JPS6210237A - Aluminum alloy for hot forging - Google Patents
Aluminum alloy for hot forgingInfo
- Publication number
- JPS6210237A JPS6210237A JP60149192A JP14919285A JPS6210237A JP S6210237 A JPS6210237 A JP S6210237A JP 60149192 A JP60149192 A JP 60149192A JP 14919285 A JP14919285 A JP 14919285A JP S6210237 A JPS6210237 A JP S6210237A
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- Prior art keywords
- alloy
- less
- alloy powder
- billet
- gas
- Prior art date
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- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は高温鍛造性が優れ、耐摩耗性を有するアルミニ
ウム合金に関するものである。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to an aluminum alloy that has excellent high-temperature forgeability and wear resistance.
（従来の技術）
従来耐摩耗性の良好なアルミニウム（Ａ１）合金として
は、例えばＪＩＳ ＡＣ３Ａ、 ＡＣ４Ａ、 ＡＣ８Ａ
などの鋳物用Ａ１合金や、ＪＩＳ ＡＤＣｌ、 ＡＤＣ
３、ＡＤＣＩＯ５ＡＤＣ１２等のダイカスト用Ａ１合金
が知られている。(Prior art) Examples of conventional aluminum (A1) alloys with good wear resistance include JIS AC3A, AC4A, and AC8A.
A1 alloy for casting such as JIS ADCl, ADC
3. A1 alloys for die casting such as ADCIO5ADC12 are known.
しかしながらこれらの高ケイ素Ａｌ合金は通常の方法で
鋳塊にした場合は組織が粗大で内部欠陥が多く、また内
部欠陥のため割れが発生し易く、強度や加工性に難点が
あった。However, when these high-silicon Al alloys are made into ingots by conventional methods, they have coarse structures and many internal defects, and cracks are likely to occur due to internal defects, resulting in difficulties in strength and workability.
また、耐摩耗性を有するＡ１合金としてケイ素（Ｓｉ）
以外の第３元素（例えばＣｕ、 Ｍｇ等）を添加したＡ
３８０合金等が知られているが、これらは鋳造合金であ
り、＃摩耗性はある程度満足できるが、耐熱性や加工性
の点で充分満足いくものは得られていない。In addition, silicon (Si) is used as an A1 alloy that has wear resistance.
A containing a third element (e.g. Cu, Mg, etc.) other than
380 alloy is known, but these are cast alloys, and although they are somewhat satisfactory in terms of abrasion resistance, they have not yet been fully satisfactory in terms of heat resistance and workability.
以上のような鋳造Ａ１合金の欠点を克服すべく、Ａ１合
金粉末の押出し成形法によってＡ１合金粉末成形体を得
る方法が提案されている（例えば、特開昭５２−１０９
４１５公報参照）、この方法によれば内燃機関用のシリ
ンダーライナーや、各種コンプレッサーのベーンに使用
すれば耐摩耗性と潤滑性に優れ、さらに高温強度にも優
れた材料が得られることから機関の寿命や効率を著しく
高め、軽量化に役立つことから最近とくに注目を集めて
いる。In order to overcome the above-mentioned drawbacks of cast A1 alloy, a method of obtaining an A1 alloy powder compact by extrusion molding of A1 alloy powder has been proposed (for example, Japanese Patent Laid-Open No. 52-109
(Refer to Publication No. 415), this method can be used for cylinder liners for internal combustion engines and vanes of various compressors to obtain materials with excellent wear resistance and lubricity, as well as excellent high-temperature strength. It has recently attracted particular attention because it significantly increases lifespan and efficiency, and helps reduce weight.
これらの過共晶ＳｉＡ１合金粉末成形体にかかわる公知
技術としては特開昭５７−５４２０３ 、特開昭５７
−１１２９２２ 、特開昭５７−１７７９５３ 、特開
昭５９−１１０７０２等がある。Known techniques related to these hypereutectic SiA1 alloy powder compacts include JP-A-57-54203 and JP-A-57.
-112922, JP-A-57-177953, and JP-A-59-110702.
（発明が解決しようとする問題点）
しかしながら従来公知のＡ１合金粉末成形体では、熱間
鍛造によってピストン、コンロッドなどの複雑な形状に
加工しようとすると、鍛造割れが発生し易く満足のゆく
形状に加工出来なかったり、あるいは鍛造がうまく出来
た場合でも製品の熱処理時にブリスターと呼ばれる気泡
が発生し充分な強度をもった製品が得られない欠点があ
った。(Problems to be Solved by the Invention) However, in conventionally known A1 alloy powder compacts, when hot forging is attempted to form complex shapes such as pistons and connecting rods, forging cracks tend to occur, resulting in unsatisfactory shapes. Even if the product could not be processed or forged successfully, bubbles called blisters were generated during the heat treatment of the product, making it difficult to obtain a product with sufficient strength.
本発明者らは、これらの原因について調査研究を行った
ところ、押出素材が多量のガス成分を含有し、これが原
因となって鍛造性を悪化させていることを見出し本発明
に至った。The present inventors investigated and researched these causes and found that the extruded material contained a large amount of gas components, which caused deterioration in forgeability, leading to the present invention.
Ａ１合金粉末成形体の脱カス方法としては、いわゆるＣ
ａｎｎｉｎｇ法が知られている。（ＵＳＰ−３９５４４
５８、ＵＳＰ−４１０４０１３１） Ｌかしながらこの
方法では操作が煩雑で生産工程には適していない。The so-called C
The annning method is known. (USP-39544
58, USP-41040131) However, this method requires complicated operations and is not suitable for production processes.
本発明者らは、上記問題点を解決するためＡ１合金粉末
成形体の脱ガス方法を詳細に検討した結果、Ａ１合金粉
末のビレットを作成した後にこれを真空中又は不活性ガ
ス中で加熱し、含有ガス量を５ｃｃ／ １００ ｇ以下
と極めて少なくすれば鍛造に適した材料が生産出来るこ
とを見出し本発明に至ったものである。In order to solve the above-mentioned problems, the present inventors investigated in detail a method for degassing an A1 alloy powder compact, and found that after creating a billet of A1 alloy powder, it was heated in a vacuum or in an inert gas. The inventors discovered that a material suitable for forging could be produced by reducing the gas content to an extremely small amount of 5 cc/100 g or less, leading to the present invention.
