JPS62188741A - Al alloy material - Google Patents
Al alloy materialInfo
- Publication number
- JPS62188741A JPS62188741A JP3012086A JP3012086A JPS62188741A JP S62188741 A JPS62188741 A JP S62188741A JP 3012086 A JP3012086 A JP 3012086A JP 3012086 A JP3012086 A JP 3012086A JP S62188741 A JPS62188741 A JP S62188741A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- weight
- powder
- alloy material
- molten
- 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.)
- Granted
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 13
- 239000000956 alloy Substances 0.000 title claims abstract description 12
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 229910052802 copper Inorganic materials 0.000 claims abstract description 4
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052790 beryllium Inorganic materials 0.000 claims abstract 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- 239000010949 copper Substances 0.000 claims 2
- 239000011777 magnesium Substances 0.000 claims 2
- 239000011572 manganese Substances 0.000 claims 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims 1
- 229910052782 aluminium Inorganic materials 0.000 claims 1
- ATBAMAFKBVZNFJ-UHFFFAOYSA-N beryllium atom Chemical compound [Be] ATBAMAFKBVZNFJ-UHFFFAOYSA-N 0.000 claims 1
- 239000010703 silicon Substances 0.000 claims 1
- 239000000843 powder Substances 0.000 abstract description 14
- 238000004519 manufacturing process Methods 0.000 abstract description 7
- 238000005245 sintering Methods 0.000 abstract description 5
- 230000015572 biosynthetic process Effects 0.000 abstract description 4
- 239000000203 mixture Substances 0.000 abstract description 4
- 239000000463 material Substances 0.000 description 11
- 238000000034 method Methods 0.000 description 9
- 229910045601 alloy Inorganic materials 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- 238000005242 forging Methods 0.000 description 6
- 239000007789 gas Substances 0.000 description 6
- 239000002184 metal Substances 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 238000001125 extrusion Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005507 spraying Methods 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910017384 Fe3Si Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000000748 compression moulding Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 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）
本発明は金属粉末原料から製造されるＡ立合全素材に関
する。DETAILED DESCRIPTION OF THE INVENTION (Industrial Field of Application) The present invention relates to an A-chiai-zen material manufactured from metal powder raw materials.
（従来の技術）
エンジンのコンロッド等の部材は高温下で使用されるた
め、耐熱性及び高強度が要求される。そこで従来にあっ
てはこれらの部材は鉄を主成分としたＷ４素材から製造
している。(Prior Art) Since components such as engine connecting rods are used at high temperatures, they are required to have heat resistance and high strength. Therefore, conventionally, these members are manufactured from W4 material whose main component is iron.
しかしながら鋼素材は重量が大であり、特にコンロッド
等の材料として用いると慣性力が大きくなる不利がある
。この不利を解消すべく軽量なＡＪＩ合金を用いてピス
トン等を構成することが考えられるが、Ｗ４素材と同等
の耐熱強度を発揮するには部材自体の厚み等を大きくし
なければならず、スペース的な不利が発生することとな
る。However, steel materials are heavy, and especially when used as materials for connecting rods, etc., there is a disadvantage that the inertia force becomes large. In order to overcome this disadvantage, it is conceivable to construct pistons etc. using lightweight AJI alloy, but in order to exhibit heat resistance strength equivalent to W4 material, the thickness of the member itself must be increased, and it takes up a lot of space. This will result in a disadvantage.
そこで本出願人は先に特願昭５９−２２３８９８号とし
て、添加元素選択の自由度が高い粉末冶金法により上記
部材を製造することを提案した。この方法によれば、原
料である金属粉末中に固溶限度以上にＳｉ、 Ｆｅ等を
添加できるため、強度的に優れたＡ立合全素材を得られ
る。Therefore, the present applicant previously proposed, in Japanese Patent Application No. 59-223898, to manufacture the above-mentioned member by a powder metallurgy method that allows a high degree of freedom in selecting additive elements. According to this method, it is possible to add Si, Fe, etc. to the metal powder as a raw material in an amount exceeding the solid solution limit, so that it is possible to obtain a material with excellent strength.
（発明が解決しよンとする問題点）
上述した粉末！ｆ３全３金法って人文合金素材を製造す
る場合には新たに以下の如き問題が生じる。(Problem to be solved by the invention) The above-mentioned powder! When manufacturing humanities alloy materials using the f3 all three-metal method, the following new problems arise.
