JPH01215901A - Manufacture of sintered aluminum alloy - Google Patents
Manufacture of sintered aluminum alloyInfo
- Publication number
- JPH01215901A JPH01215901A JP63041719A JP4171988A JPH01215901A JP H01215901 A JPH01215901 A JP H01215901A JP 63041719 A JP63041719 A JP 63041719A JP 4171988 A JP4171988 A JP 4171988A JP H01215901 A JPH01215901 A JP H01215901A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- powder
- oxide film
- alloy powder
- aluminum 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.)
- Pending
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 14
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 239000000843 powder Substances 0.000 claims abstract description 45
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 33
- 239000000956 alloy Substances 0.000 claims abstract description 33
- 238000000034 method Methods 0.000 claims abstract description 24
- 238000001816 cooling Methods 0.000 claims abstract description 6
- 230000001590 oxidative effect Effects 0.000 claims abstract description 5
- 239000011261 inert gas Substances 0.000 claims abstract description 4
- 238000005482 strain hardening Methods 0.000 claims abstract description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 10
- 239000001301 oxygen Substances 0.000 claims description 10
- 229910052760 oxygen Inorganic materials 0.000 claims description 10
- 238000000889 atomisation Methods 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 abstract description 4
- 238000005245 sintering Methods 0.000 abstract description 4
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 229910018084 Al-Fe Inorganic materials 0.000 abstract 2
- 229910021364 Al-Si alloy Inorganic materials 0.000 abstract 2
- 229910018192 Al—Fe Inorganic materials 0.000 abstract 2
- 229910052804 chromium Inorganic materials 0.000 abstract 1
- 229910052802 copper Inorganic materials 0.000 abstract 1
- 229910052749 magnesium Inorganic materials 0.000 abstract 1
- 239000002184 metal Substances 0.000 abstract 1
- 229910052751 metal Inorganic materials 0.000 abstract 1
- 229910052750 molybdenum Inorganic materials 0.000 abstract 1
- 230000000452 restraining effect Effects 0.000 abstract 1
- 229910000714 At alloy Inorganic materials 0.000 description 15
- 238000001125 extrusion Methods 0.000 description 10
- 238000005242 forging Methods 0.000 description 10
- 238000007796 conventional method Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000000465 moulding Methods 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000001112 coagulating effect Effects 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000009689 gas atomisation Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000010301 surface-oxidation reaction Methods 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、焼結アルミニウム（１）合金の製造方法に関
する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field of Application] The present invention relates to a method for producing a sintered aluminum (1) alloy.
焼結Ａ４合金には耐摩耗性に優れたＡ４−３ｉ系合金や
耐熱性に富むＡ４−Ｆｅ系合金などがあり、機械部品や
家電製品などに軽量な構造材として使用されている。Sintered A4 alloys include A4-3i series alloys with excellent wear resistance and A4-Fe series alloys with high heat resistance, and are used as lightweight structural materials for mechanical parts and home appliances.
これらの焼結Ａｔ合金は、Ａｔ合金溶湯を高圧の空気又
は不活性ガスで噴霧化すると同時に急冷するアトマイズ
法により粉末とし、このＡｔ合金粉末を押出法などによ
り成形固化して製造される。These sintered At alloys are manufactured by turning a molten At alloy into powder by an atomization method in which the molten At alloy is atomized with high-pressure air or an inert gas and simultaneously rapidly cooled, and by molding and solidifying the At alloy powder by an extrusion method or the like.
又、粉末化する方法として超急冷ディスクアトマイズ法
などが、成形固化する方法としては粉末鍛造法や押出し
た後で鍛造加工する方法なども研究されている。In addition, research is being conducted on methods for powdering, such as ultra-quenched disk atomization, and methods for forming and solidifying, such as powder forging and forging after extrusion.
更に最近では、熱間押出法により高強度の焼結Ａｔ合金
が開発され、実用化されつつある。これらの技術は特開
昭５９ ＝ １３０４０号、特開昭５９−１３０４１号
、特開昭５５−９７４４７号などに開示されている。Furthermore, recently, high-strength sintered At alloys have been developed by hot extrusion and are being put into practical use. These techniques are disclosed in JP-A-59-13040, JP-A-59-13041, JP-A-55-97447, and the like.
