JPH049443A - Aluminum series bearing alloy - Google Patents
Aluminum series bearing alloyInfo
- Publication number
- JPH049443A JPH049443A JP11021190A JP11021190A JPH049443A JP H049443 A JPH049443 A JP H049443A JP 11021190 A JP11021190 A JP 11021190A JP 11021190 A JP11021190 A JP 11021190A JP H049443 A JPH049443 A JP H049443A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- resistance
- weight
- bearing
- bearing alloy
- 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
- 239000001996 bearing alloy Substances 0.000 title claims abstract description 12
- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical group [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 title 1
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 14
- 229910052802 copper Inorganic materials 0.000 claims abstract description 12
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 9
- 229910052797 bismuth Inorganic materials 0.000 claims abstract description 7
- 229910052738 indium Inorganic materials 0.000 claims abstract description 7
- 229910052745 lead Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052787 antimony Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052712 strontium Inorganic materials 0.000 claims abstract description 3
- 229910010055 TiB Inorganic materials 0.000 claims abstract 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 13
- 229910045601 alloy Inorganic materials 0.000 abstract description 15
- 239000000956 alloy Substances 0.000 abstract description 15
- 229910052726 zirconium Inorganic materials 0.000 abstract description 7
- 239000000126 substance Substances 0.000 abstract description 5
- 229910052718 tin Inorganic materials 0.000 abstract description 3
- 230000000052 comparative effect Effects 0.000 description 16
- 230000000694 effects Effects 0.000 description 12
- 238000007792 addition Methods 0.000 description 11
- 239000000463 material Substances 0.000 description 11
- 238000000137 annealing Methods 0.000 description 8
- 230000013011 mating Effects 0.000 description 8
- 238000001953 recrystallisation Methods 0.000 description 7
- 229910000831 Steel Inorganic materials 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 239000010959 steel Substances 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 239000002245 particle Substances 0.000 description 5
- 239000002244 precipitate Substances 0.000 description 5
- 239000012071 phase Substances 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 229910000975 Carbon steel Inorganic materials 0.000 description 3
- 239000010962 carbon steel Substances 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000001965 increasing effect Effects 0.000 description 3
- 239000010687 lubricating oil Substances 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910018134 Al-Mg Inorganic materials 0.000 description 2
- 229910018467 Al—Mg Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910001018 Cast iron Inorganic materials 0.000 description 2
- 229910001141 Ductile iron Inorganic materials 0.000 description 2
- 229910000760 Hardened steel Inorganic materials 0.000 description 2
- 229910020816 Sn Pb Inorganic materials 0.000 description 2
- 229910020922 Sn-Pb Inorganic materials 0.000 description 2
- 229910008783 Sn—Pb Inorganic materials 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000003921 oil Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910018182 Al—Cu Inorganic materials 0.000 description 1
- 229910018580 Al—Zr Inorganic materials 0.000 description 1
- 229910001020 Au alloy Inorganic materials 0.000 description 1
- 229910016338 Bi—Sn Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000010828 elution Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 239000006023 eutectic alloy Substances 0.000 description 1
- 238000009661 fatigue test Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000003353 gold alloy Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
Landscapes
- Sliding-Contact Bearings (AREA)
Abstract
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
、特に硬さが伝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。Detailed Description of the Invention (Field of Industrial Application) The present invention relates to an aluminum-based bearing alloy, and particularly an aluminum-based bearing alloy that is hard, does not roughen the shaft surface, and has excellent seizure resistance. It is related to.
（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ＺｒＯ，１〜１．０％を基本成分とし
て含有し、必要によりさらにＣｕＯ１５〜２．０％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−３ｎ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５５５Ｃ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 No. 53-87917, the basic components are 25% by weight or less of Sn (hereinafter, percentages are by weight unless otherwise specified), and 1 to 1.0% of Cr or ZrO. Aluminum-based bearing alloys have been proposed that further contain 15 to 2.0% CuO or 0.5 to 2.0% Cu and 0.1 to 0.5% Be. This alloy is said to be characterized by the addition of Cr or Zr to prevent the rapid hardness reduction at high temperatures of Al-3n alloys, but it is said that the alloy is characterized by the addition of Cr or Zr to prevent the rapid hardness reduction at high temperatures of Al-3n alloys. In the example in which the properties of the alloy were evaluated through tests, Zr
No examples of additions are given.
