JPS6035987B2 - Aluminum↓-Lead-based bearing manufacturing method - Google Patents

Description

【発明の詳細な説明】 本発明は、アルミニウム−鉛系軸受の製造方法に関する
ものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method of manufacturing an aluminum-lead bearing.

一般に軸受は使用目的上、耐摩耗性、耐煉付性、耐荷重
性、耐疲労性に優れていることが必要であり、このため
軸受本体を形成する鋼板などのバックメタル表面に例え
ばアルミニウム−鉛系の皮膜を形成したりして長期間の
使用にも十分耐えうるように従来から多くの工夫がなさ
れてきた。In general, bearings must have excellent wear resistance, brick resistance, load resistance, and fatigue resistance for the purpose of use. Many efforts have been made in the past to make it durable enough for long-term use, such as by forming a lead-based film.

このアルミニウム−鉛系（以下、ＡＩ−Ｐｂ系と記す。
）皮膜を形成する方法としては、グールド法、大同法な
どの煉給による鋳造圧延による０．Ｍ．法等の種々の方
法があるが、ＡＩ粉末とＰｂ粉末を混合して、バックメ
タル上へ供給する大同法では、ＡＩ粉末とＰｂ粉末の比
重差が大きく均一な分布が得にくい。また、暁結法では
、バックメタルとの密着力及び層内の強度を得るために
は、相当の圧延率を要するため、Ｐｂ粒子が長く延び、
耐疲労性に問題が生ずる。グールド法はこの点ＡＩ一Ｐ
ｂ合金粉末を使用のため比較的細かいＰｂの分布が得ら
れるが、ＡＩ中へ多くのＰｂを細かく分散した粉末を得
ることは困難で、１０％以上のＰｂ量にすることはむず
かしい。このため性能面でや）不充分な面がある。一方
、鋳造法では、やはりＰｂを均一に分散させるためには
溶湯を急冷するなどの操作が必要であるが、相当困難で
ある。本発明の目的は上記欠点を解消し、従来法に比べ
て耐摩耗性、耐糠付性、耐疲労耐、耐荷重性に優れた山
一Ｐｂ系皮膜を有する軸受の製造方法を提供するにある
。更に本発明の目的は、Ｐｂが微粒子状に分散されてい
るＡＩ−Ｐｂ合金粉末を溶射することにより皮膜中にＰ
ｂが微細均一に分散している軸受の製造方法を提供する
にある。This aluminum-lead system (hereinafter referred to as AI-Pb system).
) The method for forming the film is 0.0000. M. There are various methods, such as the Daido method, which mixes AI powder and Pb powder and supplies them onto the back metal, but the difference in specific gravity between the AI powder and Pb powder is large and it is difficult to obtain a uniform distribution. In addition, in the glazing method, a considerable rolling rate is required in order to obtain adhesion with the back metal and strength within the layer, so the Pb particles are elongated and
Problems arise in fatigue resistance. The Gould method is AI1P in this respect.
Although a relatively fine distribution of Pb can be obtained because b alloy powder is used, it is difficult to obtain a powder in which a large amount of Pb is finely dispersed in AI, and it is difficult to achieve a Pb content of 10% or more. For this reason, there are some insufficiencies in terms of performance. On the other hand, the casting method requires operations such as rapidly cooling the molten metal in order to uniformly disperse Pb, which is quite difficult. An object of the present invention is to eliminate the above-mentioned drawbacks and provide a method for manufacturing a bearing having a Yamaichi Pb-based coating that has superior wear resistance, bran resistance, fatigue resistance, and load resistance compared to conventional methods. be. A further object of the present invention is to spray Pb into a film by thermal spraying an AI-Pb alloy powder in which Pb is dispersed in fine particles.
To provide a method for manufacturing a bearing in which b is finely and uniformly dispersed.

更に本発明の目的は、従来困難であった１０％以上のＰ
ｂを含む軸受層を得ることである。Furthermore, the purpose of the present invention is to reduce P by 10% or more, which has been difficult in the past.
The purpose is to obtain a bearing layer containing b.

