JPH09143596A - High strength copper alloy with resistance to heat and wear, and its production - Google Patents
High strength copper alloy with resistance to heat and wear, and its productionInfo
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- JPH09143596A JPH09143596A JP30137795A JP30137795A JPH09143596A JP H09143596 A JPH09143596 A JP H09143596A JP 30137795 A JP30137795 A JP 30137795A JP 30137795 A JP30137795 A JP 30137795A JP H09143596 A JPH09143596 A JP H09143596A
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は銅合金として、耐熱、耐
摩耗性に優れ機械的強度が要求される、例えば自動車の
エンジン部品のバルブシートのような耐熱性と耐摩耗性
が要求される摺動材などに有用な銅合金に関するもので
ある。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention is a copper alloy which is required to have excellent heat resistance and wear resistance and mechanical strength, for example, heat resistance and wear resistance such as valve seats of automobile engine parts. The present invention relates to a copper alloy useful as a sliding material and the like.
【０００２】[0002]
【従来の技術】従来、銅合金の中で機械的性質が良好で
耐摩耗性が良い材料として、アルミニウム青銅がある。
しかし、Ａｌを９．４ｗｔ％以上含むものは、いわゆる
α＋β相合金となる。このβ相が多くなる程、高温にお
ける硬さが低下する。2. Description of the Related Art Conventionally, aluminum bronze has been known as a material having good mechanical properties and good wear resistance among copper alloys.
However, those containing 9.4 wt% or more of Al are so-called α + β phase alloys. As this β phase increases, the hardness at high temperature decreases.
【０００３】そのため、機械的性質やコストなどの関係
でアルミニウム青銅を用いる場合は、α単相合金である
ＡＢＢ−１材(ＪＩＳＣ６１６１材)が用いられていて
る。しかし、α＋β相合金であるＡＢＢ−２材(ＪＩＳ
Ｃ６１９１材)よりも、常温での機械的性質が悪くなる
という問題点がある。Therefore, when aluminum bronze is used because of its mechanical properties and cost, the ABB-1 material (JISC6161 material), which is an α single phase alloy, is used. However, the ABB-2 material (JIS
There is a problem that the mechanical properties at room temperature are worse than those of C6191 material.
【０００４】また、特公平５ー２７６９８号公報には、
本発明品と添加元素が同じ銅合金が記載されている。し
かし、この公知例はＡｌを８．５〜１０．５ｗｔ％含ん
だ、耐摩耗性を向上させたアルミニウム青銅である。Japanese Patent Publication No. 5-27698 discloses that
A copper alloy having the same additive element as the product of the present invention is described. However, this known example is aluminum bronze containing 8.5 to 10.5 wt% of Al and having improved wear resistance.
【０００５】[0005]
【発明が解決しようとする課題】しかしこの公知例は、
前記の通りＡｌの添加量が多いため、耐熱性が問題とな
る。また、一般的に銅合金は鉄系材料やニッケル基合金
と比較して、耐熱性が劣るが、電気伝導性、熱伝導性が
良く、特に鉄系材料との接触摩耗性が良好である。However, this known example is
As described above, since the amount of Al added is large, heat resistance becomes a problem. In general, copper alloys are inferior in heat resistance to iron-based materials and nickel-based alloys, but have good electrical conductivity and thermal conductivity, and particularly good contact wear with iron-based materials.
【０００６】そして、最近、自動車エンジン部品の高性
能化等にともない、レース用等特別仕様車に、チタン合
金のバルブが使用されているが、それと共に使用される
バルブシートは、耐熱性と耐摩耗性が要求され、従来の
銅合金では満足できないものとなっている。Recently, as the performance of automobile engine parts has been improved, titanium alloy valves have been used in cars with special specifications such as for racing. The valve seat used with them has heat resistance and resistance. Abradability is required, and conventional copper alloys are not satisfactory.
【０００７】また、銅合金の中で析出硬化型銅合金とし
て、機械的性質及び物理的性質が優れたものとして、Ｂ
ｅＣｕ２５合金に代表されるＢｅＣｕ合金がある。しか
し、このＢｅＣｕ合金は高価であることと、耐摩耗性に
やや難点がある。Further, among the copper alloys, as a precipitation hardening type copper alloy, one having excellent mechanical properties and physical properties, B
There is a BeCu alloy represented by the eCu25 alloy. However, this BeCu alloy is expensive and has some difficulty in wear resistance.
