JP2787466B2 - Forming method of aluminum alloy for large diameter products - Google Patents
Forming method of aluminum alloy for large diameter productsInfo
- Publication number
- JP2787466B2 JP2787466B2 JP1091587A JP9158789A JP2787466B2 JP 2787466 B2 JP2787466 B2 JP 2787466B2 JP 1091587 A JP1091587 A JP 1091587A JP 9158789 A JP9158789 A JP 9158789A JP 2787466 B2 JP2787466 B2 JP 2787466B2
- Authority
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- Japan
- Prior art keywords
- weight
- aluminum alloy
- diameter
- alloy
- extrusion ratio
- 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
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Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0408—Light metal alloys
- C22C1/0416—Aluminium-based alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Forging (AREA)
- Powder Metallurgy (AREA)
Description
【発明の詳細な説明】 産業上の利用分野 本発明は、アルミニウム合金の成形方法に関する。Description: TECHNICAL FIELD The present invention relates to a method for forming an aluminum alloy.
従来技術とその問題点 粉末治金法（以下PM法という）により製造されたアル
ミニウム合金（以下Al合金という）は、インゴット治金
法（以下IM法という）により製造されたAl合金に比し
て、より多くの添加元素をより均一にAlマトリクス中に
分散させることが出来るので、IM法では得られなかった
優れた耐熱性、耐摩耗性などを具備している。Conventional technology and its problems Aluminum alloys (hereinafter referred to as Al alloys) manufactured by powder metallurgy (hereinafter referred to as PM method) are compared with Al alloys manufactured by ingot metallurgy method (hereinafter referred to as IM method). Since more additive elements can be more uniformly dispersed in the Al matrix, they have excellent heat resistance, abrasion resistance, etc., which cannot be obtained by the IM method.
PM法によるAl製品の製造に際しては、通常、急冷凝固
させて製造した粉末、フレークまたはリボン状の材料を
使用して、先ず熱間押出し成形を行い、次いで得られた
成形ビレットを使用して、各種成形製品を得ている。こ
の方法によれば、熱間押出し時の剪断力によって、個々
の粉末、フレークまたはリボンの表面の酸化皮膜が破ら
れ、露出したAl面同志で強固な結合が得られる。PM法の
カテゴリーに属する粉末圧延法および粉末鍛造法によっ
ても、酸化皮膜の破壊は、生じるが、剪断力が比較的小
さく、個々の粉末の変形量が押出しにおける程大きくな
いため、結合は、押出しによる場合程には、強固とはな
らない。In the production of Al products by the PM method, usually, powder, flakes or ribbon-like materials produced by rapid solidification are used, first hot-extrusion molding is performed, and then using the obtained molded billet, Various molded products have been obtained. According to this method, the oxide film on the surface of each powder, flake or ribbon is broken by the shearing force at the time of hot extrusion, and a strong bond is obtained between exposed Al surfaces. The powder rolling and powder forging methods, which belong to the PM method category, also cause the oxide film to break, but the shearing force is relatively small and the deformation of each powder is not as large as in the extrusion. It is not as strong as it is.
上記の押出し法によるPM法において十分に強固な結合
を得るためには、通常押出し比を10以上、好ましくは20
以上にする必要がある。また、PM法で使用するAl合金
は、添加元素が多い為、IM法による場合に比して、押出
し力が著しく高くなる傾向にある。従って、IM法による
材料よりも高温強度（例えば、300℃における強度）、
に優れているPM法による材料も、製造上の制約から、大
径の製品に適用することは極めて困難であった。In order to obtain a sufficiently strong bond in the PM method by the above extrusion method, the extrusion ratio is usually 10 or more, preferably 20
It is necessary to do above. In addition, since the Al alloy used in the PM method has many additional elements, the extrusion force tends to be significantly higher than in the case of the IM method. Therefore, high-temperature strength (for example, strength at 300 ℃) than the material by IM method,
It has been extremely difficult to apply a material obtained by the PM method, which has excellent performance, to a large-diameter product due to manufacturing restrictions.