本発明のＡ１合金は１重量比でＳｉｌ０．０〜３０．０
％、Ｆｅ、 ＮｉあるいはＭｎが１．０〜１５．０％（
ただし、２種以上使用の場合は合計で１．０〜１５．０
％）を含み、さらに必要に応じてＣｕ ０．５〜５．０
％、Ｍｇ０．２〜３．０％を含み、残部が不可避的不純
物を含むＡｌから成り、Ｓｉ結晶粒の大きさが１５ｇｍ
以下であり。The A1 alloy of the present invention has a Sil of 0.0 to 30.0 at a weight ratio of 1.
%, Fe, Ni or Mn is 1.0-15.0% (
However, if two or more types are used, the total will be 1.0 to 15.0.
%), and further contains Cu 0.5 to 5.0 as necessary.
%, Mg 0.2 to 3.0%, the remainder is Al containing unavoidable impurities, and the size of Si crystal grains is 15 gm.
It is below.
かつ金属間化合物の大きさが２０ル腸以下に微細化分散
しかつ全ガス量が５ｃｃ／１００ ｇ以下であるＡ１合
金粉末成形体を要旨とするものである。The object of the present invention is to provide an A1 alloy powder compact in which the intermetallic compound is finely dispersed to a size of 20 μm or less and the total gas amount is 5 cc/100 g or less.
以下この発明をさらに詳細に説明する。This invention will be explained in more detail below.
まず、本発明の合金組成について説明する。First, the alloy composition of the present invention will be explained.
一般に過共晶ＳｉのＡｌ−Ｓｉ合金はＡｌよりも小さな
熱膨張係数を有し、耐熱性耐摩耗性に優れていることは
良く知られている。過共晶Ａｌ −Ｓｉ合金鋳造材では
Ｓｉが初晶あるいは共晶としてマトリックス中に分散す
ることにより、高温強度や耐摩耗性、耐焼付性に優れた
効果を発揮する。しかし初晶Ｓｉはしばしば粗大結晶と
して晶出するため、延性や衝撃値を低下させ機械加工性
を悪化させる。また摺動材などに使用する場合は相手材
を傷付けるので粗大Ｓｉ晶は避けなければならない。It is well known that an Al-Si alloy of hypereutectic Si generally has a smaller coefficient of thermal expansion than Al and is superior in heat resistance and wear resistance. In hypereutectic Al--Si alloy casting materials, Si is dispersed in the matrix as primary crystals or eutectics, thereby exhibiting excellent high-temperature strength, wear resistance, and seizure resistance. However, since primary Si often crystallizes as coarse crystals, it lowers ductility and impact value and deteriorates machinability. Furthermore, when used in sliding materials, coarse Si crystals must be avoided as they will damage the mating material.
粗大Ｓｉ晶を防ぐ手段として過共晶Ａｌ−Ｓｉ合金を急
冷凝固させて初晶Ｓｉを微細化分散させた合金粉末をつ
くり、押出成形により機械部材に加工する技術が知られ
ている。As a means of preventing coarse Si crystals, a technique is known in which a hypereutectic Al--Si alloy is rapidly solidified to produce an alloy powder in which primary crystal Si is finely dispersed, and the alloy powder is processed into a mechanical member by extrusion molding.
本発明で使用する過共晶Ａｌ−Ｓｉ合金粉末はＦｅ又は
ＭｎあるいはＮｉを添加したものを急冷凝固させたもの
であり、初晶Ｓｉの粗大晶出を抑制すると共にＦｅ又は
ＭｎあるいはＮｉを含む金属間化合物の晶出により耐摩
耗性と高温強度をかね備えたものである。The hypereutectic Al-Si alloy powder used in the present invention is rapidly solidified by adding Fe, Mn, or Ni, and suppresses coarse crystallization of primary Si and also contains Fe, Mn, or Ni. It has both wear resistance and high temperature strength due to the crystallization of intermetallic compounds.
本発明における成分限定理由は次のとおりである。The reasons for limiting the ingredients in the present invention are as follows.
Ｓｉは１０％以下では分散量が少なく、耐熱性や耐摩耗
性に及ぼす効果が不充分である。 ＳｉｌＯ％程度の亜
共晶領域では初晶Ｓｉは晶出せず、微細な共晶組織を呈
するものとなる。Ｓｉ量が増すと共にＳｉ初晶が晶出す
るようになり、耐熱性や耐摩耗性が向上するようになる
。しかしながらＳｉが３０％を越えるといかなる急冷凝
固法を採用して粉末化しても、粗大なＳｉ初晶が消失し
難くなる。急冷速度が１０３℃／ｓｅｅ程度では初晶Ｓ
ｉを微細化するにはＳｉ量を２５％以下にする必要があ
る。If Si is less than 10%, the amount of dispersion is small and the effect on heat resistance and wear resistance is insufficient. In a hypoeutectic region of approximately SilO%, primary Si cannot be crystallized and a fine eutectic structure is exhibited. As the amount of Si increases, primary crystals of Si begin to crystallize, resulting in improved heat resistance and wear resistance. However, if the Si content exceeds 30%, coarse Si primary crystals will be difficult to disappear no matter what rapid solidification method is employed for powdering. When the quenching rate is about 103℃/see, primary S
In order to miniaturize i, it is necessary to reduce the amount of Si to 25% or less.
粗大な初晶Ｓｉ組織を有するＡ１合金粉末は押出成形加
工して使用するに際しては、粉体の圧縮性を著しく悪化
させ圧粉体が作り難くなるほか、熱間押出においても変
形抵抗が大きくなり、大きな押出力を必要とするほか、
押出ダイスの寿命を著しく短縮する結果をもたらす。When A1 alloy powder, which has a coarse primary Si structure, is extruded and used, the compressibility of the powder is significantly deteriorated, making it difficult to form a green compact, and the deformation resistance is also increased during hot extrusion. , in addition to requiring large extrusion force,
This results in a significant reduction in the life of the extrusion die.
従ってＳｉ含有量は１０．０〜３０．０％、゛好ましく
はＳｉ１５．０〜２５．０％とするのが良い。Therefore, the Si content is preferably 10.0 to 30.0%, preferably 15.0 to 25.0%.
