焼結合
金の焼結接合を実施したが、Ａｌの添加が顕著な焼結接
合性を高めている。この原因は、Ａｌ添加による焼結膨
張性にあることは明らかである。B12, 13, 14, and 15 are made of water glass of SGO graphite having a diameter of 0.05 to 10 for solid lubrication.
Sintering and joining of an iron-based sintered alloy to which graphite particles granulated to 0.85 mm were added was performed, but the addition of Al significantly enhances the sinter-bonding property. It is clear that the cause of this is the sinter expansion due to the addition of Al.

【０１３５】さらに、接合する鋼管の内径面に予めスパ
イラル状の深さ約１ｍｍ、幅５ｍｍの油溝を機械加工で
形成したものに対しても、前述されたのと略同じように
内径面に接合焼結することができることがわかる。ま
た、この溝加工部を適宜工夫し、この溝部に潤滑油を含
有させることによって、より長時間の無給脂軸受に適し
ていることがわかる。Further, even in the case where a spiral oil groove having a depth of about 1 mm and a width of 5 mm is machined in advance on the inner diameter surface of the steel pipe to be joined, the inner diameter surface is formed in the same manner as described above. It can be seen that bonding and sintering can be performed. Further, it is understood that the grooved portion is properly devised and the lubricating oil is contained in the grooved portion, which is suitable for a grease-free bearing for a longer time.

【０１３６】（実施例７）本実施例では、２５０メッシ
ュ以下のＣｕアトマイズ粉末、Ｓｎアトマイズ粉末、１
００メッシュ以下のＦｅ１５Ａｌ、Ｆｅ１０Ａｌ１０Ｎ
ｉ、Ｆｅ０．６Ｃ４Ａｌ０．７４Ｍｎ１．５１Ｃｒ０．
３８Ｍｏアトマイズ粉末を用いて、前記実施例５の表６
に示される混合粉末を調整し、４００番の研磨紙で表面
を荒し、アセトンで良く洗浄した軟鋼板（ＳＳ４００、
厚さ３．５ｍｍ、幅９０ｍｍ、長さ３００ｍｍ）への接
合焼結実験を実施した。Example 7 In this example, Cu atomized powder of 250 mesh or less, Sn atomized powder, 1
Fe15Al, Fe10Al10N of 00 mesh or less
i, Fe0.6C4Al0.74Mn1.51Cr0.
Using the 38Mo atomized powder, Table 6 of Example 5 above.
Prepared mixed powder shown in (1), roughened the surface with No. 400 abrasive paper, and washed it well with acetone (SS400,
A bonding and sintering experiment for a thickness of 3.5 mm, a width of 90 mm, and a length of 300 mm was performed.

【０１３７】この実験においては、表６中の混合粉末を
前記軟鋼板上に３ｍｍの高さで散布して、露点−３８℃
のアンモニア分解ガス雰囲気炉で、８５０℃で２０分間
加熱されるように接合焼結した後に、圧延機で焼結層が
１．７ｍｍになるように圧延し、さらに圧延した散布材
を再度前述と同じ条件で焼結した。なお、Ｎｏ．５３〜
５５は、焼結温度を９５０℃として製造し、さらにＮ
ｏ．５７は金属Ａｌ素粉末を使うと、散布方式では顕著
な膨張が起こり製造できないので、３００メッシュ以下
のＣｕ２０Ａｌ合金粉末を、Ａｌ濃度と同量に調整した
混合粉末を使い、９００℃で焼結することによって製造
した。この焼結後にその焼結層を内側にして直系４５ｍ
ｍの円筒上に丸曲げ加工を施し、その時の鋼鈑からの焼
結層の剥離状況を観察した。この結果、曲げ加工時にお
ける割れ、剥離の発生はなかった。In this experiment, the mixed powder shown in Table 6 was sprayed on the mild steel plate at a height of 3 mm to give a dew point of -38 ° C.
In the ammonia decomposing gas atmosphere furnace of No. 3, after being bonded and sintered so as to be heated at 850 ° C. for 20 minutes, it was rolled by a rolling mill so that the sintered layer was 1.7 mm, and the rolled spreading material was again as described above. Sintered under the same conditions. In addition, No. 53-
55 was manufactured with a sintering temperature of 950 ° C.
o. No. 57 cannot be manufactured by using the metal Al element powder because of remarkable expansion by the spraying method. Therefore, Cu20Al alloy powder of 300 mesh or less is mixed at the same amount as the Al concentration and mixed powder is sintered at 900 ° C. Manufactured by. After this sintering, with the sintered layer inside, 45 m
A round bending process was performed on a cylinder of m, and the state of peeling of the sintered layer from the steel plate at that time was observed. As a result, neither cracking nor peeling occurred during bending.