問題点を解決するための手段 本発明者は、上記の如き技術の問題点に鑑みて鋭意研
究を進めた結果、特定組成のAl合金粉末を使用する場合
には、10以下という比較的低い押出し比においても、さ
らには２〜５という極めて低い押出し比においても、十
分に強固な成形体が得られること、およびこの様にして
得た押出し材を拡径方向に熱間鍛造することにより、従
来技術では製造困難であるとされていた直径150mm以上
の大径の成形製品が得られることを見出した。さらに、
金型を使用して型鍛造を行なう場合には、直径200mm以
上の大径製品も得られることを見出した。Means for Solving the Problems The present inventor has conducted intensive studies in view of the problems of the above technology, and as a result, when using an Al alloy powder having a specific composition, a relatively low extrusion rate of 10 or less was used. Even at an extremely low extrusion ratio of 2 to 5 even at a very low extrusion ratio, a sufficiently strong molded body can be obtained, and the extruded material thus obtained is hot forged in the diameter expanding direction. It has been found that large-diameter molded products with a diameter of 150 mm or more, which have been considered difficult to produce with technology, can be obtained. further,
It has been found that when die forging is performed using a mold, a large-diameter product having a diameter of 200 mm or more can be obtained.
すなわち、本発明は、下記の方法を提供するものであ
る。That is, the present invention provides the following method.
（イ）Si5〜30重量％、 （ロ）Cu、Fe、Cr、Ｖ及びNiの少なくとも１種0.5〜1
0重量％ （ハ）Mo及びZrの少なくとも１種0.5〜10重量％及び （ニ）残余が実質的にAl （但し、（ロ）と（ハ）との合計量は30重量％を超えな
い）からなる合金粉末を温度350〜500℃において押出し
比２〜５で押出し成形することを特徴とする大径の製品
用アルミニウム合金の成形方法。(B) at least one of Cu, Fe, Cr, V and Ni 0.5 to 1%
0% by weight (c) 0.5 to 10% by weight of at least one of Mo and Zr and (d) the balance is substantially Al (however, the total amount of (b) and (c) does not exceed 30% by weight) A method for molding a large-diameter aluminum alloy for a product, comprising extruding an alloy powder comprising at an extrusion ratio of 2 to 5 at a temperature of 350 to 500 ° C.
上記第１項で得られた成形体をさらに温度400〜530
℃において熱間型鍛造することを特徴とする大径の製品
用アルミニウム合金の成形方法。The molded article obtained in the above item 1 is further subjected to a temperature of 400 to 530.
A method for forming a large-diameter aluminum alloy for a product, comprising hot-die forging at a temperature of ° C.
上記第１項で得られた成形体をさらに温度400〜530
℃において拡径方向に30〜80％の熱間据込み鍛造するこ
とを特徴とする大径の製品用アルミニウム合金の成形方
法。The molded article obtained in the above item 1 is further subjected to a temperature of 400 to 530.
A method for forming a large-diameter product aluminum alloy, which comprises performing hot upsetting of 30 to 80% in the diameter-expanding direction at ℃.
合金粉末の組成が、Si5〜30重量％、Fe3〜５重量
％、Ni3〜５重量％、Mo0.5〜2.5重量％及びZr0.5〜2.5
重量％を含有し、残部が実質的にAlからなる上記第１項
に記載の大径の製品用アルミニウム合金の成形方法。The composition of the alloy powder is Si5-30% by weight, Fe3-5% by weight, Ni3-5% by weight, Mo0.5-2.5% by weight and Zr0.5-2.5%
2. The method for forming a large-diameter aluminum alloy for a product according to the above item 1, wherein the aluminum alloy contains 1% by weight and the balance substantially consists of Al.