これらの焼結Ａｔ合金の製造に用いるＡ７合金粉末は酸
化されやすく、表面に安定なＡｔ○ の酸化被膜が形成
される。特に安価で一般的に使用されているアトマイズ
法で生成したＡ１合金粉末は厚い酸化被膜が形成きれや
すい。この表面酸化被膜のため焼結性が悪くなり、充分
な強度や靭性が得られない欠点があった。The A7 alloy powder used to produce these sintered At alloys is easily oxidized, and a stable At◯ oxide film is formed on the surface. In particular, A1 alloy powder produced by the atomization method, which is inexpensive and commonly used, tends to form a thick oxide film. This surface oxidation film deteriorates sinterability and has the disadvantage that sufficient strength and toughness cannot be obtained.
この表面酸化被膜を破壊してＡｔ合金粉末同志を強固に
結合させるために有効な手段とされているのが押出法で
あり、この方法では粉末が剪断変形され、表面酸化被膜
は機械的に破壊される。従って、押出法によれば比較的
高強度の焼結Ａ４合金が得られるが充分な靭性が得られ
ているとは云い難く、又押出法ではニアネットシエイブ
成形が難しいので高強度な難加工材であるほど切削や鍛
造などの後工程がコスト高になる問題が存在する。The extrusion method is considered to be an effective means to destroy this surface oxide film and firmly bond the At alloy powders together. In this method, the powder is sheared and deformed, and the surface oxide film is mechanically destroyed. be done. Therefore, although it is possible to obtain a sintered A4 alloy with relatively high strength using the extrusion method, it is difficult to say that sufficient toughness is obtained, and because near-net-shape forming is difficult with the extrusion method, it is difficult to form high-strength, difficult-to-process materials. There is a problem that the more expensive the post-processes such as cutting and forging become.
ニアネットシエイブ成形のために最も好適な方法は粉末
鍛造法であるが、この方法では表面酸化被膜を充分に破
壊できないため、押出法に比較して強度及び靭性に劣っ
ている。The most suitable method for near net sieve molding is powder forging, but since this method cannot sufficiently destroy the surface oxide film, it is inferior in strength and toughness compared to extrusion.
本発明は、Ａｔ合金粉末の表面酸化被膜を低温で短時間
に破壊して、押出法はもちろんニアネソトシエイプ成形
に有効な粉末鍛造法によっても、優れた強度と靭性を有
する焼結Ａ１合金を製造する方法を提供することを目的
としている。The present invention has developed a sintered A1 alloy that has excellent strength and toughness by destroying the surface oxide film of At alloy powder at low temperatures in a short time, and by not only extrusion method but also powder forging method, which is effective for near-sotoshape forming. The purpose is to provide a method for manufacturing.
本発明は上記の目的を達成するために、焼結アルミニウ
ム合金の製造方法として、アルミニウム合金溶湯をアト
マイズ法により１０３ｃ／秒以上の冷却速度で凝固させ
、得られた合金粉末をボールミル又はアトライタにより
非酸化性雰囲気で酸素ピンクアンプ量を５００ ｐｐｍ
以下に抑制しつつ３０分間以内て冷間加工した後、この
合金粉末を成形固化することを特徴とする手段を採るも
のである。In order to achieve the above object, the present invention is a method for producing a sintered aluminum alloy, in which molten aluminum alloy is solidified by an atomization method at a cooling rate of 103 c/sec or more, and the obtained alloy powder is non-condensed by a ball mill or an attritor. Oxygen pink amplifier amount is 500 ppm in oxidizing atmosphere
This method is characterized in that the alloy powder is compacted and solidified after being cold-worked within 30 minutes while controlling the following:
粉末冶金法では、従来がら粉末の混合と粉砕、合金化な
どにボールミルやアトライタを使用してきたが、いずれ
も数時間から数百時間の長時間処理であり、特にＡ４や
Ａ１合金では容器内壁面に凝集付着する欠点がある為こ
れらの粉末の処理には殆ど使用されていないが、使用さ
れるとしても、それらは湿式法に依っている。Ａ４合金
粉末と他の粉末などとの単なる混合は■型ミキサー等の
他の簡単な装置を利用して行なわれている。In the powder metallurgy method, ball mills and attritors have traditionally been used for mixing, crushing, and alloying powders, but these processes require long processing times ranging from several hours to hundreds of hours. Because of the disadvantage of agglomeration and adhesion, these powders are rarely used for processing, but when they are used, they rely on wet methods. Mere mixing of A4 alloy powder and other powders is carried out using other simple devices such as a type mixer.
