JPH1150296A - Sliding member - Google Patents
Sliding memberInfo
- Publication number
- JPH1150296A JPH1150296A JP10063428A JP6342898A JPH1150296A JP H1150296 A JPH1150296 A JP H1150296A JP 10063428 A JP10063428 A JP 10063428A JP 6342898 A JP6342898 A JP 6342898A JP H1150296 A JPH1150296 A JP H1150296A
- Authority
- JP
- Japan
- Prior art keywords
- coating layer
- plating
- alloy
- sliding
- weight
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
- F16C33/02—Parts of sliding-contact bearings
- F16C33/04—Brasses; Bushes; Linings
- F16C33/06—Sliding surface mainly made of metal
- F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
- F16C33/121—Use of special materials
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
- F16C33/02—Parts of sliding-contact bearings
- F16C33/04—Brasses; Bushes; Linings
- F16C33/06—Sliding surface mainly made of metal
- F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
- F16C33/122—Multilayer structures of sleeves, washers or liners
- F16C33/124—Details of overlays
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C17/00—Sliding-contact bearings for exclusively rotary movement
- F16C17/02—Sliding-contact bearings for exclusively rotary movement for radial load only
- F16C17/022—Sliding-contact bearings for exclusively rotary movement for radial load only with a pair of essentially semicircular bearing sleeves
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C2204/00—Metallic materials; Alloys
- F16C2204/30—Alloys based on one of tin, lead, antimony, bismuth, indium, e.g. materials for providing sliding surfaces
- F16C2204/36—Alloys based on bismuth
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C2360/00—Engines or pumps
- F16C2360/22—Internal combustion engines
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は摺動部材に関し、詳
しくはＰｂ（鉛）を含有しない摺動部材に関する。本発
明の摺動部材は、例えば内燃機関用のすべり軸受やブッ
シュに好適に利用することができる。The present invention relates to a sliding member, and more particularly to a sliding member containing no Pb (lead). INDUSTRIAL APPLICABILITY The sliding member of the present invention can be suitably used, for example, for a slide bearing or a bush for an internal combustion engine.
【０００２】[0002]
【従来の技術】自動車エンジンの高出力化に伴って、ク
ランクシャフトやコネクティングロッド等に使用される
すべり軸受には、低炭素鋼製の裏金に、初期なじみ性と
高い圧縮・疲労強度とを有するケルメット合金（Ｃｕ及
びＰｂを主成分とする合金）をライニングした軸受が多
く用いられている。2. Description of the Related Art Along with an increase in the output of an automobile engine, a sliding bearing used for a crankshaft, a connecting rod and the like has an initial conformability and a high compressive / fatigue strength on a low carbon steel backing metal. Bearings lined with a kelmet alloy (an alloy mainly composed of Cu and Pb) are often used.
【０００３】この軸受では、普通、ケルメット合金表面
で相手材との摺動面に電気めっき等により薄いオーバー
レイ層が形成される。これは相手材とのなじみ性をさら
に高める等の目的でなされるもので、オーバーレイ層に
は軟質なＰｂ及びＳｎを主成分とする合金が用いられ
る。なお、ケルメットの耐食性を向上させたり、オーバ
ーレイ層中のＳｎがケルメット合金中に拡散してオーバ
ーレイ層が劣化することを防止する等の目的で、ケルメ
ット表面に数μｍ程度の厚さのＮｉ等のめっき処理を施
し、このめっき層の上にオーバーレイ層を形成すること
も行われている。[0003] In this bearing, a thin overlay layer is usually formed by electroplating or the like on the sliding surface with the mating material on the surface of the kelmet alloy. This is performed for the purpose of further enhancing the compatibility with the counterpart material, and an alloy mainly composed of soft Pb and Sn is used for the overlay layer. In addition, for the purpose of improving the corrosion resistance of kelmet, preventing the Sn in the overlay layer from diffusing into the kelmet alloy and preventing the overlay layer from deteriorating, for example, Ni or the like having a thickness of about several μm is formed on the kelmet surface. A plating process is performed, and an overlay layer is formed on the plating layer.
【０００４】また、上記すべり軸受には、Ａｌ基でＳｎ
及びＰｂ等を合金化したアルミニウム合金軸受（特開平
４−２１９５２３号公報等参照）も多く用いられてい
る。[0004] Further, the above-mentioned plain bearing is made of Sn based on Al.
And an aluminum alloy bearing obtained by alloying Pb or the like (see Japanese Patent Application Laid-Open No. 4-219523) is also widely used.
【０００５】[0005]
【発明が解決しようとする課題】ところで、近年の材料
開発の動向としてＰｂフリー化の方向に進んでいる。こ
の開発動向は上記すべり軸受等の摺動部材も例外ではな
い。しかしながら、すべり軸受等の摺動部材において、
摺動特性を満足させる上でＰｂは重要である。高出力エ
ンジンのように高負荷条件部では、高い摺動特性が要求
されることから、Ｐｂは特に重要である。このため、摺
動面にＰｂを含有せずに、十分な摺動特性を備えた摺動
部材を提供することは、きわめて困難であった。Incidentally, as a trend of material development in recent years, the direction of Pb-free is progressing. This development trend is no exception for sliding members such as the above-mentioned plain bearings. However, in sliding members such as sliding bearings,
Pb is important for satisfying the sliding characteristics. Pb is particularly important in a high-load condition section such as a high-output engine because high sliding characteristics are required. For this reason, it was extremely difficult to provide a sliding member having sufficient sliding characteristics without containing Pb in the sliding surface.
【０００６】本発明は上記実情に鑑みてなされたもので
あり、少なくとも摺動面にＰｂを含有せず、しかもＰｂ
を摺動面に含有するものと同等の摺動特性を発揮しうる
摺動部材を提供することを解決すべき技術課題とするも
のである。The present invention has been made in view of the above-mentioned circumstances, and at least does not contain Pb on the sliding surface.
It is a technical problem to be solved to provide a sliding member capable of exhibiting the same sliding characteristics as those having a sliding surface.
