JP3298635B2 - Aluminum bearing alloy - Google Patents
Aluminum bearing alloyInfo
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- JP3298635B2 JP3298635B2 JP11021190A JP11021190A JP3298635B2 JP 3298635 B2 JP3298635 B2 JP 3298635B2 JP 11021190 A JP11021190 A JP 11021190A JP 11021190 A JP11021190 A JP 11021190A JP 3298635 B2 JP3298635 B2 JP 3298635B2
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Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は、アルミニウム系軸受合金に関するものであ
り、特に硬さが低い軸の表面を粗さず、耐焼付性に優れ
たアルミニウム系軸受合金に関するものである。Description: FIELD OF THE INVENTION The present invention relates to an aluminum-based bearing alloy, and particularly to an aluminum-based bearing alloy excellent in seizure resistance without roughening the surface of a shaft having low hardness. It is about.
（従来の技術） 特開昭53−87917号公報によると、Sn25重量％以下、
（以下、百分率は特に断らない限り重量％である）、Cr
またはZr0.1〜1.0％を基本成分として含有し、必要によ
りさらにCu0.5〜2.0％またはCu0.5〜2.0％とBe0.1〜0.5
％を含有するアルミニウム系軸受合金が提案されてい
る。この合金は、Al−Sn系合金の高温での急激な硬さ低
下を防ぐためにCrまたはZrを添加したことを特徴とする
と説明されているが、相手軸をS55C焼入軸とした動荷重
疲労試験により合金の特性を評価した実施例ではZr添加
の例は示されていない。(Prior Art) According to JP-A-53-87917, Sn 25% by weight or less,
(Hereinafter, percentages are% by weight unless otherwise specified), Cr
Or, Zr 0.1-1.0% is contained as a basic component, and if necessary, Cu 0.5-2.0% or Cu 0.5-2.0% and Be 0.1-0.5
% Aluminum-based bearing alloys have been proposed. This alloy is described as being characterized by the addition of Cr or Zr in order to prevent the Al-Sn-based alloy from suddenly dropping in hardness at high temperatures. Examples in which the properties of the alloy were evaluated by tests do not show examples of Zr addition.
特公昭60−55582号公報によると、Sn3〜40％、Pb0.1
〜５％、Sb0.1〜３％、Cuおよび／またはMg0.1〜3.0
％、Zrなど3.0％を超え10.0％までを含有するアルミニ
ウム系軸受合金が提案されている。この合金の特徴は、
Zrなどは硬質物形成元素として添加し、硬質物を多量に
存在させることによって相手軸に対する耐摩耗性を向上
するところにある。According to Japanese Patent Publication No. 60-55582, Sn3 to 40%, Pb0.1
-5%, Sb 0.1-3%, Cu and / or Mg 0.1-3.0
%, Zr and other aluminum alloys containing more than 3.0% and up to 10.0% have been proposed. The characteristics of this alloy are
Zr or the like is added as a hard material forming element, and the wear resistance to the mating shaft is improved by allowing a large amount of the hard material to be present.
さらに、特開昭62−63636号公報によると、Sn3〜20
％、Pb0.1〜５％、Cuおよび／またはMg0.2〜２％、Zr0.
1〜１％、Si1.5〜８％を含有するアルミニウム系軸受合
金が提案されている。この合金の特徴は、Zrの添加によ
りアルミニウム基地を固溶強化しかつ析出物の生成によ
りSnの粗大化を防ぎ、また、単体で1000以上のビッカー
ス硬さをもつSiの添加により耐焼付性および耐摩耗性を
高めたところにある。従来のアルミニウム系軸受合金で
は、主として相手軸が球状黒鉛鋳鉄であるときの耐摩耗
性向上を重視されていた。ところが近年エンジンの振
動、騒音低減の観点から、焼入鋼、炭素鋼を焼入れある
いは焼準しないで鍛造のまま非調質で使用する検討が行
われるようになった。Further, according to JP-A-62-63636, Sn3 to 20
%, Pb 0.1-5%, Cu and / or Mg 0.2-2%, Zr0.