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, Sn3-40
%, Pb0.1-5%, Sb0.1-3%, Cu and/or Mg0.1-3.0%, Zr, etc. Proposed. A feature of this alloy is that Zr and the like are added as hard substance forming elements, and by making a large amount of hard substances exist, the wear resistance against the mating shaft is improved.
さらに、特開昭６２−６３６３６号公報によると、Ｓ
ｎ ３〜２０％、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
もっ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串
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。Furthermore, according to Japanese Patent Application Laid-open No. 62-63636, S
n 3~20%, Pb0.1~5%, Cu and/or Mg0.2~2%, Zr0.1~1%, Si1.5~
An aluminum-based bearing alloy containing 8% has been proposed. The characteristics of this alloy are that the addition of Zr strengthens the aluminum matrix and prevents the coarsening of Sn by forming precipitates, and the addition of Si, which alone has a Vickers hardness of 1000 or more, improves seizure resistance and It has improved wear resistance. In conventional aluminum-based bearing alloys, emphasis has been placed primarily on improving wear resistance when the mating shaft is made of spheroidal graphite cast iron. However, in recent years, from the perspective of reducing engine vibration and noise, studies have begun to consider using quenched steel and carbon steel without quenching or skewering, instead of using them in their forged form without heat treatment.
（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。(Problem to be solved by the invention) However, when a conventional aluminum-based bearing alloy is used for a non-tempered shaft, the surface of the bearing becomes rough, and there is a problem that the bearing seizes on the shaft under a low load. Appeared.
また、近年エンジンが高出力、高速、高温、低燃費かつ
低排ガス化に伴い、通常の焼入鋼軸に対して従来のアル
ミニウム系軸受合金を使用した場合でも高面圧、高温、
高速の使用環境のもとて耐疲労性や耐焼付性が不十分に
なることがあった。In addition, in recent years, engines have become more powerful, faster, hotter, more fuel efficient, and have lower exhaust emissions.
Under high-speed usage environments, fatigue resistance and seizure resistance were sometimes insufficient.
（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％、
ＺｒＯ，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) The first aspect of the present invention for solving the above-mentioned problems is Sn2-25
Weight%, ZrO, 02' to 1.0% by weight, 0.1 to 2.5% by weight of at least one of Cu and Mg, 0.1 to 8.0% by weight of one or more of Pb, Bi, and In.
It is an aluminum-based bearing alloy characterized by containing , and the remainder consisting of inevitable 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、Ｆ
ｅ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Ａ１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。The second aspect of the present invention is 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 2.5% of at least one of Pb, Bi, and In. 1-8.0% by weight
, Mn, V, Sb, Nb%Mo, Co, Ti, TiB, F
This is an aluminum-based bearing alloy characterized by containing 0.01 to 2.0% by weight of one or more of e and Sr, with the remainder consisting of unavoidable impurities and A1.
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 explained 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, the composition common to the first invention and the second invention will be explained.
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 primarily to improve lubricity. If the Sn content is less than 2%, there will be no lubricity, while if it exceeds 25%, the entire alloy will become soft and the load resistance will deteriorate.
Fatigue resistance and corrosion resistance are reduced. The preferred Sn content is 3 to 20%. More preferable Sn content is 8
~15%.
Ｐｂ、Ｂｉ、Ｉｎ （以下ｒｐｂ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なとの分散相の一部は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なと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なとの添加により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
。Part of Pb, Bi, and In (hereinafter sometimes collectively referred to as rpb, etc.) is dispersed in the aluminum base, but part of the dispersed phase with Pb is dissolved in Sn or forms a eutectic alloy. , improves the lipophilicity of the Sn phase and the adhesion with the mating shaft. In addition, pbna itself has the effect of increasing familiarity. In this way, PB etc. and Sn have similar effects, and since Sn is stabilized by adding PB etc., the preferable amount of Sn can be set to a lower range of 3 to 20% by adding PB etc. As a result, fatigue resistance is also improved.
ｐｂなとの添加量が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−Ｓ
ｎ、Ａｌ−Ｉｎ−ＳｎＡｌ−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なとの添加量は０．１〜８．０％とする必要がある
。If the amount of Pb added is less than 0.1%, the above effect will not occur, while if it exceeds 8.0% (total amount if two or more types are added), Pb etc. will cause Al-Pb- in the aluminum alloy. S
n, Al-In-SnAl-Bi-Sn tends to form a eutectic structure with a low melting point, which reduces fatigue resistance and load resistance.