【０００７】[0007]
（１）上記課題を解決する請求項１記載の摺動部材は、
基材と、該基材の表面で相手材との摺動面に形成された
被覆層とからなる摺動部材において、上記被覆層は、Ｓ
ｎ、Ｉｎ及びＡｇよりなる群から選ばれる少なくとも一
種を含有し、残部が実質的にＢｉ及び不可避不純物より
なることを特徴とする。(1) The sliding member according to claim 1, which solves the above problem,
In a sliding member comprising a base material and a coating layer formed on a sliding surface of the base material on a sliding surface with a mating material, the coating layer is formed of S
It is characterized by containing at least one selected from the group consisting of n, In and Ag, with the balance substantially consisting of Bi and unavoidable impurities.
【０００８】（２）請求項２記載の摺動部材は、請求項
１記載の摺動部材において、前記被覆層中に含まれるＳ
ｎの量が０．１〜２５重量％であることを特徴とする。 （３）請求項３記載の摺動部材は、請求項１記載の摺動
部材において、前記被覆層中に含まれるＩｎの量が０．
１〜１０重量％であることを特徴とする。 （４）請求項４記載の摺動部材は、請求項１記載の摺動
部材において、前記被覆層中に含まれるＡｇの量が０．
５〜１０重量％であることを特徴とする。(2) The sliding member according to the second aspect is the sliding member according to the first aspect, wherein S is contained in the coating layer.
The amount of n is 0.1 to 25% by weight. (3) The sliding member according to the third aspect is the sliding member according to the first aspect, wherein the amount of In contained in the coating layer is equal to 0.1.
1 to 10% by weight. (4) The sliding member according to the fourth aspect is the sliding member according to the first aspect, wherein the amount of Ag contained in the coating layer is 0.1.
5 to 10% by weight.
【０００９】（５）請求項５記載の摺動部材は、請求項
１記載の摺動部材において、前記被覆層が、前記基材の
表面をめっき処理することにより形成されためっき皮膜
であることを特徴とする。(5) The sliding member according to the fifth aspect is the sliding member according to the first aspect, wherein the coating layer is a plating film formed by plating a surface of the base material. It is characterized by.
【００１０】[0010]
【発明の実施の形態】本発明の摺動部材は、基材と、該
基材の表面で相手材との摺動面に形成された被覆層とか
らなるものである。上記基材の種類としては特に限定さ
れず、本発明の摺動部材を適用しようとする部材に応じ
て、鋼材、鋳鉄、鉄系焼結合金、アルミニウム合金及び
銅合金等から適宜採択可能であり、これらの材料の複合
材料であってもよい。但し、この基材もＰｂを含有しな
いことが好ましい。例えば、本発明の摺動部材を内燃機
関用すべり軸受に適用する場合、鋼製裏金にＣｕ−Ｓｎ
系合金層をライニングしてなる基材や、Ａｌ−Ｓｎ−Ｓ
ｉ系合金層よりなる基材等を用いることができる。BEST MODE FOR CARRYING OUT THE INVENTION The sliding member of the present invention comprises a base material and a coating layer formed on the surface of the base material on the sliding surface with the mating material. The type of the base material is not particularly limited, and can be appropriately selected from steel, cast iron, an iron-based sintered alloy, an aluminum alloy, a copper alloy, and the like, depending on the member to which the sliding member of the present invention is applied. And a composite material of these materials. However, it is preferable that this substrate also does not contain Pb. For example, when the sliding member of the present invention is applied to a slide bearing for an internal combustion engine, the steel back metal is made of Cu-Sn.
Base material obtained by lining a base alloy layer, Al-Sn-S
A substrate made of an i-based alloy layer or the like can be used.
【００１１】上記被覆層は、基材の表面をめっき処理す
ることにより形成されためっき皮膜であることが好まし
い。被覆層がめっき皮膜であれば、密着性や皮膜強度の
点で有利となるからである。このめっき処理としては、
電気めっきや化学めっきなどの湿式めっきの他、イオン
プレーティングやスパッタリングなどのＰＶＤ法による
乾式めっきを採用することができる。なお、基材に被覆
層を形成する方法として、めっき処理の他に溶射等を採
用することも可能である。The coating layer is preferably a plating film formed by plating the surface of a substrate. This is because if the coating layer is a plating film, it is advantageous in terms of adhesion and film strength. As this plating process,
In addition to wet plating such as electroplating and chemical plating, dry plating by a PVD method such as ion plating and sputtering can be employed. In addition, as a method of forming a coating layer on a base material, thermal spraying or the like can be adopted in addition to plating.
【００１２】なお、基材表面に直接被覆層を形成しても
よいが、基材と被覆層との接合性や基材の耐食性を向上
させる等の観点から、基材表面に中間層を形成すること
が好ましい。この中間層としては、Ｎｉめっき層、Ｃｏ
めっき層やＺｎめっき層等を採用することができる。ま
た上記被覆層の厚さは１．０〜３０μｍとすることが好
ましい。被覆層の厚さが１．０μｍよりも薄いと、十分
な摺動特性を発揮することが困難となり、一方３０μｍ
よりも厚いと密着性が低下して被覆層が基材表面から剥
がれ易くなる。より好ましい被覆層の厚さは１０〜３０
μｍである。被覆層の厚さが１０μｍ以上になると、必
要ななじみ性の確保及び耐摩耗寿命の点で有利となる。Although a coating layer may be formed directly on the surface of the substrate, an intermediate layer is formed on the surface of the substrate from the viewpoint of improving the bonding property between the substrate and the coating layer and the corrosion resistance of the substrate. Is preferred. As the intermediate layer, a Ni plating layer, Co
A plating layer, a Zn plating layer, or the like can be employed. The thickness of the coating layer is preferably 1.0 to 30 μm. If the thickness of the coating layer is less than 1.0 μm, it becomes difficult to exhibit sufficient sliding characteristics, while 30 μm
If the thickness is larger than the above, the adhesiveness is reduced and the coating layer is easily peeled off from the substrate surface. More preferably, the thickness of the coating layer is 10 to 30.
μm. When the thickness of the coating layer is 10 μm or more, it is advantageous in terms of securing necessary conformability and abrasion life.