【０１３８】（実施例８）本実施例では、１００メッシ
ュ以下のＦｅアトマイズ粉末、２５０メッシュ以下のＣ
ｕアトマイズ粉末、Ｓｎアトマイズ粉末、１００メッシ
ュ以下のＦｅ１５Ａｌ、Ｆｅ１０Ａｌ１０Ｎｉアトマイ
ズ粉末を用いて表８に示される混合粉末を調整し、実施
例７と同じ鋼鈑への接合焼結実験を実施した。なお、焼
結温度は９００℃として丸曲げ加工後の焼結層の剥離状
況を観察した。この観察において剥離の発生はなかっ
た。Example 8 In this example, Fe atomized powder of 100 mesh or less and C of 250 mesh or less.
Using u atomized powder, Sn atomized powder, Fe15Al and Fe10Al10Ni atomized powder of 100 mesh or less, the mixed powder shown in Table 8 was prepared, and the same joining and sintering experiment to the steel plate as in Example 7 was carried out. The sintering temperature was set to 900 ° C., and the peeling state of the sintered layer after round bending was observed. No peeling occurred in this observation.

【０１３９】[0139]

【表８】 [Table 8]

【０１４０】次に、図１８に示される定速摩擦摩耗試験
機と試験条件、図１９に示される摺動試験片を用いて、
摺動特性を調査した。なお、比較材としては、鋼鈑に接
合焼結されたＣｕ−１０重量％Ｓｎ−１０重量％Ｐｂの
鉛青銅焼結材料（ＬＢＣ）を用いた。図２０には、異常
摩耗および異常な摩擦係数の増大が発生する時点でのＰ
Ｖ値（限界ＰＶ値）を調査した結果が示されている。こ
の結果から、５重量％以上のＦｅ１５Ａｌ規則相合金粉
末の添加によって摺動特性が改善されるが、１０重量％
以上の添加がより好ましいことは明らかである。Next, using the constant speed friction and wear tester and test conditions shown in FIG. 18, and the sliding test piece shown in FIG. 19,
The sliding characteristics were investigated. As the comparative material, a lead bronze sintered material (LBC) of Cu-10 wt% Sn-10 wt% Pb which was joined and sintered to a steel plate was used. FIG. 20 shows P at the time when abnormal wear and abnormal increase in friction coefficient occur.
The result of investigating the V value (limit PV value) is shown. From this result, the sliding property is improved by adding 5 wt% or more of the Fe15Al ordered phase alloy powder, but 10 wt%
It is clear that the above additions are more preferable.

【０１４１】（実施例９）本実施例では、溶浸方法によ
る焼結材料の製造と鋼管内径部への接合に関して試験を
行った。本実施例では、表９に示される鉄系焼結材料の
混合粉末を先の実施例６と同じ条件でプレス成形体と
し、これにＣｕ、Ｃｕ２０Ｓｎ、Ｃｕ２０Ｓｎ２２Ａｌ
２Ｔｉの組成になるように調整した混合粉末成形体を準
備し、１１５０℃の真空雰囲気中で焼結と同時に溶浸し
た。(Example 9) In this example, a test was conducted on the production of a sintered material by the infiltration method and the joining to the inner diameter of the steel pipe. In this example, a mixed powder of the iron-based sintered material shown in Table 9 was formed into a press compact under the same conditions as in Example 6 above, and Cu, Cu20Sn, Cu20Sn22Al
A mixed powder compact prepared to have a composition of 2Ti was prepared, and was infiltrated simultaneously with sintering in a vacuum atmosphere of 1150 ° C.

【０１４２】[0142]

【表９】 [Table 9]

【０１４３】溶浸後の鉄系焼結材料の寸法変化率と気孔
率が表９に示されているが、いずれの場合も顕著な膨張
を示し、気孔率は焼結体強度の観点からは十分密度の高
いものが得られることがわかる。特に、先の実施例５と
同様の方法で固体潤滑用の造粒黒鉛を添加した材料にと
っては好ましい摺動材料になることは明らかである。The dimensional change rate and the porosity of the iron-based sintered material after infiltration are shown in Table 9. In both cases, remarkable expansion was observed, and the porosity was from the viewpoint of the strength of the sintered body. It can be seen that a sufficiently high density can be obtained. In particular, it is apparent that the sliding material is preferable for the material to which the granulated graphite for solid lubrication is added by the same method as in Example 5 above.

【０１４４】また、実施例６と同じ裏金に鉄系焼結材料
のプレス成形体を配置して、溶浸処理を行った場合にお
いては、容易に想像されるように、その裏金内径部に接
合されることがわかった。When a press-formed body of an iron-based sintered material was placed on the same back metal as in Example 6 and subjected to infiltration treatment, it was joined to the inner diameter of the back metal as easily imagined. I knew it would be done.

