JPH07103455B2 - Method for manufacturing aluminum-based bearing alloy - Google Patents
Method for manufacturing aluminum-based bearing alloyInfo
- Publication number
- JPH07103455B2 JPH07103455B2 JP3084749A JP8474991A JPH07103455B2 JP H07103455 B2 JPH07103455 B2 JP H07103455B2 JP 3084749 A JP3084749 A JP 3084749A JP 8474991 A JP8474991 A JP 8474991A JP H07103455 B2 JPH07103455 B2 JP H07103455B2
- Authority
- JP
- Japan
- Prior art keywords
- aluminum
- bearing alloy
- based bearing
- alloy
- amount
- 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.)
- Expired - Lifetime
Links
- 229910052782 aluminium Inorganic materials 0.000 title claims description 17
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims description 17
- 239000001996 bearing alloy Substances 0.000 title claims description 15
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 238000000034 method Methods 0.000 title description 7
- 238000010438 heat treatment Methods 0.000 claims description 17
- 229910052718 tin Inorganic materials 0.000 claims description 14
- 239000000463 material Substances 0.000 claims description 12
- 238000005097 cold rolling Methods 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 229910052745 lead Inorganic materials 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 4
- 239000011159 matrix material Substances 0.000 claims description 4
- 229910052796 boron Inorganic materials 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 238000005728 strengthening Methods 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 229910052733 gallium Inorganic materials 0.000 claims 1
- 239000010949 copper Substances 0.000 description 16
- 239000000243 solution Substances 0.000 description 15
- 238000011282 treatment Methods 0.000 description 15
- 229910000838 Al alloy Inorganic materials 0.000 description 12
- 230000000694 effects Effects 0.000 description 11
- 239000007791 liquid phase Substances 0.000 description 8
- 238000005096 rolling process Methods 0.000 description 6
- 238000005266 casting Methods 0.000 description 5
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 239000000203 mixture Substances 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- LQBJWKCYZGMFEV-UHFFFAOYSA-N lead tin Chemical compound [Sn].[Pb] LQBJWKCYZGMFEV-UHFFFAOYSA-N 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 241001424392 Lucia limbaria Species 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 102200082816 rs34868397 Human genes 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 230000003245 working effect Effects 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Landscapes
- Sliding-Contact Bearings (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明はアルミニウム基軸受合金
の製造方法に係り、詳しくは、最終の加熱処理を僅か９
０秒以内程度付加するのみで、加工性が良く、耐焼付性
が良好で破壊強度に優れた錫−鉛含有アルミニウム基軸
受合金が製造できる方法に係る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an aluminum-based bearing alloy, and more specifically, the final heat treatment requires only 9
The present invention relates to a method capable of producing a tin-lead-containing aluminum-based bearing alloy having good workability, good seizure resistance, and excellent fracture strength, by only adding within about 0 seconds.
【０００２】[0002]
【従来の技術】従来のアルミニウム基合金から成る自動
車用の軸受材料の製造方法の一つとして、例えば特開昭
６１−２７２３５８号公報に開示される方法がある。2. Description of the Related Art As one of conventional methods for producing a bearing material for an automobile, which is made of an aluminum-based alloy, there is a method disclosed in, for example, Japanese Patent Application Laid-Open No. 61-272358.
【０００３】この方法は、８〜３５％Ｓｎ、１〜３％Ｃ
ｕ、２〜１０％Ｓｉを、含んで残部がＡｌから成るアル
ミニウム（以下、単にアルミという。）基合金の軸受材
料の製造方法である。This method uses 8-35% Sn, 1-3% C
This is a method for producing a bearing material of an aluminum (hereinafter simply referred to as aluminum) base alloy containing u and 2 to 10% Si and the balance being Al.
【０００４】しかし、この軸受材料は、２〜１０％Ｓｉ
成分を必須として含み、その上Ｃｕ含有量が１〜３％と
高いため、製造工程途中の圧延過程で加工硬化が著し
く、圧延材端部に大きな割れが発生し歩留まりが悪化す
る。However, this bearing material is 2-10% Si
Ingredients are indispensable, and since the Cu content is as high as 1 to 3%, work hardening is remarkable in the rolling process during the manufacturing process, large cracks are generated at the ends of the rolled material, and the yield is deteriorated.