即ち、本発明によるＡＩ−Ｐｂ系軸受の製造方法は、Ｐ
ｂ５なし、し４０重量％を含有するＡＩ合金粉末を鋼板
等のバックメタル上に熔射し、その後圧延、椀鈍、成形
することを特徴とするものである。That is, the method for manufacturing an AI-Pb bearing according to the present invention
This method is characterized in that an AI alloy powder containing 40% by weight without B5 is sprayed onto a back metal such as a steel plate, and then rolled, blunted, and formed.

本発明による軸受の製造方法は、例えば次の順序で行わ
れる（なお、第１図に軸受の一部拡大断面図を示す、）
：バックメタルＡ形成→（中間層ｂ形成）→ＡＩ−Ｐｂ
系熔射層Ｃ形成→圧延→焼錨→成形このとき中間層ｂ及
びＮ−Ｐｂ系溶射層ｃは、下記第１表記萩の条件より選
択される。The method for manufacturing a bearing according to the present invention is carried out, for example, in the following order (a partially enlarged sectional view of the bearing is shown in FIG. 1).
: Formation of back metal A → (formation of intermediate layer b) → AI-Pb
Formation of sprayed layer C → rolling → sintered anchor → molding At this time, the intermediate layer b and the N-Pb sprayed layer c are selected according to the conditions of the first notation Hagi below.

第１表 ＡＩ−Ｐｂ系溶射後の圧延・燐鈍したときの厚さをいう 本発明方法において、中間層ｂの厚さは０ないし０．４
８側が好ましい。Table 1: Thickness after rolling and phosphor annealing after AI-Pb thermal spraying In the method of the present invention, the thickness of the intermediate layer b is 0 to 0.4
8 side is preferred.

低荷重軸受の場合あるいは後から形成するとＡＩ−Ｐｂ
系溶射中のＰｂ含有量が少ない場合は中間層ｂを必ずし
も形成しなくてもよいが、耐荷重性、耐疲労性の面から
は中間層を設けることが望ましい。一方、二層軸受ある
いは三層軸受の場合、バックメタル（鋼板）上に形成さ
れるべき層厚さは通常０．５側以上を必要としないため
、ＡＩ−Ｐｂ系熔射層の最低厚さ０．０２肌を考慮すれ
ば中間層ｂの最大厚さは多くとも０．４８職でよい。ま
た、中間層ｂの役割は、基本的にはバックメタルａと溶
射層ｃの接着力強化にあるため中間層ｂを純Ｎとしても
よいが、山層の強度向上のためにＣｕ，Ｓｂ，Ｓｉ等を
添加してもよい。For low load bearings or when formed later, AI-Pb
When the Pb content in the thermal spraying system is low, it is not necessary to form the intermediate layer b, but it is desirable to provide the intermediate layer from the viewpoint of load resistance and fatigue resistance. On the other hand, in the case of two-layer bearings or three-layer bearings, the layer thickness to be formed on the back metal (steel plate) usually does not require a layer thickness of 0.5 or more, so the minimum thickness of the AI-Pb sprayed layer is Considering the thickness of 0.02 mm, the maximum thickness of the intermediate layer b may be at most 0.48 mm. The role of the intermediate layer b is basically to strengthen the adhesive force between the back metal a and the sprayed layer c, so the intermediate layer b may be made of pure N, but in order to improve the strength of the peak layer, Cu, Sb, Si or the like may be added.