本発明において使用するAl合金粉末は、（イ）Si5〜3
0重量％、（ロ）Cu、Fe、Cr、Ｖ及びNiの少なくとも１
種0.5〜10重量％、（ハ）Mo及びZrの少なくとも１種0.5
〜10重量％及び（ニ）残余が実質的にAl（但し、（ロ）
と（ハ）との合計量は30重量％を超えない）からなるこ
とを必須とする。この組成範囲内のAl合金は、低い押出
し比であっても個々の粉末同志が十分強固に結合するこ
とが可能で、実施例に示す様に、押出し比にかかわらず
ほぼ一定の強度と伸びを示す。これに対し、この様な特
定の組成以外のAl合金粉末を使用する場合には、温度40
0〜500℃において10以下、或いは８以下、さらに２〜５
という極めて低い押出し比で強固な結合を得ることが不
可能となる。The Al alloy powder used in the present invention is (A) Si5-3
0% by weight, (b) at least one of Cu, Fe, Cr, V and Ni
0.5 to 10% by weight of seed, (c) at least one of Mo and Zr 0.5
~ 10% by weight and (d) the balance is substantially Al (however, (b)
And (c) do not exceed 30% by weight). The Al alloy within this composition range can bond the individual powders sufficiently firmly even at a low extrusion ratio, and as shown in the examples, has almost constant strength and elongation regardless of the extrusion ratio. Show. On the other hand, when using an Al alloy powder other than such a specific composition, the
10 or less at 0 to 500 ° C, or 8 or less, and 2 to 5
It is impossible to obtain a strong bond at an extremely low extrusion ratio.
より具体的には、Si量が５重量％未満の場合には、結
合力が不十分であり、一方、30重量％を超えると、初晶
Siの体積が増え過ぎて、得られる成形体の靭性が低下す
る。Siの量は、10〜14重量％とすることがより好まし
い。More specifically, when the amount of Si is less than 5% by weight, the bonding force is insufficient.
Since the volume of Si is too large, the toughness of the obtained molded body is reduced. More preferably, the amount of Si is 10 to 14% by weight.
また、Cu、Fe、Cr、Ｖ及びNiの少なくとも１種、ある
いはMo及びZrの少なくとも１種が0.5重量％未満の場合
には、耐熱性及び強度に劣り、一方、10重量％を上回る
場合には、粗大な金属間化合物が生成されるために、靭
性が低下する。これらの金属の合計量が、30重量％を超
える場合にも、靭性の低下は、まぬがれ得ない。When at least one of Cu, Fe, Cr, V and Ni, or at least one of Mo and Zr is less than 0.5% by weight, heat resistance and strength are poor. On the other hand, when it exceeds 10% by weight, As a result, a coarse intermetallic compound is generated, so that the toughness is reduced. Even when the total amount of these metals exceeds 30% by weight, the decrease in toughness cannot be overwhelmed.
本発明で使用するAl合金粉末は、Fe3〜５重量％、Ni3
〜５重量％、Mo0.5〜2.5重量％およびZr0.5〜2.5重量％
を含有し、MoとZrとの合計量が２〜５重量％の範囲にあ
ることがより好ましい。この様な組成においては、靭性
を低下させることなく、優れた高温強度（300℃程度ま
で）および限界据込率が得られる。The Al alloy powder used in the present invention is Fe3 to 5% by weight, Ni3
~ 5 wt%, Mo0.5 ~ 2.5 wt% and Zr0.5 ~ 2.5 wt%
, And the total amount of Mo and Zr is more preferably in the range of 2 to 5% by weight. In such a composition, excellent high-temperature strength (up to about 300 ° C.) and critical upsetting rate can be obtained without reducing toughness.
本発明のAl粉末合金から得られた押出し成形体は、押
出し比に関係なく60〜70％程度の限界据込率を有するの
に対し、本発明の組成範囲外のAl合金を使用する場合に
は、２〜５という低い押出し比で得たビレットは、十分
な鍛造成形性を示さないので、温度400〜530℃で拡径方
向に30〜80％の熱間据込み鍛造することが出来ない。The extruded body obtained from the Al powder alloy of the present invention has a critical upsetting ratio of about 60 to 70% regardless of the extrusion ratio, whereas when an Al alloy outside the composition range of the present invention is used. The billet obtained at an extrusion ratio as low as 2 to 5 does not exhibit sufficient forgeability, so that hot upsetting of 30 to 80% in the diameter increasing direction at a temperature of 400 to 530 ° C. cannot be performed. .