【００１３】上記被覆層は、Ｓｎ（スズ）、Ｉｎ（イン
ジウム）及びＡｇ（銀）よりなる群から選ばれる少なく
とも一種を含有し、残部が実質的にＢｉ（ビスマス）及
び不可避不純物よりなるものであり、この被覆層にはＰ
ｂが含有されていない。かかるＢｉ合金よりなる被覆層
は、硬さが高過ぎることがなくなじみ性が良好で、か
つ、潤滑性が良くて耐焼付き性が良好で、しかも耐摩耗
性も良好となる。The coating layer contains at least one selected from the group consisting of Sn (tin), In (indium) and Ag (silver), and the balance substantially consists of Bi (bismuth) and unavoidable impurities. There is a P
b is not contained. The coating layer made of such a Bi alloy has good conformability without being too hard, and has good lubricity, good seizure resistance, and good wear resistance.
【００１４】したがって、上記Ｂｉ合金よりなる被覆層
が基材の表面で相手材との摺動面に形成された本発明に
係る摺動部材は、少なくとも摺動面にＰｂを含有しない
にもかかわらず、なじみ性、耐焼付き性及び耐摩耗性の
摺動特性が良好となる。ここに、ＳｎはＢｉ合金の耐焼
付き性の向上に寄与する。上記被覆層において、Ｓｎの
含有量が０．１重量％未満になると、潤滑性が十分でな
く耐焼付き性向上の効果がみられない。一方、Ｓｎの含
有量が２５重量％を超えると、合金融点が低下して高温
下における耐焼付き性が不十分となる。このため、上記
被覆層におけるＳｎの含有量は０．１〜２５重量％とす
ることが好ましい。また、Ｓｎ含有量が多いほど耐焼付
き性が向上することから、耐焼付き性の観点からはＳｎ
含有量の下限を１重量％とすることが好ましい。一方、
Ｓｎ含有量が多いほど主相の融点が低下し、Ｓｎ含有量
が２重量％を超えると低融点の共晶相（Ｂｉ−４３Ｓｎ
相）の生成が認められ、Ｓｎ含有量が５重量％を超える
とこの共晶相の影響により耐熱性が低下するおそれがあ
る。このため、耐熱性向上の観点からは、上記被覆層に
おけるＳｎの含有量の上限は５重量％とすることが好ま
しく、２重量％とすることがより好ましい。Therefore, the sliding member according to the present invention in which the coating layer made of the Bi alloy is formed on the sliding surface with the mating material on the surface of the base material, although at least the sliding surface does not contain Pb. And the sliding properties of conformability, seizure resistance and abrasion resistance are improved. Here, Sn contributes to improvement of the seizure resistance of the Bi alloy. If the content of Sn in the coating layer is less than 0.1% by weight, the lubricating property is not sufficient and the effect of improving seizure resistance is not seen. On the other hand, if the Sn content exceeds 25% by weight, the melting point of the alloy is lowered, and the seizure resistance at high temperatures becomes insufficient. Therefore, the content of Sn in the coating layer is preferably set to 0.1 to 25% by weight. Further, since the seizure resistance increases as the Sn content increases, the Sn resistance increases from the viewpoint of the seizure resistance.
It is preferable that the lower limit of the content be 1% by weight. on the other hand,
The higher the Sn content, the lower the melting point of the main phase. If the Sn content exceeds 2% by weight, the low melting point eutectic phase (Bi-43Sn)
Phase) is recognized, and when the Sn content exceeds 5% by weight, the heat resistance may decrease due to the influence of the eutectic phase. For this reason, from the viewpoint of improving the heat resistance, the upper limit of the Sn content in the coating layer is preferably set to 5% by weight, more preferably 2% by weight.
【００１５】ＩｎはＳｎと同様の効果があり、上記被覆
層において、Ｉｎの含有量が０．１重量％未満になると
潤滑性の向上に対して効果がなく、一方１０重量％を超
えると合金の硬さが低下して耐摩耗性が不十分となる。
このため、上記被覆層におけるＩｎの含有量は０．１〜
１０重量％とすることが好ましい。ＡｇはＢｉ合金の耐
摩耗性及び耐焼付き性向上に寄与する。上記被覆層にお
いて、Ａｇの含有量が０．５重量％未満になると、Ｂｉ
合金の耐摩耗性及び耐焼付き性の向上に対して効果がな
い。一方、１０重量％を超えると、Ｂｉ合金の硬さが高
くなり過ぎてなじみ性が低下するとともに、材料コスト
が高くなる。このため、上記被覆層におけるＡｇの含有
量は０．５〜１０重量％とすることが好ましい。In has the same effect as Sn. When the content of In in the coating layer is less than 0.1% by weight, there is no effect on the improvement of lubricity. And the abrasion resistance becomes insufficient.
Therefore, the content of In in the coating layer is 0.1 to
It is preferably 10% by weight. Ag contributes to improving the wear resistance and seizure resistance of the Bi alloy. In the above coating layer, when the Ag content is less than 0.5% by weight, Bi
It has no effect on improving the wear resistance and seizure resistance of the alloy. On the other hand, if it exceeds 10% by weight, the hardness of the Bi alloy becomes too high, the conformability decreases, and the material cost increases. Therefore, the content of Ag in the coating layer is preferably 0.5 to 10% by weight.
【００１６】上記Ｓｎ、Ｉｎ及びＡｇは二種以上を同時
に含有させることもできる。この場合、Ｂｉ合金中のＢ
ｉの含有量はＢｉ基のなじみ特性を確保する観点から７
５重量％以上を確保することが好ましい。また、上記被
覆層に含まれるＳｎ、Ｉｎ及びＡｇの総量が２５重量％
を超えると、合金融点が低下して高温下における軸受性
能が低下する。一方、Ｓｎ、Ｉｎ及びＡｇの総量が２重
量％未満になると、潤滑性が十分でなく、耐焼付き性向
上がみられない。したがって、Ｓｎ、Ｉｎ及びＡｇの総
量は２〜２５重量％とすることが好ましい。The above-mentioned Sn, In and Ag may be used in combination of two or more. In this case, B in the Bi alloy
The content of i is 7 from the viewpoint of securing the conformability of the Bi group.