Ｆｅ、 Ｍｎ、 Ｎｉは本発明においては重要な成分で
ある。ＦｅまたはＭｎあるいはＮｉはＡｌ中への溶解度
が低くかつ拡散速度が遅いことを利用して微細な化合物
として分散晶出させ高温強度を嵩める目的で添加する。Fe, Mn, and Ni are important components in the present invention. Fe, Mn, or Ni is added for the purpose of increasing high-temperature strength by crystallizing it as a fine compound in a dispersed manner, taking advantage of its low solubility in Al and slow diffusion rate.
Ｆｅ、 Ｍｎ、 Ｎｉ等を固溶限界を越えて添加すると
、Ａｌ−Ｓｉ −（Ｆｅ、 Ｍｎ、）系あるいはＡｌ
−Ｎｔ系の金属間化合物として析出し、その形状は添加
量が多いほど、また冷却速度が遅いほど粗大化する。こ
の金属間化合物は分散急冷凝固法による合金粉末におい
ては棒状組織として存在し、後続の熱間押出工程におい
て分断され、マトリックス中に微細に分散する。この化
合物は高温においても安定でかつ粗大化成長することも
なく、長時間高温保持しても強度の低下はおこらない。When Fe, Mn, Ni, etc. are added beyond the solid solution limit, Al-Si-(Fe, Mn,) system or Al
It precipitates as a -Nt-based intermetallic compound, and its shape becomes coarser as the amount added is larger and the cooling rate is slower. This intermetallic compound exists as a rod-like structure in the alloy powder produced by the dispersion rapid solidification method, and is fragmented in the subsequent hot extrusion step and finely dispersed in the matrix. This compound is stable even at high temperatures, does not grow coarse, and does not lose strength even when kept at high temperatures for a long time.
従ってシリンダーライナー、コンロッド、ロッカーアー
ム、コンプレッサー用ベーン等高温にさらされ、しかも
強度を要求される機械部品用材料として適したものとな
る。Therefore, it is suitable as a material for mechanical parts that are exposed to high temperatures and require strength, such as cylinder liners, connecting rods, rocker arms, and compressor vanes.
Ｆｅ、 Ｍｎ、 Ｎｉの添加量は１．０〜１５．０％、
（ただし２種以−ヒの場合は合計で１．０〜１５．０％
）が適当である。ＦｅまたはＭｎ又は旧添加量が１．０
％以下では高温強度や耐摩耗性に及ぼす効果が認められ
ず、１５％を越えた場合は硬さや耐摩耗性がかえって低
くなり、成形体を作った場合には材質が脆くなる傾向が
ある。The amount of Fe, Mn, and Ni added is 1.0 to 15.0%,
(However, in the case of species 2 or more, the total amount is 1.0 to 15.0%.
) is appropriate. Fe or Mn or old addition amount is 1.0
If it is less than 15%, no effect on high temperature strength or abrasion resistance is observed, and if it exceeds 15%, the hardness and abrasion resistance are rather low, and when a molded article is made, the material tends to become brittle.
本発明におけるＡ１合金では必要に応じてＣｕやＭｇを
添加しても良い、 ＣｕやＭｇはＡ１合金において時効
硬化性を付与して材質を強化する成分として広く使用さ
れており、適正な添加−量はＣｕは０．５〜５．０％、
Ｍｇは０．２〜３．０％の範囲である０本発明において
も溶体化処理温度での固溶限度内の範囲でＣｕやＭｇを
添加することは材質を強化するのに有効である。In the A1 alloy of the present invention, Cu and Mg may be added as necessary. Cu and Mg are widely used in the A1 alloy as ingredients that impart age hardenability and strengthen the material, and appropriate addition. The amount of Cu is 0.5-5.0%,
Mg is in the range of 0.2 to 3.0%. Also in the present invention, adding Cu and Mg within the solid solubility limit at the solution treatment temperature is effective for strengthening the material.
本発明の合金においては高温強度を改善する目的で、さ
らにＴｉ、 Ｚｒ、ＭＯｌＶ、 Ｃｏ、 Ｚｎ、 Ｌｉ
等を少量添加することは何ら支障はない、しかし添加量
があまり多くなると成分管理、溶解温度の上昇など製造
上の問題が生じてくる。In the alloy of the present invention, for the purpose of improving high temperature strength, Ti, Zr, MOLV, Co, Zn, Li
There is no problem in adding a small amount of the same, but if the amount added is too large, manufacturing problems such as component control and increase in melting temperature will arise.
次にＡ１合金中の全ガス量を５ｃｃ７１００ ｇ以下と
したのは、鍛造割れを防止するためである。全ガス量は
４１合金粉末を圧縮成形した段階で５ｃｃ／１００ｇ以
下となっていれば充分である。圧縮成形体の大きさにも
よるが、直径３００ｆｆ１層、長さ５００ｍｍ程度のビ
レットまではビレットの平均値が５ｃｃ／１００ ｇ以
下となっていれば、後続の熱間鍛造や熱処理においてふ
くれや割れが発生することはない。Next, the reason why the total amount of gas in the A1 alloy was set to 5cc7100g or less was to prevent forging cracks. It is sufficient that the total gas amount is 5 cc/100 g or less at the stage of compression molding the 41 alloy powder. Although it depends on the size of the compression molded product, if the average value of the billet is 5cc/100g or less for up to a billet with a diameter of 300ff and 1 layer and a length of about 500mm, there will be no blistering or cracking during subsequent hot forging or heat treatment. will never occur.
Ａ１合金中のＳｉ結晶粒の大きさを１５ＪＪ、Ｉ以下と
したのは、主として初晶Ｓｉの大きさが１５ｐＬｆｆ１
以上になると後続の合金粉末の成形加工性が悪くなり、
材料特性が悪化するからである。The reason why the size of the Si crystal grains in the A1 alloy is set to 15JJ,I or less is mainly because the size of the primary Si is 15pLff1.
If the temperature exceeds that level, the moldability of the subsequent alloy powder will deteriorate.
This is because the material properties deteriorate.