【０１４５】（実施例１０）実施例６で製造したＢ１２
〜１５および実施例９で製造したＤ４，９，１１，１２
を用いて、実施例３と同じ方法で含油処理した後に、摺
動試験を実施した。本実施例に供する試験片はすべて、
焼結または溶浸後に急冷して焼入れ硬化するように調整
し、Ｈｖ４５０以上の硬さに調整したものである。(Example 10) B12 produced in Example 6
~ 15 and D4, 9, 11, 12 produced in Example 9
Was subjected to an oil impregnation treatment in the same manner as in Example 3, and then a sliding test was performed. All the test pieces used in this example are
After sintering or infiltration, the hardness was adjusted to quench and harden by quenching, and the hardness was adjusted to Hv 450 or higher.

【０１４６】さらに、予備テストの結果、Ｂ１２〜１５
の試験片の端面部が面圧５００ｋｇｆ／ｃｍ２以上にお
いて欠ける場合のあることがわかったので、本実施例に
供する試験片は、内周面の油溝加工を止めるとともに、
両端面内周面に端面から３ｍｍ位置から３０°の面取り
を施したものとした。Further, as a result of the preliminary test, B12 to B15
Since it was found that the end surface portion of the test piece of 1 may be chipped at a surface pressure of 500 kgf / cm 2 or more, the test piece provided in this example stops the oil groove processing on the inner peripheral surface, and
The inner peripheral surfaces of both end surfaces were chamfered at 30 ° from a position 3 mm from the end surfaces.

【０１４７】図２１に摺動試験の結果が示されている。
Ａｌ添加量の少ないＢ１２，Ｂ１３，Ｄ１２は比較的低
面圧で焼付くが、先の図１６の結果と比較すると明らか
に黒鉛潤滑剤を分散させたことによる耐焼付き性の改善
が認められる。さらに、４重量％以上のＡｌを添加した
Ｂ１４，Ｂ１５，Ｄ４，Ｄ９，Ｄ１１の耐焼付き性改善
が顕著であることも明らかである。FIG. 21 shows the result of the sliding test.
B12, B13, and D12 with a small amount of added Al seize at a relatively low surface pressure, but in comparison with the results shown in FIG. 16, the seizure resistance is clearly improved by dispersing the graphite lubricant. Further, it is clear that the seizure resistance of B14, B15, D4, D9, and D11 containing 4% by weight or more of Al is significantly improved.

【図面の簡単な説明】[Brief description of drawings]

【図１】図１（ａ）は、Ｆｅ−Ａｌ−Ｃｏ三元合金を１
２００℃に加熱後急冷したもののビッカース硬さ分布を
示す図、図１（ｂ）は、この急冷後に６００℃で１０時
間時効処理したもののビッカース硬さ分布を示す図であ
る。FIG. 1 (a) shows a Fe-Al-Co ternary alloy as a 1
The figure which shows the Vickers hardness distribution of what was rapidly cooled after heating at 200 degreeC, and FIG.1 (b) is a figure which shows the Vickers hardness distribution of what was aged for 10 hours at 600 degreeC after this rapid cooling.

【図２】図２は、図１（ｂ）における０，１０，１５，
２０，３０，４０原子％Ｃｏ断面におけるＡｌ濃度（原
子％）と硬さとの関係を示すグラフである。FIG. 2 is a schematic diagram of 0, 10, 15, in FIG.
It is a graph which shows the relationship between Al concentration (atomic%) and hardness in a 20, 30, 40 atomic% Co cross section.

【図３】図３は、Ｆｅ−Ａｌ系合金相の規則不規則変態
領域を示すグラフである。FIG. 3 is a graph showing an ordered disordered transformation region of a Fe—Al based alloy phase.

【図４】図４は、摩耗試験の試験装置の概念図と試験条
件を示す図である。FIG. 4 is a conceptual diagram of a test apparatus for a wear test and a diagram showing test conditions.

【図５】図５は、Ｆｅ系規則相材料の硬さと摩耗比との
関係を示すグラフである。FIG. 5 is a graph showing the relationship between the hardness and wear ratio of Fe-based ordered phase materials.

【図６】図６は、摺動試験に供した試験片形状を示す断
面図である。FIG. 6 is a cross-sectional view showing the shape of a test piece used in a sliding test.

【図７】図７は、摺動試験装置の概念図（ａ）と試験条
件（ｂ）を示す図である。FIG. 7 is a diagram showing a conceptual diagram (a) and a test condition (b) of a sliding test device.

【図８】図８は、Ｆｅ系規則相材の摺動摩擦係数の推移
を示すグラフである。FIG. 8 is a graph showing changes in the sliding friction coefficient of the Fe-based ordered phase material.

【図９】図９は、Ｆｅ系規則相材の摺動摩耗量の推移を
示すグラフである。FIG. 9 is a graph showing changes in sliding wear amount of Fe-based ordered phase material.