一方、ＡＩ−Ｐｂ系溶射層を薄くするときは、溶射層が
摩耗した場合中間層が軸受の一部としての作用を行う場
合もあるので、ＡＩに潤滑成分としてＰｂ，Ｓｎ，Ｃｄ
，Ｚｎ等を加えもよく、また所望によりＡＩ素地強化の
目的でＣｕ，Ｓｂ，Ｓｉ等を添加してもよい。中間層ｂ
の形成は、例えば熔解圧延接着法、粉末暁結法、溶射法
、溶融めつき、亀気めつき、薄膜の圧嬢等従来公知の方
法にて行われる。次に、本発明によるＡＩ−Ｐｂ系合金
粉末は合金中に微粒状に分散したＰｂないし４０重量％
を含むことよりなる。On the other hand, when making the AI-Pb sprayed layer thinner, if the sprayed layer wears out, the intermediate layer may act as part of the bearing, so it is necessary to add Pb, Sn, and Cd as lubricating components to the AI.
, Zn, etc. may be added, and if desired, Cu, Sb, Si, etc. may be added for the purpose of strengthening the AI substrate. middle class b
The formation is carried out by conventionally known methods such as melt rolling adhesion method, powder deposition method, thermal spraying method, melt plating, flash plating, and thin film pressing. Next, the AI-Pb alloy powder according to the present invention contains 40% by weight of Pb dispersed in fine particles in the alloy.
It consists of including.

これはＰｂが５重量％以下ではＡＩに添加しても良好な
潤滑効果を挙げることは期待できず、また４の重量以上
でも逆に耐荷重性、耐疲労性が劣化して好ましくないか
らである。またＮ−Ｐｂ系合金粉末は、潤滑油に対する
耐食性向上のためＰｂに対し２なし、し１０重量％のＳ
ｎを含ませることができる。更に所望により、その他の
金属成分、例えばＣｄ，Ｃ山 Ｚｎ，Ｎｉ，Ｓｉ，Ｃｒ
，Ｓｂ，Ｂｉ等を潤滑性向上及びＮ素地強化のため０な
いし５重量％の範囲で添加してもよい。このＮ−Ｐｂ系
溶射層を形成するには、従来は単にＡＩ，Ｐｂ，及び他
の金属粉末を混合して得た混合粉末を溶射していたに過
ぎなかった。This is because if Pb is less than 5% by weight, it cannot be expected to have a good lubrication effect even if added to AI, and if Pb is more than 4% by weight, the load resistance and fatigue resistance will deteriorate, which is undesirable. be. In addition, the N-Pb alloy powder contains 2% by weight and 10% by weight of S for Pb to improve corrosion resistance against lubricating oil.
n can be included. Furthermore, if desired, other metal components such as Cd, C mountain, Zn, Ni, Si, Cr
, Sb, Bi, etc. may be added in an amount of 0 to 5% by weight to improve lubricity and strengthen the N matrix. In order to form this N-Pb based thermal spray layer, conventionally, a mixed powder obtained by mixing AI, Pb, and other metal powders was simply thermal sprayed.

そのためＰｂ粒子の分布が不均一で粒子サイズも粗く、
良好な溶射層が得られなかった。本発明方法では各金属
成分を予じめ溶融した後、アトマィズ法等により微粒子
状にするので、各々の成分粒子が互いの間に間隙を形成
せず細かく分散するので、均一で微細なＰ雌位子が平均
して存在するＡＩ−Ｐｂ系粉末が得られる。Ｐｂの分布
状態の一例を第２図イ，口，ハに示すが、１つのＮ−Ｐ
ｂ系粉末粒子１にＰｂ粒子２が１つ以上、好ましくはな
るべく多く存在するとよく、第２図でイは好ましくなく
、口望しくはハの状態にすべきである。Therefore, the distribution of Pb particles is uneven and the particle size is coarse.
A good sprayed layer could not be obtained. In the method of the present invention, each metal component is melted in advance and then made into fine particles by an atomization method, etc., so each component particle is finely dispersed without forming any gaps between them, so that uniform and fine P particles are formed. An AI-Pb based powder is obtained in which ions are present on average. An example of the distribution state of Pb is shown in Figure 2 A, C and C.
It is preferable that one or more Pb particles 2 exist in the b-based powder particles 1, preferably as many as possible. In FIG.