Ａ１合金中の金属間化合物の大きさを２０４ ｒａ以下
としたのは、高温強度とｍ摩耗性を改善するためである
。Ａｌ−Ｓｉ −（Ｆｅ、 Ｎｉ）系あるいはＡｌ−Ｎ
ｉ系金属間化合物の大きさを実質的には５ＡＬｍ以下、
大きなものでも２０ｇｍ以下に微細かつ均一に分散させ
ることにより機械的特性を著しく改善することができる
。金属間化合物とＳｉの微細結晶が混ざり合って均一に
分布していると一段と潰れた効果を発揮する０本発明の
Ａ１合金は先で前記目標組成を有する合金溶湯をアトマ
イズ法、遠心力による微粉化法等の通常用いられている
金属溶湯からの微粉末製造手段を利用して０．５＋ａｍ
以下の粒子サイズに急速分散凝固させて４１合金粉末を
得る。冷却速度は１０３℃７ｓｅｃ程度以上あれば充分
であり、合金成分量が多くなるほど冷却速度を早くしな
いと微細組織は得られない、このようにして得られたＡ
１合金粉末は大きさが１５１Ｌｍ以下のＳ１結晶と成長
を抑制された金属化合物品を有しており、このような組
織の合金を鋳造法で得ることは困難である。The reason why the size of the intermetallic compound in the A1 alloy is set to 204 ra or less is to improve high temperature strength and m-abrasion resistance. Al-Si-(Fe, Ni) system or Al-N
The size of the i-based intermetallic compound is substantially 5 ALm or less,
By finely and uniformly dispersing even large particles to 20 gm or less, mechanical properties can be significantly improved. When the intermetallic compound and Si microcrystals are mixed and distributed uniformly, the effect of crushing is further enhanced.The A1 alloy of the present invention is produced by first atomizing a molten alloy having the target composition, and finely powdering it by centrifugal force. 0.5+am using commonly used means of producing fine powder from molten metal such as
41 alloy powder is obtained by rapid dispersion and solidification to the following particle size. A cooling rate of about 7 seconds or more at 103°C is sufficient, and as the amount of alloy components increases, a microstructure cannot be obtained unless the cooling rate is increased.
1 alloy powder has S1 crystals with a size of 151 Lm or less and metal compound articles whose growth is suppressed, and it is difficult to obtain an alloy with such a structure by a casting method.
次に本発明のＡ１合金は前記４１合金粉末を成形加工し
、脱ガス処理して得られるものである。成形加工に際し
て高温強度、耐摩耗性、耐焼付性を良くするためには、
初晶Ｓｉの大きさ七金属間化合物の大きさが重要な因子
であり、この両者をできる限り微細にする必要がある。Next, the A1 alloy of the present invention is obtained by molding the 41 alloy powder and degassing it. In order to improve high-temperature strength, wear resistance, and seizure resistance during molding,
The size of the primary Si crystal and the size of the seven intermetallic compounds are important factors, and both need to be made as fine as possible.
このような組織を有するＡ１合金粉末成形体は、前記発
明によるＡ１合金粉末を予め圧粉成形し、脱ガスを行っ
た後熱間押出することにより得られる。The A1 alloy powder compact having such a structure can be obtained by compacting the A1 alloy powder according to the invention in advance, degassing it, and then hot extruding it.
圧粉成形は熱間押出の為の準備作業としておこなうもの
であり冷間静水圧プレスあるいは油圧プレス等を用いる
通常の方法で何ら支障はない、油圧プレスを用いる一例
を示せば、合金粉末を２００〜３００℃程度に加熱して
おこなうのが好ましい。Powder compaction is performed as a preparatory work for hot extrusion, and there is no problem with normal methods using cold isostatic presses or hydraulic presses.An example of using a hydraulic press is to compress alloy powder into It is preferable to carry out heating to about 300°C.
３００℃を越えると酸化が著しくなるのでＮ やＡｒ等
の雰囲気中で加工する必要が生じるが、低温では大気中
で可能である。If the temperature exceeds 300°C, oxidation will become significant and processing will need to be carried out in an atmosphere of N2, Ar, etc., but processing can be carried out in the air at low temperatures.
成形圧力は０．５ｗ ５ ｔｏｎ／ ｃ ｒｎ’程度
が適当で、圧粉体密度が真密度の７０％以上となるよう
にする。Appropriate compacting pressure is about 0.5 w 5 ton/c rn', and the green compact density is set to be 70% or more of the true density.
脱ガス工程は１本発明において最も重要な工程である。The degassing step is the most important step in the present invention.
ガス成分はＡ１合金粉末を製造する工程において、たと
えばエアー７トマイズ法によった場合、膨大な表面積を
もった粉末は空気中の水蒸気により約５０ｃｃ／ （１
００ｇ Ａ１合金）もの大量のガスを含有している。こ
のアトマイズ粉を加熱し、ついで圧粉成形を行い、ビレ
ットとし従来法の如く大気中で熱間押出を行ったＡ１合
金材料中のガス量は１０〜２０ｃｃ７１００ ｇと低下
はするが、この値は鍛造Ａｌ中のガス量が０．ｔ 〜０
．３ ｃｃ７１００ ｇとくらべると約１００倍にも達
する。In the process of producing A1 alloy powder, for example, when the air totomization method is used, the gas component is reduced to about 50 cc/(1
00g A1 alloy). This atomized powder is heated, then compacted, and made into a billet. The amount of gas in the A1 alloy material, which is hot extruded in the atmosphere as in the conventional method, is 10 to 20 cc7100 g, although this value is The amount of gas in forged Al is 0. t~0
．． Compared to 3cc7100g, it is about 100 times larger.
１０〜２０ｃｃ／ １００ ｇのガス量をもつＡ１合金
は、４５０℃以上に加熱すると合金表面にガス成分によ
るフクレ（ブリスター）が発生したり１合金内部に数周
〜数１００ＩＬの空孔を発生する。このためこの合金を
鍛造する場合、約４５０℃−以上に加熱するとこのブリ
スターのため製品表面に割れが発生したり、あるいは形
が壊れたりして製品を得ることが出来ない６本発明は、
この鍛造割れの原因となるガス成分を除去することによ
る鍛造用Ａ１合金に関するものである。When an A1 alloy with a gas amount of 10 to 20 cc/100 g is heated above 450°C, blisters will occur on the alloy surface due to the gas component, and pores of several circles to several hundred IL will be generated inside the alloy. . Therefore, when forging this alloy, if it is heated above about 450°C, cracks will occur on the surface of the product due to the blisters, or the shape will break, making it impossible to obtain the product.
This invention relates to an A1 alloy for forging by removing gas components that cause forging cracks.
本発明に使用する脱ガス法は、カンの中に粉末を入れて
真空とし脱ガスするキャニング法が良く知られている。The degassing method used in the present invention is a well-known canning method in which powder is placed in a can and evacuated to degas it.