An aluminum-based bearing alloy containing 1 to 1% and 1.5 to 8% of Si has been proposed. The features of this alloy are solid solution strengthening of the aluminum matrix by the addition of Zr and the prevention of coarsening of Sn by the formation of precipitates, and the addition of Si, which has a Vickers hardness of 1000 or more by itself, has seizure resistance and It is where the abrasion resistance is enhanced. In conventional aluminum-based bearing alloys, emphasis has been placed on improving wear resistance when the mating shaft is made of spheroidal graphite cast iron. However, in recent years, from the viewpoint of reducing engine vibration and noise, studies have been made to use quenched steel or carbon steel without forging or tempering without tempering.
（発明が解決しようとする課題） ところが、従来のアルミニウム系軸受合金を非調質軸
に対して使用すると軸受が軸の表面を粗してしまい、軸
受が軸に低い荷重で焼付いてしまう問題が現れた。(Problems to be Solved by the Invention) However, when a conventional aluminum-based bearing alloy is used for a non-heat-treated shaft, the problem is that the bearing roughens the surface of the shaft and the bearing is seized with a low load on the shaft. Appeared.
（課題を解決するための手段） 上記した課題を解決する本発明の第１は、 Sn2〜25重量％、 Zr0.02〜1.0重量％、 CuおよびMgの少なくとも１種0.1〜2.5重量％ Pb、BiおよびInの１種以上0.1〜8.0重量％、 を含有し、残部が不可避的不純物及びAlからなることを
特徴とするアルミニウム系軸受合金である。(Means for Solving the Problems) A first aspect of the present invention for solving the above-mentioned problems is that Sn2 to 25% by weight, Zr 0.02 to 1.0% by weight, at least one of Cu and Mg 0.1 to 2.5% by weight Pb, An aluminum-based bearing alloy containing 0.1 to 8.0% by weight of at least one of Bi and In, with the balance being unavoidable impurities and Al.
本発明の第２は、 Sn2〜25重量％、 Zr0.02〜1.0重量％、 CuおよびMgの少なくとも１種0.1〜2.5重量％ Pb、BiおよびInの１種以上0.1〜8.0重量％、 Mn、Ｖ、Sb、Nb、Mo、Co、Ti、TiB、FeおよびSrの１
種以上0.01〜2.0重量％ を含有し、残部が不可避的不純物及びAlからなることを
特徴とするアルミニウム系軸受合金である。In the second aspect of the present invention, Sn2 to 25% by weight, Zr 0.02 to 1.0% by weight, at least one of Cu and Mg 0.1 to 2.5% by weight Pb, at least one of Bi and In 0.1 to 8.0% by weight, Mn, V, Sb, Nb, Mo, Co, Ti, TiB, Fe and Sr
An aluminum-based bearing alloy containing at least 0.01% to 2.0% by weight of a seed, with the balance being unavoidable impurities and Al.
以下、本発明の構成を詳しく説明する。 Hereinafter, the configuration of the present invention will be described in detail.
先ず第１発明と第２発明に共通する組成について説明
する。First, a composition common to the first invention and the second invention will be described.
Snは潤滑性向上を主目的として添加される元素であ
る。Snの含有量が２％未満であると、潤滑性がなく、一
方25％を超えると合金全体が軟質になって耐荷重性、耐
疲労性および耐食性が低下する。好ましいSnの含有量は
３〜20％である。より好ましいSnの含有量は８〜15％で
ある。Sn is an element added mainly for improving lubricity. If the Sn content is less than 2%, there is no lubricity, while if it exceeds 25%, the entire alloy becomes soft and the load resistance, fatigue resistance and corrosion resistance are reduced. The preferred Sn content is 3-20%. A more preferred Sn content is 8 to 15%.
Pb、Bi,In（以下「Pbなど」と総称することもある）
は一部はアルミニウム基地に分散するが、そのPbなどの
分散相の一部はSnに固溶しあるいは共晶合金を作り、Sn
相の親油性や相手軸との凝着性を改善する。また、Pbな
どはそれ自体でなじみ性を高める作用をもつ。このよう
にPbなどとSnは作用が類似しまたPbなどの添加によりSn
が安定化するために、Pbなどを添加するとSnの好ましい
量を３〜20％のより低い範囲とすることができ、この結
果耐疲労性も向上する。Pb, Bi, In (hereinafter sometimes collectively referred to as "Pb etc.")