【０００５】とくに、最悪の場合には、圧延後の材料か
ら軸受材料を取り出すことが出来なかったり、圧延の中
間で、加工歪を除去するために熱処理を施さなければな
らないという問題がある。Particularly, in the worst case, there is a problem that the bearing material cannot be taken out from the material after rolling or that heat treatment must be performed in the middle of rolling in order to remove working strain.
【０００６】また、Ｓｎ添加量を少なくした場合（９〜
１３％Ｓｎ）は耐焼付性が悪化し、逆にＳｎ添加量を多
くした場合は（１５〜２５％Ｓｎ）は破壊強度が悪くな
るという問題もあった。When the amount of addition of Sn is reduced (9-
13% Sn) deteriorates the seizure resistance, and conversely, when the amount of Sn added is increased (15 to 25% Sn), the breaking strength also deteriorates.
【０００７】[0007]
【発明が解決しようとする課題】本発明はこの様な従来
の問題点に着目してなされたもので、重量％で少なくと
も８〜１８％Ｓｎならびに６％未満（０を含まず）Ｐｂ
を含むほか、Ｓｉはほとんど含むことないとともに、Ｃ
ｕは１％未満（０を含まず）しか含むことなく、しか
も、例えば、９０秒以内のように、きわめて短時間の加
熱で十分な溶体化処理効果が得られ、なかでも、圧延段
階での加工硬化が軽減でき、Ｓｎ添加量が少なくても耐
焼付性を悪化させることなく破壊強度の良好なアルミ基
軸受合金が製造できる。SUMMARY OF THE INVENTION The present invention has been made by paying attention to such a conventional problem, and is at least 8 to 18% Sn by weight% and less than 6% (not including 0) Pb.
In addition to containing, Si hardly contains, and C
u contains less than 1% (not including 0), and a sufficient solution treatment effect can be obtained by heating for an extremely short time, for example, within 90 seconds, and in particular, in the rolling stage. It is possible to reduce the work hardening, and it is possible to manufacture an aluminum-based bearing alloy having good fracture strength without deteriorating the seizure resistance even if the amount of Sn added is small.
【０００８】[0008]
【課題を解決するための手段】すなわち、本発明方法は
重量％で少なくとも８〜１８％Ｓｎ、６％〜０．５％Ｐ
ｂ、１％〜０．１％Ｃｕを含み残余が実質的にアルミニ
ウムから成るアルミニウム合金を冷間圧延したのちに、
この冷延材を４００〜５５０℃で９０秒以内最終の加熱
処理し、その後、１８０℃／分〜５０℃／分以上の速度
で冷却することを特徴とする。That is, the method of the present invention comprises at least 8-18% Sn and 6% -0.5% P by weight.
b, after cold rolling an aluminum alloy containing 1% to 0.1% Cu and the balance essentially consisting of aluminum,
This cold rolled material is subjected to a final heat treatment at 400 to 550 ° C for 90 seconds or less, and then cooled at a rate of 180 ° C / min to 50 ° C / min or more.
【０００９】以下、本発明の手段たる構成ならびにその
作用について説明すると、次の通りである。The structure and operation of the means of the present invention will be described below.
【００１０】一般に、アルミ合金で強度向上の手段とし
て溶体化処理は有効であることが知られている。It is generally known that solution treatment is effective as a means for improving strength in aluminum alloys.
【００１１】しかし、溶体化処理には、高温の加熱時間
は少なくとも４時間以上は必要であると云われ、このた
め、強度向上の手段として用いられていない。However, it is said that the solution heat treatment requires a high temperature heating time of at least 4 hours or more, and therefore is not used as a means for improving strength.
【００１２】これに対し、本発明においては、アルミ合
金に対しＳｎとともにＰｂを多く配合する。これらＳｎ
ならびにＰｂは低融点金属であるところから、比較的低
い温度で液相が多く発生し、極めて短時間、ちなみに、
後記の実施例で示すように９０秒以内で十分な溶体化処
理効果が得られる。On the other hand, in the present invention, a large amount of Pb is added to the aluminum alloy together with Sn. These Sn
Also, since Pb is a low melting point metal, a large amount of liquid phase is generated at a relatively low temperature, and for an extremely short time, by the way,
As shown in the examples described below, a sufficient solution treatment effect can be obtained within 90 seconds.