その他の方法としては真空中又はＡｒ、 Ｎ２中のよ
うな不活性雰囲気中にて圧粉成形ビレットを４００〜５
２０℃に加熱する方法も利用できる。４００℃以下では
付着したガス成分（主としてＮ２０とＮ２）は、温度が
低過ぎて脱ガスは期待出来ない、又５２０℃以上では合
金組成によっては溶融する場合もあり溶融しない場合で
も急冷凝固により微細化したＳｉ晶、金属間化合物粒子
の粗大化が起り好ましくはない。Another method is to compress the powder-formed billet in vacuum or in an inert atmosphere such as Ar or N2.
A method of heating to 20°C can also be used. At temperatures below 400℃, the adhered gas components (mainly N20 and N2) cannot be expected to degas because the temperature is too low, and above 520℃, depending on the alloy composition, they may melt, and even if they do not melt, they become fine due to rapid solidification. This is not preferable because the resulting Si crystals and intermetallic compound particles become coarse.
真空の場合、真空度は０．１気圧以下、好ましくは０．
Ｏ１気圧以下にする必要がある。In the case of vacuum, the degree of vacuum is 0.1 atmosphere or less, preferably 0.1 atmosphere.
It is necessary to keep the O pressure below 1 atmosphere.
固な成形体に加工するための工程である。This is a process for processing into a hard molded body.
熱間押出は合金粉末中に晶出している初晶Ｓｉ相、共晶
相、金属間化合物相の結晶相を微細化し、材料としての
機械的特性を改善すると同時に、強固な成形体に加工す
るための工程である。Hot extrusion refines the primary Si phase, eutectic phase, and intermetallic compound phase crystallized in the alloy powder, improves the mechanical properties of the material, and at the same time processes it into a strong compact. This is a process for
熱間押出は３５０℃以上の温度領域でおこなう。Hot extrusion is performed in a temperature range of 350°C or higher.
これは圧粉体の加工が容易な範囲で粒子間結合を促進さ
せて強固な成形体にするためである。さらに過飽和固溶
分の元素を微細析出させるとともに、初晶Ｓｉや金属間
化合物の棒状組織を分断して微細化し、成形体の強度と
耐摩耗性を改善するためである。This is to promote interparticle bonding within a range where the green compact can be easily processed to form a strong compact. Furthermore, the purpose is to finely precipitate the elements in the supersaturated solid solution, and to divide and refine the rod-like structure of primary crystal Si and intermetallic compounds, thereby improving the strength and wear resistance of the compact.
本発明により得られた合金粉末成形体に各種の熱処理を
施し、材料特性をさらに改善することは何ら支障はない
、また１本発明により得られた成形体はシリンダーライ
ナーやスリーブのごとき部材としてそのまま使用しても
良いし、この成形体を素材として更に機械加工や熱間鍛
造あるいは冷間鍛造を施こして機械部品としても良い。There is no problem in further improving the material properties by subjecting the alloy powder compact obtained by the present invention to various heat treatments. The molded body may be used as a raw material and further subjected to machining, hot forging, or cold forging to be made into a mechanical part.
本発明による脱ガス処理を行って生産されたＡ１合金粉
末成形体のガス量は１〜５ ｃｃ／ １００ ｇであり
、未処理のものにくらべ１／２〜ｌ／２０に減少してい
る。ＷＩ造Ａｌにくらべると依然として１０倍から５０
倍程度となっているが５００℃に加熱してもブリスター
の発生もなく何ら実用上問題もない、脱ガス押出材は従
来の未脱ガス材にくらべると特に高温での伸びが改善さ
れており、このため熱間鍛造時の材料流れを容易とし割
れの発生を防止する。また本発明によるＡ１合金粉末成
形体は従来のＡｌ合金粉末成形体品に比較して高温強度
も若干ではあるが改善されており、耐摩耗性、耐焼付性
、耐応力腐食割性にも優れたものである。ざらに庁擦係
数が小さいので高温で使用され、かつ耐摩耗性が要求さ
れる摺動部材として最適なものである。用途としてはシ
リンダーライナーやコンロッド、ピストン、ロッカーア
ーム等の自動車部品、コンプレッサー用ベーン、ライナ
ー、バルブプレート等の油・空圧機器部品、ＶＴＲ用ド
ラム、軸受等の家電用部品、事務機器用のギヤー、スイ
ッチ、カム、クラッチハブ等の精密部品などのほか、航
空機や宇宙産業用の広範囲の用途が期待される。The gas amount of the A1 alloy powder compact produced by performing the degassing treatment according to the present invention is 1 to 5 cc/100 g, which is reduced to 1/2 to 1/20 of that of the untreated compact. It is still 10 to 50 times cheaper than WI-built aluminum.
Although the temperature is about twice as high, there is no problem in practical use, with no blistering occurring even when heated to 500℃.Degassed extruded materials have particularly improved elongation at high temperatures compared to conventional non-degassed materials. This facilitates material flow during hot forging and prevents cracks from occurring. In addition, the A1 alloy powder compact according to the present invention has slightly improved high-temperature strength compared to conventional Al alloy powder compacts, and has excellent wear resistance, seizure resistance, and stress corrosion cracking resistance. It is something that Since it has a relatively small coefficient of friction, it is ideal for sliding members that are used at high temperatures and require wear resistance. Applications include automobile parts such as cylinder liners, connecting rods, pistons, and rocker arms, oil and pneumatic equipment parts such as compressor vanes, liners, and valve plates, home appliance parts such as VTR drums and bearings, and gears for office equipment. In addition to precision parts such as switches, cams, and clutch hubs, it is expected to have a wide range of applications in the aircraft and space industries.
次に実施例をあげて本発明を説明する。Next, the present invention will be explained with reference to Examples.
実施例
表−１に示す組成の高Ｓｉアルミニウム合金溶湯をエア
ーアトマイズして一４８ｓｅｇｈの粉末とした。Example A molten high-Si aluminum alloy having the composition shown in Table 1 was air atomized to form a powder of 148 segh.
次にこれらのＡ１合金粉末を加熱して１．５ｔｏｎ ／
ｃｒｎ’の圧力で圧縮成形して直径２０４謬■、長さ２
００Ｉ！ｍのビレットとした。Next, these A1 alloy powders are heated to 1.5 tons/
Compression molded at crn' pressure, diameter 204mm, length 2
00I! It was made into a billet of m.