Is partially dispersed in the aluminum matrix, but a part of the dispersed phase such as Pb is dissolved in Sn or forms a eutectic alloy,
Improves the lipophilicity of the phase and the adhesion to the mating shaft. In addition, Pb and the like have an action of enhancing familiarity by themselves. As described above, Sn and Pb etc. have similar actions, and Sn
When Pb or the like is added in order to stabilize, the preferable amount of Sn can be set to a lower range of 3 to 20%, and as a result, fatigue resistance is also improved.
Pbなどの添加量が0.1％未満では上記の作用がなく、
一方8.0％（２種以上添加の場合は合計量）を超える
と、Pbなどはアルミニウム合金中でAl−Pb−Sn,Al−In
−Sn,Al−Bi−Snは低融点の共晶組織を作り易く、耐疲
労性や耐荷重性が低下するので、Pbなどの添加量は0.1
〜8.0％とする必要がある。If the added amount of Pb or the like is less than 0.1%, the above effect is not obtained.
On the other hand, if the content exceeds 8.0% (the total amount in the case of adding two or more types), Pb and the like in the aluminum alloy Al-Pb-Sn, Al-In
-Sn, Al-Bi-Sn tends to form a eutectic structure with a low melting point, and reduces fatigue resistance and load resistance.
It must be ~ 8.0%.
Zrはアルミニウム基地に固溶することによって、Alの
再結晶温度を上げかつ固溶強化する。また、再結晶温度
を上げることは軸受がさらされる内燃機関の高温環境で
も安定した機械的性質を維持するのに効果がある。Zr increases the recrystallization temperature of Al and strengthens the solid solution by forming a solid solution in the aluminum matrix. Increasing the recrystallization temperature is also effective in maintaining stable mechanical properties even in a high-temperature environment of the internal combustion engine to which the bearing is exposed.
Zrを添加した本発明合金の特に優れた性質は高温硬さ
が高いことである。これは固溶強化が顕著であるために
基地の高温での硬度低下が少ないこと、および再結晶軟
化温度が高温側にずれることによる。A particularly excellent property of the alloy of the present invention to which Zr is added is that the high-temperature hardness is high. This is due to the fact that the solid solution strengthening is remarkable, so that the hardness of the matrix hardly decreases at a high temperature, and the recrystallization softening temperature shifts to the high temperature side.
ZrのAl中の最大固溶量は平衡状態図から0.28％程度で
あると考えられる。一方、平衡状態ではない鋳造時には
さらに固溶量を増し、過飽和固溶体を作るが、本発明の
含有量範囲でZrの一部は析出する。Zrの析出物が微細に
分散することは高温硬さの維持に良い影響を与え、また
Sn粒子の粗大化やその移動を直接妨げ、またAlの結晶粒
界の移動を阻止し、結晶粒界の移動に伴うSn粒子の粗大
化を間接的に妨げる。したがって、圧延と焼鈍の繰り返
しによって微細化されたSn粒子を軸受使用中に微細に保
つことができる。また、Sn粒子が微細なまま保持されて
アルミニウム基地中に存在することは232℃という低融
点をもつSn粒子が高温で溶け出すと言う溶出現象を防止
するためにも効果的である。From the equilibrium diagram, the maximum solid solution amount of Zr in Al is considered to be about 0.28%. On the other hand, when casting is not in an equilibrium state, the amount of solid solution is further increased to form a supersaturated solid solution, but a part of Zr is precipitated within the content range of the present invention. Fine dispersion of Zr precipitates has a good effect on maintaining high temperature hardness,
It directly hinders the coarsening and movement of the Sn particles, and also prevents the movement of the Al grain boundaries, and indirectly hinders the Sn particles from moving along with the grain boundaries. Therefore, Sn particles refined by repeating rolling and annealing can be kept fine during use of the bearing. The fact that the Sn particles are kept fine and exist in the aluminum matrix is also effective for preventing the elution phenomenon that Sn particles having a low melting point of 232 ° C. are melted at a high temperature.