【００１３】また、本発明においては、処理すべきアル
ミ合金中にＳｎとＰｂが共存する。このため、液相発生
温度範囲が広くなり、固溶体処理効果を得るために、Ｃ
ｕの含有量を多く、例えば、１％以上にする必要はな
く、Ｃｕ１％未満で十分にその効果が達成できる。Further, in the present invention, Sn and Pb coexist in the aluminum alloy to be treated. For this reason, the temperature range in which the liquid phase is generated becomes wider, and in order to obtain the solid solution treatment effect, C
It is not necessary to increase the content of u, for example, 1% or more, and if it is less than 1% Cu, the effect can be sufficiently achieved.
【００１４】従って、Ｃｕが多いと効果が過大となった
り、制御が困難となるが、このような問題がない。Therefore, when the amount of Cu is large, the effect becomes excessive and the control becomes difficult, but there is no such problem.
【００１５】また、Ｓｉ成分がなくとも、つまり必須成
分としなくとも、アルミ合金の溶体化処理は達成でき
る。Further, the solution treatment of the aluminum alloy can be achieved without the Si component, that is, without using the essential component.
【００１６】そこで、処理すべきアルミ合金の各成分の
限定理由から説明すると、次の通りである。Therefore, the reason for limiting each component of the aluminum alloy to be treated is as follows.
【００１７】このアルミ軸受合金は重量％で少なくとも
８〜１８％Ｓｎ、６％未満（０を含まず）Ｐｂ、１％未
満（０を含まず）Ｃｕを含む。The aluminum bearing alloy contains, by weight, at least 8 to 18% Sn, less than 6% Pb (not containing 0), Cu less than 1% (not containing 0).
【００１８】まず、錫（Ｓｎ）は８〜１８％添加され、
後記のように添加される鉛（Ｐｂ）と相まって、液相発
生温度を低下させるとともに比較的多くの液相を発生さ
せる。このため、後記のように、ちなみに９０秒以内の
ような短時間で十分に溶体化処理が達成でき、機械的強
度を向上させることができる。First, 8 to 18% of tin (Sn) is added,
Together with lead (Pb) added as described later, the liquid phase generation temperature is lowered and a relatively large amount of liquid phase is generated. Therefore, as described later, the solution treatment can be sufficiently achieved in a short time such as 90 seconds or less, and the mechanical strength can be improved.
【００１９】すなわち、一般に、軸受合金では、錫（Ｓ
ｎ）は主に耐焼付性のために添加される。この意味で
は、１８％を超えると、軟質相が多くなり、軸受合金強
度が低下し破壊強度が損なわれ、好ましくない。That is, in general, in a bearing alloy, tin (S
n) is added mainly for seizure resistance. In this sense, if it exceeds 18%, the soft phase increases, the bearing alloy strength decreases, and the fracture strength deteriorates, which is not preferable.
【００２０】しかし、ある程度発生液相量を確保して短
時間で溶体化処理を達成するのには、錫（Ｓｎ）は８〜
１８％必要であり、８％未満では、発生液相量が少なく
なり、高温短時間での固溶量も少なく、溶体化処理効果
も不十分になり、その上、破壊強度や耐焼付性が確保で
きない。However, in order to secure the generated liquid phase amount to some extent and achieve the solution treatment in a short time, tin (Sn) is 8 to 10.
18% is required, and if it is less than 8%, the amount of liquid phase generated is small, the amount of solid solution in a short time at high temperature is small, the solution treatment effect is insufficient, and in addition, the breaking strength and seizure resistance are low. Cannot be secured.
【００２１】次に、鉛（Ｐｂ）は、アルミ軸受合金にお
いては耐焼付性向上成分として添加されるが、本発明で
は、先にのべた通り、錫（Ｓｎ）との共存によって液相
発生温度を降下させ、発生液相量を多くして、溶体化処
理の効果を十分に達成させる。Next, lead (Pb) is added as a seizure resistance improving component in the aluminum bearing alloy, but in the present invention, as described above, the coexistence with tin (Sn) causes the liquid phase generation temperature. And the amount of the generated liquid phase is increased to sufficiently achieve the effect of the solution treatment.
【００２２】この場合、少ない銅含有量（１％未満）で
溶体処理効果を確保できる。In this case, the solution treatment effect can be secured with a small copper content (less than 1%).
【００２３】添加量の上限としてはアルミ合金中で著し
い偏析を起こさない範囲として６％未満であり、下限と
しては後の実施例に示すように０．５％は必要である。The upper limit of the amount added is less than 6% in the range where significant segregation does not occur in the aluminum alloy, and the lower limit is required to be 0.5% as shown in the following examples.