また、本発明のAl粉末合金から得られた押出成形体か
らは、添付した第１図に示すような形状に熱間型鍛造を
行なうことにより、最大径部では押出材の1.5倍以上の
直径を有する鍛造品が得られる。この様な鍛造加工を行
なう場合には、最大径部が、最も大きな加工を受けるこ
とになるので、気孔などの内部欠陥が無く、理論密度が
実質的に100％にも達し且つ強度に極めて優れた製品が
得られる。この様にして得られた鍛造品を回転機構部品
として使用する場合には、第１図において、矢印で示す
方向（最大遠心力のかかる方向）と押出成形時の材料粉
末のフローの方向（強度の最も高い方向）とが一致する
ので、極めて有利である。Also, from the extruded body obtained from the Al powder alloy of the present invention, a hot die forging into a shape as shown in FIG. Is obtained. When such a forging process is performed, the largest diameter portion is subjected to the largest process, so there are no internal defects such as pores, the theoretical density substantially reaches 100%, and the strength is extremely excellent. Product is obtained. When the forged product obtained in this manner is used as a rotating mechanism component, the direction indicated by the arrow in FIG. 1 (the direction in which the maximum centrifugal force is applied) and the direction of the flow of the material powder during extrusion (strength). Is the highest direction), which is extremely advantageous.
発明の効果 特定組成のAl合金粉末を使用する本発明によれば、10
以下という低い押出し比で強固な結合を得ることが出来
る。According to the present invention using an Al alloy powder having a specific composition,
A strong bond can be obtained with a low extrusion ratio of:
また、得られた押出し成形体を熱間据込み鍛造する場
合には、大径の製品、例えば、高温に曝されて高速回転
する各種の大型ローターなどを得ることが出来る。When the obtained extruded product is hot upset-forged, a product having a large diameter, for example, various large-sized rotors that rotate at high speed when exposed to high temperature can be obtained.
実 施 例 以下に実施例を示し、本発明の特徴とするところをよ
り一層明確にする。EXAMPLES Examples are shown below to further clarify features of the present invention.
実施例１ 第１表に示す組成のAl合金をエアアトマイズ法により
粉末化し、−100メッシュに分級した。なお、第１表に
おいて、各成分の量は、重量％を示し、残余は実質的に
Alである。Example 1 An Al alloy having the composition shown in Table 1 was powdered by an air atomizing method and classified into -100 mesh. In Table 1, the amounts of the respective components indicate% by weight, and the balance is substantially the same.
Al.
得られたAl合金粉末を直径30mm×高さ80mmのビレット
に冷間予備成形した後、450℃において押出し比を変え
て押出した。得られた押出し棒から引張試験片を作製
し、室温及び300℃で引張試験を行った。 The obtained Al alloy powder was cold preformed into a billet having a diameter of 30 mm and a height of 80 mm, and then extruded at 450 ° C. while changing the extrusion ratio. A tensile test piece was prepared from the obtained extruded rod, and a tensile test was performed at room temperature and 300 ° C.
室温における引張強度（kg/mm2）および伸び（％）を
第２−Ａ表（押出し比3:1）、第２−Ｂ表（押出し比5:
1）および第２−Ｃ表（押出し比20:1）に示す。The tensile strength (kg / mm 2 ) and elongation (%) at room temperature are shown in Table 2-A (extrusion ratio 3: 1) and Table 2-B (extrusion ratio 5:
1) and Table 2-C (extrusion ratio 20: 1).
また、300℃における引張強度（kg/mm2）および伸び
（％）を第３−Ａ表（押出し比3:1）、第３−Ｂ表（押
出し比5:1）および第３−Ｃ表（押出し比20:1）に示
す。The tensile strength (kg / mm 2 ) and elongation (%) at 300 ° C. are shown in Table 3-A (extrusion ratio 3: 1), Table 3-B (extrusion ratio 5: 1) and Table 3-C. (Extrusion ratio 20: 1).
第２−Ａ表乃至第２−Ｃ表並びに第３−Ａ表乃至第３
−Ｃ表に示す結果から明らかな様に、本発明のAl合金N
o.1〜３および７〜９を使用する場合には、押出し比に
は関係なく、ほぼ一定の強度および伸びを示している。
すなわち、押出し比３という低い押出し比においても、
十分な強度と伸びとが得られている。 Tables 2-A to 2-C and Tables 3-A to 3
As is clear from the results shown in Table C, the Al alloy N of the present invention
When o.1-3 and 7-9 are used, almost constant strength and elongation are exhibited regardless of the extrusion ratio.