【図１０】図１０は、引張試験片の形状を示す図であ
る。FIG. 10 is a diagram showing a shape of a tensile test piece.

【図１１】図１１は、ＦｅＡｌＣｕ系焼結特性（１１４
０℃）を示すグラフである。FIG. 11 shows FeAlCu-based sintering characteristics (114
It is a graph which shows (0 degreeC).

【図１２】図１２は、ＦｅＡｌＣｕ系焼結特性（１２０
０℃）を示すグラフである。FIG. 12 shows FeAlCu-based sintering characteristics (120
It is a graph which shows (0 degreeC).

【図１３】図１３は、ＦｅＡｌＣｕ系焼結特性（１２５
０℃）を示すグラフである。FIG. 13 shows FeAlCu-based sintering characteristics (125
It is a graph which shows (0 degreeC).

【図１４】図１４は、各種Ｆｅ系規則相焼結合金の焼結
組織（金属組織）を示す写真である。FIG. 14 is a photograph showing a sintered structure (metal structure) of various Fe-based ordered phase sintered alloys.

【図１５】図１５は、Ｆｅ−Ａｌ系規則相焼結合金の焼
結収縮性に対するＳｉ，Ｃｏ，Ｎｉの影響を示すグラフ
である。FIG. 15 is a graph showing the influence of Si, Co, and Ni on the sintering shrinkage of the Fe—Al based ordered phase sintered alloy.

【図１６】図１６は、Ｆ系規則相焼結合金の耐焼付き性
（気孔率約１０体積％）を示すグラフである。FIG. 16 is a graph showing seizure resistance (porosity: about 10% by volume) of an F-type ordered phase sintered alloy.

【図１７】図１７は、Ｆ系規則相焼結合金の耐焼付き性
（気孔率約２０体積％）を示すグラフである。FIG. 17 is a graph showing seizure resistance (porosity: about 20% by volume) of an F-type ordered phase sintered alloy.

【図１８】図１８は、定速摩擦摩耗試験機と試験条件を
示す図である。FIG. 18 is a diagram showing a constant speed friction wear tester and test conditions.

【図１９】図１９は、定速摩擦摩耗試験用の摺動試験片
形状を示す図である。FIG. 19 is a diagram showing a shape of a sliding test piece for a constant speed friction wear test.

【図２０】図２０は、Ｆｅ系焼結材料の摺動特性を示す
グラフである。FIG. 20 is a graph showing sliding characteristics of a Fe-based sintered material.

【図２１】図２１は、黒鉛分散摺動材料の耐焼付き性を
示すグラフである。FIG. 21 is a graph showing seizure resistance of a graphite-dispersed sliding material.

───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｆ１６Ｃ 33/12 Ｆ１６Ｃ 33/12 Ａ 33/14 33/14 Ｚ (72)発明者 大西 哲雄 大阪府枚方市上野３丁目１−１ 株式会社 小松製作所生産技術開発センタ内 Ｆターム(参考） 3J011 AA01 BA02 BA06 DA01 DA02 QA03 SB02 SB03 SB04 SB12 SB13 SB14 SB15 4K018 AA29 AA31 AB01 AB02 AB03 AB05 AB07 BA02 BA04 BA08 BA19 BC19 BD08 CA07 FA36 FA42 GA03 HA07 JA02 JA10 JA24 KA03 KA22 ─────────────────────────────────────────────────── ─── Continuation of front page (51) Int.Cl. 7 Identification code FI theme code (reference) F16C 33/12 F16C 33/12 A 33/14 33/14 Z (72) Inventor Tetsuo Onishi Osaka Hirakata City Ueno 3-chome 1-1 Komatsu Ltd. Production Technology Development Center F-term (reference) 3J011 AA01 BA02 BA06 DA01 DA02 QA03 SB02 SB03 SB04 SB12 SB13 SB14 SB15 4K018 AA29 AA31 AB01 AB02 AB03 AB05 AB07 BA02 BA04 BA08 BA19 BC19 BD08 CA07 FA36 FA42 GA03 HA07 JA02 JA10 JA24 KA03 KA22

Claims (30)

