JPS61186443A - High strength, heat and wear resistant al alloy - Google Patents

Abstract

PURPOSE:To obtain a high strength Al alloy having superior heat and wear resistances, satisfactory hot workability and machinability as well as superior strength at ordinary and high temps. by blending Al with specified amounts of Si and Cu. CONSTITUTION:The composition of an Al alloy is composed of,by weight, 12-30% Si, 2-10% Cu and the balance Al with inevitable impurities. The composition may further contain one or more kinds of alloying elements selected among 2-15% Mn, 0.5-8% Fe, 0.5-3% Ni, 0.1-1% Zr and 0.1-3% Cr.

Description

【発明の詳細な説明】 ［産業上の利用分野］ 本発明は常温強度及び耐熱性の優れたＡ１合金に関し、
詳細には高温強度の低下を招かず熱間加工性や切削加工
性等においても優れた特性を発揮する高力耐熱耐摩耗性
Ａ１合金に関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to an A1 alloy with excellent room temperature strength and heat resistance,
Specifically, the present invention relates to a high-strength, heat-resistant and wear-resistant A1 alloy that exhibits excellent properties in terms of hot workability, cutting workability, etc. without causing a decrease in high-temperature strength.

［従来の技術］ 各種車両に搭載されるエンジンやカーエアコン用コンプ
レッサー等については、近年の軽量化要請を受け、Ａ１
合金製４品の開発が進められている。この様なＡｌ合金
化は、車両重量の軽減化に伴なう燃費向上に市まらず、
熱伝導率の面で鋳鉄製４品を陵忽するところから放熱性
の向上等も期待されている。[Conventional technology] In response to recent demands for weight reduction in engines installed in various vehicles and compressors for car air conditioners, A1
Four alloy products are currently being developed. This kind of Al alloying is not only effective in improving fuel efficiency by reducing vehicle weight, but also
It is expected to improve heat dissipation as it is comparable to the four cast iron products in terms of thermal conductivity.

車両用Ａ１合金として特に高い期待が寄せられているの
は高Ｓｉ含有Ａ１合金であり、耐摩耗性の優秀さや熱膨
張率の低さ等の面で有望視され、特に摺動部材への適用
が進んでいる。しかしながら従来の開発されている高Ｓ
ｉ含有Ａ１合金では熱間加工時の割れや切削加工性が問
題とされており、これらの改善が当面の解決課題となっ
ている。The high-Si content A1 alloy has particularly high expectations as an A1 alloy for vehicles, and is seen as promising due to its excellent wear resistance and low coefficient of thermal expansion, and is especially suitable for application to sliding parts. is progressing. However, conventionally developed high S
The i-containing A1 alloy has problems with cracking during hot working and machinability, and improvement of these issues is an immediate problem.

［発明が解決しようとする問題点］ 従来の高Ｓｉ含有Ａ１合金が上述の如き問題点を有する
ことの原因については種々検討されており、溶解鋳造法
で製造するときの冷却速度が遅く初晶Ｓｔが巨大粒とし
て成長するからであろうという点で一致を見ている。そ
こで急冷凝固の期待される粉末冶金法が応用されるに及
び、初晶Ｓｉの微細分散が達成されて熱間加工性や切削
加工性の低下といった問題点が解消される様になった。[Problems to be solved by the invention] Various studies have been conducted on the causes of the above-mentioned problems in the conventional high-Si content A1 alloy. There is a consensus that this is probably because St grows as giant grains. With the application of powder metallurgy, which is expected to achieve rapid solidification, fine dispersion of primary Si has been achieved, and problems such as poor hot workability and machinability have been solved.

また粉末冶金法では、従来の溶解鋳造法では得られなか
った様な高Ｓｉ含有量を達成することもでき、これまで
開発されていない様な新合金の製造も期待される。In addition, the powder metallurgy method can achieve a high Si content that could not be obtained with the conventional melting and casting method, and is expected to produce new alloys that have not been developed so far.