That is, even at an extrusion ratio as low as 3
Sufficient strength and elongation are obtained.
これに対し、本発明外の組成のAl合金No.4〜６を使用
する場合には、低押出し比では、十分の強度および／ま
たは伸びが得られない。On the other hand, when Al alloys Nos. 4 to 6 having compositions other than the present invention are used, sufficient strength and / or elongation cannot be obtained at a low extrusion ratio.
さらに、上記と同様にして得た押出し棒から直径7mm
×長さ10.5mmの試験片を切り出し、450℃で据込み試験
を行い、限界据込率（％）を測定した。第４表に各押出
し比における結果を示す。Furthermore, from the extruded rod obtained in the same manner as above, a diameter of 7 mm
× A test piece having a length of 10.5 mm was cut out, an upsetting test was performed at 450 ° C., and a critical upsetting rate (%) was measured. Table 4 shows the results at each extrusion ratio.
なお、据込み試験は、日本塑性加工学会冷間鍛造分科
会基準「金属材料の冷間据込み性試験方法」（暫定基
準）に従って行なった。The upsetting test was carried out in accordance with the standards of the Cold Forging Subcommittee of the Japan Society for Technology of Plasticity “Cold Upsetting Test Method for Metallic Materials” (tentative standard).
第４表に示す結果から明らかな様に、本発明のAl合金
No.1〜３および７〜９を使用する場合には、押出し比と
関係なく、ほぼ60〜70％の限界据込率が得られている。 As is clear from the results shown in Table 4, the Al alloy of the present invention
When Nos. 1-3 and 7-9 are used, a critical upsetting of approximately 60-70% is obtained, irrespective of the extrusion ratio.
これに対し、本発明外の組成のAl合金No.4〜６を使用
する場合には、３〜５程度の低い押出比においては、十
分な鍛造成形性を示さない。On the other hand, when Al alloys Nos. 4 to 6 having compositions other than the present invention are used, sufficient forgeability is not exhibited at a low extrusion ratio of about 3 to 5.
実施例２ 12Si−4Fe−4Ni−2Mo−1.5Zrなる組成のAl合金のアト
マイズ粉末（−100メッシュ）を使用して、直径230mmの
冷間成形体（密度比75％）を作成した後、450℃で直径1
50mmの丸棒に押出成形した（押出し比＝2.4）。Example 2 A cold compact (diameter: 75%) having a diameter of 230 mm was prepared using atomized powder (-100 mesh) of an Al alloy having a composition of 12Si-4Fe-4Ni-2Mo-1.5Zr. Diameter at ℃ 1
It was extruded into a 50 mm round bar (extrusion ratio = 2.4).
得られた丸棒を長さ300mmに切断し、最終的に第２図
に示す形状および寸法（単位は、mm）となる様に、480
℃で２段型鍛造を行なった。The obtained round bar was cut into a length of 300 mm, and finally the shape and dimensions (unit: mm) shown in FIG.
The two-stage die forging was performed at ℃.
この鍛造材の張出部（直径250mmの部分）は、70％程
度の据込み率となっているためにもかかわらず、割れは
全く発生していなかった。The overhang portion (250 mm diameter portion) of this forged material had no upsetting rate despite having an upsetting ratio of about 70%.
次いで、第２図に示すこの鍛造材の（ａ）、（ｂ）お
よび（ｃ）部分から、平行部分の直径6mm×長さ40mm、
全長80mmの試験片をそれぞれ切出し、300℃で引張試験
を行なった。Next, from the (a), (b) and (c) portions of this forged material shown in FIG.
Test pieces having a total length of 80 mm were cut out and subjected to a tensile test at 300 ° C.
結果を第５表に示す。 The results are shown in Table 5.
第５表に示す結果から明らかな様に、鍛造により強く
加工されている（ｃ）の部分は、（ａ）および（ｂ）の
部分に比して、より優れた高温強度を発揮する。 As is evident from the results shown in Table 5, the part (c) that has been strongly processed by forging exhibits more excellent high-temperature strength than the parts (a) and (b).