即ち、Ａｌは酸素との結合力が極めて強く、そのためＡ
交合金粉末を製造する時に粉末表面に酸化被膜（Ａ文２
０３）が生成され、この酸化被膜が水分子を吸着してＡ
見２０３・３Ｈ２０となり、後に合金粉末を圧縮成形及
び焼結する際の熱により水分子が分解し、この分解によ
って発生するＨ２カスが焼結後の合金中に残存し、加熱
工程時にブリスタが発生し、強度及び衝撃値の低下を招
く。In other words, Al has an extremely strong bonding force with oxygen, so Al
When producing cross-alloy powder, an oxide film (A-pattern 2) is formed on the powder surface.
03) is generated, and this oxide film adsorbs water molecules to form A
203.3H20, water molecules are decomposed by the heat during compression molding and sintering of the alloy powder, H2 residue generated by this decomposition remains in the alloy after sintering, and blisters occur during the heating process. This results in a decrease in strength and impact value.
このブリスタの発生を抑制する手段として不活性雰囲気
で焼結を行うことが考えられるが、コントロールが極め
て難しく、量産には不向きである。Sintering in an inert atmosphere may be considered as a means to suppress the generation of blisters, but this is extremely difficult to control and is not suitable for mass production.
尚、従来の鋳造法にあってはＢｅを添加し、Ａ文酸化物
の生成を抑制することが行われているが、Ｂｅの添加量
は０．００４ ｌ量％以下でないと伸び、靭性が低下す
るため、充分にＡｕ酸化物の生成を抑制できない。In addition, in conventional casting methods, Be is added to suppress the formation of A grain oxides, but unless the amount of Be added is 0.004 l% or less, elongation and toughness will occur. Therefore, the generation of Au oxide cannot be sufficiently suppressed.
（問題点を解決するための手段）
上記問題点を解決すべく本発明は、人文中にＳｌ、Ｆｅ
、 Ｃｕ、 Ｍｎ、 Ｍｇを添加することで耐摩耗性、
ヤング率、高温強度及びマトリックス強化を向上させる
とともにＢｅを０．１重量％以上、３．０重量％以下の
割合で添加するようにした。(Means for Solving the Problems) In order to solve the above problems, the present invention aims to solve the problems described above.
, Cu, Mn, and Mg improve wear resistance.
In addition to improving Young's modulus, high-temperature strength, and matrix reinforcement, Be is added in a proportion of 0.1% by weight or more and 3.0% by weight or less.
（作用）
Ｂｅを添加することにより、Ａｌ合金粉末を製造する際
に、酸化被膜の生成が抑〃Ｉされ、焼結時のＨ２ガスの
発生が低減し、したがって加熱工程時にブリスタの発生
がない。(Function) By adding Be, when producing Al alloy powder, the formation of oxide film is suppressed, the generation of H2 gas during sintering is reduced, and therefore no blisters are generated during the heating process. .
（実施例）
以下に本発明の詳細な説明する。先ず本発明にあっては
Ａｌ合金溶湯を用意し、以下の如き添加組成からなるＡ
ｌ合金素材を後述する噴霧法及び成形工程を経て製造す
る。(Example) The present invention will be described in detail below. First, in the present invention, a molten Al alloy is prepared, and A having the following additive composition is prepared.
The alloy material is manufactured through the spraying method and molding process described below.
１２．０％≦Ｓｉ≦２８．０Ｘ ２、Ｏ１≦Ｆｅ≦１０．０％ ０．８＄≦Ｃｕ≦５．Ｏｚ ０．５Ｘ≦Ｍｎ≦５．０１ ０．３％≦Ｈｇ≦３．５％ ０．１＄≦Ｂｅ≦３．Ｈ 残部をＡ！ｌ及び不可避不純物とする。12.0%≦Si≦28.0X 2, O1≦Fe≦10.0% 0.8$≦Cu≦5. Oz 0.5X≦Mn≦5.01 0.3%≦Hg≦3.5% 0.1$≦Be≦3. H A for the rest! 1 and unavoidable impurities.
Ｓｉを添加したのは、耐摩耗性及びヤング率を向上させ
るとともに、熱膨張率を低く抑え、熱伝導率を高めるた
めである。そして上記の割合とじたのは、１２ｆｉｉ％
未満とすると上記の効果が十分に発揮されず、また２８
重量％を超えると圧粉、抑圧、鍛造等の成形加工におけ
る成形性が悪化し、量産性に欠けることによる。The reason for adding Si is to improve wear resistance and Young's modulus, keep the coefficient of thermal expansion low, and increase thermal conductivity. And the above percentage is 12fii%
If it is less than 28, the above effects will not be fully exhibited, and
If it exceeds % by weight, formability in forming processes such as powder compaction, compression, and forging will deteriorate, resulting in a lack of mass productivity.
