JPS62235438A - Manufacture of bearing alloy - Google Patents
Manufacture of bearing alloyInfo
- Publication number
- JPS62235438A JPS62235438A JP7800286A JP7800286A JPS62235438A JP S62235438 A JPS62235438 A JP S62235438A JP 7800286 A JP7800286 A JP 7800286A JP 7800286 A JP7800286 A JP 7800286A JP S62235438 A JPS62235438 A JP S62235438A
- Authority
- JP
- Japan
- Prior art keywords
- billet
- ratio
- matrix
- bearing
- sectional area
- 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.)
- Pending
Links
- 239000001996 bearing alloy Substances 0.000 title claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 9
- 238000001125 extrusion Methods 0.000 claims abstract description 30
- 239000000843 powder Substances 0.000 claims abstract description 29
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 17
- 229910052718 tin Inorganic materials 0.000 claims abstract description 16
- 239000011159 matrix material Substances 0.000 claims abstract description 15
- 229910052802 copper Inorganic materials 0.000 claims abstract description 13
- 229910052745 lead Inorganic materials 0.000 claims abstract description 13
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 11
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 10
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 229910052787 antimony Inorganic materials 0.000 claims abstract description 7
- 229910052797 bismuth Inorganic materials 0.000 claims abstract description 7
- 229910052738 indium Inorganic materials 0.000 claims abstract description 7
- 230000001050 lubricating effect Effects 0.000 claims description 17
- 229910052751 metal Inorganic materials 0.000 claims description 9
- 239000002184 metal Substances 0.000 claims description 9
- 150000002739 metals Chemical class 0.000 claims description 9
- 239000002245 particle Substances 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 5
- 230000003014 reinforcing effect Effects 0.000 claims description 4
- 238000000034 method Methods 0.000 abstract description 11
- 238000005728 strengthening Methods 0.000 abstract 2
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000000463 material Substances 0.000 description 21
- 238000010438 heat treatment Methods 0.000 description 17
- 239000010949 copper Substances 0.000 description 15
- 229910045601 alloy Inorganic materials 0.000 description 12
- 239000000956 alloy Substances 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 12
- 239000011856 silicon-based particle Substances 0.000 description 11
- 230000002706 hydrostatic effect Effects 0.000 description 10
- 239000010953 base metal Substances 0.000 description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 238000009694 cold isostatic pressing Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 239000012535 impurity Substances 0.000 description 5
- 239000011812 mixed powder Substances 0.000 description 5
- 239000012299 nitrogen atmosphere Substances 0.000 description 5
- 238000002485 combustion reaction Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 229910000831 Steel Inorganic materials 0.000 description 3
- 238000000137 annealing Methods 0.000 description 3
- 229910052796 boron Inorganic materials 0.000 description 3
- 230000013011 mating Effects 0.000 description 3
- 229910052761 rare earth metal Inorganic materials 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- 238000005253 cladding Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000005461 lubrication Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910052706 scandium Inorganic materials 0.000 description 2
- 230000035900 sweating Effects 0.000 description 2
- 229910052727 yttrium Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910020816 Sn Pb Inorganic materials 0.000 description 1
- 229910020922 Sn-Pb Inorganic materials 0.000 description 1
- 229910008783 Sn—Pb Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 239000012790 adhesive layer Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000007796 conventional method 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
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 235000012438 extruded product Nutrition 0.000 description 1
- 229910052733 gallium Inorganic materials 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 208000014617 hemorrhoid Diseases 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000010902 straw Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Abstract
Description
【発明の詳細な説明】
［発明の目的］
（産業上の利用分野）
この発明は、自動車、工作機械、農業機械等の各種機械
装置の構造部品として使用される軸受ならびに摺動部材
用の素材として適する軸受合金に関し、とくに銅系の軸
受材料に比べて軽量であってしかも耐疲労性９表面性能
にすぐれたアルミニウム系の軸受台金に関するものであ
る。[Detailed Description of the Invention] [Objective of the Invention] (Industrial Application Field) This invention relates to materials for bearings and sliding members used as structural parts of various mechanical devices such as automobiles, machine tools, and agricultural machinery. The present invention relates to bearing alloys suitable as bearing materials, and particularly to aluminum-based bearing base metals that are lighter than copper-based bearing materials and have excellent fatigue resistance and surface performance.
（従来の技術）
従来、すべり軸受の素材として用いられる合金には、Ｃ
ｕ−Ｐｂ系、バビット系等が使用目的などに応じて使用
されているが、近年、とくに内燃機関用の軸受台金とし
ては、耐熱＃摩耗性、＃腐食性、耐疲労性等の点からＡ
文系の軸受台金が注目されている。なかでも、Ａｎ−３
ｎ系、ＡｆＬ−Ｓｎ−Ｐｂ系の軸受台金は上記性能の点
で他の材質のものに比べてかなりすぐれているため、最
近に至り急速にその使用量が増加している。(Prior art) Conventionally, alloys used as materials for sliding bearings contain C.
u-Pb series, Babbitt series, etc. are used depending on the purpose of use, etc., but in recent years, especially as bearing base metals for internal combustion engines, from the viewpoint of heat resistance, wear resistance, corrosion resistance, fatigue resistance, etc. A
The bearing base metal of liberal arts is attracting attention. Among them, An-3
N-type and AfL-Sn-Pb type bearing base metals are considerably superior to those made of other materials in terms of the above-mentioned performance, so their usage has been rapidly increasing recently.
しかしながら、内燃機関の小型化による軸受幅の縮小、
高出力化に伴う軸受負荷の増大等の内燃機関の高性能化
により、軸受に課せられる要求はさらに強まり、とりわ
け耐疲労性の面、すなわち軸受台金の亀裂あるいは鋼裏
金からの局部的剥離を抑制すべく改善が望まれているの
が現状である。However, due to the miniaturization of internal combustion engines, the width of the bearings has decreased,
As the performance of internal combustion engines increases, such as the increase in bearing load associated with higher output, the demands placed on bearings are becoming even stronger. The current situation is that improvements are desired to suppress this problem.