また１つのＡＩ−Ｐｂ系粉末粒子中Ｐｂ粒子の占める面
積割合はＮ素地に対し１′沙〆下であるようにすること
が望ましい。この場合、Ｐｂ粒子はＳｎ及びその他の元
素を含んでいてもよい。また合金粉末を純アルミニウム
粉末との混合粉末の溶射も可能で、Ｐｑ粉末とＡＩ粉末
を混合したものよりも微細なＰｂの分散層が得られる。
ＡＩ−Ｐｂ系粉末の溶射装置は通常用いられるプラズマ
溶射機（例えばメテコ 乳 Ｍ，７Ｍ）、ガス（サーモ
スプレ−）溶射機（例えばメテコ 坪，解）等が用いら
れる。Further, it is desirable that the area ratio occupied by the Pb particles in one AI-Pb powder particle is 1' below the N substrate. In this case, the Pb particles may contain Sn and other elements. It is also possible to thermal spray a mixed powder of alloy powder and pure aluminum powder, and a finer Pb dispersed layer can be obtained than a mixture of Pq powder and AI powder.
As a thermal spraying apparatus for the AI-Pb powder, a commonly used plasma spraying machine (for example, Metco Milk M, 7M), gas (thermo spray) spraying machine (for example, Metco Tsubo, Kai), etc. is used.

次に、上記のような方法にて溶射層を形成した鋼板をロ
ール圧延等の方法で、Ｎ−Ｐｂ系溶射層について圧延率
が１０なし、し８０％程度となるように圧延する。Next, the steel plate on which the sprayed layer has been formed by the method described above is rolled by a method such as roll rolling so that the N--Pb sprayed layer has a rolling ratio of about 10 to 80%.

このとき、圧延率が１０％以下であると表面を滑らかに
し、層を繊密にするという当初の目的を達成することが
できず、また８０％以上にするとＰｂ粒子が伸びて耐荷
電性、耐疲労性が劣化してしまうので好ましくない。糠
鈍は３００〜４５０００の温度にて、０．５〜５時間、
水素雰囲気等非酸化性の雰囲気中にて行う。At this time, if the rolling rate is less than 10%, the original purpose of making the surface smooth and the layer dense will not be achieved, and if it is more than 80%, the Pb particles will stretch and the charge resistance will deteriorate. This is not preferable because fatigue resistance deteriorates. For bran bran, at a temperature of 300 to 45,000 ℃, for 0.5 to 5 hours,
It is carried out in a non-oxidizing atmosphere such as a hydrogen atmosphere.

次に本発明方法を実施例及び比較例を用いて更に詳しく
説明する。但し、％は重量％を表わす。実施例 １１．
２脚の冷間圧延鋼板をトリクレン脱脂し、ベルトサンダ
−で粗面化を行った。Next, the method of the present invention will be explained in more detail using Examples and Comparative Examples. However, % represents weight %. Example 11.
Two cold-rolled steel plates were degreased using trichlene and their surfaces were roughened using a belt sander.