The amount of pb added must be 0.1 to 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。By dissolving Zr in the aluminum base, it becomes Al
Raise the recrystallization temperature and solid solution strengthen.
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。Furthermore, increasing the recrystallization temperature is effective in maintaining stable mechanical properties even in the high-temperature environment of an 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 Zr-added alloy according to the invention is its high high temperature hardness. This is because solid solution strengthening is significant, so the hardness of the matrix decreases little at high temperatures, 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
物が微細に不分散することは高温硬さの維持に良い影響
を与え、またＳ ｎ粒子の粗大化やその移動を直接妨げ
、またＡ１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
溶は出すと言う溶出現象を防止するためにも効果的であ
る。The maximum solid solution amount of Zr in Al is 0.28% from the equilibrium phase diagram.
It is considered that the 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 precipitates within the content range of the present invention. The fine dispersion of Zr precipitates has a positive effect on maintaining high-temperature hardness, directly prevents the coarsening and movement of Sn particles, and also prevents the movement of grain boundaries of A1, resulting in crystal growth. This indirectly prevents Sn particles from becoming coarser due to movement of grain boundaries. Therefore, the Sn particles made fine by repeated rolling and annealing can be kept fine during use of the bearing. Furthermore, keeping the Sn particles as fine as they are in the aluminum matrix is effective in preventing the elution phenomenon in which Sn particles, which have a low melting point of 232° C., melt out at high temperatures.
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（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 added is less than 0.02%, the above effects will not occur, and if it exceeds 1.0%, a large amount of Al-Zr intermetallic compounds will precipitate coarsely, making the alloy hard and brittle. The essential performance of the bearing will be lost, and the bearing will seriously damage the non-tempered shaft.The preferred amount of Zr added is 0.05~
It is 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金合金、Ｃｕおよび
／またはＭｇを添加したＡｌ−Ｓｎ−Ｐｂ合金についＺ
ｒ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−Ａ１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 types of Cu and Mg are added mainly to ensure high hardness at high temperatures. Z for Al-Sn-Pb gold alloys without the addition of Cu and/or Mg, and Al-Sn-Pb alloys with the addition of Cu and/or Mg.
Comparing the effect of r, it is recognized that the effect of Zr is quantitatively more significant in the latter case. Therefore, the presence of Cu and Mg as solute atoms in the α-A1 phase is advantageous in terms of enhancing the above-mentioned effect of Zr.
本発明の第２の軸受台金は上記した組成にさらに、Ｍｎ
、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 base metal of the present invention further includes Mn in addition to the above-described composition.
, V, Sb, Nb%Mo, Co%Ti, TiB, Fe, and Sr in an amount of 0.01 to 2.0%. These elements generate hard substances and improve wear resistance, but if they exceed 2.0%, the bearing tends to scratch the mating material, so the addition must be limited to 2.0% or less. Also, if the amount added is less than 0.01%, there is no effect.
本発明の軸受け、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。The bearing of the present invention is manufactured by processes such as casting, cold rolling, intermediate annealing, and pressure welding to a backing metal. If the rolled product is significantly work hardened, final annealing may be performed if necessary.
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かを取
り除くために２２０’Ｃ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３００〜５
２０℃が好ましい。焼鈍温度が５２０℃を超えると、Ａ
ｌ−Ｃｕ−Ｘ系の多元共晶温度に近付き、Ｓｎ以外にＡ
ｌ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 temperature of intermediate annealing and final annealing is preferably within the range of 220 to 520°C. If the temperature is below 220°C, aging precipitation of Al-Cu and Al-Mg will occur, but Al-
Precipitation of Cu, Al-Mg is not essential for achieving the characteristics of the present invention, and a temperature of 220'C or higher is preferred to eliminate work hardening during the rolling process. Furthermore, in order to finely precipitate the supersaturated solid solution part of Zr, 300 to 5
20°C is preferred. When the annealing temperature exceeds 520°C, A
It approaches the multi-component eutectic temperature of the l-Cu-X system, and in addition to Sn, A
The annealing temperature is preferably 520° C. or lower because the liquid phase of L appears, the strength of the alloy decreases, and the Sn phase becomes coarser.