【００２４】次に、銅（Ｃｕ）はアルミ合金を強化させ
る成分であるが、本発明においてはＳｎとＰｂの共存の
もとで高温加熱後急冷する事でアルミ基地中には小量の
Ｃｕでも十分にＣｕを固溶させることができ、強度と伸
びを大幅に改善し、結果として軸受合金としての破壊強
度を向上させる。Next, copper (Cu) is a component that strengthens the aluminum alloy. In the present invention, a small amount of Cu is contained in the aluminum matrix by heating at high temperature and then rapidly cooling under the coexistence of Sn and Pb. However, Cu can be sufficiently solid-dissolved, and the strength and elongation are significantly improved, and as a result, the fracture strength as a bearing alloy is improved.
【００２５】添加量として、Ｃｕは１％以上では圧延段
階での加工効果が大きくなり、圧延材端部に大きな割れ
が発生し歩留まりが悪化し、それを軽減するために１回
以上の中間熱処理が必要となる。また、Ｃｕが１％以上
だと溶体処理効果が過大となってかえって軸受合金とし
ての特性（異物埋収性等）を阻害したり、効果に対する
熱処理の制御が困難となる。When Cu is added in an amount of 1% or more, the working effect in the rolling stage becomes large, and large cracks are generated at the end of the rolled material to deteriorate the yield. To reduce it, one or more intermediate heat treatments are performed. Is required. Further, if Cu is 1% or more, the solution treatment effect becomes too large and the characteristics as a bearing alloy (for example, foreign matter embeddability) are impaired, and it becomes difficult to control the heat treatment for the effect.
【００２６】添加量の下限としては常温で固溶するＣｕ
量以上が必要なので、０．１％以上が望ましい。The lower limit of the amount of addition is Cu which forms a solid solution at room temperature.
Since more than the amount is required, 0.1% or more is desirable.
【００２７】その他の基地強化成分（Ｆｅ、Ｍｎ、Ｃ
ｒ、Ｎｉ） その他の基地成分としては通常の展伸用アルミ合金に含
まれる成分のうち銅以外に固溶体効果のあるＭｇ、Ｚｎ
を除く基地強化成分Ｆｅ、Ｍｎ、Ｃｒ、Ｎｉのうちから
１種または２種以上を合計で３％を超えない範囲で添加
しても本発明の範囲を逸脱するものではない。Other matrix strengthening components (Fe, Mn, C
r, Ni) Other base components include Mg, Zn which has a solid solution effect in addition to copper among the components contained in a normal wrought aluminum alloy.
It does not deviate from the scope of the present invention even if one or two or more of the matrix strengthening components except Fe, Mn, Cr and Ni are added within a range not exceeding 3% in total.
【００２８】微細化成分（Ｔｉ、Ｚｒ、Ｖ、Ｂ、Ｇａ、
Ｓｒ） 合計組成の微細化成分としてのＴｉ、Ｚｒ、Ｖ、Ｂ、Ｇ
ａ、Ｓｒは合計で０．１％を超えない範囲で添加を妨げ
るものではない。Finer components (Ti, Zr, V, B, Ga,
Sr) Ti, Zr, V, B, G as a refined component of the total composition
Addition of a and Sr does not hinder addition within a range not exceeding 0.1% in total.
【００２９】次に、以上の組成のアルミ合金を鋳造で溶
製し、この鋳造時の歪などを熱処理で除去してから、冷
間圧延し、これに４００℃〜５５０℃×９０秒以内の最
終加熱処理を付加し、その後１８０℃／分〜５０℃／分
の冷却速度で冷却する。Next, the aluminum alloy having the above composition is melted by casting, strains and the like at the time of casting are removed by heat treatment, and then cold rolling is carried out, which is 400 ° C to 550 ° C for 90 seconds or less. A final heat treatment is added, followed by cooling at a cooling rate of 180 ° C / min to 50 ° C / min.
【００３０】この場合、最終加熱処理が４００℃以下で
あると、後記の実施例にも示す通り、溶体化処理が不十
分で軸受としての破壊強度が得られない。In this case, if the final heat treatment is 400 ° C. or lower, the solution treatment is insufficient and the fracture strength as a bearing cannot be obtained, as will be shown in Examples described later.
【００３１】[0031]
【実施例】以下、実施例について説明する。EXAMPLES Examples will be described below.