これに対して、本発明ではＡｔ合金粉末の表面酸化被膜
の機械的破壊にボールミル又はアトライタを用いるので
あり、依ってＡｔ合金粉末一種類のみを乾式で処理し、
処理時間は３０分以内と極めて短時間である。In contrast, in the present invention, a ball mill or an attritor is used to mechanically destroy the surface oxide film of the At alloy powder, and therefore only one type of At alloy powder is dry-processed.
The processing time is extremely short, within 30 minutes.
全てのＡ１合金粉末にこの処理を適用でさ、例えばＡ／
−８ｉ合金やこれにＦｅ、 Ｎｉ、 Ｏｕ、 Ｍｇ等を
添加した合金、及びＡ４−Ｆｅ合金やこれにＮｉ、Ｏｒ
。This treatment can be applied to all A1 alloy powders, for example A/
-8i alloy and alloys to which Fe, Ni, Ou, Mg, etc. are added, and A4-Fe alloys and alloys to which Ni, Or, etc. are added.
.
Ｍｏ等を添加した合金に適用できる。It can be applied to alloys containing Mo or the like.
本発明方法で用いるＡ１合金粉末は上記の如く組成的に
は制限はないが、アトマイズ法により冷却速度１０Ｃ／
秒以上で急冷凝固させた粉末を使用する。これより遅い
冷却速度で形成した粉末を用いたのでは、充分に微細な
組織の焼結Ａｔ合金が得られないからである。The A1 alloy powder used in the method of the present invention is not limited in terms of composition as described above, but it can be used at a cooling rate of 10C/
Use powder that has been rapidly solidified in seconds or more. This is because if a powder formed at a cooling rate slower than this is used, a sintered At alloy with a sufficiently fine structure cannot be obtained.
かかるＡ１合金粉末は、焼結前にボールミル又はアトラ
イタでの冷間加工処理により、表面酸化被膜が極めて短
時間で、通常は３０分間以内で破壊されて新しい合金面
が現われる。−船釣には３０分を超えて処理しても意味
がないばかりか、Ａｔ合金が容器内壁に凝集付着しやす
くなる。Before sintering, such A1 alloy powder undergoes cold working treatment in a ball mill or attritor to destroy the surface oxide film in a very short time, usually within 30 minutes, and a new alloy surface appears. - For boat fishing, there is no point in treating for more than 30 minutes, and the At alloy tends to coagulate and adhere to the inner wall of the container.
この表面酸化被膜の破壊処理中には新たな酸化を防ぐ必
要があるので、非酸化性雰囲気で酸素ピックアップ量（
処理前後の粉末の酸素量の差）を５０（ｌ Ｔ）１）ｍ
以下に抑制する。酸素ピックアップ量が５００ Ｐｐｍ
を超えると新たな酸化被膜の形成が大きくなり、表面酸
化被膜を破壊する効果がなくなるからである。非酸化性
雰囲気としてはＡｒ等の不活性ガス雰囲気が好ましく、
その酸素濃度を１１０００ｐｐ以下にすれば酸素ピック
アップ量をほぼ５００ｐｐｍ以下に制御できる。During the destruction process of this surface oxide film, it is necessary to prevent new oxidation, so the amount of oxygen picked up (
The difference in the amount of oxygen in the powder before and after treatment is 50 (l T) 1) m
Suppress below. Oxygen pickup amount is 500 Ppm
This is because if the amount exceeds 100%, the formation of a new oxide film becomes large and the effect of destroying the surface oxide film is lost. The non-oxidizing atmosphere is preferably an inert gas atmosphere such as Ar,
By setting the oxygen concentration to 11,000 ppm or less, the amount of oxygen picked up can be controlled to approximately 500 ppm or less.
又、ボールミルまたはアトライタの容器内壁の温度を６
０ Ｃ以下に保持することによって、Ａ１合金の容器内
壁への凝集付着を完全に防止することができ、従ってよ
り簡便な乾式アトライタの使用が可能になる。Also, the temperature of the inner wall of the ball mill or attritor container should be set to 6
By maintaining the temperature at 0 C or lower, it is possible to completely prevent the A1 alloy from coagulating and adhering to the inner wall of the container, and therefore a simpler dry attritor can be used.
このようにボールミル又はアトライタにより表面酸化被
膜を破壊したＡ１合金粉末は新しい合金表面が現われて
いるので焼結性が極めて良好である。The A1 alloy powder whose surface oxide film has been destroyed by the ball mill or attritor has extremely good sinterability because a new alloy surface appears.