【特許請求の範囲】[Claims] 【請求項１】 鉄系焼結摺動材料であって、少なくとも
０．５重量％以上のＡｌを不可避成分として含有すると
ともに、Ｃｕを１０〜５０重量％含有してなることを特
徴とする焼結摺動材料。1. An iron-based sintered sliding material, characterized by containing at least 0.5% by weight of Al as an unavoidable component and containing 10 to 50% by weight of Cu. Bonding sliding material. 【請求項２】 Ｆｅ合金相において、少なくともＡｌを
２〜３５重量％含有する請求項１に記載の焼結摺動材
料。2. The sintered sliding material according to claim 1, wherein the Fe alloy phase contains at least 2 to 35% by weight of Al. 【請求項３】 Ｆｅ合金相において、Ａｌ＋Ｓｉを２〜
３５重量％含有する請求項１または２に記載の焼結摺動
材料。3. In the Fe alloy phase, Al + Si is 2 to
The sintered sliding material according to claim 1 or 2, containing 35% by weight. 【請求項４】 Ｆｅ合金相において、Ｃｏ、Ｎｉの一種
以上を５〜４０重量％含有し、Ｆｅ系規則相の硬さをＨ
ｖ３００〜８００に調整する請求項１〜３のいずれかに
記載の焼結摺動材料。4. The Fe alloy phase contains 5 to 40% by weight of at least one of Co and Ni, and the Fe-based ordered phase has a hardness of H.
The sintered sliding material according to any one of claims 1 to 3, which is adjusted to v300 to 800. 【請求項５】 Ｆｅ合金相において、炭素を０．０５〜
１．５重量％含有する請求項１〜４のいずれかに記載の
焼結摺動材料。5. The Fe alloy phase contains carbon in an amount of 0.05 to
The sintered sliding material according to any one of claims 1 to 4, containing 1.5% by weight. 【請求項６】 前記Ｆｅ合金相が、マルテンサイト、ベ
イナイト、粒状セメンタイトの一種以上の組織からなっ
ている請求項５に記載の焼結摺動材料。6. The sintered sliding material according to claim 5, wherein the Fe alloy phase has a structure of one or more of martensite, bainite, and granular cementite. 【請求項７】 Ｆｅ合金相の焼入れ硬化性および／また
は時効硬化性を高めるためのＳｉ、Ｍｎ、Ｎｉ、Ｃｒ、
Ｍｏ、Ｖ、Ｐ、Ｔｉ、Ｗ、Ｃｏの一種以上の合金元素を
各々０．１〜５重量％で含有する請求項１〜６のいずれ
かに記載の焼結摺動材料。7. Si, Mn, Ni, Cr, for increasing the quench hardenability and / or age hardenability of the Fe alloy phase.
The sintered sliding material according to any one of claims 1 to 6, which contains 0.1 to 5% by weight of one or more alloy elements of Mo, V, P, Ti, W, and Co, respectively. 【請求項８】 焼結性を改善するためのＳｎ、Ｔｉ、
Ｐ、Ｓｉの一種以上を０．１〜５重量％で含有する請求
項１〜７のいずれかに記載の焼結摺動材料。8. Sn, Ti, for improving the sinterability,
The sintered sliding material according to any one of claims 1 to 7, which contains 0.1 to 5% by weight of one or more of P and Si. 【請求項９】 予め成分調整されたＡｌを含まないかも
しくは最小限に含んだ鉄系焼結材料に、その鉄系焼結材
料より低融点に成分調整された銅系および／または銅ア
ルミニウム系材料を前記鉄系焼結材料の焼結時に溶浸す
るか、もしくは一旦焼結した鉄系焼結材料に溶浸してな
る請求項１〜８のいずれかに記載の焼結摺動材料。9. A copper-based and / or copper-aluminum-based material in which an iron-based sintered material containing no or a minimum amount of Al whose content has been adjusted in advance has a lower melting point than the iron-based sintered material. 9. The sintered sliding material according to claim 1, wherein the material is infiltrated during sintering of the iron-based sintered material, or infiltrated into the iron-based sintered material that has been once sintered. 【請求項１０】 前記焼結摺動材料の粒界に分散する元
液相のＣｕ合金相および／または前記焼結摺動材料のＦ
ｅ合金相中に析出する微粒子のＣｕ合金相が、Ｃｕ−Ａ
ｌ状態図中に記載されるβ相および／またはその変態相
を含んでいる請求項１〜９のいずれかに記載の焼結摺動
材料。10. A Cu alloy phase of an original liquid phase dispersed in a grain boundary of the sintered sliding material and / or F of the sintered sliding material.
The fine Cu alloy phase precipitated in the e alloy phase is Cu-A
The sintered sliding material according to any one of claims 1 to 9, which contains the β phase and / or its transformation phase described in the l phase diagram. 【請求項１１】 使用する鉄および／または鉄合金粉末
が６０μｍ以下の微粉末である請求項１〜１０のいずれ
かに記載の焼結摺動材料。11. The sintered sliding material according to claim 1, wherein the iron and / or iron alloy powder used is a fine powder of 60 μm or less. 【請求項１２】 銅系焼結摺動材料であって、少なくと
も２．０〜３５重量％のＡｌを含有し、２５重量％以下
のＣｕと、０．０５〜１．５重量％のＣと、５〜４０重
量％のＣｏと、５〜４０重量％のＮｉと、０．０５〜
５．０重量％のＳｉ、Ｍｎ、Ｎｉ、Ｃｒ、Ｍｏ、Ｖ、Ｔ
ｉ、Ｐ、Ｃｏ、Ｓｎの一種以上を含有する鉄合金相が、
５〜５０重量％分散されてなることを特徴とする焼結摺