Zrの添加量が0.02％未満であると上記した作用が発現
せず、1.0％を超えるとAl−Zrの金属間化合物が多量か
つ粗大に析出し、合金が硬くかつ脆くなり軸受の本質的
性能が失われてしまいかつ、軸受が非調質軸を著しく疵
付ける。好ましいZrの添加量は0.05〜0.3％である。If the amount of Zr is less than 0.02%, the above-mentioned effects are not exhibited. If the amount exceeds 1.0%, a large amount of Al-Zr intermetallic compound precipitates coarsely, the alloy becomes hard and brittle, and the essential performance of the bearing is obtained. Are lost and the bearings severely scratch the non-heat treated shaft. The preferable addition amount of Zr is 0.05 to 0.3%.
CuおよびMgは主として高温での高硬度を確保するため
に、１種または２種添加される。Cuおよび／またはMgを
添加しないAl−Sn−Pb合金と、Cuおよび／またはMgを添
加したAl−Sn−Pb合金についZrの作用を比較すると、後
者の方がZrの作用が量的に顕著であることが認められ
る。したがって、α−Al相中にCuおよびMgを溶質原子と
して存在させることはZrの上記作用を高める面からも有
利である。One or two kinds of Cu and Mg are mainly added to ensure high hardness at high temperatures. Comparing the effect of Zr on the Al-Sn-Pb alloy to which Cu and / or Mg is not added and the effect of Zr for the Al-Sn-Pb alloy to which Cu and / or Mg is added, the effect of Zr is remarkably quantitative in the latter. Is recognized. Therefore, the presence of Cu and Mg as solute atoms in the α-Al phase is also advantageous from the viewpoint of enhancing the above-described action of Zr.
本発明の第２の軸受合金は上記した組成にさらに、M
n、Ｖ、Sb、Nb、Mo、Co、Ti、TiB、FeおよびSrの１種以
上を0.01〜2.0％含有することを特徴とする。これらの
元素は硬質物を発生させ、耐摩耗性を向上するが、2.0
％を超えると軸受が相手材を疵つける傾向が現れるので
2.0％以下に制限して添加しなければならない。また添
加量が0.01％未満では効果がない。The second bearing alloy of the present invention further comprises M
It is characterized by containing 0.01 to 2.0% of at least one of n, V, Sb, Nb, Mo, Co, Ti, TiB, Fe and Sr. These elements generate hard materials and improve wear resistance.
%, The bearing tends to damage the mating material.
Must be added limited to 2.0% or less. If the amount is less than 0.01%, there is no effect.
本発明の軸受は、鋳造、冷間圧延、中間焼鈍、裏金へ
の圧接等の工程により製造される。圧延品が著しく加工
硬化しているときは必要により最終焼鈍を行ってもよ
い。中間焼鈍および最終焼鈍の温度は220〜520℃の範囲
内であることが好ましい。温度が220℃未満であるとAl
−Cu,Al−Mgの時効析出は起こるがAl−Cu,Al−Mgの析出
は本発明の特性達成のために本質的ではなく、また圧延
過程における加工硬化を取り除くために220℃以上の温
度が好ましい。さらにZrの過飽和固溶部分を微細析出さ
せるには300〜520℃が好ましい。焼鈍温度が520℃を超
えると、Al−Cu−Ｘ系の多元共晶温度に近付き、Sn以外
にAlの液相が表れ、合金の強度が低下しさらにSn相が粗
大化するので、520℃以下の焼鈍温度が好ましい。The bearing of the present invention is manufactured by processes such as casting, cold rolling, intermediate annealing, and pressing against a back metal. If the rolled product is extremely work-hardened, final annealing may be performed if necessary. The temperature of the intermediate annealing and the final annealing is preferably in the range of 220 to 520 ° C. If the temperature is lower than 220 ° C,
-Aging precipitation of Cu, Al-Mg occurs, but precipitation of Al-Cu, Al-Mg is not essential for achieving the characteristics of the present invention, and a temperature of 220 ° C or higher to remove work hardening in the rolling process. Is preferred. Further, in order to finely precipitate the supersaturated solid solution portion of Zr, the temperature is preferably 300 to 520 ° C. When the annealing temperature exceeds 520 ° C, the temperature approaches the multi-eutectic temperature of the Al-Cu-X system, a liquid phase of Al appears in addition to Sn, the strength of the alloy is reduced, and the Sn phase is further coarsened. The following annealing temperatures are preferred.