従って、このＡ７！合金粉末は熱間押出ばかりでなくホ
ットプレス、熱間静水圧プレス、フンフオーム等の全て
の方法によって、即ちニアネットシエイプ成形の利点が
ありながら従来は適用困難であった粉末鍛造によっても
、充分優れた強度及び靭性を有する焼結体に成形固化さ
せることができる。Therefore, this A7! Alloy powder can be processed not only by hot extrusion, but also by all methods such as hot pressing, hot isostatic pressing, and hunforming, in other words, by powder forging, which has the advantage of near net shape forming but was difficult to apply in the past. It can be molded and solidified into a sintered body with high strength and toughness.
エアアトマイズ法（０＝０．２ｗｔ％）とＮ ガスアト
マイズ法（０＝０．０８ｗｔ％）とにより、Ａｔ−２０
Ｓｉ−５Ｆｅ一２Ｎ１の組成（重量％）のＡｔ合金粉末
を夫々形成した。これらのＡ４合金粉末を、乾式アトラ
イタを用いて酸素濃度５０ ｐｐｍのＡｒガス雰囲気中
で容器内壁温度を３０Ｃに保持しながら、５分間冷間に
て処理した。得られた処理Ａｔ合金粉末の酸素ピックア
ップ量は１１）ｐｍ以下であった。この処理Ａ１合金粉
末を熱間押出法（４５０Ｕｓ押出比１ ： ２０）及び
粉末鍛造法（４５０Ｃｚ ３ ｔｏｎ膚）で夫々成形固
化した。By air atomization method (0=0.2wt%) and N gas atomization method (0=0.08wt%), At-20
At alloy powders having a composition (wt%) of Si-5Fe-2N1 were respectively formed. These A4 alloy powders were cold treated for 5 minutes using a dry attritor in an Ar gas atmosphere with an oxygen concentration of 50 ppm while maintaining the inner wall temperature of the container at 30C. The oxygen pickup amount of the obtained treated At alloy powder was 11) pm or less. This treated A1 alloy powder was molded and solidified by hot extrusion (450Us extrusion ratio 1:20) and powder forging (450Cz 3 ton), respectively.
比較の為に、乾式アトライターでの処理を行なわない以
外は上記と同様にして焼結Ａ４合金を製造した。For comparison, a sintered A4 alloy was produced in the same manner as above except that the dry attritor treatment was not performed.
得られた各試料について、室温での引張強度と室温での
破断伸びを測定した。結果を下記表に示した。For each sample obtained, the tensile strength at room temperature and the elongation at break at room temperature were measured. The results are shown in the table below.
未処理Ａ１合金粉末を用いる従来方法では、押出法に比
べて粉末鍛造法では引張強度及び破断伸び共著しく劣っ
たものしか得られなかった。一方、本発明においては、
粉末鍛造法によっても非常に優れた引張強度及び破断伸
びを達成できることが判る。又、本発明では押出法でも
従来より優れた特性が得られ、特に破断伸びは従来より
も飛躍的に改善されている。In the conventional method using untreated A1 alloy powder, the powder forging method could only provide significantly inferior tensile strength and elongation at break compared to the extrusion method. On the other hand, in the present invention,
It can be seen that very excellent tensile strength and elongation at break can also be achieved by the powder forging method. Furthermore, in the present invention, properties superior to those of the conventional method can be obtained even by extrusion, and in particular, the elongation at break is dramatically improved compared to the conventional method.
本発明によれば、Ａ１合金粉末の焼結性を改善すること
ができ、強度ならびに靭性に優れた焼結Ａｔ合金を製造
することができる。特に、従来は焼結が不可能であった
粉末鍛造法によっても充分固化することが可能になり、
完成品に近い形状のニアネットシエイブ成形ができるの
で、コスト低減にも寄与できる。According to the present invention, the sinterability of A1 alloy powder can be improved, and a sintered At alloy with excellent strength and toughness can be manufactured. In particular, it has become possible to solidify sufficiently even with the powder forging method, which was previously impossible to sinter.
Near-net-shave molding can be performed in a shape close to that of the finished product, which can also contribute to cost reduction.
出願人 住友電気工業株盛会社Applicant: Sumitomo Electric Industries, Ltd.