（以下余白）
次にこれらのビレット１０本を脱ガス炉に入れ、アルゴ
ンガス流量２（ＩｆＬ／ａ＋ｉｎ中で４８０℃、８０分
加熱して脱ガスを行った。(Left below) Next, these 10 billets were placed in a degassing furnace, and degassed by heating at 480° C. for 80 minutes in an argon gas flow rate of 2 (IfL/a+in).
次にこれらのビレットを４００℃にし、同温度に予熱保
持された内径２０６ＩＩｌ１１のコンテナー中に挿入し
、直径５０ａ＋ｍのダイスで間接押出法により押出（押
出比＝１７）して成形体を得た。これらの成形体をＴ
処理あるいは３００℃Ｘ１００Ｈｒの熱処理（０）を施
こした後、標点間距離５０ｍｍ、平行部直径６ＩＩｍの
引張試験片に加工して室温から２５０℃までの温度で引
張試験を実施した。引張試験は各試験温度で試料を１０
０Ｈｒ保持した後に実施した。さらに各温度での引張試
験終了後の試験片のチャック部の端部を使用して硬さ測
定を行った。また室温試験の試片を切断し顕微値組−観
察をして結晶組織の大きさを測定した。これらの結果を
表−１にまとめて示す。Next, these billets were heated to 400° C., inserted into a container with an inner diameter of 206II11 and preheated at the same temperature, and extruded by indirect extrusion (extrusion ratio = 17) using a die with a diameter of 50a+m to obtain a molded body. These molded bodies are T
After treatment or heat treatment (0) at 300° C. for 100 hours, it was processed into a tensile test piece with a gage distance of 50 mm and a parallel part diameter of 6 II m, and a tensile test was conducted at temperatures from room temperature to 250° C. The tensile test was conducted by testing 10 samples at each test temperature.
It was carried out after holding for 0 hours. Further, after the tensile test at each temperature, the hardness was measured using the end of the chuck part of the test piece. In addition, specimens tested at room temperature were cut and microscopically observed to measure the size of the crystal structure. These results are summarized in Table-1.
また同じ試験片を真空溶融抽出法（ステンレスパイプ使
用）にてガス分析を行ったところ表−２の結果となった
。When the same test piece was subjected to gas analysis using a vacuum melt extraction method (using a stainless steel pipe), the results shown in Table 2 were obtained.
表−２
次に前記熱間押出成形体を切断し、熱間鍛造により直径
７０ｍｍ、長さ１０ＩＩＩ１１の素−材を作り、機械加
工により各種試験片を作って耐摩耗性試験、耐焼付性試
験、摩擦係数測定を実施した。Table 2 Next, the hot extrusion molded body was cut, and a material with a diameter of 70 mm and a length of 10III11 was made by hot forging, and various test pieces were made by machining to perform wear resistance tests and seizure resistance tests. , the friction coefficient was measured.
耐摩耗性試験は直径７０ｍｍの円板状試片に５×５Ｘ１
０ｍｍのＣｒメッキを施こした球状黒鉛鋳鉄を相手材と
して使用し、速度５ｍ／ｓｅｃ 、押圧１００Ｋｇ／ｃ
ｒｎ’ 、摺動圧ｇｉ ５００Ｋｍとして摩耗量を測
定した。The abrasion resistance test was performed using a 5x5x1 disk-shaped specimen with a diameter of 70mm.
Spheroidal graphite cast iron with 0mm Cr plating was used as the mating material, speed 5m/sec, pressing force 100Kg/c.
The amount of wear was measured with rn' and a sliding pressure gi of 500 Km.
なお、潤滑油として摺動面に５ＡＥ２０エンジンオイル
（温度９０℃）を５００ｍ１／ｍｉｎ滴下した。Note that 5AE20 engine oil (temperature 90° C.) was dropped onto the sliding surface as a lubricating oil at a rate of 500 ml/min.
耐焼付性テストは前記耐摩耗性試験と同様にして抑圧を
１００Ｋｇ／ ｃ ｍ”から５Ｋｇ／ ｃ ｍ” ＊
ｌ１ｉｎの割合で増加させ焼付が発生する時の面押圧
を測定した。The seizure resistance test was conducted in the same way as the wear resistance test above, and the suppression was from 100Kg/cm" to 5Kg/cm" *
The surface pressure when seizure occurred was measured by increasing the pressure at a rate of 1 inch.
摩擦係数は耐摩耗性試験において２００Ｋｍ走行時点で
のトルクを測定し算出した。The friction coefficient was calculated by measuring the torque at the time of running 200 km in the wear resistance test.
これらの結果を表−３に示す。These results are shown in Table 3.
（以下余白）
表 ３
また供試材Ｎｏ１〜５について熱間鍛造を行った。直径
５０ｍｍの押出材を長さ１００ｍｍに切断し、４８０℃
に加熱した。これを３５０°Ｃ加熱した金型により １
００ｍｍ／ｓｅｃの速度にて直径８０ｍｍの自動車用ピ
ストンを作成した。押出素材中のガス成分が少ないため
４８０℃に加熱してもブリスターの発生がなく、かつサ
ンプルが高温状態で良好な伸びを持つため、Ｎｏｔ〜Ｎ
Ｏ５の５コのピストンは割れの発生のない良好なものが
得られた。(The following is a blank space) Table 3 Hot forging was also performed on sample materials Nos. 1 to 5. Extruded material with a diameter of 50 mm was cut into lengths of 100 mm and heated at 480°C.
heated to. This is heated to 350°C in a mold. 1
An automobile piston with a diameter of 80 mm was produced at a speed of 0.00 mm/sec. Because the extruded material has a small gas component, no blisters occur even when heated to 480°C, and the sample has good elongation at high temperatures, resulting in Not~N
Five O5 pistons were found to be in good condition with no cracking.
以上の結果から本発明のＡ１合金粉末成形体は高温強度
、耐摩耗性、耐焼付性に優れ、しかも熱間鍛造性が良好
な材料であることは明らかである。From the above results, it is clear that the A1 alloy powder compact of the present invention is a material that has excellent high temperature strength, wear resistance, and seizure resistance, and also has good hot forgeability.