動材料。12. A copper-based sintered sliding material, containing at least 2.0 to 35% by weight of Al, not more than 25% by weight of Cu, and 0.05 to 1.5% by weight of C. , 5-40 wt% Co, 5-40 wt% Ni, 0.05-
5.0 wt% Si, Mn, Ni, Cr, Mo, V, T
The iron alloy phase containing at least one of i, P, Co and Sn is
A sintered sliding material characterized by being dispersed in an amount of 5 to 50% by weight. 【請求項１３】 Ｃｕ合金相において、少なくともＡ
ｌ、Ｓｎ、Ｔｉの一種以上を含有し、Ｃｕ−Ａｌ状態図
中に記載されるβ相および／またはその変態相を含んで
いる請求項１２に記載の焼結摺動材料。13. In the Cu alloy phase, at least A
The sintered sliding material according to claim 12, which contains one or more of 1, Sn, and Ti and contains the β phase and / or its transformation phase described in the Cu-Al phase diagram. 【請求項１４】 前記焼結摺動材料中に分散するＦｅ合
金相が、マルテンサイト、ベイナイト、粒状セメンタイ
トの一種以上の組織からなっている請求項１２または１
３に記載の焼結摺動材料。14. The Fe alloy phase dispersed in the sintered sliding material has one or more structures of martensite, bainite and granular cementite.
The sintered sliding material according to item 3. 【請求項１５】 鉄系焼結体の気孔率が３〜３０体積％
に調整され、各気孔に潤滑油が含浸されている請求項１
〜１４のいずれかに記載の焼結摺動材料。15. The porosity of the iron-based sintered body is 3 to 30% by volume.
The lubricating oil is impregnated into each of the pores.
The sintered sliding material according to any one of 1 to 14. 【請求項１６】 黒鉛、ＭｏＳ２、ＷＳ２、ＭｎＳ、Ｃ
ａＦ２等の固体潤滑剤および／またはＭｏ、Ｗ等の金属
粒子、酸化物、炭化物、窒化物等のセラミックス、超
硬、サーメット、高速度鋼粉末等の炭化物、窒化物を含
有する硬質分散材、さらにはＦｅＣｏ、ＮｉＡｌ、Ｔｉ
Ａｌ、ＮｉＳｉ、ＮｉＴｉ等の金属間化合物の一種以上
が含有されている請求項１〜１５のいずれかに記載の焼
結摺動材料。16. Graphite, MoS 2 , WS 2 , MnS, C
A hard lubricant containing a solid lubricant such as aF 2 and / or metal particles such as Mo and W, ceramics such as oxides, carbides and nitrides, carbides such as cemented carbide, cermet and high speed steel powder, and nitrides. , And FeCo, NiAl, Ti
The sintered sliding material according to any one of claims 1 to 15, containing at least one intermetallic compound such as Al, NiSi, and NiTi. 【請求項１７】 少なくとも２〜９重量％の造粒された
黒鉛が分散され、さらに０．１〜５重量％のＭｏＳ２、
ＷＳ２、ＭｎＳが分散されている請求項１６に記載の焼
結摺動材料。17. At least 2-9% by weight of granulated graphite is dispersed, and further 0.1-5% by weight of MoS 2 ,
The sintered sliding material according to claim 16, wherein WS 2 and MnS are dispersed. 【請求項１８】 請求項１〜１７のいずれかに記載の焼
結摺動材料を円筒状、略円筒状もしくは板状に成形・加
工し、鉄系材料よりなる裏金に一体化してなることを特
徴とする焼結摺動部材。18. The sintered sliding material according to claim 1, which is formed and processed into a cylindrical shape, a substantially cylindrical shape or a plate shape, and which is integrated with a backing metal made of an iron-based material. Characteristic sintered sliding member. 【請求項１９】 前記裏金となる鉄系材料の焼入れ性が
ＤＩ値＝２．０以下で、ガス急冷もしくは油焼入れによ
ってもフェライト、パーライト、ベイナイトのいずれか
の組織を示し、この裏金に焼結接合する鉄系焼結摺動材
料中のＦｅ合金相の一部以上をマルテンサイト化するこ
とによって、この鉄系焼結摺動材料に圧縮残留応力が働
くようにする請求項１８に記載の焼結摺動部材。19. The hardenability of the iron-based material as the backing metal is DI value = 2.0 or less, and even if gas quenching or oil quenching shows a structure of either ferrite, pearlite, or bainite, the backing metal is sintered. The firing according to claim 18, wherein a compressive residual stress acts on the iron-based sintered sliding material by converting a part or more of the Fe alloy phase in the iron-based sintered sliding material to be joined into martensite. Bonding sliding member. 【請求項２０】 前記裏金となる鉄系材料の気孔率が３
〜２０体積％に調整され、各気孔に潤滑油が含浸されて
いる請求項１８または１９に記載の焼結摺動部材。20. The porosity of the iron-based material used as the back metal is 3
The sintered sliding member according to claim 18 or 19, wherein the pores are adjusted to -20% by volume and the pores are impregnated with lubricating oil. 【請求項２１】 円筒状もしくは略円筒状に成形されて
複層焼結ブッシュとされた複層焼結摺動部材であって、
両端面部の外周面の面取りが内周面の面取りよりも小さ
くされている請求項１８〜２０のいずれかに記載の焼結