従って、本実施例の様にして得られた鍛造材から機械
加工により回転体を製造する場合には、最も強い遠心力
がかかる（ｃ）方向の部分が最高の強度を発揮するの
で、高温で使用される高速回転体の製造に特に好適であ
る。Therefore, when the rotating body is manufactured by machining from the forged material obtained as in the present embodiment, the portion in the direction (c) where the strongest centrifugal force is exerted exhibits the highest strength, so It is particularly suitable for the production of the high-speed rotating bodies used.
第１図は、本発明により得られる鍛造製品において、最
大遠心力のかかる方向と押出成形時の材料粉末のフロー
の方向との関係を模式的に示す断面図である。 第２図は、本願実施例３において得られた鍛造体の形状
を示す図面である。FIG. 1 is a cross-sectional view schematically showing the relationship between the direction in which the maximum centrifugal force is applied and the direction of the flow of material powder during extrusion in a forged product obtained by the present invention. FIG. 2 is a drawing showing the shape of the forged body obtained in Example 3 of the present application.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 楠井 潤 大阪府大阪市中央区久太郎町３丁目６番 ８号 東洋アルミニウム株式会社内 (72)発明者 川井 正彦 大阪府大阪市中央区久太郎町３丁目６番 ８号 東洋アルミニウム株式会社内 (56)参考文献 特開 昭61−243138（ＪＰ，Ａ) 特開 昭61−84343（ＪＰ，Ａ) 特開 昭64−56806（ＪＰ，Ａ) 特開 昭63−42344（ＪＰ，Ａ) 特開 平２−101125（ＪＰ，Ａ) 特公 昭46−13617（ＪＰ，Ｂ１) (58)調査した分野(Int.Cl.6，ＤＢ名) B22F 3/00 - 3/26 C22C 1/04──────────────────────────────────────────────────続 き Continuation of the front page (72) Inventor Jun Kusui 3-6-8 Kutarocho, Chuo-ku, Osaka-shi, Osaka Inside Toyo Aluminum Co., Ltd. (72) Masahiko Kawai 3-chome Kutarocho, Chuo-ku, Osaka-shi, Osaka No. 6-8 Inside Toyo Aluminum Co., Ltd. (56) References JP-A-61-243138 (JP, A) JP-A-61-84343 (JP, A) JP-A-64-56806 (JP, A) 63-42344 (JP, A) JP-A-2-101125 (JP, A) JP-B 46-13617 (JP, B1) (58) Fields investigated (Int. Cl. 6 , DB name) B22F 3/00 -3/26 C22C 1/04
Claims (4)
重量％ （ハ）Mo及びZrの少なくとも１種0.5〜10重量％及び （ニ）残余が実質的にAl （但し、（ロ）と（ハ）との合計量は30重量％を超えな
い）からなる合金粉末を温度350〜500℃において押出し
比２〜５で押出し成形することを特徴とする大径の製品
用アルミニウム合金の成形方法。(1) at least one of Cu, Fe, Cr, V, and Ni in an amount of 0.5 to 10%;
(C) at least one of Mo and Zr 0.5 to 10% by weight and (d) the balance is substantially Al (however, the total amount of (b) and (c) does not exceed 30% by weight) A method for forming a large-diameter aluminum alloy for a product, comprising extruding an alloy powder at a temperature of 350 to 500 ° C. at an extrusion ratio of 2 to 5.
400〜530℃において熱間型鍛造することを特徴とする大
径の製品用アルミニウム合金の成形方法。2. The molded article obtained in the above item 1 is further heated to a temperature.
A method for forming a large-diameter aluminum alloy for a product, comprising hot-die forging at 400 to 530 ° C.
400〜530℃において拡径方向に30〜80％の熱間据込み鍛
造することを特徴とする大径の製品用アルミニウム合金
の成形方法。3. The molded article obtained in the above item 1 is further heated to a temperature.
A method for forming a large-diameter aluminum alloy for a product, comprising hot upsetting at a temperature of 400 to 530 [deg.] C. in the diameter increasing direction by 30 to 80%.