このような内燃機関の高性能化に対応できるＡｌ系の軸
受合金の一例として、本発明者らは特願昭６０−２６８
８６６号明細書に示すようなＡｎ−Ｐｂ−５ｎ系のアト
マイズ合金粉末に押出加工を加えることにより、高い疲
労強度と優れた潤滑性とを合わせ持たせた新しいタイプ
の軸受台金を開発した。As an example of an Al-based bearing alloy that can meet the high performance of internal combustion engines, the present inventors have proposed
By applying extrusion processing to An-Pb-5n-based atomized alloy powder as shown in the specification of No. 866, we have developed a new type of bearing base metal that has both high fatigue strength and excellent lubricity.
このアルミニウム系軸受合金は、Ａｌを主成分とし、潤
滑成分としてＰｂ、Ｓｎ、Ｉｎ、Ｓｂ。This aluminum-based bearing alloy has Al as its main component, and Pb, Sn, In, and Sb as lubricating components.
Ｂｉよりなる群から選ばれた１種以上の金属をＡｎマト
リックスに対する断面積比で０．０４超過０．０７以下
、硬質成分としてＳｉを同じく断面積比で０．０１以上
０．１７以上１強化成分としてＣｕ、Ｃｒ、Ｍｇ、Ｍｎ
、Ｎｉ 、Ｚｎ。One or more metals selected from the group consisting of Bi are reinforced with a cross-sectional area ratio of 0.04 to 0.07 to the An matrix, and Si as a hard component is also reinforced with a cross-sectional area ratio of 0.01 to 0.17 to 1. Cu, Cr, Mg, Mn as components
, Ni, Zn.
Ｆｅよりなる群から選ばれた１種以上の金属を０．２〜
５，０重量％、必要に応じて微細化成分としてＴｉ 、
Ｂ、Ｚｒ、Ｖ、Ｇａ、ＲＥＭ（Ｓｃ、Ｙを含む希土類元
素の１種以上）よりなる群から選ばれた１種以上の金属
を全合金に対して０．０１〜３．０重量％含み、均一微
細に分散した潤滑成分の大きさが８μｍ以下である合金
粉末から成形したビレットを押出比１０以上で押出成形
して成り、Ａｎマトリックス中に分散したＳｉ粒子の大
きさが１２μｍ以下、とくに望ましくは６〜１２μｍ、
常温での引張強さが１２ｋｇｆ／ｍｍ２以上、常温での
伸びが１１％以上であることを特徴としており、Ａ９．
系の軸受合金そのものとして使用したり、該軸受合金を
鋼板等と直接、あるいはＡｌ、Ｎｉ等の密着層を介して
接合した軸受として使用したりすることを特徴としてい
るものである。One or more metals selected from the group consisting of Fe from 0.2 to
5.0% by weight, Ti as a finer component if necessary,
Contains 0.01 to 3.0% by weight of one or more metals selected from the group consisting of B, Zr, V, Ga, and REM (one or more rare earth elements including Sc and Y) based on the total alloy. , a billet formed from an alloy powder in which the size of lubricating components uniformly and finely dispersed is 8 μm or less is extruded at an extrusion ratio of 10 or more, and the size of Si particles dispersed in the An matrix is 12 μm or less, especially Desirably 6 to 12 μm,
A9.
It is characterized in that it can be used as a bearing alloy itself, or as a bearing in which the bearing alloy is bonded to a steel plate or the like directly or through an adhesive layer of Al, Ni, etc.
そして、上記したアルミニウム系軸受合金を製造するに
あたっては、Ａ文−８〜１２重量％Ｐｂ−０，４〜１．
８重量％５ｎ−１．０−１５重量％５ｉ−０，２〜５．
０重量％（Ｃｕ。In manufacturing the above-mentioned aluminum-based bearing alloy, A-8 to 12% by weight Pb-0.4 to 1.
8% by weight 5n-1.0-15% by weight 5i-0,2-5.
0% by weight (Cu.
Ｃｒ、Ｍｇ、Ｍｎ、Ｎｉ 、Ｚｎ、Ｆｅの１種以Ｊ：、
）の合金粉末に３５０〜５５０℃で加熱処理を施してＳ
ｉ粒子を６〜１２μｍに成長させた後、前記合金粉末に
、Ａ９．−１０〜２０重量％Ｓｎ系あるいはＡ文−１０
〜２０重量％５ｎ−１，０〜１５重量％５ｉ−０，２〜
５．０重量％（Ｃｕ、Ｃｒ、Ｍｇ、Ｍｎ、Ｎｉ 、Ｚｎ
、Ｆｅの１種以上）系等のＡ見−潤滑成分（ｐｂ。One or more of Cr, Mg, Mn, Ni, Zn, Fe.
) alloy powder was heat-treated at 350-550℃ to form S
After growing the i particles to 6-12 μm, A9. -10 to 20% by weight Sn-based or A-10
~20% by weight 5n-1,0-15% by weight 5i-0,2~
5.0% by weight (Cu, Cr, Mg, Mn, Ni, Zn
, one or more types of Fe)-based lubricating components (pb.