次に、この鋼板に下記の条件でＡＩ−Ｐｂ（一Ｓｎ）合
金粉末を厚さ０．５帆になるように熔射した。熔射装置
：４０ｋｗプラズマ礎射装置 溶射用合金粉末： Ａ ＡＩ−３８．２％Ｐｂ−２．１％Ｓｎ合金粉末（ア
トマィズ粉末）１００〜２５０メッシュＢ ＡＩ−３０
．３％Ｐｂ−１．６％Ｓｎ合金粉末（アトマィズ粉末）
１００〜２５０メッシュＣ ＡＩ−１９．６％Ｐｂ−０
．９％Ｓｎ合金粉末（アトマィズ粉末）１００〜２５０
メッシュＤ ＡＩ−１０．３％Ｐｂ−０．６％Ｓｎ合金
粉末（アトマィズ粉末）１００〜２５０メッシュＥ Ａ
Ｉ−６．２％Ｐｂ−０．４％Ｓｎ合金粉末（アトマィズ
粉末）１００〜２５０〆ツシュ溶射条件 プラズマガス・・・アルゴン；１５庇ＣＦＨ、水素；虫
ＣＦＨ電流・電圧・・・５０船、７５Ｖ 溶射距離・・・１２仇廠 冷却ェア・・・５０ＰＳ１、クロスジェット距離１７０
粉末供聯合速度・・・３．１５ｋ９／Ｈｒ予熱温度・・
・２５０００ 得られた溶射組織の断面組織をみると、Ｐｂ−Ｓｎ合金
粒子はアルミニウム中に細かく、均一に分布していた。Next, AI-Pb(-Sn) alloy powder was sprayed onto this steel plate under the following conditions to a thickness of 0.5 mm. Spraying equipment: 40kw plasma spraying equipment Alloy powder for thermal spraying: A AI-38.2%Pb-2.1%Sn alloy powder (atomized powder) 100-250 mesh B AI-30
．． 3%Pb-1.6%Sn alloy powder (atomized powder)
100-250 mesh C AI-19.6%Pb-0
．． 9% Sn alloy powder (atomized powder) 100-250
Mesh D AI-10.3%Pb-0.6%Sn alloy powder (atomized powder) 100-250 mesh E A
I-6.2%Pb-0.4%Sn alloy powder (atomized powder) 100-250〆Tsch thermal spraying conditions Plasma gas... Argon; 15 eaves CFH, hydrogen; Insect CFH Current/voltage... 50 ships, 75V Spraying distance...12 stations Cooling air...50PS1, Cross jet distance 170
Powder supply combination speed...3.15k9/Hr Preheating temperature...
-25000 Looking at the cross-sectional structure of the obtained thermal sprayed structure, the Pb-Sn alloy particles were finely and uniformly distributed in the aluminum.

一例として、ＡＩ−４０％Ｐｂ−２％Ｓｎ合金粉末を溶
射した場合の、断面組織の顕微鏡写真を第３図に示す。
なお、溶射層中のＰｂ−Ｓｎ量は溶射前の値に対し、約
５〜１０％減少していた（第２表参照）。次に前記の熔
射鋼板を溶射層の圧延率５０％に圧延し、３５０００で
２時間水素雰囲気中で焼鈍した。As an example, FIG. 3 shows a micrograph of a cross-sectional structure when sprayed with AI-40%Pb-2%Sn alloy powder.
Note that the amount of Pb-Sn in the sprayed layer was reduced by about 5 to 10% compared to the value before spraying (see Table 2). Next, the above-mentioned hot-sprayed steel sheet was rolled to a rolling ratio of 50% of the sprayed layer, and annealed at 35,000° C. for 2 hours in a hydrogen atmosphere.

この結果得られた圧延板から平板試験片を作成し、機械
試験型摩擦摩耗試験機により、焼付面圧及び摩擦係数を
求めた。試験の条件は下記の通りである。・ 相手材（
円筒試験片）：Ｓ４皮、硬さＨｖ２１０〜２３０ ・ 円筒試験片回転数：１００仇．ｐ．ｍ．（すべり速
度１１９．３仇／ｓｅｃ）・潤滑油：キヤツスルクリー
ンカスタム ＳＡＥ３００ ・ 油温３５〜４０００（但し、試験開始時）この結果
及び軸受層の成分、硬さ、表面粗さを第２表に示す。A flat plate test piece was prepared from the resulting rolled plate, and the seizure surface pressure and friction coefficient were determined using a mechanical test type friction and wear tester. The test conditions are as follows.・Mating material (
Cylindrical test piece): S4 skin, hardness Hv210-230 ・Cylindrical test piece rotation speed: 100 m. p. m. (Sliding speed 119.3 m/sec) - Lubricating oil: Cattle Clean Custom SAE300 - Oil temperature 35-4000 (however, at the start of the test) This result and the components, hardness, and surface roughness of the bearing layer were Shown in the table.