Claims (1)
５．０％またはＭｎ１．０〜１５．０％またはＮｉ１．
０〜１５．０％のうち１種または２種以上（２種以上の
場合は合計で１．０〜１５．０％）と、さらに必要に応
じてＣｕ０．５〜５．０％およびＭｇ０．２〜３．０％
残部が不可避的不純物を含むＡｌとからなる合金溶湯の
分散急冷凝固粉末押出材であり、Ｓｉ結晶粒の大きさが
１５μｍ以下であり、かつ金属間化合物の大きさが２０
μｍ以下に微細化分散した組織を有し、全ガス量が５ｃ
ｃ／１００ｇ以下であることを特徴とする熱間鍛造用ア
ルミニウム合金。Weight ratio: Si10.0-30.0%, Fe1.0-1
5.0% or Mn1.0-15.0% or Ni1.
One or more of 0 to 15.0% (in the case of two or more, the total is 1.0 to 15.0%), and if necessary, Cu0.5 to 5.0% and Mg0. 2-3.0%
This is a dispersed rapidly solidified powder extruded material of a molten alloy consisting of Al, the remainder of which contains unavoidable impurities, in which the size of Si crystal grains is 15 μm or less, and the size of intermetallic compounds is 20 μm or less.
It has a finely dispersed structure of less than μm, and the total gas amount is 5c.
An aluminum alloy for hot forging, characterized in that it is less than c/100g.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60149192A JPS6210237A (en) | 1985-07-09 | 1985-07-09 | Aluminum alloy for hot forging |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60149192A JPS6210237A (en) | 1985-07-09 | 1985-07-09 | Aluminum alloy for hot forging |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6210237A true JPS6210237A (en) | 1987-01-19 |
Family
ID=15469816
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60149192A Pending JPS6210237A (en) | 1985-07-09 | 1985-07-09 | Aluminum alloy for hot forging |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6210237A (en) |
Cited By (22)
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|---|---|---|---|---|
| JPS6230839A (en) * | 1985-07-30 | 1987-02-09 | Sumitomo Light Metal Ind Ltd | Heat-and wear-resisting aluminum alloy stock suitable for hot working |
| JPS62185857A (en) * | 1986-02-12 | 1987-08-14 | Honda Motor Co Ltd | Heat resistant and high strength aluminum alloy |
| JPH01123245A (en) * | 1987-11-06 | 1989-05-16 | Minolta Camera Co Ltd | Organic lamination type photosensitive body |
| JPH01180938A (en) * | 1988-01-12 | 1989-07-18 | Ryobi Ltd | Wear-resistant aluminum alloy |
| JPH01247546A (en) * | 1988-03-30 | 1989-10-03 | Showa Denko Kk | Aluminum-based composite material and its manufacture |
| JPH01255640A (en) * | 1988-04-01 | 1989-10-12 | Honda Motor Co Ltd | Sliding member made of sintered al alloy |
| JPH01255641A (en) * | 1988-04-01 | 1989-10-12 | Honda Motor Co Ltd | Sliding member made of sintered al alloy |
| JPH0254737A (en) * | 1988-08-18 | 1990-02-23 | Hiroshima Alum Kogyo Kk | Forgings made of al alloy and its manufacture |
| JPH02149632A (en) * | 1988-11-30 | 1990-06-08 | Showa Alum Corp | Low thermal expansion aluminum alloy having excellent wear resistance and heat conductivity |
| JPH04323343A (en) * | 1991-04-24 | 1992-11-12 | Showa Alum Corp | Aluminum alloy excellent in wear resistance |
| JPH04365833A (en) * | 1991-06-14 | 1992-12-17 | Mitsubishi Materials Corp | Hot forged al-si alloy member having high toughness |
| JPH055146A (en) * | 1991-06-26 | 1993-01-14 | Showa Alum Corp | Aluminum alloy excellent in wear resistance and thermal conductivity |
| JPH055147A (en) * | 1991-06-26 | 1993-01-14 | Showa Alum Corp | Low thermal expansion aluminum alloy excellent in wear resistance |
| JPH07138614A (en) * | 1993-06-03 | 1995-05-30 | Mazda Motor Corp | Production of plastically worked and molded goods |
| US5545487A (en) * | 1994-02-12 | 1996-08-13 | Hitachi Powdered Metals Co., Ltd. | Wear-resistant sintered aluminum alloy and method for producing the same |
| JPH08246087A (en) * | 1994-10-28 | 1996-09-24 | Mercedes Benz Ag | Cylinder bush made of hyper-eutectic aluminum/ silicon alloy and used for casting into crank case of reciprocating piston engine and preparation thereof |
| US6096143A (en) * | 1994-10-28 | 2000-08-01 | Daimlerchrysler Ag | Cylinder liner of a hypereutectic aluminum/silicon alloy for use in a crankcase of a reciprocating piston engine and process for producing such a cylinder liner |
| JP2006328482A (en) * | 2005-05-26 | 2006-12-07 | Honda Motor Co Ltd | Forged piston |
| JP2017078213A (en) * | 2015-10-21 | 2017-04-27 | 昭和電工株式会社 | Aluminum alloy powder for hot forging for slide component, method for producing the same, aluminum alloy forging for slide component, and method for producing the same |
| JP2017222893A (en) * | 2016-06-13 | 2017-12-21 | 昭和電工株式会社 | Aluminum alloy forging article and manufacturing method therefor |
| JP2019026859A (en) * | 2017-07-25 | 2019-02-21 | 昭和電工株式会社 | Aluminum alloy forging article for high speed moving component, and manufacturing method therefor |
| JP2021008651A (en) * | 2019-07-01 | 2021-01-28 | スズキ株式会社 | Aluminum alloy working material and method for manufacturing the same |
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| JPS5913040A (en) * | 1982-07-12 | 1984-01-23 | Showa Denko Kk | Heat- and wear-resistant high-strength aluminum alloy powder and molded body of said alloy powder and their manufacture |
| JPS5913041A (en) * | 1982-07-12 | 1984-01-23 | Showa Denko Kk | Aluminum alloy powder having high resistance to heat and abrasion and high strength and molding of said alloy powder and its production |
| JPS5966918A (en) * | 1982-10-12 | 1984-04-16 | Showa Denko Kk | Double layer structure hollow member made of aluminum alloy |
| JPS60121203A (en) * | 1983-12-02 | 1985-06-28 | Sumitomo Electric Ind Ltd | Manufacture of aluminum alloy material |