本発明の軸受の相手軸は非調質鋼材である。鋼材とし
ては炭素鋼が一般に使用される。Ｖなどの硬化元素を微
量添加した炭素鋼の非調質鋼が軸として使用される場合
にも本発明の軸受が使用される。鋼材の炭素量は一般に
0.4〜0.65％の中炭素含有量である。本発明の軸受の相
手材としては鋳鉄は使用されない。また「非調質」とは
圧延あるいは鍛造のままと言う意味であり、硬さでは特
にHv＝180〜330の状態を指している。The mating shaft of the bearing of the present invention is a non-heat treated steel material. Carbon steel is generally used as the steel material. The bearing of the present invention is also used when a non-heat treated steel of carbon steel to which a small amount of a hardening element such as V is added is used as a shaft. The carbon content of steel is generally
Medium carbon content of 0.4-0.65%. Cast iron is not used as a mating material of the bearing of the present invention. The term "non-heat treated" means that the steel sheet is in a rolled or forged state, and the hardness particularly indicates a state of Hv = 180 to 330.
（作用） 実施例で説明する試験方法により下記の４種類の合金
の特性を評価した。(Operation) The characteristics of the following four alloys were evaluated by the test methods described in the examples.
本発明 Al−13％Sn−２％Pb−１％Cu−0.2％Zr 比較例 Al−13％Sn −１％Cu−0.2％Zr 比較例 Al−13％Sn−２％Pb−１％Cu−0.2％Cr 比較例 Al−13％Sn−２％Pb−１％Cu−0.2％Zr
−３％Si 各材料は鋳造により製造したストリップを６回圧延
し、最終板厚が1mmの板に加工した。圧延の途中で220〜
520℃で中間焼鈍を行った。得られた板をNiめっきされ
た裏金鋼板（SPCC）に圧接してバイメタルを作り、これ
を試験片形状に加工した。試験結果は以下のとおりであ
った。Present invention Al-13% Sn-2% Pb-1% Cu-0.2% Zr Comparative Example Al-13% Sn-1% Cu-0.2% Zr Comparative Example Al-13% Sn-2% Pb-1% Cu- 0.2% Cr Comparative Example Al-13% Sn-2% Pb-1% Cu-0.2% Zr
-3% Si For each material, a strip produced by casting was rolled six times to be processed into a plate having a final thickness of 1 mm. 220 ~ in the middle of rolling
Intermediate annealing was performed at 520 ° C. The obtained plate was pressed against a Ni-plated backed steel plate (SPCC) to form a bimetal, which was processed into a test piece shape. The test results were as follows.
この結果の比較より各成分の作用が分かる。 The effect of each component can be understood from the comparison of the results.
まず、相手軸が球状黒鉛鋳鉄（FCD）であると、Siを
含有させることによりすぐれた特性が得られる（比較例
）。First, when the mating shaft is spheroidal graphite cast iron (FCD), excellent characteristics can be obtained by containing Si (Comparative Example).
次に、焼入鋼（S50C−Ｈ、硬さHv＝600）や圧延のま
まの鋼（S50C−Ｒ），硬さHv＝230）が相手軸である
と、Siは特性を却って低下させている（比較例または
比較例と比較例の対比）。Next, if the quenched steel (S50C-H, hardness Hv = 600) or the as-rolled steel (S50C-R), hardness Hv = 230, is the mating shaft, Si will deteriorate its properties rather. (Comparative Example or Comparative Example and Comparative Example).