第 ２ 表 × ２５０ｋｇ／の以上の試験は不能（機械能力）＊失
摩擦係数は２５０ｋタイあのものはその面圧、１９５
ｋｇイめで暁付いたものは暁付前の値を示した。Table 2 × Tests over 250 kg/impossible (mechanical ability)
Those that reached dawn in kg showed the values before dawn.

比較例 １溶射粉末が下記のようなＮとＰｂ−Ｓｎ合金
の混合粉末である以外は、実施例１と全く同様のことを
行った。Comparative Example 1 The same procedure as in Example 1 was carried out except that the thermal spray powder was a mixed powder of N and Pb-Sn alloy as shown below.

・ 溶射粉末…ＡＩ粉末（１００〜２５０メッシュ）と
Ｐｂ−Ｓｎ合金粉末（１００〜２５０メッシュ）をＶ型
ツクスウェル で１０分間緊密に混合する。- Thermal spray powder: AI powder (100-250 mesh) and Pb-Sn alloy powder (100-250 mesh) are intimately mixed in a V-shaped Tuxwell for 10 minutes.

Ｆ 純ＡＩ粉末６０％十Ｐｂ（９５％）一Ｓｎ（５％）
合金粉末 ４０％Ｇ 純ＡＩ粉末７０％十Ｐｂ（９５
％）−Ｓｎ（５％）合金粉末 ３０％Ｈ 純ＡＩ粉末
８０％十Ｐｂ（９５％）−Ｓｎ（５％）合金粉末 ２
０％１ 純ＡＩ粉末９０％十Ｐｂ（９５％）−Ｓｎ（５
％）合金粉末 １０％Ｊ 純ＡＩ粉末９５％十Ｐｂ（
９５％）−Ｓｎ（５％）合金粉末この漆射層の断面組織
をみると、Ｐｂ−Ｓｎ合金粒子は粗く、しかも不均一な
分布であった。F Pure AI powder 60% - Pb (95%) - Sn (5%)
Alloy powder 40%G Pure AI powder 70%10Pb (95
%)-Sn (5%) alloy powder 30%H Pure AI powder 80% 10Pb (95%)-Sn (5%) alloy powder 2
0%1 Pure AI powder 90%10Pb(95%)-Sn(5
%) Alloy powder 10%J Pure AI powder 95% 10Pb (
95%)-Sn(5%) alloy powder Looking at the cross-sectional structure of this lacquered layer, the Pb-Sn alloy particles were coarse and non-uniformly distributed.

一例として試料Ｆの粉末による断面組織の顕微鏡写真図
を第４図に示す。なお、溶射層中のＰｂ−Ｓｎ量は溶射
前の値に対し、約１０〜３０％減少していた。圧延・暁
鎚後の軸受層の成分、硬さ、表面粗さ、及び機械試験所
型摩擦摩耗における暁付面圧及び摩擦係数を第３表に示
す。第 ３ 表 実施例 ２ 幅３１肌、肉厚１．５肌（バックメタル厚１．２肌）、
径４７．８０の平軸受を下記第４表のように１２種類作
成した。As an example, FIG. 4 shows a micrograph of the cross-sectional structure of the powder of Sample F. Note that the amount of Pb-Sn in the sprayed layer was reduced by about 10 to 30% compared to the value before spraying. Table 3 shows the components, hardness, surface roughness, and surface pressure and friction coefficient of the bearing layer after rolling and hammering, as well as the rolling contact pressure and friction coefficient in mechanical testing laboratory type friction wear. Table 3 Example 2 Width: 31 skins, wall thickness: 1.5 skins (back metal thickness: 1.2 skins),
Twelve types of plain bearings with a diameter of 47.80 mm were prepared as shown in Table 4 below.

この軸受を倉田式動荷重試験機を用いて、軸受の耐疲労
性を調べた。The fatigue resistance of this bearing was examined using a Kurata dynamic load tester.