It is preferable to secure 5% by weight or more. The total amount of Sn, In and Ag contained in the coating layer is 25% by weight.
If the temperature exceeds the above range, the melting point of the alloy decreases, and the bearing performance at high temperatures decreases. On the other hand, if the total amount of Sn, In, and Ag is less than 2% by weight, the lubricity is insufficient, and no improvement in seizure resistance is observed. Therefore, the total amount of Sn, In and Ag is preferably set to 2 to 25% by weight.
【００１７】したがって、本発明の摺動部材は内燃機関
用のすべり軸受やブッシュに好適に利用することが可能
となる。Therefore, the sliding member of the present invention can be suitably used for a slide bearing or a bush for an internal combustion engine.
【００１８】[0018]
【実施例】以下、実施例により本発明を具体的に説明す
る。 ［第１実施例］鋼製裏金付きのＣｕ−Ｓｎ合金（Ｃｕ：
９４．５重量％、Ｓｎ：５重量％）試験片を準備し、こ
の試験片のＣｕ−Ｓｎ合金表面に、以下に示すように、
表１に示す化学組成よりなる厚さ１０〜３０μｍの被覆
層を電気めっきにより形成した。The present invention will be described below in detail with reference to examples. [First Embodiment] A Cu-Sn alloy (Cu:
94.5% by weight, Sn: 5% by weight) A test piece was prepared, and on the surface of the Cu-Sn alloy of the test piece,
A coating layer having a chemical composition shown in Table 1 and having a thickness of 10 to 30 μm was formed by electroplating.
【００１９】[0019]
【表１】 [Table 1]
【００２０】（実施例１〜７）表２に示す組成よりなる
ホウフッ化浴を用い、表３に示すめっき条件により電気
めっきすることにより、Ｂｉ−Ｓｎ合金よりなる被覆層
を形成した。なお、表２中、光沢剤はＰ−フェノールス
ルホン酸ナトリウム（又はアルデヒドーアミン系光沢
剤）を示す。(Examples 1 to 7) A coating layer made of a Bi-Sn alloy was formed by electroplating using a borofluoride bath having the composition shown in Table 2 under the plating conditions shown in Table 3. In Table 2, the brightener indicates sodium P-phenolsulfonate (or aldehyde-amine brightener).
【００２１】[0021]
【表２】 [Table 2]
【００２２】[0022]
【表３】 （実施例８、９）表２に示す組成からホウフッ化スズを
除くホウフッ化浴よりなるめっき液を用い、めっき液温
度：２０〜３０℃、電流密度：１〜５Ａ／ｄｍ2 の条件
で電気めっきすることにより、Ｂｉよりなる被覆層を形
成した。そして、このめっき皮膜の上にさらにＩｎめっ
きを行った後、熱処理（１５０〜１７０℃、３０〜６０
分）によりＩｎをめっき皮膜中に拡散させて表１に示す
組成となるように処理することにより、Ｂｉ−Ｉｎ合金
よりなる被覆層を形成した。[Table 3] (Examples 8 and 9) Using a plating solution composed of a borofluoride bath except for tin borofluoride from the composition shown in Table 2, and using a plating solution temperature of 20 to 30 ° C. and a current density of 1 to 5 A / dm 2 to produce electricity. A coating layer made of Bi was formed by plating. Then, after further performing In plating on the plating film, heat treatment (150 to 170 ° C., 30 to 60 ° C.)
In), a coating layer made of a Bi-In alloy was formed by diffusing In into the plating film to obtain a composition shown in Table 1.
【００２３】なお、Ｉｎめっきは、スルファミン酸浴を
用い、めっき液温度：２０〜３０℃、電流密度：１〜５
Ａ／ｄｍ2 の条件で行った。 （実施例１０、１１）表２に示す組成よりなるホウフッ
化浴を用い、表３に示すめっき条件により電気めっきす
ることにより、Ｂｉ−Ｓｎ合金よりなるめっき皮膜を形
成した。そして、このめっき皮膜の上にさらにＩｎめっ
きを行った後、熱処理（１５０〜１７０℃、３０〜６０
分）によりＩｎをめっき皮膜中に拡散させて表１に示す
組成となるように処理することにより、Ｂｉ−Ｓｎ−Ｉ
ｎ合金よりなる被覆層を形成した。The In plating uses a sulfamic acid bath, a plating solution temperature: 20 to 30 ° C., and a current density: 1 to 5
The test was performed under the condition of A / dm 2 . (Examples 10 and 11) A plating film made of a Bi-Sn alloy was formed by performing electroplating under a plating condition shown in Table 3 using a fluorinated bath having a composition shown in Table 2. Then, after further performing In plating on the plating film, heat treatment (150 to 170 ° C., 30 to 60 ° C.)
In), by diffusing In into the plating film and treating to obtain the composition shown in Table 1, Bi-Sn-I
A coating layer made of an n alloy was formed.
【００２４】なお、Ｉｎめっきの条件は上記と同様であ
る。（実施例１２）表４に示す組成よりなるホウフッ化
浴を用い、表３に示すめっき条件により電気めっきする
ことにより、Ｂｉ−Ａｇ合金よりなるめっき皮膜を形成
した。そして、このめっき皮膜の上にさらにＩｎめっき
を行った後、熱処理（１５０〜１７０℃、３０〜６０
分）によりＩｎをめっき皮膜中に拡散させて表１に示す
組成となるように処理することにより、Ｂｉ−Ｉｎ−Ａ
ｇ合金よりなる被覆層を形成した。The conditions for the In plating are the same as described above. (Example 12) Using a fluorination bath having the composition shown in Table 4, electroplating was performed under the plating conditions shown in Table 3, thereby forming a plating film made of a Bi-Ag alloy. Then, after further performing In plating on the plating film, heat treatment (150 to 170 ° C., 30 to 60 ° C.)
In), the In-diffusion into the plating film and treatment to obtain the composition shown in Table 1 yields Bi-In-A.
A coating layer made of the g alloy was formed.
【００２５】なお、Ｉｎめっきの条件は上記と同様であ
る。The conditions for the In plating are the same as described above.