Ｓｎ、Ｉｎ、Ｓｂ、Ｂｉの１種以上）−硬質成分（Ｓｉ
）−強化成分（Ｃｕ ｔ Ｃｒ ＋ Ｍ ｇ ＋ Ｍ
ｎ ＋Ｎｉ、Ｚｎ、Ｆｅの１種以上）−微細化成分（Ｔ
ｉ 、Ｂ、Ｚｒ、Ｖ、Ｇａ、ＲＥＭの１種以上）合金粉
末を前記アルミニウム系軸受合金の成分範囲となるよう
に混合し、さらに該混合粉末をビレットに成形した後該
ビレットを押出比１０以上で押出成形するようにしたこ
とを特徴としているものである。one or more of Sn, In, Sb, Bi) - hard component (Si
) - reinforcing component (Cut Cr + M g + M
n + one or more of Ni, Zn, Fe) - refining component (T
i, B, Zr, V, Ga, REM) alloy powders are mixed so as to have the composition range of the aluminum-based bearing alloy, and the mixed powder is formed into a billet, and then the billet is extruded at an extrusion ratio of 10. This is characterized in that the above is extrusion molded.
Ｌ記製造法においてＳｉ粒子を６〜１２４ｍに成長させ
た理由は、上記アルミニウム系合金を軸受材として用い
た場合にその相罫材が鋳造材であると、この鋳造材の切
削加工時に遊離黒鉛の周囲に微細なパリを生じ、このパ
リが軸受表面を傷つけるため、これを防ぐ意味からＳｉ
粒子の大きさをある程度大きくし、この硬いＳｉ粒子で
パリを取り除く必要があるからである。The reason why the Si particles were grown to a length of 6 to 124 m in the manufacturing method described in L is that when the above aluminum alloy is used as a bearing material and the interlining material is a cast material, free graphite is generated during cutting of the cast material. Si
This is because it is necessary to increase the size of the particles to a certain extent and remove the particles with these hard Si particles.
また、この合金はＰｂ、Ｓｎのような潤滑成分が断面積
比で０．０４超過０．０７以下と多量であるため、押出
し後に押出材に対して加熱処理を施すという通常の方法
では、Ｐｂ、Ｓｎのような潤滑成分が表面へしみ出すと
いう現象（Ｓｗｅａｔ ｉ ｎｇ）を生ずるという問題
があったため、上記製造法のように粉末を加熱処理する
方法をとっている。In addition, this alloy has a large amount of lubricating components such as Pb and Sn in the cross-sectional area ratio of more than 0.04 and less than 0.07, so the usual method of heat-treating the extruded material after extrusion Because of the problem that lubricating components such as , Sn seep out to the surface (sweating), a method of heat-treating the powder as in the above manufacturing method is used.
（発明が解決しようとする問題点）
しかしながら、粉末に加熱処理を施すと当該粉末が凝集
するおそれがあること、また成分含有量の異なる２種の
粉末を混合して押出し、その押出し温度が２００〜４０
０℃と低く、押出し後の熱処理も行わないため、合金元
素の拡散が不十分でＳｉ、Ｓｎなどの偏析が生じる可能
性があること、が上記製造法の問題点として残されてい
た。(Problems to be Solved by the Invention) However, if the powder is heat-treated, there is a risk that the powder will agglomerate, and if two types of powder with different component contents are mixed and extruded, the extrusion temperature is 200 ~40
Since the temperature is as low as 0° C. and no heat treatment is performed after extrusion, there remains a problem with the above manufacturing method that the diffusion of alloying elements is insufficient and segregation of Si, Sn, etc. may occur.
そして、とくに一方の粉末のＳｎ添加量が１０〜２０重
量％と多いためＳｎの偏析が生じやすく、これが原因と
なって押出材の表面欠陥の発生や押出材の疲労強度の低
下が生じることもあった。In particular, since the amount of Sn added to one of the powders is as high as 10 to 20% by weight, Sn segregation tends to occur, which may cause surface defects in the extruded material and a decrease in the fatigue strength of the extruded material. there were.
この発明はこのような従来の問題点に着目してなされた
もので、粉末を単一の完全合金粉末とし、この合金粉末
から成形した理論密度比８０〜９５％のビレットに３５
０〜５５０℃で加熱処理を施してＳｉ粒子を６〜１２Ｉ
Ｌｍに成長させた後、当該ビレットを押出比１０以上で
押出成形することにより、Ｓｔ、Ｓｎなどの偏析を防止
しながら、Ｓｉ粒子を最適な大きさに成長させて前記問
題点を解決することを目的としている。This invention was made by focusing on such conventional problems, and the powder is made into a single complete alloy powder, and the billet formed from this alloy powder has a theoretical density ratio of 80 to 95%.
Heat treatment is performed at 0 to 550°C to convert Si particles to 6 to 12I.
After growing to Lm, the billet is extruded at an extrusion ratio of 10 or more to grow Si particles to an optimal size while preventing segregation of St, Sn, etc., thereby solving the above problem. It is an object.
［発明の構成］
（問題点を解決するための手段）
この発明による軸受台金の製造方法は、Ａｌを主成分と
し、１！Ｉ滑成分としてＰｂ、Ｓｎ、Ｉｎ。[Structure of the Invention] (Means for Solving the Problems) A method for manufacturing a bearing base metal according to the present invention includes Al as a main component, and 1! Pb, Sn, and In as lubricant components.
Ｓｂ、Ｂｉよりなる群から選ばれた１種以上の金属をＡ
ｌマトリックスに対する断面積比で０．０４以上０．０
７以下、硬質成分としてＳｉを同じく断面積比で０．０
１以上０．１７以下、強化成分としてＣｕ、Ｃｒ、Ｍｇ
、Ｍｎ、Ｎｉ 。A of one or more metals selected from the group consisting of Sb and Bi.
0.04 or more 0.0 in cross-sectional area ratio to l matrix
7 or less, Si as a hard component also has a cross-sectional area ratio of 0.0
1 or more and 0.17 or less, Cu, Cr, Mg as reinforcing components
, Mn, Ni.