第４表に疲労面圧（繰り返し数１０７回に於る）を示す
。なお本試験は下記条件のもとで行われた。・ 回転数
・…・・２８０仇．ｐ．ｍ（速度７ｍ／ｓｅｃ）・ 軸
材質・・・・・・Ｓ５に（硬さＨＲＣ５０、粗さ０．８
山Ｒｚ）・ 潤滑油・・・・・・ＳＡＦ３０メッシュ、
ＭＳ−ＤＭ級・ 給油圧・・・・・・４．０ｋ９／地・
給油温度・・・・・・８０００ ・ オイルクリアランス…・・・０．０４〜０．０６帆
第 ４ 表任‐１） 溶射粉末、溶射条件は実施例１、
比較例１と同じ圧２ ） 溶射後は圧延（５０略）、燐
鈍（３５０℃×２時市母）を行った。Table 4 shows the fatigue surface pressure (at 107 repetitions). This test was conducted under the following conditions.・ Number of revolutions...280. p. m (speed 7m/sec)・Shaft material...S5 (hardness HRC50, roughness 0.8
Mountain Rz)・Lubricating oil・・・SAF30 mesh,
MS-DM class・Supply oil pressure...4.0k9/earth・
Oil supply temperature...8000 ・Oil clearance...0.04~0.06 Sails 4th assignment-1) Thermal spray powder and thermal spraying conditions are as in Example 1,
The same pressure as in Comparative Example 1) After thermal spraying, rolling (50 omitted) and phosphor annealing (350° C. x 2 o'clock molding) were performed.

注３）平軸受の製造方法は公知の方法によった。上記結
果より明らかなように、軸受を本発明方法により製造す
ると、メタル部分にＰｂ粒子が細かく均一に分布し、し
かもＰｂ量の自由度の高い漆射層が形成されるため軸受
の耐摩耗性及び耐焼付性が向上し、良好な軸受を得るこ
とができる。Note 3) The plain bearing was manufactured using a known method. As is clear from the above results, when a bearing is manufactured by the method of the present invention, Pb particles are finely and uniformly distributed in the metal part, and a lacquered layer with a high degree of freedom in the amount of Pb is formed, which improves the wear resistance of the bearing. And the seizure resistance is improved, and a good bearing can be obtained.

【図面の簡単な説明】[Brief explanation of the drawing]

第１図は軸受の一部拡大断面図、第２図イ〜ハは本発明
方法で得られるＮ−Ｐｂ系合金粉末中のＰｂ分布を示す
拡大模式図、第３図は実施例１で得られるＡＩ一Ｐｂ系
溶射層の顕微鏡写真図（×１００）、第４図は比較例１
で得られるＡＩ−Ｐｂ系溶射層の顕微鏡写真図（×１０
０）、を表わす。 図中、ａ・・・・・・バックメタル、ｂ・・・…中間層
、ｃ・・・…溶射層、１・・・・・・ＡＩ−Ｐｂ系粉末
、２……Ｐｂ粒子を表わす。第１図 第２図 第３図 第４図Fig. 1 is a partially enlarged sectional view of the bearing, Fig. 2 A to C are enlarged schematic diagrams showing the Pb distribution in the N-Pb alloy powder obtained by the method of the present invention, and Fig. 3 is a partially enlarged sectional view of the bearing. A microscopic photograph (×100) of the AI-Pb sprayed layer, Figure 4 is Comparative Example 1.
Microscopic photograph of the AI-Pb sprayed layer obtained in (×10
0). In the figure, a...back metal, b...intermediate layer, c...sprayed layer, 1...AI-Pb powder, 2...Pb particles. Figure 1 Figure 2 Figure 3 Figure 4

Claims (1)

【特許請求の範囲】[Claims] １ 鉛５ないし４０重量％を含有する鉛粒子が分散され
ているアルミニウム合金粉末をバツクメタル上に溶射し
、その後圧延、焼鈍、成形することを特徴とするアルミ
ニウム−鉛系軸受の製造方法。1. A method for manufacturing an aluminum-lead bearing, which comprises spraying aluminum alloy powder in which lead particles containing 5 to 40% by weight of lead are dispersed onto a back metal, followed by rolling, annealing, and forming.