Claims (1)
＾３Ｃ／秒以上の冷却速度で凝固させ、得られた合金粉
末をボールミル又はアトライタにより非酸化性雰囲気で
酸素ピツクアツプ量を５００ｐｐｍ以下に抑制しつつ３
０分間以内で冷間加工した後、この合金粉末を成形固化
することを特徴とする焼結アルミニウム合金の製造方法
。（２）非酸化性雰囲気が酸素濃度１０００ｐｐｍ以下
の不活性ガス雰囲気である、請求項（１）記載の焼結ア
ルミニウム合金の製造方法。 （３）ボールミル又はアトライタの容器内壁の温度を６
０℃以下に保持する、請求項（１）記載の焼結アルミニ
ウム合金の製造方法。[Claims] (1) Molten aluminum alloy is heated to 10% by atomization method.
Solidify the resulting alloy powder at a cooling rate of 3 C/sec or more, and process the resulting alloy powder in a non-oxidizing atmosphere using a ball mill or attritor while suppressing the amount of oxygen pick-up to 500 ppm or less.
1. A method for producing a sintered aluminum alloy, which comprises cold working within 0 minutes and then compacting and solidifying the alloy powder. (2) The method for producing a sintered aluminum alloy according to claim (1), wherein the non-oxidizing atmosphere is an inert gas atmosphere with an oxygen concentration of 1000 ppm or less. (3) Set the temperature of the inner wall of the ball mill or attritor container to 6
The method for producing a sintered aluminum alloy according to claim (1), wherein the temperature is maintained at 0°C or lower.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63041719A JPH01215901A (en) | 1988-02-24 | 1988-02-24 | Manufacture of sintered aluminum alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63041719A JPH01215901A (en) | 1988-02-24 | 1988-02-24 | Manufacture of sintered aluminum alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01215901A true JPH01215901A (en) | 1989-08-29 |
Family
ID=12616233
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63041719A Pending JPH01215901A (en) | 1988-02-24 | 1988-02-24 | Manufacture of sintered aluminum alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01215901A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110079689A (en) * | 2019-05-06 | 2019-08-02 | 西南交通大学 | A kind of in-situ Al-base composition and preparation method thereof |
-
1988
- 1988-02-24 JP JP63041719A patent/JPH01215901A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110079689A (en) * | 2019-05-06 | 2019-08-02 | 西南交通大学 | A kind of in-situ Al-base composition and preparation method thereof |
| CN110079689B (en) * | 2019-05-06 | 2021-08-03 | 西南交通大学 | In-situ aluminum-based composite material and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US3950166A (en) | Process for producing a sintered article of a titanium alloy | |
| WO2007111342A1 (en) | High-strength high-toughness magnesium alloy and method for producing the same | |
| JPS63274736A (en) | Niobium alloy | |
| JPH03122205A (en) | Manufacture of ti powder | |
| JPH02197535A (en) | Manufacture of intermetallic compound | |
| JPH0225961B2 (en) | ||
| JPH01215901A (en) | Manufacture of sintered aluminum alloy | |
| JPH06330263A (en) | Production of high toughness al-si series alloy | |
| JP3113639B2 (en) | Manufacturing method of alloy powder | |
| JPH05171321A (en) | Titanium alloy for high density powder sintering | |
| JP2551285B2 (en) | Titanium alloy for high density powder sintering | |
| JP2588889B2 (en) | Forming method of Ti-Al based intermetallic compound member | |
| JPH02259029A (en) | Manufacture of aluminide | |
| JPH0643628B2 (en) | Method for manufacturing aluminum alloy member | |
| JPS6347343A (en) | Powder metallurgical production of processed product made of heat resistant aluminum alloy | |
| JPH0257121B2 (en) | ||
| JPS62151533A (en) | Production of age hardening type copper strip | |
| JP2917999B2 (en) | Method for producing high-strength aluminum alloy compact | |
| JP3113893B2 (en) | Manufacturing method of plastic working material and manufacturing method of plastic working material | |
| JPS62188735A (en) | Manufacture of tini alloy wire or plate | |
| JPS61502615A (en) | Titanium, hafnium and zirconium group 4B transition metal group passivated metal powder for powder metallurgy and method for producing the same | |
| JPH0192328A (en) | Manufacture of aluminum powder metallurgical alloy | |
| JPH04337001A (en) | Low-alloy steel powder for powder metallurgy and its sintered molding and tempered molding | |
| JPH055139A (en) | Production of silver or silver-copper alloy-metal oxide composite material | |
| JP4264587B2 (en) | Ultrafine-grained steel and method for producing the same |