【００３２】表１に示す所定組成のアルミ合金（ただ
し、Ｎｏ．１〜５が本発明に係り、Ｎｏ．１１〜１４は
比較例）を鋳造により溶製し、厚さ２０ｍｍの板とし
た。この鋳造時の歪を除去するために熱処理（３００℃
ｘ４時間）し、鋳肌を除去した。Aluminum alloys having a predetermined composition shown in Table 1 (however, Nos. 1 to 5 relate to the present invention, Nos. 11 to 14 are comparative examples) were melted by casting to obtain a plate having a thickness of 20 mm. Heat treatment (300 ° C to remove the strain during casting)
x4 hours), and the casting surface was removed.
【００３３】その後、１ｍｍの板厚まで冷間圧延した。After that, cold rolling was performed to a plate thickness of 1 mm.
【００３４】この冷間圧延途中段階で比較例１４は、Ｃ
ｕ２％も含まれることもあって、圧延割れが激しく評価
試料は得られなかった。In the intermediate stage of the cold rolling, Comparative Example 14 was C
Since u2% was also included, rolling cracks were severe and an evaluation sample could not be obtained.
【００３５】他のアルミ合金薄板について表１に示す最
終熱処理条件で最終の熱処理を溶体化処理として実施し
た。For other aluminum alloy thin plates, final heat treatment was carried out as solution treatment under the final heat treatment conditions shown in Table 1.
【００３６】[0036]
【表１】 [Table 1]
【００３７】その後、各試料について、ＪＩＳ５号試験
片に加工して引張試験機にて破壊強度を測定した。その
結果を表２に示す。本発明例のＮｏ．１〜５は破壊強度
１３．７〜１７．４Ｋｇｆ／ｍｍ２であり、比較例１３
はＳｎ５％、Ｐｂ０．５％であったが、Ｃｕ０．７％を
含むため、破壊強度は１７Ｋｇｆ／ｍｍ２を示してい
る。Thereafter, each sample was processed into a JIS No. 5 test piece and the breaking strength was measured by a tensile tester. The results are shown in Table 2. No. 1 of the present invention example. 1 to 5 have a breaking strength of 13.7 to 17.4 Kgf / mm 2 , and Comparative Example 13
Was Sn 5% and Pb 0.5%, but since Cu 0.7% was included, the fracture strength was 17 Kgf / mm 2 .
【００３８】次に、鈴木式摩擦摩耗試験機を用いて耐焼
付試験を行なった。焼付試験条件は次の通りである。Next, a seizure resistance test was conducted using a Suzuki type friction and wear tester. The seizure test conditions are as follows.
【００３９】摩擦速度 ４ｍ／秒 相手材 材質 Ｓ４５Ｃ 硬さ ＨＲＣ ５５ 面粗さ ０．８〜１．０Ｓ 使用オイル ＳＡＥ２０Ｗ−４０ 油温 １５０±５℃ テスト数 各２ 焼付荷重 ２０Ｋｇｆ／ｃｍ２から１０Ｋｇｆ／ｃ
ｍ２毎に面圧を上げていき、焼付をおこした面圧を焼付
荷重とする。 尚、焼付の判定は材料温度が１８０℃を超えた場合また
は摩擦力が２５．５Ｋｇｆを超えた場合とする。Friction speed 4 m / sec Counterpart material S45C Hardness HRC 55 Surface roughness 0.8-1.0S Oil used SAE20W-40 Oil temperature 150 ± 5 ° C Number of tests 2 Each seizure load 20 Kgf / cm 2 to 10 Kgf / c
The surface pressure is increased every m 2 and the surface pressure after the seizure is used as the seizure load. The seizure is judged when the material temperature exceeds 180 ° C. or when the frictional force exceeds 25.5 Kgf.
【００４０】その結果を表２に示す。本発明例のすべて
は焼付荷重１２０〜２３０Ｋｇｆで優れた耐焼付性を示
している。なお、比較例１３はＰｂが少なくＳｎが５％
と少ないため、焼付荷重は７０Ｋｇｆときわめて低く、
耐焼付性が劣化していることがわかる。The results are shown in Table 2. All of the examples of the present invention exhibit excellent seizure resistance under a seizure load of 120 to 230 Kgf. In Comparative Example 13, Pb is small and Sn is 5%.
Therefore, the seizure load is as low as 70 Kgf,
It can be seen that the seizure resistance has deteriorated.