| JPS60125345A (en) * | 1983-12-09 | 1985-07-04 | Sumitomo Electric Ind Ltd | Aluminum alloy having high heat resistance and wear resistance and manufacture thereof |
| JPS60204805A (en) * | 1984-03-29 | 1985-10-16 | Nissan Motor Co Ltd | Locking bolt for component parts of aluminum alloy engine |
| JPS60208443A (en) * | 1984-03-31 | 1985-10-21 | Sumitomo Light Metal Ind Ltd | Aluminum alloy material |
| JPS61166931A (en) * | 1985-01-17 | 1986-07-28 | Sumitomo Light Metal Ind Ltd | Method for molding al-si alloy powder |
-
1985
- 1985-07-09 JP JP60149192A patent/JPS6210237A/en active Pending
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5913040A (en) * | 1982-07-12 | 1984-01-23 | Showa Denko Kk | Heat- and wear-resistant high-strength aluminum alloy powder and molded body of said alloy powder and their manufacture |
| JPS5913041A (en) * | 1982-07-12 | 1984-01-23 | Showa Denko Kk | Aluminum alloy powder having high resistance to heat and abrasion and high strength and molding of said alloy powder and its production |
| JPS5966918A (en) * | 1982-10-12 | 1984-04-16 | Showa Denko Kk | Double layer structure hollow member made of aluminum alloy |
| JPS60121203A (en) * | 1983-12-02 | 1985-06-28 | Sumitomo Electric Ind Ltd | Manufacture of aluminum alloy material |
| JPS60125345A (en) * | 1983-12-09 | 1985-07-04 | Sumitomo Electric Ind Ltd | Aluminum alloy having high heat resistance and wear resistance and manufacture thereof |
| JPS60204805A (en) * | 1984-03-29 | 1985-10-16 | Nissan Motor Co Ltd | Locking bolt for component parts of aluminum alloy engine |
| JPS60208443A (en) * | 1984-03-31 | 1985-10-21 | Sumitomo Light Metal Ind Ltd | Aluminum alloy material |
| JPS61166931A (en) * | 1985-01-17 | 1986-07-28 | Sumitomo Light Metal Ind Ltd | Method for molding al-si alloy powder |
Cited By (24)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6230839A (en) * | 1985-07-30 | 1987-02-09 | Sumitomo Light Metal Ind Ltd | Heat-and wear-resisting aluminum alloy stock suitable for hot working |
| JPS62185857A (en) * | 1986-02-12 | 1987-08-14 | Honda Motor Co Ltd | Heat resistant and high strength aluminum alloy |
| JPH01123245A (en) * | 1987-11-06 | 1989-05-16 | Minolta Camera Co Ltd | Organic lamination type photosensitive body |
| JPH01180938A (en) * | 1988-01-12 | 1989-07-18 | Ryobi Ltd | Wear-resistant aluminum alloy |
| JPH01247546A (en) * | 1988-03-30 | 1989-10-03 | Showa Denko Kk | Aluminum-based composite material and its manufacture |
| JPH01255640A (en) * | 1988-04-01 | 1989-10-12 | Honda Motor Co Ltd | Sliding member made of sintered al alloy |
| JPH01255641A (en) * | 1988-04-01 | 1989-10-12 | Honda Motor Co Ltd | Sliding member made of sintered al alloy |
| JPH0254737A (en) * | 1988-08-18 | 1990-02-23 | Hiroshima Alum Kogyo Kk | Forgings made of al alloy and its manufacture |
| JPH02149632A (en) * | 1988-11-30 | 1990-06-08 | Showa Alum Corp | Low thermal expansion aluminum alloy having excellent wear resistance and heat conductivity |
| JPH0480108B2 (en) * | 1988-11-30 | 1992-12-17 | Showa Aluminium Co Ltd | |
| JPH04323343A (en) * | 1991-04-24 | 1992-11-12 | Showa Alum Corp | Aluminum alloy excellent in wear resistance |
| JPH04365833A (en) * | 1991-06-14 | 1992-12-17 | Mitsubishi Materials Corp | Hot forged al-si alloy member having high toughness |
| JPH055146A (en) * | 1991-06-26 | 1993-01-14 | Showa Alum Corp | Aluminum alloy excellent in wear resistance and thermal conductivity |
| JPH055147A (en) * | 1991-06-26 | 1993-01-14 | Showa Alum Corp | Low thermal expansion aluminum alloy excellent in wear resistance |
| JPH07138614A (en) * | 1993-06-03 | 1995-05-30 | Mazda Motor Corp | Production of plastically worked and molded goods |
| US5545487A (en) * | 1994-02-12 | 1996-08-13 | Hitachi Powdered Metals Co., Ltd. | Wear-resistant sintered aluminum alloy and method for producing the same |
| JPH08246087A (en) * | 1994-10-28 | 1996-09-24 | Mercedes Benz Ag | Cylinder bush made of hyper-eutectic aluminum/ silicon alloy and used for casting into crank case of reciprocating piston engine and preparation thereof |
| US6096143A (en) * | 1994-10-28 | 2000-08-01 | Daimlerchrysler Ag | Cylinder liner of a hypereutectic aluminum/silicon alloy for use in a crankcase of a reciprocating piston engine and process for producing such a cylinder liner |
| US6309480B1 (en) * | 1994-10-28 | 2001-10-30 | Daimlerchrysler Ag | Cylinder liner comprising a supereutectic aluminum/silicon alloy for sealing into a crankcase of a reciprocating piston engine |
| JP2006328482A (en) * | 2005-05-26 | 2006-12-07 | Honda Motor Co Ltd | Forged piston |
| JP2017078213A (en) * | 2015-10-21 | 2017-04-27 | 昭和電工株式会社 | Aluminum alloy powder for hot forging for slide component, method for producing the same, aluminum alloy forging for slide component, and method for producing the same |
| JP2017222893A (en) * | 2016-06-13 | 2017-12-21 | 昭和電工株式会社 | Aluminum alloy forging article and manufacturing method therefor |
| JP2019026859A (en) * | 2017-07-25 | 2019-02-21 | 昭和電工株式会社 | Aluminum alloy forging article for high speed moving component, and manufacturing method therefor |
| JP2021008651A (en) * | 2019-07-01 | 2021-01-28 | スズキ株式会社 | Aluminum alloy working material and method for manufacturing the same |
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