Ｚｎ 、Ｆｅよりなる群から選ばれた１種以上の金属を
０．２〜５．０重量％含み、均一微細に分散した潤滑成
分の大きさが８ｐｍ以下であるアルミニウム合金粉末を
圧粉成形し、理論密度比８０〜９５％のビレットとした
後３５０〜５５０ ”Ｏにて加熱処理を施してＳｉ粒子
を６〜１２ＪＬｍに成長させ、その後該ビレットを押出
比１０以上で押出成形するようにしたことを特徴とする
ものである。An aluminum alloy powder containing 0.2 to 5.0% by weight of one or more metals selected from the group consisting of Zn and Fe and having lubricating components uniformly and finely dispersed with a size of 8 pm or less is powder-molded. After forming a billet with a theoretical density ratio of 80 to 95%, heat treatment was performed at 350 to 550"O to grow Si particles to 6 to 12 JLm, and then the billet was extruded at an extrusion ratio of 10 or more. It is characterized by this.
以下、それぞれの成分および数値の限定理由について説
明する。The reasons for limiting each component and numerical value will be explained below.
（１）Ｐｂ、Ｓｎ、Ｉｎ、Ｓｂ、Ｂｉは潤滑成分として
有効であり、耐焼付性にすぐれたものである。しかし、
潤滑成分の総量が断面積比（体積比）で０．０４未満の
場合は異物埋収性が劣り、また０、０７を超えるとマト
リックスの疲労強度不足となり、耐荷重性の点で軸受性
能を満足できなくなる。(1) Pb, Sn, In, Sb, and Bi are effective as lubricating components and have excellent seizure resistance. but,
If the total amount of lubricating components is less than 0.04 in terms of cross-sectional area ratio (volume ratio), the foreign matter embedding property will be poor, and if it exceeds 0.07, the fatigue strength of the matrix will be insufficient, which will affect the bearing performance in terms of load resistance. You won't be satisfied.
さらに、潤滑成分の粒子径については、粒子径が過大で
あると軸受合金の性能に悪影響を及ぼすので８ｐｍ以下
とするのが良い。Furthermore, the particle size of the lubricating component is preferably 8 pm or less, since excessive particle size will have a negative effect on the performance of the bearing alloy.
（２）Ｓｉは硬質成分として添加するものであり、共晶
Ｓｉまたは初晶ＳｉとしてＡｎ中に分散し、硬質物質と
して軸受強度の向上および耐摩耗性の向上に寄与する。(2) Si is added as a hard component, and is dispersed in An as eutectic Si or primary Si, and as a hard substance, contributes to improving bearing strength and wear resistance.
このＳｉの添加量としては断面積比（体積比）で前記潤
滑成分の１／４から２．５倍程度までの量が望ましく、
多く添加するともろくなり加工性を阻害するので、マト
リックスに対する断面積比を０．０１以上０．１７以下
とするのが良い。The amount of Si added is preferably from 1/4 to 2.5 times the amount of the lubricating component in terms of cross-sectional area ratio (volume ratio).
If too much is added, it becomes brittle and impedes workability, so it is preferable that the cross-sectional area ratio to the matrix is 0.01 or more and 0.17 or less.
またＳｉ粒子径については、６Ｊｊ、ｍ未満であると切
削加工時に生じる相手材の小さなパリを取り除く効果が
薄れ、また１２ＩＬｍを超えると相手材を傷つけ分散の
面密度が低下し、耐摩耗性が劣化するので６〜１２μｍ
とするのが良い。Regarding the Si particle size, if it is less than 6Jj,m, the effect of removing small particles of the mating material that occurs during cutting will be weakened, and if it exceeds 12ILm, it will damage the mating material and reduce the areal density of dispersion, resulting in poor wear resistance. 6 to 12 μm due to deterioration
It is better to
（３）Ｃｕ、Ｃｒ、Ｍｇ、Ｍｎ、Ｎｉ、Ｚｎ。(3) Cu, Cr, Mg, Mn, Ni, Zn.
ＦｅはＡＩマトリックスの強度を高めるのに有効な成分
である。これらのうちＣｕはクリープ強度すなわち高温
軟化抵抗を高める主要な元素であり、高温摺動下におけ
る耐疲労性に寄与する。しかし、０．２重量％未満では
上記した効果が少なく、５．０重量％を超えると針状の
ＣｕＡＪｌｚ化合物が多量に析出して脆くなり、＃疲労
性の低下を招く。またＣｕ以外にマトリックスの強度を
高める元素として、Ｃｒ、Ｍｇ、Ｍｎ、Ｎｉ 。Fe is an effective component for increasing the strength of the AI matrix. Among these, Cu is a main element that increases creep strength, that is, high-temperature softening resistance, and contributes to fatigue resistance under high-temperature sliding. However, if it is less than 0.2% by weight, the above-mentioned effects will be small, and if it exceeds 5.0% by weight, a large amount of acicular CuAJlz compounds will precipitate and become brittle, leading to a decrease in #fatigue properties. In addition to Cu, other elements that increase the strength of the matrix include Cr, Mg, Mn, and Ni.
Ｚｎ 、Ｆｅがあり、Ａ１合金展伸材の添加元素として
よく使用されるもので、Ｃｕを含むこれらの元素の１種
以上を０．２〜５．０重量％の範囲で添加してもよい。Zn and Fe are often used as additive elements for A1 alloy wrought material, and one or more of these elements including Cu may be added in a range of 0.2 to 5.0% by weight. .
（４）前記組成のアルミニウム合金粉末を圧粉成形した
ビレット（圧粉体）の理論密度比については、８０％未
満では加熱時に空孔内に偏在する潤滑成分が大きくなり
、押出時に欠陥が発生し、９５％超過では潤滑成分が表
面へしみ出すという現象（Ｓｗｅ ａｔ ｉ ｎｇ）を
生ずるノテ、８０〜９５％とした。(4) Regarding the theoretical density ratio of a billet (green compact) obtained by compacting aluminum alloy powder with the above composition, if it is less than 80%, the lubricating components unevenly distributed in the pores will increase during heating, causing defects during extrusion. However, if it exceeds 95%, the lubricating component will seep out to the surface (sweating), so it was set at 80 to 95%.