【００４１】[0041]
【表２】 [Table 2]
【００４２】[0042]
【発明の効果】以上説明した通り、本発明方法は重量％
で少なくとも８〜１８％Ｓｎ、６％〜０．５％Ｐｂ、１
％〜０．１％Ｃｕを含むアルミ軸受合金材を冷間圧延な
どを介して製造する際に、４００〜５５０℃の最終加熱
を９０秒以内に行なって、１８０℃／分〜５０℃／分の
速度で冷却する。このため、本発明方法によると、Ｃｕ
が少なく加工性が良く、耐焼付性が良好であるほか、溶
体化処理が十分に行なわれるところから、破壊強度に優
れる錫−鉛含有アルミ基軸受合金が製造できる。As described above, the method of the present invention is used in% by weight.
At least 8-18% Sn, 6% -0.5% Pb, 1
% -0.1% Cu aluminum bearing alloy material is manufactured through cold rolling or the like, final heating at 400 to 550 ° C. is performed within 90 seconds to obtain 180 ° C./min to 50 ° C./min. Cool at the speed of. Therefore, according to the method of the present invention, Cu
The tin-lead-containing aluminum-based bearing alloy having excellent fracture strength can be produced because the solution treatment is sufficiently performed and the solution treatment is sufficiently performed.
Claims (3)
％〜０．５％Ｐｂ、１％〜０．１％Ｃｕを含み残余が実
質的にアルミニウムから成るアルミニウム合金を冷間圧
延したのちに、この冷延材を４００〜５５０℃で９０秒
以内最終の加熱処理し、その後、１８０℃／分〜５０℃
／分以上の速度で冷却することを特徴とするアルミニウ
ム基軸受合金の製造方法。1. At least 8-18% Sn, 6 by weight.
% -0.5% Pb, 1% -0.1% Cu, and the balance consisting essentially of aluminum. After cold rolling, this cold rolled material is finished at 400-550 ° C. within 90 seconds. Heat treatment, then 180 ℃ / min ~ 50 ℃
A method for producing an aluminum-based bearing alloy, which comprises cooling at a speed of not less than 1 minute.
ｒ、Ｎｉの内から１種または２種以上を合計で３％を超
えない範囲で含有することを特徴とする請求項１記載の
アルミニウム基軸受合金の製造方法。2. Fe, Mn, C as a matrix strengthening component
The method for producing an aluminum-based bearing alloy according to claim 1, wherein one or two or more of r and Ni are contained in a range not exceeding 3% in total.
Ｇａ、Ｓｒの内から１種または２種以上を合計で０．１
％を超えない範囲で含有することを特徴とする請求項１
又は２記載のアルミニウム基軸受合金の製造方法。3. Ti, Zr, V, B as a refinement component,
One or two or more of Ga and Sr in total is 0.1
% Is contained in the range not exceeding 1.
Alternatively, the method for producing the aluminum-based bearing alloy according to 2 above.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3084749A JPH07103455B2 (en) | 1991-03-25 | 1991-03-25 | Method for manufacturing aluminum-based bearing alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3084749A JPH07103455B2 (en) | 1991-03-25 | 1991-03-25 | Method for manufacturing aluminum-based bearing alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04297558A JPH04297558A (en) | 1992-10-21 |
| JPH07103455B2 true JPH07103455B2 (en) | 1995-11-08 |
Family
ID=13839346
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3084749A Expired - Lifetime JPH07103455B2 (en) | 1991-03-25 | 1991-03-25 | Method for manufacturing aluminum-based bearing alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07103455B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE4434801A1 (en) * | 1994-09-29 | 1996-04-04 | Kolbenschmidt Ag | Plain bearing material |
| CN104789822B (en) * | 2015-03-26 | 2017-01-11 | 湖北宏鑫复合材料有限公司 | Aluminum base alloy of sliding bearing and preparation method for aluminum base alloy |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5144883A (en) * | 1974-10-16 | 1976-04-16 | Hitachi Ltd | Handotaisochi oyobi sonoseizohoho |
| JPS5814866A (en) * | 1981-07-20 | 1983-01-27 | Konishiroku Photo Ind Co Ltd | Magnetic brush developing device |
| JPS59193254A (en) * | 1983-04-14 | 1984-11-01 | Taiho Kogyo Co Ltd | Preparation of aluminum alloy bearing |
| GB8513330D0 (en) * | 1985-05-28 | 1985-07-03 | Ae Plc | Bearing materials |
-
1991
- 1991-03-25 JP JP3084749A patent/JPH07103455B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH04297558A (en) | 1992-10-21 |
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