本発明の軸受の相手軸は焼入鋼材、調質鋼材（鋳鉄は含
まない、以下同じ）軸あるい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。ｍ材の炭素量は一
般に０．４〜０，６５％の中炭素含有量である０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Ｊ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 made of hardened steel, tempered steel (excluding cast iron, the same applies hereinafter), or non-tempered steel. Carbon steel is generally used as the steel material. The bearing of the present invention can also be used when a non-heat treated carbon steel to which a small amount of a hardening element such as V is added is used as the shaft. The carbon content of the m material is generally a medium carbon content of 0.4 to 0.65%. Cast iron is not used as a mating material for the bearing of the present invention. Also, ``Non-tempered J'' means that it is as rolled or forged,
In particular, hardness refers to 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。(Function) The characteristics of the following four types of alloys were evaluated by the test method described in the examples.
本発明 Ａ ｆｉ −１３％Ｓｎ−２％Ｐｂ−１％
Ｃｕ−０，２％Ｚｒ比較例■ Ａ ｎ −１３％Ｓｎ
−１％Ｃｕ−０，２％Ｚｒ比較例■ Ａ Ａ
−１３％Ｓｎ−２％Ｐｂ−１％Ｃｕ−０，２％Ｃｒ比較
例■ Ａ Ｉ２−１３％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りた。This invention A fi -13%Sn-2%Pb-1%
Cu-0,2%Zr comparative example ■ A n -13%Sn
-1%Cu-0,2%Zr comparative example■ A A
-13%Sn-2%Pb-1%Cu-0,2%Cr Comparative example■ A I2-13%Sn-2%Pb-1%Cu-
Each of the 0.2% Zr-3% Si materials was produced by casting a strip and rolling it six times to form a plate with a final thickness of 1 mm. Intermediate annealing was performed at 220 to 520°C during rolling. The obtained plate is made of Ni-plated backing steel plate (SPCC).
A bimetal was created by pressure welding, and this was processed into the shape of a test piece. The test results were as follows.
本発明
比較例■
比較例■
焼付面圧（ｋｇ／ｅｍｚ）
ＦＣＤ７０ ５５０Ｃ−１（５５０Ｃ−Ｒ疲労面圧
高温
」ｈ凶１５」肚
７００ １９．８
６８０ ２０．４
６８０ １８．５
この結果の比較より各成分の作用が分かる。Comparative example of the present invention ■ Comparative example ■ Seizure surface pressure (kg/emz) FCD70 550C-1 (550C-R fatigue surface pressure
High temperature "h15" 700 19.8 680 20.4 680 18.5 Comparison of these results reveals the effects of each component.
まず、相手軸が球状黒鉛鋳鉄（ＦＣ：Ｄ）であると、Ｓ
ｉ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, if the mating shaft is made of spheroidal graphite cast iron (FC:D), S
By containing i, excellent properties can be obtained (Comparative Example ■).
次に、焼入鋼（Ｓ５０Ｃ−Ｉ１硬さＨｖ＝６００）や圧
延のままの鋼（５５０Ｃ−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, hardened steel (S50C-I1 hardness Hv = 600) and as-rolled steel (550C-R), hardness Hv = 230)
is the other axis, Si actually deteriorates the characteristics (Comparative Example ■ or Comparison of 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ａｃｒ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。Comparative example (2) contains Cr, which is not an additive component of the present invention, but since there is a general explanation in JP-A-53-87917 that Cr can be substituted for Zr (not based on the examples), Cr In order to compare the effects of acr and Zr on the basis of data, Comparative Example
The effect of is quantitatively superior to that of Cr (Comparative example ■
and the present invention), and the high temperature hardness of Zr is also higher than that of Cr.
better than.
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）をである０本発明の材
料は３６０℃から再結晶軟化が始まり、比較例材は３０
０℃から軟化が始まっていること分かる。Cr is less effective than Zr in delaying recrystallization. 1st
The figure shows the recrystallization softening after 60% cold rolling of the "invention" material and the comparative example ■ material, the horizontal axis is the heating temperature (℃), and the vertical axis is the hardness measured after cooling to room temperature (Hv). The material of the present invention starts recrystallization softening at 360°C, and the comparative example material starts to soften at 360°C.