（５）Ｓｉ粒子径を６〜１２ＪＬｍに成長させる加熱温
度は、３５０℃未満ではＳｉを成長させるのに極めて長
い時間を必要とするため実用的でなく、また５５０″Ｃ
を超える温度ではＳｉ粒子が粗大になりすぎたり、マト
リックスの結晶粒が粗大化したりするので、加熱温度範
囲は３５０〜５５０℃が好ましい。(5) The heating temperature for growing the Si particle size to 6 to 12 JLm is impractical if it is less than 350°C because it takes an extremely long time to grow Si;
If the temperature exceeds 350°C to 550°C, the Si particles will become too coarse or the crystal grains of the matrix will become coarse. Therefore, the heating temperature range is preferably 350 to 550°C.
（６）押出比については、押出比が１０未満であると内
部クラックおよび押出後の軸受台金素材の表面割れを生
じ実用に供しうるちのは得られないため、押出比１０以
上が好ましい。(6) Regarding the extrusion ratio, an extrusion ratio of 10 or more is preferable, since if the extrusion ratio is less than 10, internal cracks and surface cracks of the bearing base metal material after extrusion will occur, making it impossible to obtain a material that can be put to practical use.
なお、この発明における軸受台金の原料粉末中に、Ａ１
合金の結晶粒微細化元素であるＴＩ。In addition, in the raw material powder of the bearing base metal in this invention, A1
TI is a grain refining element for alloys.
Ｂ、Ｚｒ、Ｖ、Ｃａ、ＲＥＭ（Ｙ、Ｓｃを含む希土類元
素の１種以上）などを必要に応じて添加して組織の均一
微細化を図ってもよいことはもちろんである。Of course, B, Zr, V, Ca, REM (one or more rare earth elements including Y and Sc), etc. may be added as necessary to achieve uniform refinement of the structure.
（実施例１）
重量％で、Ｐｂ：１２．０％、Ｓｎ：３．０％、Ｓｔ
：４．０％、Ｃｕ：０．７５％、Ｃｒ：０．５％、残部
実質的にＡｎおよび不純物よりなるアルミニウム合金粉
末を、直径１００ｍｍ。(Example 1) In weight%, Pb: 12.0%, Sn: 3.0%, St
: 4.0%, Cu: 0.75%, Cr: 0.5%, and the remainder substantially consists of An and impurities, with a diameter of 100 mm.
長さ１００ｍｍｃ７）円柱形状に２．０ｔｏｎｆ／ｃｍ
２の静水圧にて冷間静水圧成形し、理論密度比９１％の
ビレッｉ・とじた。Length 100mmc7) Cylindrical shape 2.0tonf/cm
It was cold isostatically pressed at a hydrostatic pressure of 2 and closed into a billet with a theoretical density ratio of 91%.
次に、前記ビレットに対し窒素雰囲気中にて５３０″Ｃ
Ｘ８時″間の加熱処理を施し、その後４００℃にて押出
しを行って押出成形体を得た。Next, the billet was heated to 530"C in a nitrogen atmosphere.
A heat treatment was performed for 8 hours, followed by extrusion at 400° C. to obtain an extruded product.
次いで、この押出成形体に対し、押出成形体→圧延前加
熱処理→圧延→アニール→純ＡＬ；Ｌ板とプレクラッド
→アニール→鋼板とクラッド→アニール→機械加工の工
程で軸受を製作した。Next, a bearing was manufactured from this extruded body through the following steps: extrusion molded body → pre-rolling heat treatment → rolling → annealing → pure AL; L plate and pre-cladding → annealing → steel plate and cladding → annealing → machining.
（実施例２） 重量％で、Ｐｂ：９．６％、Ｓｎ：３．０％。(Example 2) In weight%, Pb: 9.6%, Sn: 3.0%.
Ｓｉ：４．０％、Ｃｕ：０．７５％、Ｃｒ：０．５％、
残部実質的にＡｌｌおよび不純物よりなるアルミニウム
合金粉末を、直径１００ｍｍ。Si: 4.0%, Cu: 0.75%, Cr: 0.5%,
Aluminum alloy powder with a diameter of 100 mm, the remainder consisting essentially of All and impurities.
長さ１００ｍｍの円柱形状に２．０ｔｏｎｆ／ｃｍ２の
静水圧にて冷間静水圧成形し、理論密度比９１％のビレ
ットとした。It was cold isostatically formed into a cylindrical shape with a length of 100 mm under a hydrostatic pressure of 2.0 tonf/cm 2 to obtain a billet with a theoretical density ratio of 91%.
次に、前記ビレットに対し窒素雰囲気中にて５３０’Ｏ
Ｘ８時間の加熱処理を施し、その後３５０℃にて押出し
を行って押出成形体を得た。Next, the billet was heated to 530'O in a nitrogen atmosphere.
A heat treatment was performed for 8 hours, followed by extrusion at 350° C. to obtain an extrusion molded product.
次いで、この押出成形体を用いて実施例１と同じ工程で
軸受を製作した。Next, a bearing was manufactured using this extruded body in the same process as in Example 1.
（実施例３） 重量％で、Ｐｂニア、０％、Ｓｎ：６．１％。(Example 3) In weight%, Pb nia: 0%, Sn: 6.1%.
Ｓｉ：５．６％、Ｃｕ：０．５３％、残部実質的にＡｎ
および不純物よりなるアルミニウム合金粉末を、直径１
００ｍｍ、長さ１００ｍｍの円柱形状に２．０ｔｏｎｆ
／ｃｍ２の静水圧にて冷間静水圧成形し、理論密度比９
２％のビレットとした。Si: 5.6%, Cu: 0.53%, remainder substantially An
Aluminum alloy powder consisting of aluminum alloy powder and impurities was
00mm, 2.0tonf in a cylindrical shape with a length of 100mm
Cold isostatic pressing was performed at a hydrostatic pressure of /cm2, and the theoretical density ratio was 9.