この様な状況下で既に幾つかの新合金が提案されており
１代表的なものとして特開昭５９−１３０４０が挙げら
れる。この提案によるとＡ１合金中に大量のＳｉを添加
して耐摩耗性を向上するだけでなく、ＦｅやＭｎの添加
による耐熱性の向上、ＣｕやＭｇの添加による時効硬化
の発現まども試みられている。即ちＡＩマトリックス中
に加えられたＣｕは一般にＡＩとの金属間化合物（Ｃｕ
Ａ１２）を形成し、これがマトリックスとの整合析出物
（ＧＰゾーン）や部分的整合析出物（θ′）として析出
するため時効硬化を発現する。Under these circumstances, several new alloys have already been proposed, and one representative example is JP-A-59-13040. According to this proposal, in addition to improving wear resistance by adding a large amount of Si to A1 alloy, it was also attempted to improve heat resistance by adding Fe and Mn, and to cause age hardening by adding Cu and Mg. ing. That is, Cu added to the AI matrix generally forms an intermetallic compound with AI (Cu
A12) is formed, and this precipitates as a coherent precipitate (GP zone) or a partially coherent precipitate (θ') with the matrix, thereby causing age hardening.

一方Ｍｇ自体は単独添加による時効効果は殆んど発揮し
ないものの、Ｃｕ等との複合的添加によって時効硬化を
促進する方向に作用することが知られている。従って上
記公開公報の提案に係る合金は十分な時効硬化を発現す
るはずなのであるが、添加されたＭｇはＳｔとも結合す
る性質を有し、Ｉｉ＃摩耗性向上元素として期待されて
いるＳｔを消費（Ｍｇ２Ｓｉを形成）する結果、微細初
晶Ｓｉ粒子の形成を阻害して耐摩耗性の向上が不十分に
終るということが分かってきた。On the other hand, although Mg itself exhibits almost no aging effect when added alone, it is known that Mg acts in the direction of promoting age hardening when added in combination with Cu or the like. Therefore, the alloy proposed in the above publication should exhibit sufficient age hardening, but the added Mg has the property of also bonding with St, consuming St, which is expected to be an element that improves Ii# wear properties. It has been found that as a result of (forming Mg2Si), the formation of fine primary Si particles is inhibited, resulting in insufficient improvement in wear resistance.

そこで本発明者等は次の２つの方向からアプローチする
ことを考え、 （１）原則的にＭｇ非配合とし、他に好適な合金元素を
添加して耐摩耗性及び時効硬化の十分な発現を狙う、 （２）Ｍｇの含有量を低下し、他の合金元素の適正配合
を付加して同上の効果を狙う、 という観点で研究、を行なった６本発明は（１）のアプ
ローチに基づいて完成された発明であり、（２）のアプ
ローチに基づ〈発明は別途特許出願した。Therefore, the present inventors considered an approach from the following two directions: (1) In principle, Mg is not added, and other suitable alloying elements are added to achieve sufficient wear resistance and age hardening. (2) Aiming for the same effect by lowering the Mg content and adding an appropriate blend of other alloying elements.6 The present invention is based on the approach (1). This is a completed invention, and a separate patent application was filed for the invention based on approach (2).

［問題点を解決する為の手段］ Ｓｉ：１２〜３０％＜ｇＬ量％の意味、以下回）Ｃｕ：
２　Ｎ１０％ 残部：Ａｌ及び不可避不純物 であり、これによって耐摩耗性の向上と時効硬化の発現
を同時的に達成し、熱間加工性や切削加工性の向上に寄
与することがでさた。又更に下記合金元素群から選択さ
れる１種以上の元素を配合することにより材料特性の一
層の向上を果たすことができた。[Means for solving the problem] Si: 12-30% < Meaning of gL amount %, below) Cu:
2 N10% Balance: Al and unavoidable impurities, which simultaneously achieved improvement in wear resistance and expression of age hardening, contributing to improvement in hot workability and cutting workability. Furthermore, by blending one or more elements selected from the following alloying element group, the material properties could be further improved.