【００２６】[0026]
【表４】 （実施例１３）表２及び表４に示す組成よりなるホウフ
ッ化浴を用い、表３に示すめっき条件により電気めっき
することにより、Ｂｉ−Ｓｎ−Ａｇ合金よりなる被覆層
を形成した。[Table 4] (Example 13) A coating layer made of a Bi-Sn-Ag alloy was formed by electroplating using a borofluoride bath having the composition shown in Tables 2 and 4 under the plating conditions shown in Table 3.
【００２７】（実施例１４）表２及び表４に示す組成よ
りなるホウフッ化浴を用い、表３に示すめっき条件によ
り電気めっきすることにより、Ｂｉ−Ｓｎ−Ａｇ合金よ
りなるめっき皮膜を形成した。そして、上記と同様に、
このめっき皮膜の上にさらにＩｎめっきを行った後、熱
処理によりＩｎをめっき皮膜中に拡散させて表１に示す
組成となるように処理することにより、Ｂｉ−Ｓｎ−Ｉ
ｎ−Ａｇ合金よりなる被覆層を形成した。Example 14 A plating film made of a Bi-Sn-Ag alloy was formed by electroplating using a borofluoride bath having the composition shown in Tables 2 and 4 under the plating conditions shown in Table 3. . And, as above,
After further In plating is performed on this plating film, In is diffused into the plating film by a heat treatment so as to have a composition shown in Table 1, whereby Bi-Sn-I
A coating layer made of an n-Ag alloy was formed.
【００２８】（実施例１５、１６）表４に示す組成より
なるホウフッ化浴を用い、表３に示すめっき条件により
電気めっきすることにより、Ｂｉ−Ａｇ合金よりなる被
覆層を形成した。 （比較例１）ホウフッ化浴よりなるめっき液を用い、め
っき液温度２０〜３０℃、電流密度２〜５Ａ／ｄｍ2 の
条件でめっき処理することにより、Ｐｂ−Ｓｎ合金より
なる被覆層を形成した。(Examples 15 and 16) A coating layer made of a Bi-Ag alloy was formed by electroplating using a borofluoride bath having the composition shown in Table 4 under the plating conditions shown in Table 3. (Comparative Example 1) A coating layer made of a Pb-Sn alloy was formed by plating using a plating solution consisting of a borofluoride bath at a plating solution temperature of 20 to 30 ° C and a current density of 2 to 5 A / dm 2. did.
【００２９】（比較例２）ホウフッ化浴よりなるめっき
液を用い、めっき液温度２０〜３０℃、電流密度２〜５
Ａ／ｄｍ2 の条件でめっき処理することにより、Ｐｂ−
Ｓｎ−Ｉｎ合金よりなる被覆層を形成した。 （比較例３）ホウフッ化浴よりなるめっき液を用い、め
っき液温度２０〜３０℃、電流密度２〜５Ａ／ｄｍ2 の
条件でめっき処理することにより、Ｃｕを微量に含有す
るＰｂ−Ｓｎ合金（Ｐｂ−Ｓｎ−Ｃｕ合金）よりなる被
覆層を形成した。(Comparative Example 2) Using a plating solution composed of a fluorinated bath, a plating solution temperature of 20 to 30 ° C and a current density of 2 to 5
By plating under the condition of A / dm 2 , Pb-
A coating layer made of a Sn-In alloy was formed. (Comparative Example 3) A Pb-Sn alloy containing a trace amount of Cu by plating using a plating solution composed of a borofluoride bath at a plating solution temperature of 20 to 30 ° C and a current density of 2 to 5 A / dm 2. A coating layer made of (Pb-Sn-Cu alloy) was formed.
【００３０】なお、上記比較例２、３に係る被覆層は、
現在オーバーレイとして普通に用いられている合金層で
ある。（比較例４）ホウフッ化浴よりなるめっき液を用
い、めっき液温度２０〜３０℃、電流密度２〜５Ａ／ｄ
ｍ2 の条件でめっき処理することにより、Ｓｎよりなる
被覆層を形成した。The coating layers according to Comparative Examples 2 and 3 were:
This is an alloy layer commonly used as an overlay at present. (Comparative Example 4) Using a plating solution composed of a fluorinated bath, a plating solution temperature of 20 to 30 ° C and a current density of 2 to 5 A / d
By plating under the condition of m 2, a coating layer made of Sn was formed.
【００３１】なお、上記比較例４に係る被覆層は、一部
のすべり軸受のオーバーレイ層として、現在用いられて
いる合金層である。 （比較例５）表２に示す組成からホウフッ化スズを除い
た組成よりなるホウフッ化浴を用い、表３に示すめっき
条件で電気めっきすることにより、純Ｂｉよりなる被覆
層を形成した。The coating layer according to Comparative Example 4 is an alloy layer that is currently used as an overlay layer for some slide bearings. (Comparative Example 5) A coating layer made of pure Bi was formed by electroplating under a plating condition shown in Table 3 using a borofluoride bath having a composition shown in Table 2 except for tin borofluoride.
【００３２】なお、上記比較例５に係る被覆層は、実施
例の被覆層と融点を比較するために作成したものであ
る。 （硬さの評価）上記実施例１〜１６及び比較例１〜４の
被覆層の硬さをマイクロビッカース硬度計により測定し
た。その結果を表５及び図１に示す。The coating layer according to Comparative Example 5 was prepared to compare the melting point with the coating layer of Example. (Evaluation of Hardness) The hardness of the coating layers of Examples 1 to 16 and Comparative Examples 1 to 4 was measured with a micro Vickers hardness meter. The results are shown in Table 5 and FIG.