It was made into a 2% billet.
次に、前記ビレットに対し窒素雰囲気中にて５２０’０
Ｘ１２時間の加熱処理を施し、その後３２０℃にて押出
しを行って押出成形体を得た。Next, the billet was heated to 520'0 in a nitrogen atmosphere.
A heat treatment was performed for 12 hours, followed by extrusion at 320° C. to obtain an extrusion molded product.
次いで、この押出成形体を用いて実施例１と同じ工程で
軸受を製作した。Next, a bearing was manufactured using this extruded body in the same process as in Example 1.
（比較例１）
実施例１において用いたアルミニウム合金粉末を直径１
００ｍｍ、長さ１００ｍｍの円柱形状に２．０ｔｏｎｆ
／ｃｍ２の静水圧にて冷間静水圧成形し、理論密度比９
１％のビレットとした。(Comparative Example 1) The aluminum alloy powder used in Example 1 was
00mm, 2.0tonf in a cylindrical shape with a length of 100mm
Cold isostatic pressing was performed at a hydrostatic pressure of /cm2, and the theoretical density ratio was 9.
It was made into a 1% billet.
次に、前記ビレットに加熱処理を施さずに４００℃にて
押出しを行って押出成形体を得た。Next, the billet was extruded at 400° C. without being subjected to heat treatment to obtain an extruded body.
次いで、この押出成形体を用いて実施例１と同じ工程で
軸受を製作した。Next, a bearing was manufactured using this extruded body in the same process as in Example 1.
（比較例２）
実施例２において用いたアルミニウム合金粉末を直径１
００ｍｍ、長さ１００ｍｍの円柱形状に２．０ｔｏｎｆ
／ｃｍ２の静水圧にて冷間静水圧成形し、理論密度比９
１％のビレットとした。(Comparative Example 2) The aluminum alloy powder used in Example 2 was
00mm, 2.0tonf in a cylindrical shape with a length of 100mm
Cold isostatic pressing was performed at a hydrostatic pressure of /cm2, and the theoretical density ratio was 9.
It was made into a 1% billet.
次に、前記ビレットに対し加熱処理を施さずに３５０℃
にて押出しを行って押出成形体を得た。Next, the billet was heated to 350°C without being subjected to heat treatment.
Extrusion was performed to obtain an extrusion molded product.
次いで、この押出成形体を用いて実施例１と同じ工程で
軸受を製作した。Next, a bearing was manufactured using this extruded body in the same process as in Example 1.
（比較例３）
実施例３において用いたアルミニウム合金粉末を直径１
００ｍｍ、長さ１００ｍｍの円柱形状に２．０ｔｏｎｆ
／ｃｍ２の静水圧にて冷間静水圧成形し、理論密度比９
２％のビレ−／ ）とした。(Comparative Example 3) The aluminum alloy powder used in Example 3 was
00mm, 2.0tonf in a cylindrical shape with a length of 100mm
Cold isostatic pressing was carried out at a hydrostatic pressure of /cm2, and the theoretical density ratio was 9.
2% belay/).
次に、前記ビレットに対し加熱処理を施さずに３２０
’Ｏにて押出しを行って押出成形体を得た。Next, the billet was heated to 320°C without being subjected to heat treatment.
Extrusion was performed at 'O' to obtain an extrusion molded product.
次いで、この押出成形体を用いて実施例１と同じ工程で
軸受を製作した。Next, a bearing was manufactured using this extruded body in the same process as in Example 1.
（比較例４）
重量％で、Ｐｂ： １２．０％、Ｓｎ：１．０％、Ｓｉ
：５．０％、Ｃｕ：０．９５％、Ｃｒ：０．６％、残部
実質的にＡｉおよび不純物よりなるアルミニウム合金粉
末に５３０℃×８時間の加熱処理を施した後、Ａ！；Ｌ
−１１重量％Ｓｎのアルミニウム合金粉末と４：ｌの重
量比で混合し、実施例２と同組成の混合粉末を得た。(Comparative Example 4) In weight%, Pb: 12.0%, Sn: 1.0%, Si
: 5.0%, Cu: 0.95%, Cr: 0.6%, and the remainder substantially consists of Al and impurities. After heat treatment at 530° C. for 8 hours, A! ;L
-11 wt % Sn aluminum alloy powder was mixed at a weight ratio of 4:1 to obtain a mixed powder having the same composition as in Example 2.
次に、この混合粉末を直径１００ ｍ ｍ 、長さ１０
０ｍｍの円柱形状に２．０ｔｏｎｆ／ｃｍ２の静水圧に
て冷間静水圧成形し、理論密度比９０％のビレットとし
た。Next, this mixed powder was made into a shape with a diameter of 100 mm and a length of 10 mm.
It was cold isostatically pressed into a cylindrical shape with a diameter of 0 mm under a hydrostatic pressure of 2.0 tonf/cm 2 to obtain a billet with a theoretical density ratio of 90%.
次いで、このビレットを３５０℃にて押出加工して押出
成形体を得たのち、この押出成形体を用いて実施例１と
同じ工程で軸受を製作した。Next, this billet was extruded at 350° C. to obtain an extruded body, and a bearing was manufactured using this extruded body in the same process as in Example 1.