Ｍｎ：２〜１５％ Ｆ　ｅ　　：　０．５　〜８％ Ｎｉ：０．５　〜３％ Ｚｒ：０．１−１．０％ Ｃｒ　　：　０．１　〜３％ ［作用］ 本発明における合金元素の種類並びに配合量を選定した
理由を述べることによって本発明の作用効果を説明する
。尚本発明合金は上記説明の趣旨から明白である様に粉
末冶金法で製造するという技術の延長上にある。即ち粉
末冶金法では粉末製造時の凝固速度が溶解鋳造法におけ
る凝固速度に比べて著しく速い、その為各合金元素の固
溶度が、　増大し、又金属粒子や各種金属間化合物を微
細に均一分散させることができ、その結果として強度、
耐熱性、熱間加工性、切削加工性等の開時性が改善され
るとの期待があり、本発明の目的を達成する上で適合性
が高いからである。従って高Ｓ【含有Ａｌ合金自体の製
造も可能であり、更に固化成形法が容易であるという点
においても粉末冶金法の利点を見出すことができる。そ
して粉末冶金法において溶融状態から固相状態へ変態さ
せるときの冷却速度は１０２に／ｓｅｃ以上、好ましく
は１０　’　Ｋ／ｓｅｃ以上とし、アトマイズ粉末に限
られず、急冷薄片や急冷薄帯を粉砕して得られる粉末等
も適用できる。Mn: 2-15% Fe: 0.5-8% Ni: 0.5-3% Zr: 0.1-1.0% Cr: 0.1-3% [Function] The alloying elements in the present invention The effects of the present invention will be explained by describing the reasons for selecting the types and blending amounts. As is clear from the purpose of the above description, the alloy of the present invention is an extension of the technology of manufacturing by powder metallurgy. In other words, in the powder metallurgy method, the solidification rate during powder production is significantly faster than that in the melt casting method, which increases the solid solubility of each alloying element and makes it possible to finely and uniformly form metal particles and various intermetallic compounds. can be dispersed, resulting in strength,
This is because it is expected to improve opening properties such as heat resistance, hot workability, cutting workability, etc., and is highly compatible with achieving the object of the present invention. Therefore, the advantages of the powder metallurgy method can be found in that it is possible to manufacture a high S content Al alloy itself, and furthermore, the solidification molding method is easy. In the powder metallurgy method, the cooling rate when transforming from a molten state to a solid state is set to 102/sec or more, preferably 10' K/sec or more, and is used to crush not only atomized powder but also quenched flakes and quenched ribbons. Powder etc. obtained by

Ｓｉ：１２〜３０％ １２％未満ではせっかくの急冷効果による初晶Ｓｔ粒子
の分散量が少なくなり１強度・耐熱性・耐摩耗性のいず
れにおいても満足な物性を得るには至らない、一方３０
％を超えると急冷凝固法を採用しているにもかかわらず
初晶Ｓｉ粒子のかなりの部分が巨大化し、靭性や衝撃値
の低下を招き、又切削加工性も悪くなる。更に熱間加工
時の成形性が著しく悪化したり、加工圧力が著しく増大
するといった固化成形性の面において重要な欠陥が生じ
る。Si: 12 to 30% If it is less than 12%, the amount of dispersion of primary St particles due to the quenching effect will decrease, making it impossible to obtain satisfactory physical properties in terms of strength, heat resistance, and abrasion resistance.
If it exceeds %, a considerable portion of the primary Si particles becomes gigantic even though the rapid solidification method is adopted, leading to a decrease in toughness and impact value, and also resulting in poor machinability. Furthermore, important defects occur in terms of solidification formability, such as a marked deterioration in formability during hot working and a marked increase in processing pressure.