摺動部材。21. A multi-layer sintered sliding member formed into a multi-layer sintered bush formed into a cylindrical shape or a substantially cylindrical shape,
The sintered sliding member according to any one of claims 18 to 20, wherein the chamfers of the outer peripheral surfaces of both end surface portions are smaller than the chamfer of the inner peripheral surface. 【請求項２２】 円筒状もしくは略円筒状に成形された
複層焼結摺動部材であって、スラスト荷重を受けて摺動
するように前記裏金に鍔部が設けられ、この鍔部摺動面
に焼入れ硬化処理が施されているか、もしくは耐摩耗材
料および／または摺動材料が配されている請求項１８〜
２１のいずれかに記載の焼結摺動部材。22. A multi-layer sintered sliding member formed into a cylindrical shape or a substantially cylindrical shape, wherein the back metal is provided with a collar portion so as to slide under a thrust load, and the collar portion slides. The surface is subjected to quench hardening treatment, or is provided with an abrasion resistant material and / or a sliding material.
21. The sintered sliding member according to any one of 21. 【請求項２３】 前記耐摩耗材料もしくは摺動材料が、
超硬、ステライト、鉄系耐摩耗材料、セラミックス、Ｃ
ｕ系耐摩耗材料のうちの一種であり、これらが溶射、ロ
ウ付け、焼結接合、溶浸接合、接着のうちのいずれかの
手段で一体化される請求項２２に記載の焼結摺動部材。23. The wear resistant material or sliding material,
Carbide, stellite, iron-based wear resistant material, ceramics, C
23. The sintered slide according to claim 22, which is one of u-based wear resistant materials, and these are integrated by any one of thermal spraying, brazing, sinter joining, infiltration joining, and gluing. Element. 【請求項２４】 請求項１〜１７のいずれかに記載の焼
結摺動材料が前記鍔部摺動面において一体化されている
請求項２２に記載の焼結摺動部材。24. The sintered sliding member according to claim 22, wherein the sintered sliding material according to any one of claims 1 to 17 is integrated on the flange sliding surface. 【請求項２５】 円筒状もしくは略円筒状に成形された
複層焼結摺動部材の製造方法であって、予め成分調整さ
れた鉄系焼結材料の成形体もしくは焼結体を、円筒状も
しくは略円筒状の鉄系材料よりなる裏金の内径面に略内
接するように配置し、前記鉄系焼結材料より低融点に成
分調整された銅系または銅アルミニウム系材料を前記鉄
系焼結材料の成形体もしくは焼結体に加熱しながら溶浸
することによってその鉄系焼結材料を膨張させながら前
記裏金に接合することを特徴とする焼結摺動部材の製造
方法。25. A method of manufacturing a multilayer sintered sliding member formed into a cylindrical shape or a substantially cylindrical shape, wherein a molded body or a sintered body of an iron-based sintered material whose components are adjusted in advance is formed into a cylindrical shape. Alternatively, a copper-based or copper-aluminum-based material whose component is adjusted to have a lower melting point than the iron-based sintered material is placed so as to be substantially inscribed on the inner diameter surface of the backing metal made of a substantially cylindrical iron-based material. A method for manufacturing a sintered sliding member, characterized in that the iron-based sintered material is infiltrated while being heated into a molded body or a sintered body of the material so as to be bonded to the back metal while expanding. 【請求項２６】 円筒状もしくは略円筒状に成形された
複層焼結摺動部材の製造方法であって、鉄系または銅系
焼結摺動材料を、円筒状もしくは略円筒状の鉄系材料よ
りなる裏金の内径面に略内接するように配置するととも
に、それら焼結摺動材料と裏金との間にロウ剤を配置
し、前記焼結摺動材料の内周面からの高周波加熱によっ
てその焼結摺動材料を前記裏金に押し付けながらロウ付
けすることを特徴とする焼結摺動部材の製造方法。26. A method of manufacturing a multilayer sintered sliding member formed into a cylindrical shape or a substantially cylindrical shape, wherein an iron-based or copper-based sintered sliding material is formed into a cylindrical or substantially cylindrical iron-based material. It is arranged so as to be substantially inscribed on the inner diameter surface of the back metal made of a material, and a brazing agent is arranged between the sintered sliding material and the back metal, and by high frequency heating from the inner peripheral surface of the sintered sliding material. A method of manufacturing a sintered sliding member, characterized in that the sintered sliding material is brazed while being pressed against the back metal. 【請求項２７】 円筒状もしくは略円筒状に成形された