【００３３】（摩擦摩耗特性の評価）上記実施例１〜１
６及び比較例１〜４の被覆層を摺動面に形成したφ７ｍ
ｍ×Ｌ１２ｍｍのピンよりなる試験片について、摩擦摩
耗試験を行った。その結果を表５及び図２、図４に示
す。なお、試験条件は以下のとおりである。 試験装置 ：ピンオンディスク試験機 すべり速度 ：０．５ｍ／ｓ 荷重 ：９Ｎ 潤滑 ：無潤滑（５×１０-2Ｔｏｒｒの真空中） 温度 ：室温 試験時間 ：３０分（但し、摩耗量が多くて３０分も
たないものについては、３０分摩耗を行ったものとして
換算した。） 相手材 ：ディスクテストピース、ＳＵＳ４３０
（硬さ：Ｈｖ２９０、表面粗さ：０．５μｍＲｚ） （耐焼付き性の評価）上記実施例１〜１６及び比較例１
〜４の被覆層を摺動面に形成した３０ｍｍ×３０ｍｍ、
厚さ２ｍｍのプレート（摺動面３０ｍｍ×３０ｍｍ）よ
りなる試験片について、焼付き試験を行った。その結果
を表５及び図３に示す。なお、試験条件は以下のとおり
である。(Evaluation of Friction and Wear Characteristics) Examples 1 to 1
6 and Comparative Examples 1-4 with a coating layer formed on the sliding surface
A friction and wear test was performed on a test piece consisting of a pin of mx L12 mm. The results are shown in Table 5 and FIGS. The test conditions are as follows. Test device: Pin-on-disk test machine Sliding speed: 0.5 m / s Load: 9 N Lubrication: No lubrication (in a vacuum of 5 × 10 -2 Torr) Temperature: Room temperature Test time: 30 minutes (however, the amount of wear is large) Those that did not last 30 minutes were converted as if they had been worn for 30 minutes.) Counterpart material: Disc test piece, SUS430
(Hardness: Hv290, Surface Roughness: 0.5 μm Rz) (Evaluation of Seizure Resistance) Examples 1 to 16 and Comparative Example 1
30 mm x 30 mm formed with a coating layer of ~ 4 on the sliding surface,
A seizure test was performed on a test piece composed of a plate having a thickness of 2 mm (sliding surface 30 mm × 30 mm). The results are shown in Table 5 and FIG. The test conditions are as follows.
【００３４】 試験装置 ：円筒×平板テストピーススラスト試験機 すべり速度 ：２．０ｍ／ｓ 荷重 ：ステップアップ漸増法（５ｋｇｆ／ステ
ップ） 潤滑 ：５Ｗ−３０基油（油浴） 温度 ：室温〜なりゆき 試験時間 ：ステップアップ／５分毎 相手材 ：円筒テストピース、炭素鋼（Ｓ５０Ｃ、
硬さ：Ｈｖ６００、表面粗さ：０．８μｍＲｚ）Test apparatus: Cylindrical × plate test piece thrust tester Sliding speed: 2.0 m / s Load: Step-up incremental method (5 kgf / step) Lubrication: 5W-30 base oil (oil bath) Temperature: Room temperature to room temperature Test time: Step up / every 5 minutes Mate material: Cylindrical test piece, carbon steel (S50C,
(Hardness: Hv600, surface roughness: 0.8 μm Rz)
【００３５】[0035]
【表５】 [Table 5]
【００３６】表５及び図１〜図４から明らかなように、
実施例１〜１６は比較例１〜４と比べて、硬さが高くな
っており、耐摩耗性は全て大幅に優れていた。実施例１
〜１６は、比較例１〜４と比べて、摩擦係数が同等以下
となっていた。また、比較例１〜４では焼付き試験中に
被覆層が摩耗して低荷重で焼き付きに至るのに対し、実
施例１〜１６は全て優れた耐焼付き性を示した。As is clear from Table 5 and FIGS.
In Examples 1 to 16, the hardness was higher than in Comparative Examples 1 to 4, and the abrasion resistance was all significantly excellent. Example 1
No. to No. 16 had a coefficient of friction equal to or less than Comparative Examples 1 to 4. Further, in Comparative Examples 1 to 4, the coating layer was worn during the seizure test and the seizure was caused with a low load, whereas Examples 1 to 16 all exhibited excellent seizure resistance.
【００３７】特に、実施例１２〜１４は潤滑性を示すＳ
ｎ及び／又はＩｎと、耐摩耗性に寄与するＡｇとの添加
により、優れた摺動特性を示した。したがって、摺動部
材の表面で相手材との摺動面に形成する被覆層として
は、Ｓｎ及びＩｎのうちの一種とＡｇとを含有し、残部
が実質的にＢｉ及び不可避不純物よりなる、すなわちＢ
ｉ−Ｓｎ−Ａｇ合金、Ｂｉ−Ｉｎ−Ａｇ合金又はＢｉ−
Ｓｎ−Ｉｎ−Ａｇ合金よりなる被覆層が特に好ましいこ
とがわかる。In particular, Examples 12 to 14 show S
The addition of n and / or In and Ag that contributes to abrasion resistance showed excellent sliding characteristics. Therefore, the coating layer formed on the sliding surface of the sliding member with the mating material on the surface of the sliding member contains one of Sn and In and Ag, and the balance substantially consists of Bi and inevitable impurities. B
i-Sn-Ag alloy, Bi-In-Ag alloy or Bi-
It is understood that a coating layer made of a Sn-In-Ag alloy is particularly preferable.
【００３８】（融点の評価）実施例１〜５及び比較例５
（純Ｂｉ）に関する示差熱曲線を図５に示す。示差熱曲
線の吸熱ピークから求めた主相の融点を図６に示す。図
５（ｂ）は、図５（ａ）の縦軸の感度を３倍にして表示
したものである。上記実施例１〜５及び比較例２〜５の
被覆層をカッターで細かく削り取り、示差熱分析器（Ｄ
ＴＡ）により昇温速度：１０℃／分の条件で熱分析を行
い、融点を測定した。その結果を表６に示す。(Evaluation of melting point) Examples 1 to 5 and Comparative Example 5
FIG. 5 shows a differential heat curve of (pure Bi). FIG. 6 shows the melting point of the main phase determined from the endothermic peak of the differential heat curve. FIG. 5B shows the sensitivity of the vertical axis of FIG. 5A tripled. The coating layers of Examples 1 to 5 and Comparative Examples 2 to 5 were finely scraped off with a cutter, and were then analyzed by a differential thermal analyzer (D
TA), a thermal analysis was performed at a heating rate of 10 ° C./min, and the melting point was measured. Table 6 shows the results.