Ｃｕ：２〜１０％ ＣｕはＡ１合金に時効硬化性を４える元素であり強度向
上の為に必須である。２％未満ではこの効果が十分発揮
されず、一方１０％を超えると急冷凝固法を採用してい
るにもかかわらず巨大な金属間化合物の形成を見ること
がある。尚Ｃｕの添加による強度上昇効果は５．５％添
加を超えるあたりから顕著になり８％を超えると靭性低
下を招き或は耐食性に悪影響を与えはじめるので、実用
上は５゜５〜８％の範囲がもっとも有効と考えられる。Cu: 2-10% Cu is an element that imparts age hardenability to the A1 alloy and is essential for improving strength. If it is less than 2%, this effect will not be sufficiently exhibited, while if it exceeds 10%, giant intermetallic compounds may be formed even though the rapid solidification method is employed. The strength-increasing effect of adding Cu becomes noticeable when the addition exceeds 5.5%, and when it exceeds 8%, it causes a decrease in toughness or begins to have an adverse effect on corrosion resistance. Range is considered the most effective.

Ｍｎ、Ｆｅ、Ｎｉ、Ｃｒ及びＺｒの１種以上：これらの
元素に共通の作用効果は、急速冷却下における固溶強化
に寄与する点、高温条件の下で安定な微細分散相を均一
に形成すると共に再結晶防止効果を発揮し高温強度の増
大に寄与する点等である。これらの寄与を有効ならしめ
る為、Ｍｎは２％以上、ＦｅとＮｉは各々０．５％以上
、ＺｒとＣｒは各々０．１％以上の添加が必要である。One or more of Mn, Fe, Ni, Cr, and Zr: The common effects of these elements are that they contribute to solid solution strengthening under rapid cooling, and that they uniformly form a stable finely dispersed phase under high temperature conditions. At the same time, it exhibits a recrystallization prevention effect and contributes to an increase in high-temperature strength. In order to make these contributions effective, it is necessary to add 2% or more of Mn, 0.5% or more of each of Fe and Ni, and 0.1% or more of each of Zr and Cr.

しかしＭｎが１５％、Ｆｅが８％、Ｎｉが３％、Ｚｒが
１．０％、Ｃｒが３％という夫々の上限を超えると、急
冷凝固化であっても固溶限界を超えることになり１分散
相の粗大化を招いて耐熱耐摩耗性を低下させる。尚上記
各元素は上記以外にも夫々特有の作用が期待されるもの
であり、以下各論的に説明する。まずＭｎは常温強度の
向上並びに耐熱性の向上効果を発揮する。Ｆｅ、Ｎｉ。However, if Mn exceeds the upper limits of 15%, Fe 8%, Ni 3%, Zr 1.0%, and Cr 3%, the solid solubility limit will be exceeded even in rapid solidification. 1. This leads to coarsening of the dispersed phase and reduces heat and wear resistance. It should be noted that each of the above elements is expected to have a unique effect in addition to the above, and will be explained in detail below. First, Mn exhibits the effect of improving room temperature strength and heat resistance. Fe, Ni.

Ｃｒ、Ｚｒは常温並びに高温強度の向上に有効であり、
且つ耐彦耗性向上効果を発揮する。そしてこれらの４元
素はＡｌ中における拡散速度が小さく、急冷凝固法によ
っていったんマトリックス中へ微細分散されたものは高
温条件下におかれても粗大化されにくく、高温強度の低
下を防止し、また高温下における耐摩耗性の発揮に寄与
する。Cr and Zr are effective in improving strength at room temperature and high temperature,
It also exhibits the effect of improving wear resistance. These four elements have a low diffusion rate in Al, and once they are finely dispersed into the matrix by the rapid solidification method, they do not become coarse even under high temperature conditions, preventing a decrease in high temperature strength, and Contributes to exhibiting wear resistance under high temperatures.