複層焼結摺動部材の製造方法であって、鉄系または銅系
焼結材料を膨張させる金属であるＡｌを少なくとも０．
１重量％以上含有するとともに、高温度側で液相を発生
させて焼結体強度と焼結接合性を確保するために、１０
〜５０重量％のＣｕ、０．１〜１０重量％のＳｎおよび
０．１〜１０重量％のＴｉのいずれか一種以上を含有し
てなり、円筒状もしくは略円筒状の鉄系材料よりなる裏
金の内径と略同じか、または僅かに小さい外径を有する
鉄系または銅系焼結材料よりなる円筒状の成形体を、前
記裏金の内径面に挿入・配置し、（ａ）７００℃以上の
温度で所定時間加熱することによって、前記焼結材料を
膨張させて前記裏金に焼結接合させ、（ｂ）さらに昇温
して８２０℃以上の温度で加熱することによりＣｕ系合
金液相を発生させることによって、前記焼結材料を緻密
化させることを特徴とする焼結摺動部材の製造方法。27. A method of manufacturing a multilayer sintered sliding member formed into a cylindrical shape or a substantially cylindrical shape, wherein Al, which is a metal for expanding an iron-based or copper-based sintered material, is at least 0.
In order to secure the strength and sinter bondability of the sintered body by containing 1 wt% or more and generating a liquid phase on the high temperature side,
~ 50 wt% Cu, 0.1 to 10 wt% Sn and 0.1 to 10 wt% Ti, and a backing metal made of a cylindrical or substantially cylindrical iron-based material. A cylindrical molded body made of an iron-based or copper-based sintered material having an outer diameter that is substantially the same as or slightly smaller than the inner diameter of the back metal is inserted and arranged on the inner diameter surface of the back metal, and By heating at a temperature for a predetermined time, the sintered material is expanded and sinter-bonded to the back metal, and (b) further heated and heated at a temperature of 820 ° C. or higher to generate a Cu-based alloy liquid phase. A method of manufacturing a sintered sliding member, characterized in that the sintered material is densified by the above. 【請求項２８】 焼結接合後の冷却過程において、炭素
を含有するＦｅ合金相をマルテンサイト変態によって硬
化させるとともに膨張させ、同時に前記裏金は焼入れ硬
化させないように焼入れ性を調整することによって、前
記焼結材料および焼結接合を強化する圧縮残留応力を作
用させるようにした請求項２５〜２７のいずれかに記載
の焼結摺動部材の製造方法。28. In the cooling process after sinter bonding, the Fe alloy phase containing carbon is hardened and expanded by martensitic transformation, and at the same time, the hardenability is adjusted so that the back metal is not hardened by quenching. The method for producing a sintered sliding member according to any one of claims 25 to 27, wherein a compressive residual stress that strengthens the sintered material and the sintered joint is applied. 【請求項２９】 円筒状もしくは略円筒状に成形された
複層焼結摺動部材の製造方法であって、円筒状もしくは
略円筒状の鉄系材料よりなる裏金にスラスト荷重を受け
て摺動するように鍔部が設けられ、この裏金の内径面に
鉄系または銅系焼結摺動材料を焼結接合すると同時に、
前記鍔部摺動面に耐摩耗材料および／または摺動材料を
接合することを特徴とする焼結摺動部材の製造方法。29. A method for manufacturing a multilayer sintered sliding member formed into a cylindrical shape or a substantially cylindrical shape, which comprises sliding a backing metal made of a cylindrical or substantially cylindrical iron-based material under a thrust load. The collar is provided so that the iron-based or copper-based sintered sliding material is sinter-bonded to the inner diameter surface of the back metal at the same time.
A method for manufacturing a sintered sliding member, characterized in that an abrasion resistant material and / or a sliding material is bonded to the sliding surface of the flange portion. 【請求項３０】 前記耐摩耗材料および／または摺動材
料は、少なくとも炭素１．５〜３．５重量％、Ｃｒ５〜
１７重量％を含有する高炭素高Ｃｒ鉄合金焼結材料であ
る請求項２９に記載の焼結摺動部材の製造方法。30. The wear resistant material and / or the sliding material is at least 1.5 to 3.5% by weight of carbon and 5 to 5% of Cr.
The method for producing a sintered sliding member according to claim 29, which is a high carbon, high Cr iron alloy sintered material containing 17% by weight.
JP2002152222A 2002-05-27 2002-05-27 Sintered sliding material, sintered sliding member, and production method thereof Pending JP2003342700A (en)

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