Ｆｅを添加したのは、高温強度及びヤング率向上を図る
ためである。そして上記の割合としたのは、 ２．０ｉ
９５未満とすると添加による効果が十分に発揮されず
、また１０．０重量％を超えると量産設備等を考慮した
場合高速熱間鍛造加工が極めて困難となることによる。The reason for adding Fe is to improve high temperature strength and Young's modulus. And the above ratio is 2.0i
If it is less than 95, the effect of the addition will not be sufficiently exhibited, and if it exceeds 10.0% by weight, high-speed hot forging becomes extremely difficult when considering mass production equipment.
Ｃｕを添加したのは、熱処理に伴うマトリックス強化を
図るためであり、上記の割合としたのは、０．８重量％
未満とすると添加による効果が十分に発揮されず、また
５、０重量％を超えると耐応力腐食割れ特性が悪化し、
高温強度が低下することによる。The purpose of adding Cu was to strengthen the matrix during heat treatment, and the above ratio was 0.8% by weight.
If it is less than 5.0% by weight, the effect of addition will not be sufficiently exhibited, and if it exceeds 5.0% by weight, stress corrosion cracking resistance will deteriorate.
This is due to a decrease in high temperature strength.
Ｍｎを添加したのは、高温強度の改善、熱間鍛造加工性
の向上及び耐応力腐食割れ特性の改善を図るためであり
、上記の割合としたのは、 ０．５重量％未満とすると
添加による効果が十分に発揮されず、また５、０重量％
を超えると却って熱間鍛造加工性が悪化することによる
。The purpose of adding Mn was to improve high-temperature strength, hot forging workability, and stress corrosion cracking resistance. 5.0% by weight
If it exceeds this, the hot forging workability will actually deteriorate.
Ｍｇを添加したのは、（ｕと同様に熱処理に伴うマトリ
ックス強化を図るためであり、上記の割合としたのは、
０．３重量％未満では添加による効果が十分に発揮さ
れず、また３、５重量％を超えると耐応力腐食割れ特性
及び熱間鍛造加工性が悪化することによる。The reason why Mg was added was to strengthen the matrix during heat treatment like (U), and the above ratio was set as follows.
If it is less than 0.3% by weight, the effect of addition will not be sufficiently exhibited, and if it exceeds 3.5% by weight, stress corrosion cracking resistance and hot forging workability will deteriorate.
また、Ｂｅを添加したのは前述の如く、酸化被膜の生成
を抑制しＨ２ガスの発生を防止することの他に、Ｂｅの
微細な析出により高温強度及びヤング率の向上を図るた
めであり、上記の割合としたのは、 ０．１重量％未満
では添加による効果が十分に発揮されず、また３、０重
量％を超えるとＢｅは活性であるため生産効率の低下を
招くことによる。In addition, as mentioned above, Be was added to suppress the formation of an oxide film and prevent the generation of H2 gas, as well as to improve high-temperature strength and Young's modulus through fine precipitation of Be. The reason why the above ratio is set is that if it is less than 0.1% by weight, the effect of addition will not be sufficiently exhibited, and if it exceeds 3.0% by weight, Be is active, leading to a decrease in production efficiency.
次にＡ文合金溶湯からＡｌ合金粉末を噴霧法（ａｉｒ
ａｔｏｍｉｚｉｎｇ法）により作成する方法について述
べる。この方法はノズルから噴出する溶湯を急速冷却し
て溶湯を粉化するものであり、この際の冷却速度として
は１０２°Ｃ／ｓｅｃ以上とする。Next, Al alloy powder is applied from the molten A pattern alloy by a spraying method (air
A method for producing the film using the atomizing method will be described. This method rapidly cools the molten metal spouted from a nozzle to powder the molten metal, and the cooling rate at this time is set to 102°C/sec or more.
即ち、冷却速度が１０２°Ｃ／ｓｅｅ未満であると、析
出するＡ文］ Ｆｅ、 Ａ ｆＬ １２ Ｆｅ３Ｓｉ、
Ａ ｌ ９Ｆｅ２Ｓｉｚ等の金属間化合物の大きさが１
０μｍ以上となり、その結果疲労強度が低下し成形性も
悪化することによる。That is, when the cooling rate is less than 102°C/see, A sentence precipitates] Fe, A fL 12 Fe3Si,
The size of intermetallic compounds such as A l 9Fe2Siz is 1
This is because the thickness becomes 0 μm or more, resulting in a decrease in fatigue strength and deterioration in formability.