［実施例］ 第１表に示す各種組成のＡｌ合金溶湯を１０３Ｋ　／ｓ
ａｃの冷却速度で急冷凝固し合金粉末を得た。[Example] Molten Al alloys having various compositions shown in Table 1 were heated at 103K/s.
The alloy powder was rapidly solidified at a cooling rate of ac to obtain an alloy powder.

次にこれらを温間にて圧粉成形し、更に押出比１４で熱
間押出加工を行ない、２０ｍｍφの押出材を得た０次い
で粉末冶金品は４８０℃Ｘ２ｈｒの溶体化処理、並びに
１７０℃Ｘ１Ｏｈｒの時効処理を行なった。また比較材
として用いた鋳造物’Ａ３９０は５００℃×４ｈ「の溶
体化処理後、同様に１７０℃Ｘ１０ｈｒの時効処理を行
なった。Next, these were compacted in a warm state, and then hot extruded at an extrusion ratio of 14 to obtain an extruded material of 20 mmφ.Next, the powder metallurgy product was subjected to solution treatment at 480°C for 2 hours and at 170°C for 1 Ohr. The aging process was carried out. Further, the cast 'A390 used as a comparative material was subjected to solution treatment at 500° C. for 4 hours and then similarly subjected to aging treatment at 170° C. for 10 hours.

これらの押出材および鋳造物について次に示す各試験を
行なった。The following tests were conducted on these extruded materials and cast products.

耐摩耗性試験 次の条件下に大越式摩耗試験を行なった。Wear resistance test The Okoshi type abrasion test was conducted under the following conditions.

相手材：　　Ｆｅ１２ 摩擦速度：　１．Ｉ］７ｍ／＋ｅｃ 摩擦距離：１００ｍ 潤滑手段：なし 荷重：　２．２Ｋｇ 彦耗試験後の摩耗痕を観察し摩耗量を測定した。各試料
間の耐摩耗性比較は粉末冶金にょるＡｌ−２０Ｓｉ（比
較材Ｎｏ、１３）ノ摩耗量を１．０としたときの比較値
を求め、第１表に併記する様な結果を得た。Mating material: Fe12 Friction speed: 1. I]7m/+ec Friction distance: 100m Lubricating means: None Load: 2.2Kg After the wear test, the wear marks were observed and the amount of wear was measured. To compare the wear resistance between each sample, we calculated the comparative value when the wear amount of Al-20Si (comparative material No. 13) made by powder metallurgy was set to 1.0, and obtained the results as shown in Table 1. Ta.

室温及び高温引張試験 平行部６鳳■φ、標点距＠３０鳳１のテストピースを用
い、室温、１００℃、２００℃、３００”Ｃ！の下で引
張試験を行ない、各温度での引張強度及び室温伸びを求
めた。結果は第１表に併記する通りである。Room Temperature and High Temperature Tensile Test Using a test piece with a parallel section of 6 mm x φ and a gauge length of 30 mm, a tensile test was conducted at room temperature, 100°C, 200°C, and 300”C!. The strength and elongation at room temperature were determined.The results are shown in Table 1.

上記各試験結果をまとめてみる。Ｎｏ、１〜４の本発明
材とＮｏ、１３〜１５の比較材を見比べると、Ｃｕによ
る顕著な時効硬化を確認することができる。尚Ｃｕ添加
量が２％未満のもの（Ｎｏ。Let's summarize the results of each test above. When comparing the present invention materials Nos. 1 to 4 and the comparative materials Nos. 13 to 15, significant age hardening due to Cu can be confirmed. In addition, the amount of Cu added is less than 2% (No.