（比較例５）
重量％で、Ｐｂ：ｌＯ，０％、Ｓｎ：１．０％、Ｓｉ
：８．０％、Ｃｕ：０．７５％、残部実質的にＡｎおよ
び不純物よりなるアルミニウム合金粉末に５２０℃×１
２時間の加熱処理を施した後、Ａｌ−１８ｉ量％Ｓｎの
アルミニウム合金粉末と７＝３の重量比で混合し、実施
例３と同組成の混合粉末を得た。(Comparative Example 5) In weight%, Pb: 1O, 0%, Sn: 1.0%, Si
: 8.0%, Cu: 0.75%, and the remainder essentially consists of An and impurities at 520°C x 1
After heat treatment for 2 hours, it was mixed with an aluminum alloy powder of Al-18i content % Sn at a weight ratio of 7=3 to obtain a mixed powder having the same composition as in Example 3.
次に、この混合粉末を直径１００ｍｍ、長さ１００ｍｍ
の円柱形状に２．０ｔｏｎｆ／ｃｍ２の静水圧にて冷間
静水圧成形し、理論密度比９２％のビレットとした。Next, this mixed powder is 100 mm in diameter and 100 mm in length.
It was cold isostatically formed into a cylindrical shape under a hydrostatic pressure of 2.0 tonf/cm2 to obtain a billet with a theoretical density ratio of 92%.
次いで、このビレットを３２０℃にて押出加工して押出
成形体を得たのち、この押出成形体を用いて実施例１と
同じ工程で軸受を製作した。Next, this billet was extruded at 320° C. to obtain an extrusion molded body, and then a bearing was manufactured using the extrusion molded body in the same process as in Example 1.
（比較例６）
実施例３において用いたアルミニウム合金粉末を直径１
００ｍｍ、長さ１００ｍｍ（７）円柱形状に３．２ｔｏ
ｎｆ／ｃｍ２の静水圧にて冷間静水圧成形し、理論密度
比９６％のビレットとした。(Comparative Example 6) The aluminum alloy powder used in Example 3 was
00mm, length 100mm (7) 3.2to in cylindrical shape
Cold isostatic pressing was performed under a hydrostatic pressure of nf/cm2 to form a billet with a theoretical density ratio of 96%.
次に、窒素雰囲気中にて５２０℃の加熱処理を施したと
ころ、Ｐｂ、Ｓｎがビレットの表面にしみ出してしまっ
た。Next, when heat treatment was performed at 520° C. in a nitrogen atmosphere, Pb and Sn seeped out onto the surface of the billet.
（比較例７）
実施例３において用いたアルミニウム合金粉末を直径１
００ｍｍ、長さ１００ｍｍの円柱形状に０．７ｔｏｎｆ
／Ｃｍ２の静水圧にて冷間静水圧成形し、理論密度比７
８％のビレットとした。(Comparative Example 7) The aluminum alloy powder used in Example 3 was
0.7 tonf in a cylindrical shape with a length of 00 mm and a length of 100 mm.
Cold isostatic pressing at a hydrostatic pressure of /Cm2, theoretical density ratio 7
It was made into an 8% billet.
次に、前記ビレットに対して窒素雰囲気中にて５２０’
０Ｘ１２時間の加熱処理を施し、その後３２０″Ｃにて
押出しを行ったが、押出材に耳割れと表面割れが発生し
た。Next, the billet was heated for 520' in a nitrogen atmosphere.
Heat treatment was performed for 0×12 hours, and then extrusion was performed at 320″C, but edge cracks and surface cracks occurred in the extruded material.
第１表に、軸受を製造した実施例１〜３．比較例１〜５
の潤滑成分および硬質成分であるＳｉのＡｎマトリック
スに対する断面積比とＳｉ粒子の大きさを示した。Table 1 shows Examples 1 to 3 in which bearings were manufactured. Comparative examples 1 to 5
The cross-sectional area ratio of Si, which is a lubricating component and hard component, to the An matrix and the size of Si particles are shown.
軸受耐疲労性試験
実施例１〜３および比較例１〜５において製作した軸受
に対して第２表に示すような苛酷な軸受耐疲労性試験を
行った。この試験結果を第１図に示す。Bearing fatigue resistance test The bearings manufactured in Examples 1 to 3 and Comparative Examples 1 to 5 were subjected to a severe bearing fatigue resistance test as shown in Table 2. The test results are shown in FIG.
第１図より明らかなように、本発明による実施例１〜３
の軸受は、比較例１〜５の軸受に比べて優れた耐久性を
有していることがわかる。As is clear from FIG. 1, Examples 1 to 3 according to the present invention
It can be seen that the bearings have superior durability compared to the bearings of Comparative Examples 1 to 5.
第２表 軸受耐疲労性試験条件
摩擦試験
次に、本発明合金の表面性能を調べるために、実施例２
．比較例２および比較例４の押出後の材料から試料を切
り出し、第３表および第２図に示す条件で摩擦試験を行
った。その結果を第３図に示す。Table 2 Bearing fatigue resistance test conditions Friction test Next, in order to investigate the surface performance of the alloy of the present invention, Example 2
．． Samples were cut from the extruded materials of Comparative Examples 2 and 4, and friction tests were conducted under the conditions shown in Table 3 and FIG. 2. The results are shown in FIG.
第３表 摩擦試験条件
第３図に示すように、この発明による軸受台金（実施例
２）は従来法による軸受台金（比較例２．４）よりも優
れた表面性能を有していることが明らかである。Table 3: Friction test conditions As shown in Figure 3, the bearing base according to the present invention (Example 2) has a better surface performance than the bearing base according to the conventional method (Comparative Example 2.4). That is clear.
［発明の効果］
以上説明してきたように、この発明による軸受合金の製
造方法は、ＡＩを主成分とし、潤滑成分としてＰｂ、Ｓ
ｎ、Ｉｎ、Ｓｂ、Ｂｉよりなる群から選ばれた１種以上
の金属をＡｎマトリクスに対する断面積比で０．０４以
上０．０７以下、硬質成分としてＳｉを同じく断面積比
で０．０１以上０．１７以下、強化成分としてＣｕ、Ｃ
ｒ。[Effects of the Invention] As explained above, the method for producing a bearing alloy according to the present invention contains AI as a main component and Pb and S as lubricating components.