比較例は本発明の添加成分ではないCrを含有する
が、特開昭53−87917号公報においてCrがZrと代替可能
であると（実施例には基づかない）一般説明があるの
で、CrとZrの作用をデータに基づいて比較するために比
較例を示した。CrとZrの耐焼付性向上作用は量的に同
じであるが、耐疲労性向上の面ではZrの作用がCrの作用
よりも量的に優れている（比較例と本発明との比
較）。また、高温硬さもZrの方がCrよりも優れている。The comparative example contains Cr which is not an additive component of the present invention. However, in JP-A-53-87917, there is general explanation that Cr can be substituted for Zr (not based on the examples). A comparative example was given to compare the effects of Zr based on the data. The effect of improving seizure resistance of Cr and Zr is quantitatively the same, but the effect of Zr is quantitatively superior to that of Cr in terms of improving fatigue resistance (comparison between comparative example and the present invention). . Also, Zr is superior to Cr in high-temperature hardness.
CrはZrよりも再結晶を遅らせる効果が少ない。第１図
は「本発明」材と比較例の材料の60％冷間圧延後の再
結晶軟化を示し、横軸は加熱温度（℃）、縦軸は室温へ
冷却後測定した硬さ（Hv）である。本発明の材料は360
℃から再結晶軟化が始まり、比較例材は300℃から軟化
が始まっていることが分かる。Cr has less effect of delaying recrystallization than Zr. FIG. 1 shows the recrystallization softening of the “inventive” material and the material of the comparative example after 60% cold rolling. The horizontal axis is the heating temperature (° C.), and the vertical axis is the hardness (Hv) measured after cooling to room temperature. ). The material of the present invention is 360
It can be seen that the recrystallization softening started at ℃ and the softening of the comparative material started at 300 ℃.
Pbは耐焼付性を向上させる（比較例と本発明の比
較）。Pbの添加により高温硬さは若干低下するが、特性
は優れている。これはSnが潤滑油との親油性が改善され
るためであると考えられる。Pb improves seizure resistance (comparison between comparative examples and the present invention). Although the high-temperature hardness is slightly reduced by the addition of Pb, the properties are excellent. This is considered to be because Sn improves the lipophilicity with the lubricating oil.
以下、実施例によりさらに詳しく本発明を説明する。 Hereinafter, the present invention will be described in more detail with reference to Examples.
（実施例） 表１の組成の合金を溶解し、前述の方法でバイメタル
状の軸受とし、以下の条件で試験を行った。(Examples) An alloy having the composition shown in Table 1 was melted to obtain a bimetallic bearing by the above-described method, and a test was performed under the following conditions.
焼付試験 （１）ジャーナル型焼付き試験機 （２）回転数−1500rpm （３）荷重増加法−50Kg/cm2を30分毎に増加（焼付いた
時の面圧測定） （４）潤滑油−SAE10W30 （５）給油温度−140℃ （６）相手軸−S50C鍛造のまま（硬度Hv＝230） 疲労試験 （１）往復動荷重試験機 （２）回転数−3000rpm （３）荷重−107回で疲労する面圧を測定 （４）潤滑油−SAE10W30 （５）給油温度−140℃ （発明の効果） 以上説明したように、本発明請求項１記載の軸受合金
は特開昭53−87918号（Cr添加）のものに比較して耐疲
労性が優れ、また特開昭62−63636号（Si含有）に比較
して耐焼付性および耐疲労性に優れている。Seizure test (1) journaled seizure tester (2) increasing the rotational speed -1500Rpm (3) load increase method -50Kg / cm 2 every 30 minutes (surface pressure measurement when seizure) (4) lubricating oil - SAE10W30 (5) Lubrication temperature -140 ° C (6) Mating shaft-As forged S50C (hardness Hv = 230) Fatigue test (1) Reciprocating dynamic load tester (2) Rotational speed-3000 rpm (3) Load-10 7 times (4) Lubricating oil-SAE10W30 (5) Lubrication temperature-140 ° C (Effects of the Invention) As described above, the bearing alloy according to claim 1 of the present invention has better fatigue resistance than that of JP-A-53-87918 (Cr addition), and Superior in seizure resistance and fatigue resistance compared to No. 63636 (containing Si).
さらに、必要により請求項２記載のように硬質物形成
元素を添加して耐摩耗性を向上させることができる。Further, if necessary, a hard material-forming element may be added to improve the wear resistance.