【００３９】[0039]
【表６】 純Ｂｉの融点は約２７０℃であるが、Ｓｎとの合金化に
より低融点（１３９℃）の共晶相（Ｂｉ−４３Ｓｎ相）
ができると、高温での耐摩耗性が低下する。図５に示す
本実施例１〜４及び比較例５の純Ｂｉめっきの示差熱曲
線から、被覆層におけるＳｎの含有量が１重量％未満の
実施例１及び２では共晶が認められず、融点は純Ｂｉの
比較例５と同様である。[Table 6] The melting point of pure Bi is about 270 ° C, but a low melting point (139 ° C) eutectic phase (Bi-43Sn phase) due to alloying with Sn.
, The wear resistance at high temperatures decreases. From the differential thermal curves of the pure Bi plating of Examples 1 to 4 and Comparative Example 5 shown in FIG. 5, no eutectic was observed in Examples 1 and 2 in which the content of Sn in the coating layer was less than 1% by weight, The melting point is the same as in Comparative Example 5 of pure Bi.
【００４０】また、主たる相の融点はＳｎの含有量が多
くなるに従って低下するが、Ｓｎ含有量が２重量％以下
では融点の低下はわずかで、Ｓｎ含有量が２重量％であ
る実施例４でも融点の低下は５℃にとどまる。しかし、
Ｓｎ含有量が４．９重量％である実施例５では、主相の
融点が１０℃低下した上に、低融点の共晶相の比率が大
きくなっている。The melting point of the main phase decreases as the Sn content increases, but when the Sn content is 2% by weight or less, the melting point decreases only slightly, and the Sn content is 2% by weight. However, the decrease in melting point is limited to 5 ° C. But,
In Example 5 in which the Sn content was 4.9% by weight, the melting point of the main phase was reduced by 10 ° C., and the ratio of the eutectic phase having a low melting point was large.
【００４１】さらに、実施例１〜４と実施例５とを比較
するとわかるように、Ｓｎ含有量が２重量％以下の実施
例１〜４は実施例５と比べて耐焼付性がやや劣るが、摩
擦係数がやや低い点で優れる。また、実施例１〜４で
は、低融点の共晶相がほとんど無い、若しくは極めて少
ないため、低摩擦性の他に耐熱性の点でも実施例５より
優れている。Further, as can be seen from a comparison between Examples 1 to 4 and Example 5, Examples 1 to 4 having a Sn content of 2% by weight or less are slightly inferior in seizure resistance to Example 5. Excellent in that the coefficient of friction is slightly lower. Further, in Examples 1 to 4, the eutectic phase having a low melting point is scarcely or extremely small, and therefore, is superior to Example 5 in terms of heat resistance in addition to low friction.
【００４２】以上より、主相の融点低下及び共晶相の生
成を抑えて耐熱性を向上させるとともに、低摩擦性を達
成するためには、Ｓｎ含有量を２重量％以下とすること
が特に好ましいことがわかる。 ［第２実施例］本実施例は本発明の摺動部材を内燃機関
用すべり軸受に適用したものである。As described above, in order to suppress the lowering of the melting point of the main phase and the formation of the eutectic phase to improve the heat resistance and to achieve the low friction property, it is particularly preferable to set the Sn content to 2% by weight or less. It turns out to be preferable. [Second Embodiment] In this embodiment, the sliding member of the present invention is applied to a slide bearing for an internal combustion engine.
【００４３】図７に示すように、鋼製裏金１に、外径４
８ｍｍ、肉厚１．５ｍｍのＣｕ−Ｓｎ合金層（Ｃｕ：９
４．５重量％、Ｓｎ：５重量％）２をライニングしてな
る基材を準備した。この基材のＣｕ−Ｓｎ合金層２の表
面、すなわち相手材との摺動面に１．５μｍの厚さのＮ
ｉめっき層２’を形成した。なお、このときのめっき条
件は、めっき液：ワット浴、めっき液温度：５０℃、電
流密度：６Ａ／ｄｍ2である。As shown in FIG. 7, the steel back metal 1 has an outer diameter of 4 mm.
8 mm, 1.5 mm thick Cu—Sn alloy layer (Cu: 9
(4.5% by weight, Sn: 5% by weight) 2 was prepared as a base material. The surface of the Cu—Sn alloy layer 2 of this substrate, that is, the sliding surface with the mating material, has a 1.5 μm thick N
An i-plated layer 2 'was formed. The plating conditions at this time were: plating solution: watt bath, plating solution temperature: 50 ° C., current density: 6 A / dm 2 .
【００４４】そして、このＮｉめっき層２’の表面に、
前記第１実施例と同様の方法により被覆層３を形成し
て、すべり軸受を作製した。第１実施例で示した実施例
１〜１６及び比較例１〜４の被覆層を上記すべり軸受の
被覆層３に適用したものについて、軸受単体試験を行っ
た。その結果を図８に示す。なお、試験条件は以下のと
おりである。Then, on the surface of the Ni plating layer 2 ′,
The coating layer 3 was formed in the same manner as in the first embodiment to produce a plain bearing. A single bearing test was performed on the sliding layers of the sliding bearings of Examples 1 to 16 and Comparative Examples 1 to 4 shown in the first example. FIG. 8 shows the result. The test conditions are as follows.
【００４５】 試験装置 ：静荷重軸受試験機 回転数 ：５０００ｒｐｍ（周速：１２．５ｍ／
ｓ） 潤滑油 ：ＳＡＥ１０Ｗ−３０ 給油量 ：０．１リットル／分 給油温度 ：１００℃ 相手材 ：炭素鋼（Ｓ５０Ｃ、Ｈｖ：６００、表面
粗さ：０．８μｍＲｚ） 図８から明らかなように、すべり軸受の表面で相手材と
の摺動面に本発明に係る被覆層を形成することにより、
比較例１〜４と同等以上の軸受性能を発揮させることが
できた。Test apparatus: Static load bearing tester Rotation speed: 5000 rpm (peripheral speed: 12.5 m /
s) Lubricating oil: SAE10W-30 Lubrication amount: 0.1 liter / min Lubrication temperature: 100 ° C. Counterpart material: carbon steel (S50C, Hv: 600, surface roughness: 0.8 μmRz) As is clear from FIG. By forming the coating layer according to the present invention on the sliding surface with the mating material on the surface of the sliding bearing,
Bearing performance equal to or higher than Comparative Examples 1 to 4 could be exhibited.