It can be seen that softening begins at 0°C.
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ろ。PB improves the seizure resistance (comparison between Comparative Example 3 and the present invention). Although the high temperature hardness slightly decreases due to the addition of PB, the properties are excellent. This is thought to be due to the improved lipophilicity of Sn with 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 explained 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。(Example) An alloy having the composition shown in Table 1 was melted, a bimetallic bearing was prepared by the method described above, and a test was conducted 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／ｃ＋ｏ”を３０分毎に増
加（焼付いた時の面圧測定）
（４）潤滑油−５ＡＥ１０Ｗ３０
（５１ｋ油温度−１４０℃
（６）相手軸−３５０Ｃ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−３０００ｒｐ＋ｍ
（３）荷重 −１０７回で疲労する面圧を測定潤滑油−
５ＡＥ１０Ｗ３０
給油温度−
１４０℃
（以下、
余白）
（発明の効果）
以上説明したように、本発明請求項１記載の軸受台金は
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（Ｓ
ｉ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) Journal type seizure tester (2) Rotation speed - 1500 rpm (3) Load increase method - Increase 50Kg/c+o'' every 30 minutes (measurement of surface pressure at the time of seizure) (4) Lubricating oil - 5AE10W30 (51k oil temperature -140℃ (6) Mating shaft - 350C as forged (hardness Hv = 230
) Fatigue test (1) Reciprocating load testing machine (2) Rotation speed - 3000 rpm + m (3) Load - Measure the surface pressure that causes fatigue at 107 times Lubricating oil -
5AE10W30 Oil supply temperature - 140°C (hereinafter referred to as margin) (Effects of the invention) As explained above, the bearing base metal according to claim 1 of the present invention has a lower temperature than that of JP-A-53-87918 (Cr addition). It has excellent fatigue resistance and is
It has superior seizure resistance and fatigue resistance compared to (containing i).
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。Furthermore, if necessary, a hard substance forming element can be added as described in claim 2 to improve the wear resistance.
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。FIG. 1 is a graph showing the influence of addition of Zr (invention material) and Cr (comparative material 2) on recrystallization softening.
Claims (2)
、 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。1. 2-25% by weight of Sn, 0.02-1.0% by weight of Zr, 0.1-2.5% by weight of at least one of Cu and Mg.
, 0.1 to 8.0% by weight of one or more of Pb, Bi and In
An aluminum-based bearing alloy comprising: , and the remainder consisting of inevitable impurities and Al.
、 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。2. 2-25% by weight of Sn, 0.02-1.0% by weight of Zr, 0.1-2.5% by weight of at least one of Cu and Mg.
, 0.1 to 8.0% by weight of one or more of Pb, Bi and In
, Mn, V, Sb, Nb, Mo, Co, Ti, TiB, Fe and Sr 0.01 to 2
．． 0% by weight, and the remainder consists of inevitable impurities and Al.
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 true JPH049443A (en) | 1992-01-14 |
| JP3298635B2 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) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1998017833A3 (en) * | 1996-10-18 | 1998-08-06 | Miba Gleitlager Ag | Sliding bearing material made from an aluminium alloy which is silicon-free apart from impurities necessitated by steel production |
| 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 |
| US6673168B1 (en) * | 1998-07-23 | 2004-01-06 | Ks Gleitlager Gmbh | Material on an aluminum basis for anti-friction bearings |
| EP1475449A1 (en) * | 2003-03-14 | 2004-11-10 | Miba Gleitlager GmbH | Wrought aluminium alloy |
-
1990
- 1990-04-27 JP JP11021190A patent/JP3298635B2/en not_active Expired - Fee Related
Cited By (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 |
| WO1998017833A3 (en) * | 1996-10-18 | 1998-08-06 | Miba Gleitlager Ag | Sliding bearing material made from an aluminium alloy which is silicon-free apart from impurities necessitated by steel production |
| US6673168B1 (en) * | 1998-07-23 | 2004-01-06 | Ks Gleitlager Gmbh | Material on an aluminum basis for anti-friction bearings |
| EP1475449A1 (en) * | 2003-03-14 | 2004-11-10 | Miba Gleitlager GmbH | Wrought aluminium alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3298635B2 (en) | 2002-07-02 |
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