【図面の簡単な説明】 第１図はZr（本発明材）とCr（比較材）添加による再
結晶軟化に及ぼす影響を示すグラフである。BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a graph showing the effect of adding Zr (the material of the present invention) and Cr (a comparative material) on recrystallization softening.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 二村 憲一朗 愛知県豊田市緑ケ丘３丁目65番地 大豊 工業株式会社内 (56)参考文献 特開 昭62−235436（ＪＰ，Ａ) 特開 昭62−224722（ＪＰ，Ａ) 特開 昭62−110021（ＪＰ，Ａ) 特開 昭58−67841（ＪＰ，Ａ) 特開 昭56−35744（ＪＰ，Ａ) 特開 昭57−207151（ＪＰ，Ａ) ──────────────────────────────────────────────────続 き Continuation of the front page (72) Inventor Kenichiro Nimura 3-65 Midorigaoka, Toyota City, Aichi Prefecture Inside Taitoyo Kogyo Co., Ltd. (56) References JP-A-62-235436 (JP, A) JP-A-62-224722 (JP, A) JP-A-62-110021 (JP, A) JP-A-58-67841 (JP, A) JP-A-56-35744 (JP, A) JP-A-57-207151 (JP, A)
Claims (2)
度Hv180〜330の非調質鋼材軸を相手軸とする耐焼付性及
び耐疲労性が優れたアルミニウム系軸受合金。1. An alloy containing 2 to 25% by weight of Sn, 0.02 to 1.0% by weight of Zr, 0.1 to 2.5% by weight of at least one of Cu and Mg, and 0.1 to 8.0% by weight of at least one of Pb, Bi and In. Aluminum bearing alloy whose balance is made of unavoidable impurities and Al, and which has a non-heat-treated steel shaft with a hardness of Hv180 to 330 and has excellent seizure resistance and fatigue resistance.
0.01〜2.0重量％ を含有し、残部が不可避的不純物およびAlからなり、硬
度Hv180〜330の非調質鋼材軸を相手軸とする耐焼付性及
び耐疲労性が優れたアルミニウム系軸受合金。2. 2 to 25% by weight of Sn, 0.02 to 1.0% by weight of Zr, 0.1 to 2.5% by weight of at least one of Cu and Mg, 0.1 to 8.0% by weight of at least one of Pb, Bi and In, Mn, V , Sb, Nb, Mo, Co, Ti, TiB, Fe and at least one of Sr
Aluminum bearing alloy containing 0.01 to 2.0% by weight, the balance consisting of unavoidable impurities and Al, and having excellent anti-seizure and fatigue resistance with a non-heat-treated steel shaft having a hardness of Hv 180 to 330 as the mating shaft.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11021190A JP3298635B2 (en) | 1990-04-27 | 1990-04-27 | Aluminum bearing alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11021190A JP3298635B2 (en) | 1990-04-27 | 1990-04-27 | Aluminum bearing alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH049443A JPH049443A (en) | 1992-01-14 |
| JP3298635B2 true JP3298635B2 (en) | 2002-07-02 |
Family
ID=14529878
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11021190A Expired - Fee Related JP3298635B2 (en) | 1990-04-27 | 1990-04-27 | Aluminum bearing alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3298635B2 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AT405296B (en) * | 1995-12-20 | 1999-06-25 | Miba Gleitlager Ag | SLIDING BEARING MATERIAL FROM ONE UP TO MELTING-BASED IMPURITIES SILICON-FREE ALUMINUM ALLOY |
| WO1998017833A2 (en) * | 1996-10-18 | 1998-04-30 | Miba Gleitlager Aktiengesellschaft | Sliding bearing material made from an aluminium alloy which is silicon-free apart from impurities necessitated by steel production |
| DE19833200A1 (en) * | 1998-07-23 | 2000-01-27 | Ks Gleitlager Gmbh | Aluminum-tin or aluminum-lead plain bearing alloy, contains iron, manganese and silicon or cobalt or molybdenum for globular mixed iron aluminide formation |
| AT412284B (en) * | 2003-03-14 | 2004-12-27 | Miba Gleitlager Gmbh | Wrought aluminum |
-
1990
- 1990-04-27 JP JP11021190A patent/JP3298635B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH049443A (en) | 1992-01-14 |
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