次いで上記によって得られたＡｌ合金粉末を圧粉して４
００°Ｃの均熱炉内に保持し、その後３８０℃にて熱間
押出し加工を施して押出材又は製品を製造する。尚押出
し方法としては直接押出し１間接押出しのいずれでもよ
い。このようにして得られた素材の組成割合は前記した
ものとなっている。Next, the Al alloy powder obtained above was pressed into 4
The sample is held in a soaking furnace at 00°C and then hot extruded at 380°C to produce an extruded material or product. The extrusion method may be either direct extrusion or indirect extrusion. The composition ratio of the material thus obtained is as described above.
この後、上記押出材を熱間鍛造することで目的とするＡ
ｌ合金部材を製造してもよい。After that, the above extruded material is hot forged to achieve the desired A.
l alloy parts may also be manufactured.
（発明の効果）
［表］は本発明の組成からなる押出材と従来の鍛造用素
材とを、Ｈ２ガス量、高温強度及びシャルピー衝撃値に
ついて比較したものである。(Effects of the Invention) [Table] compares the extruded material having the composition of the present invention and a conventional forging material in terms of H2 gas amount, high temperature strength, and Charpy impact value.
尚、Ｈ２ガス量は溶融ガスキャリア法にて測定し、高温
強度は平行部径５ｍ脂、平行部長さ３０層層の引張試験
片を切出し、２００℃で１ｏＯＨｒ保持後、２００°Ｃ
にて引張試験を行ってＪｌｌｌ定し、更にＪＩＳＺ２２
４２に規定するシャルピー衝撃値については、１０ｍｍ
Ｘ ｌＯｍｍＸ ５５ｍｍの切欠なしテストピースによ
り求めた。In addition, the amount of H2 gas was measured by the molten gas carrier method, and the high temperature strength was measured by cutting out a tensile test piece with a parallel part diameter of 5 m and a parallel part length of 30 layers.
A tensile test was conducted to determine Jllll, and further JISZ22
For the Charpy impact value specified in 42, 10 mm
It was determined using a test piece without notches of X 10 mm and 55 mm.
［表］からも明らかなように本発明によれば、含有Ｈ２
ガス量が極めて少なく、高温強度及びシャルピー衝撃値
に優れたＡｆＬ合全合材部材ることができる。As is clear from the [Table], according to the present invention, the contained H2
It is possible to produce an AfL composite material with an extremely small amount of gas and excellent high-temperature strength and Charpy impact value.
Claims (1)
．０乃至１０．０重量％、Ｃｕ（銅）を０．８乃至５．
０重量％、Ｍｎ（マンガン）を０．５乃至５．０重量％
、Ｍｇ（マグネシウム）を０．３乃至３．５重量％、Ｂ
ｅ（ベリリウム）を０．１乃至３．０重量％、残部がＡ
ｌ（アルミニウム）及び不可避不純物からなるＡｌ合金
素材。12 to 28% by weight of Si (silicon), 2% of Fe (iron)
．． 0 to 10.0% by weight, Cu (copper) 0.8 to 5% by weight.
0% by weight, Mn (manganese) 0.5 to 5.0% by weight
, 0.3 to 3.5% by weight of Mg (magnesium), B
0.1 to 3.0% by weight of e (beryllium), the balance being A
Al alloy material consisting of l (aluminum) and inevitable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3012086A JPH0742538B2 (en) | 1986-02-14 | 1986-02-14 | Sintered material made of Al alloy with excellent high temperature strength and Charpy impact value |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3012086A JPH0742538B2 (en) | 1986-02-14 | 1986-02-14 | Sintered material made of Al alloy with excellent high temperature strength and Charpy impact value |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62188741A true JPS62188741A (en) | 1987-08-18 |
| JPH0742538B2 JPH0742538B2 (en) | 1995-05-10 |
Family
ID=12294919
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3012086A Expired - Lifetime JPH0742538B2 (en) | 1986-02-14 | 1986-02-14 | Sintered material made of Al alloy with excellent high temperature strength and Charpy impact value |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0742538B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0645465A1 (en) * | 1993-08-28 | 1995-03-29 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Aluminium alloy casting having high laser weldability, joint of aluminium alloy casting and method for improving aluminium alloy cast structural member |
-
1986
- 1986-02-14 JP JP3012086A patent/JPH0742538B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0645465A1 (en) * | 1993-08-28 | 1995-03-29 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Aluminium alloy casting having high laser weldability, joint of aluminium alloy casting and method for improving aluminium alloy cast structural member |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0742538B2 (en) | 1995-05-10 |
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