One or more metals selected from the group consisting of n, In, Sb, and Bi with a cross-sectional area ratio of 0.04 to 0.07 with respect to the An matrix, and Si as a hard component with a cross-sectional area ratio of 0.01 or more. 0.17 or less, Cu, C as a reinforcing component
r.
Ｍｇ、Ｍｎ、Ｎｉ 、Ｚｎ、Ｆｅよりなる群から選ばれ
た１種以上の金属を０．２〜５．０重量％含み、均一微
細に分散した潤滑成分の大きさが８ｐｍ以下であるアル
ミニウム合金粉末を圧粉成形し、理論密度比８０〜９５
％のビレットとした後３５０〜５５０℃にて加熱処理を
施してＳｉ粒子を６〜１２４ｍに成長させ、その後該ビ
レットを押出比１０以上で押出成形するようにしたこと
を特徴とするものであるから、耐疲労性および表面性能
（潤滑性能）という二律背反特性の両方共が従来にない
高い水準をもつ優れた軽量軸受合金を提供することが可
能であり、とくにこの発明の製造方法により製造された
軸受台金は相手材の材質が鋼の場合のみならず鋳鉄の場
合でも同様に優れた特性を示すことから、極めて広い応
用範囲を有するものであるという非常に優れた効果がも
たらされる。An aluminum alloy containing 0.2 to 5.0% by weight of one or more metals selected from the group consisting of Mg, Mn, Ni, Zn, and Fe, and in which the size of uniformly finely dispersed lubricating components is 8 pm or less The powder is compacted to a theoretical density ratio of 80 to 95.
% billet, heat-treated at 350-550°C to grow Si particles to 6-124 m, and then extrusion-molded the billet at an extrusion ratio of 10 or more. Therefore, it is possible to provide an excellent lightweight bearing alloy that has unprecedentedly high levels of both the antinomic properties of fatigue resistance and surface performance (lubrication performance), and in particular, it is possible to provide an excellent lightweight bearing alloy that has unprecedentedly high levels of both fatigue resistance and surface performance (lubrication performance). The bearing base metal exhibits excellent properties not only when the material of the mating material is steel but also when it is cast iron, so it has an extremely excellent effect that it has an extremely wide range of applications.
第１図は軸受の耐疲労性試験結果を示すグラフ、第２図
は摩擦試験の際の負荷パターンを示す説明図、第３図は
摩擦試験結果を示すグラフである。
特許出願人 日産自動車株式会社
同出願人 工ヌデーシー株式会社代理人弁理士
小 塩 豊
第１図
（士も×）１痔
８ 目 ； 藁
ｃ５ ｅｓ ｃ＞ ６今ｊし
避夕FIG. 1 is a graph showing the fatigue resistance test results of the bearing, FIG. 2 is an explanatory diagram showing the load pattern during the friction test, and FIG. 3 is a graph showing the friction test results. Patent applicant: Nissan Motor Co., Ltd. Patent attorney: NDC Co., Ltd.
Yutaka Ko Shio Figure 1 (Shimo ×) 1 Hemorrhoid 8th; Straw c5 es c> 6 Now and then taking shelter
Claims (1)
１種以上の金属をＡｌマトリックスに対する断面積比で
０．０４以上０．０７以下、硬質成分としてＳｉを同じ
く断面積比で０．０１以上０．１７以下、強化成分とし
てＣｕ、Ｃｒ、Ｍｇ、Ｍｎ、Ｎｉ、Ｚｎ、Ｆｅよりなる
群から選ばれた１種以上の金属を０．２〜５．０重量％
含み、均一微細に分散した潤滑成分の大きさが８μｍ以
下であるアルミニウム合金粉末を圧粉成形し、理論密度
比８０〜９５％のビレットとした後３５０〜５５０℃に
て加熱処理を施してＳｉ粒子を６〜１２μｍに成長させ
、その後該ビレットを押出比１０以上で押出成形するこ
とを特徴とするアルミニウム系軸受合金の製造方法。(1) Al is the main component, and one or more metals selected from the group consisting of Pb, Sn, In, Sb, and Bi are used as a lubricating component, with a cross-sectional area ratio of 0.04 to 0.07 to the Al matrix; The hard component is Si with a cross-sectional area ratio of 0.01 or more and 0.17 or less, and the reinforcing component is 0.01 or more of one or more metals selected from the group consisting of Cu, Cr, Mg, Mn, Ni, Zn, and Fe. 2-5.0% by weight
Aluminum alloy powder containing lubricating components uniformly and finely dispersed with a size of 8 μm or less is compacted to form a billet with a theoretical density ratio of 80 to 95%, and then heat treated at 350 to 550°C to form a Si A method for producing an aluminum-based bearing alloy, which comprises growing particles to a size of 6 to 12 μm, and then extruding the billet at an extrusion ratio of 10 or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7800286A JPS62235438A (en) | 1986-04-03 | 1986-04-03 | Manufacture of bearing alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7800286A JPS62235438A (en) | 1986-04-03 | 1986-04-03 | Manufacture of bearing alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62235438A true JPS62235438A (en) | 1987-10-15 |
Family
ID=13649590
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7800286A Pending JPS62235438A (en) | 1986-04-03 | 1986-04-03 | Manufacture of bearing alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62235438A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5902943A (en) * | 1995-05-02 | 1999-05-11 | The University Of Queensland | Aluminium alloy powder blends and sintered aluminium alloys |
-
1986
- 1986-04-03 JP JP7800286A patent/JPS62235438A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5902943A (en) * | 1995-05-02 | 1999-05-11 | The University Of Queensland | Aluminium alloy powder blends and sintered aluminium alloys |
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