５重量％、Ni3〜５重量％、Mo0.5〜2.5重量％及びZr0.5
〜2.5重量％を含有し、残部が実質的にAlからなる上記
第１項に記載の大径の製品用アルミニウム合金の成形方
法。4. The composition of the alloy powder is 5 to 30% by weight of Si, 3 to 30% by weight of Fe.
5% by weight, Ni3-5% by weight, Mo0.5-2.5% by weight and Zr0.5
2. The method for forming a large-diameter aluminum alloy for a product according to the above item 1, wherein the aluminum alloy contains about 2.5% by weight and the balance substantially consists of Al.
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1091587A JP2787466B2 (en) | 1988-05-12 | 1989-04-10 | Forming method of aluminum alloy for large diameter products |
| DE68912394T DE68912394T2 (en) | 1988-05-12 | 1989-05-11 | Process for deforming a large aluminum alloy product. |
| EP89108490A EP0341714B1 (en) | 1988-05-12 | 1989-05-11 | Method of forming large-sized aluminum alloy product |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63-115625 | 1988-05-12 | ||
| JP11562588 | 1988-05-12 | ||
| JP1091587A JP2787466B2 (en) | 1988-05-12 | 1989-04-10 | Forming method of aluminum alloy for large diameter products |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0250902A JPH0250902A (en) | 1990-02-20 |
| JP2787466B2 true JP2787466B2 (en) | 1998-08-20 |
Family
ID=26433032
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1091587A Expired - Lifetime JP2787466B2 (en) | 1988-05-12 | 1989-04-10 | Forming method of aluminum alloy for large diameter products |
Country Status (3)
| Country | Link |
|---|---|
| EP (1) | EP0341714B1 (en) |
| JP (1) | JP2787466B2 (en) |
| DE (1) | DE68912394T2 (en) |
Families Citing this family (19)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0366134B1 (en) * | 1988-10-27 | 1994-01-19 | Toyo Aluminium Kabushiki Kaisha | Aluminum alloy useful in powder metallurgy process |
| JPH03177530A (en) * | 1988-10-27 | 1991-08-01 | Toyo Alum Kk | Heat-resistant and creep-resistant aluminum alloy |
| JPH03180440A (en) * | 1989-08-23 | 1991-08-06 | Kubota Corp | Heat resistant high strength Al alloy material |
| JPH05117797A (en) * | 1990-04-18 | 1993-05-14 | Toyo Alum Kk | Heat and creep resistant aluminum alloy excellent in toughness |
| DE69221690T2 (en) * | 1991-04-03 | 1998-04-02 | Sumitomo Electric Industries | ROTOR FOR OIL PUMP FROM AN ALUMINUM ALLOY AND ITS PRODUCTION METHOD |
| JP3123114B2 (en) * | 1991-05-23 | 2001-01-09 | 住友電気工業株式会社 | Manufacturing method of high precision aluminum alloy parts |
| JPH04323342A (en) * | 1991-04-24 | 1992-11-12 | Sumitomo Electric Ind Ltd | Transition element added powdery aluminum alloy and its production |
| JPH0579468A (en) * | 1991-05-02 | 1993-03-30 | Mitsubishi Materials Corp | Manufacture of gear for fluid machine |
| JP3240182B2 (en) * | 1992-04-28 | 2001-12-17 | マツダ株式会社 | Manufacturing method of magnesium alloy member |
| DE19532253C2 (en) * | 1995-09-01 | 1998-07-02 | Peak Werkstoff Gmbh | Process for the production of thin-walled pipes (II) |
| DE19532244C2 (en) * | 1995-09-01 | 1998-07-02 | Peak Werkstoff Gmbh | Process for the production of thin-walled tubes (I) |
| DE19532252C2 (en) * | 1995-09-01 | 1999-12-02 | Erbsloeh Ag | Method of manufacturing bushings |
| GB2316094B (en) * | 1996-08-06 | 2000-04-12 | Kubota Kk | Cast iron pipe surface-modified for corrosion prevention and method of modifying the cast iron pipe surface for corrosion prevention |