１４）では時効硬化が少なく、他方１０％を超えるもの
（Ｎｏ、１５）では伸びが極端に低下している。又Ｃｕ
含有量が最好適範囲にあるもの同士の比較（Ｎｏ、５．
８とＮｏ、１６．１７の比較）によると、Ｓｔ添加量が
１２％未満では十分な耐摩耗性が得られていないこと、
逆にＳｉが３０％を超えたものでは室温伸びが極端に低
下していることなどが分かる。In No. 14), the age hardening is small, while in No. 15, which exceeds 10%, the elongation is extremely reduced. Also Cu
Comparison of those whose content is within the optimum range (No, 5.
8 and No. 16.17), sufficient wear resistance is not obtained when the amount of St added is less than 12%.
On the contrary, it can be seen that the room temperature elongation is extremely reduced in the case where the Si content exceeds 30%.

Ｍｇの影響についてはＮｏ、２とＮｏ、１８〜２０の比
較によって分かる様に、Ｍｇの増大につれて耐摩耗性が
低下し、また室温伸びが極端に低下している。Ｍｇ非配
合の有利さが理解できる。Regarding the influence of Mg, as can be seen by comparing No. 2 and No. 18 to 20, as the Mg content increases, the wear resistance decreases and the room temperature elongation decreases extremely. The advantage of not incorporating Mg can be understood.

Ｆｅ、Ｍｎ、Ｃｒ、ＮｉおよびＺｒについては、Ｎｏ、
７〜１２に示す様に耐熱性及び耐摩耗性の両面において
効果的元素であるが、Ｎｏ、２１〜２５に示される様な
過剰添加では分散相の粗大化を誘起して耐摩耗性を低下
させている。尚耐摩耗性材として汎用されているＡ３９
０材と比較すると、強度、耐熱性および耐摩耗性のいず
れにおいても優れていることが分かった。For Fe, Mn, Cr, Ni and Zr, No,
As shown in Nos. 7 to 12, it is an effective element in terms of both heat resistance and wear resistance, but excessive addition as shown in Nos. and 21 to 25 induces coarsening of the dispersed phase and reduces wear resistance. I'm letting you do it. A39 is commonly used as a wear-resistant material.
It was found that the material was superior in strength, heat resistance, and abrasion resistance when compared to material No.

［発明の効果］ 本発明は上記の様に構成され・Ｃいるので、常温並びに
高温強度が優れると共に耐熱性及び耐摩耗性が著しく優
れ、熱間加工性及び切削加工性の良好な高力Ａ１合金が
提供されることとなった。[Effects of the Invention] Since the present invention is constructed as described above, it has excellent strength at room temperature and high temperature, extremely excellent heat resistance and wear resistance, and high strength A1 with good hot workability and cutting workability. Alloy will be provided.

Claims (2)

【特許請求の範囲】[Claims] （１）Ｓｉ：１２〜３０重量％ Ｃｕ：２〜１０重量％ を含み残部が実質的にＡｌ及び不可避不純物よりなるも
のであることを特徴とする高力耐熱耐摩耗性Ａｌ合金。(1) A high-strength, heat-resistant and wear-resistant Al alloy, characterized in that it contains Si: 12 to 30% by weight and Cu: 2 to 10% by weight, with the remainder consisting essentially of Al and inevitable impurities. （２）Ｓｉ：１２〜３０重量％ Ｃｕ：２〜１０重量％ を含む他、更に Ｍｎ：２〜１５重量％ Ｆｅ：０．５〜８重量％ Ｎｉ：０．５〜３重量％ Ｚｒ：０．ｌ〜１．０重量％ Ｃｒ：０．１〜３重量％ よりなる群から選択される１種以上の合金元素を含み残
部が実質的にＡ１及び不可避不純物よりなるものである
ことを特徴とする高力耐熱耐摩耗性Ａｌ合金。(2) Contains Si: 12-30% by weight, Cu: 2-10% by weight, and further includes Mn: 2-15% by weight, Fe: 0.5-8% by weight, Ni: 0.5-3% by weight, Zr: 0 ．． It is characterized by containing one or more alloying elements selected from the group consisting of 1 to 1.0% by weight, Cr: 0.1 to 3% by weight, and the remainder substantially consisting of A1 and inevitable impurities. High strength heat and wear resistant Al alloy.