【００４６】なお、上記実施例では、電気めっきにより
被覆層を形成した場合の結果を示したが、ＰＶＤ等の気
相めっき法で被覆層を形成した場合も同様の結果が得ら
れることを確認した。In the above example, the results in the case where the coating layer was formed by electroplating were shown. However, it was confirmed that similar results were obtained when the coating layer was formed by vapor phase plating such as PVD. did.
【００４７】[0047]
【発明の効果】以上詳述したように本発明の摺動部材
は、摺動面にＰｂを含有しないものであるが、摺動面に
Ｐｂ含有するものと同等の摺動特性を発揮することがで
きるAs described in detail above, the sliding member of the present invention does not contain Pb on the sliding surface, but exhibits the same sliding characteristics as those containing Pb on the sliding surface. Can
【図１】第１実施例に係り、被覆層の硬さの測定結果を
示す棒グラフである。FIG. 1 is a bar graph showing measurement results of hardness of a coating layer according to a first example.
【図２】第１実施例に係り、被覆層の摩擦係数の評価結
果を示す棒グラフである。FIG. 2 is a bar graph showing an evaluation result of a friction coefficient of a coating layer according to the first embodiment.
【図３】第１実施例に係り、被覆層の耐焼付き性の評価
結果を示す棒グラフである。FIG. 3 is a bar graph showing evaluation results of seizure resistance of a coating layer according to the first example.
【図４】第１実施例に係り、被覆層の耐摩耗性の評価結
果を示す棒グラフである。FIG. 4 is a bar graph showing evaluation results of abrasion resistance of a coating layer according to the first example.
【図５】第１実施例に係り、被覆層の融点の評価結果を
示す示差熱曲線であり、図（ｂ）は図（ａ）の縦軸の感
度を３倍にしたものである。FIG. 5 is a differential thermal curve showing evaluation results of the melting point of the coating layer according to the first example, and FIG. 5B is a graph in which the sensitivity on the vertical axis of FIG.
【図６】第１実施例に係り、上記示差熱曲線の吸熱ピー
クから求めた主相の融点を示す棒グラフである。FIG. 6 is a bar graph showing the melting point of the main phase determined from the endothermic peak of the differential heat curve according to the first example.
【図７】第２実施例に係り、すべり軸受の一部断面図で
ある。FIG. 7 is a partial cross-sectional view of a sliding bearing according to a second embodiment.
【図８】第２実施例に係り、被覆層の耐焼付き性の評価
結果を示す棒グラフである。FIG. 8 is a bar graph showing evaluation results of seizure resistance of the coating layer according to the second example.
１…鋼製裏金、２…Ｃｕ−Ｓｎ合金層、２’…Ｎｉめっ
き層、３…被覆層DESCRIPTION OF SYMBOLS 1 ... Steel back metal, 2 ... Cu-Sn alloy layer, 2 '... Ni plating layer, 3 ... Coating layer
フロントページの続き (72)発明者 不破 良雄 愛知県豊田市トヨタ町１番地 トヨタ自動 車株式会社内 (72)発明者 志村 好男 愛知県愛知郡長久手町大字長湫字横道41番 地の１株式会社豊田中央研究所内 (72)発明者 堀田 滋 愛知県愛知郡長久手町大字長湫字横道41番 地の１株式会社豊田中央研究所内Continued on the front page (72) Inventor Yoshio Fuwa 1 Toyota Town, Toyota City, Aichi Prefecture Inside Toyota Motor Co., Ltd. (72) Inventor Yoshio Shimura 41 Co., Ltd. Inside Toyota Central Research Laboratory (72) Inventor Shigeru Hotta 41, Ochimichi, Nagakute-cho, Aichi-gun, Aichi Prefecture
Claims (5)
面に形成された被覆層とからなる摺動部材において、 上記被覆層は、Ｓｎ、Ｉｎ及びＡｇよりなる群から選ば
れる少なくとも一種を含有し、残部が実質的にＢｉ及び
不可避不純物よりなることを特徴とする摺動部材。1. A sliding member comprising a base material and a coating layer formed on a sliding surface of the base material on a sliding surface with a mating material, wherein the coating layer is made of a group consisting of Sn, In and Ag. A sliding member comprising at least one selected member, with the balance substantially consisting of Bi and unavoidable impurities.
〜２５重量％であることを特徴とする請求項１記載の摺
動部材。2. The amount of Sn contained in the coating layer is 0.1
2. The sliding member according to claim 1, wherein the amount is from about 25% by weight to about 25% by weight.
〜１０重量％であることを特徴とする請求項１記載の摺
動部材。3. The amount of In contained in the coating layer is 0.1.
The sliding member according to claim 1, wherein the content is 10 to 10% by weight.
〜１０重量％であることを特徴とする請求項１記載の摺
動部材。4. The amount of Ag contained in the coating layer is 0.5
The sliding member according to claim 1, wherein the content is 10 to 10% by weight.
理することにより形成されためっき皮膜であることを特
徴とする請求項１記載の摺動部材。5. The sliding member according to claim 1, wherein said coating layer is a plating film formed by plating a surface of said base material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP06342898A JP3249774B2 (en) | 1997-06-05 | 1998-03-13 | Sliding member |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9-148262 | 1997-06-05 | ||
| JP14826297 | 1997-06-05 | ||
| JP06342898A JP3249774B2 (en) | 1997-06-05 | 1998-03-13 | Sliding member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH1150296A true JPH1150296A (en) | 1999-02-23 |
| JP3249774B2 JP3249774B2 (en) | 2002-01-21 |
Family
ID=26404551
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP06342898A Expired - Fee Related JP3249774B2 (en) | 1997-06-05 | 1998-03-13 | Sliding member |
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| Country | Link |
|---|---|
| JP (1) | JP3249774B2 (en) |
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