| DE10006269A1 (en) * | 2000-02-12 | 2001-08-16 | Bayerische Motoren Werke Ag | Method for producing a metal component for a drive unit, in particular an internal combustion engine, which interacts with a friction partner via a sliding surface |
| WO2006103885A1 (en) | 2005-03-29 | 2006-10-05 | Kabushiki Kaisha Kobe Seiko Sho | Al BASE ALLOY EXCELLENT IN HEAT RESISTANCE, WORKABILITY AND RIGIDITY |
| CN103357803A (en) * | 2013-06-09 | 2013-10-23 | 大连冶金轴承股份有限公司 | A processing method of 22224 self-aligning spherical roller pressing die blank |
| JP2019026859A (en) * | 2017-07-25 | 2019-02-21 | 昭和電工株式会社 | Aluminum alloy forged product for high-speed moving parts and method for producing the same |
| FR3083479B1 (en) * | 2018-07-09 | 2021-08-13 | C Tec Constellium Tech Center | METHOD OF MANUFACTURING AN ALUMINUM ALLOY PART |
| FR3083478B1 (en) | 2018-07-09 | 2021-08-13 | C Tec Constellium Tech Center | METHOD OF MANUFACTURING AN ALUMINUM ALLOY PART |
Family Cites Families (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2978798A (en) * | 1955-08-31 | 1961-04-11 | Metallgesellschaft Ag | Aluminum and silicon containing metal powder and method of producing workpieces therefrom |
| GB912959A (en) * | 1959-02-03 | 1962-12-12 | Schmidt Gmbh Karl | Improvements in or relating to cylinder blocks, cylinder bushings and cylinder heads |
| CA1230761A (en) * | 1982-07-12 | 1987-12-29 | Fumio Kiyota | Heat-resistant, wear-resistant, and high-strength aluminum alloy powder and body shaped therefrom |
| DE3481322D1 (en) * | 1983-12-02 | 1990-03-15 | Sumitomo Electric Industries | ALUMINUM ALLOYS AND METHOD FOR THEIR PRODUCTION. |
| JPS6184343A (en) * | 1984-10-02 | 1986-04-28 | Honda Motor Co Ltd | Method for manufacturing aluminum alloy members |
| CA1284896C (en) * | 1984-10-23 | 1991-06-18 | Paul S. Gilman | Method for producing dispersion strengthened aluminum alloys |
| DE3541781C2 (en) * | 1984-11-28 | 1999-09-02 | Honda Motor Co Ltd | Process for producing a component from a heat-resistant, high-strength, sintered aluminum alloy and a heat-resistant, high-strength aluminum alloy |
| JPS61243138A (en) * | 1985-04-17 | 1986-10-29 | Honda Motor Co Ltd | Production of structural member made of heat-resistant high-strength al sintered alloy |
| JPS6342344A (en) * | 1986-08-06 | 1988-02-23 | Honda Motor Co Ltd | Al alloy for powder metallurgy with excellent high-temperature strength properties |
| FR2604186A1 (en) * | 1986-09-22 | 1988-03-25 | Peugeot | PROCESS FOR MANUFACTURING HYPERSILICALLY ALUMINUM ALLOY PARTS OBTAINED FROM COOLED COOLED POWDERS AT HIGH SPEED |
| JPS6456806A (en) * | 1987-08-27 | 1989-03-03 | Sumitomo Electric Industries | Spiral parts made of aluminum powder alloy having low strain |
| JP2746390B2 (en) * | 1988-10-07 | 1998-05-06 | 住友軽金属工業株式会社 | Manufacturing method of aluminum alloy with excellent tensile and fatigue strength |
-
1989
- 1989-04-10 JP JP1091587A patent/JP2787466B2/en not_active Expired - Lifetime
- 1989-05-11 EP EP89108490A patent/EP0341714B1/en not_active Expired - Lifetime
- 1989-05-11 DE DE68912394T patent/DE68912394T2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| EP0341714A1 (en) | 1989-11-15 |
| DE68912394D1 (en) | 1994-03-03 |
| EP0341714B1 (en) | 1994-01-19 |
| DE68912394T2 (en) | 1994-05-26 |
| JPH0250902A (en) | 1990-02-20 |
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