【０００８】そこでアルミニウム青銅並みの機械的性質
および耐摩耗性を有し、耐熱性も良好な銅合金の開発が
望まれる。このような目的から注目されている銅合金
に、コルソン合金がある。このコルソン合金は、Ｃｕ−
Ｎｉ−Ｓｉ系のもので、実験してみた結果は、耐熱性は
かなり良く、銅合金の中では軟化温度が高いものとなっ
ている。しかし、この３元系だけでは機械的強度がＪＩ
ＳＣ６１９１材のアルミニウム青銅より劣るものとなっ
ている。そこで、本発明に於いては、これに他元素を添
加して改良する事とした。Therefore, it is desired to develop a copper alloy having mechanical properties and wear resistance comparable to those of aluminum bronze and having good heat resistance. Corson alloy is a copper alloy that has been attracting attention for such a purpose. This Corson alloy is Cu-
As a result of an experiment, it is a Ni—Si based material, which shows that the heat resistance is quite good and that the softening temperature is high among the copper alloys. However, this ternary system alone has a mechanical strength of JI
It is inferior to the aluminum bronze of SC6191 material. Therefore, in the present invention, it was decided to improve by adding other elements thereto.
【０００９】そして、目標とする機械的性質および物理
的性質は以下の通りとした。 引張強さ(Ｎ／ｍｍ2) ６３５以上 伸び(％) ５以上 硬さ(ＨＲＢ) ９５以上 導電率(ＩＡＣＳ％) １０以上 高温硬さ(ＨＢ10/500) ６００℃にて ６０以上 耐摩耗性(常温) 比較材としてＡＢＢ−２材
より良好なことThe target mechanical properties and physical properties are as follows. Tensile strength (N / mm 2 ) 635 or more Elongation (%) 5 or more Hardness (HRB) 95 or more Conductivity (IACS%) 10 or more High temperature hardness (HB10 / 500) 60 or more at 600 ℃ Wear resistance ( (At room temperature) Better than ABB-2 as a comparative material
【００１０】[0010]
【課題を解決するための手段】本発明は上述の如き課題
を解決するため、第１の発明は、Ｎｉ３．５〜５．０ｗ
ｔ％，Ｓｉ０．５〜２．０ｗｔ％，Ａｌ３．０〜５．５
ｗｔ％，Ｆｅ０．５〜２．５ｗｔ％，Ｍｎ０．５〜１．
５ｗｔ％及び残部が不可避的な不純物を除く銅よりなる
ものである。In order to solve the above problems, the first invention is Ni3.5 to 5.0w.
t%, Si 0.5 to 2.0 wt%, Al 3.0 to 5.5
wt%, Fe 0.5 to 2.5 wt%, Mn 0.5 to 1.
5 wt% and the balance is copper excluding unavoidable impurities.
【００１１】また、第２の発明は、Ｎｉ３．５〜５．０
ｗｔ％，Ｓｉ０．５〜２．０ｗｔ％，Ａｌ３．０〜５．
５ｗｔ％，Ｆｅ０．５〜２．５ｗｔ％，Ｍｎ０．５〜
１．５ｗｔ％及び残部が不可避的な不純物を除く銅より
なり、これらに金型圧力鋳造または、鋳塊に熱間塑性加
工を加え、その後８５０〜９７０℃にて溶体化処理し、
次に処理温度４７０〜６００℃にて時効処理を行うこと
を特徴とするものである。The second aspect of the present invention is Ni 3.5 to 5.0.
wt%, Si 0.5-2.0 wt%, Al 3.0-5.
5 wt%, Fe 0.5 to 2.5 wt%, Mn 0.5 to
1.5 wt% and the balance consisting of copper excluding unavoidable impurities, mold pressure casting or hot plastic working of the ingot, and then solution treatment at 850 to 970 ° C.,
Next, the aging treatment is performed at a treatment temperature of 470 to 600 ° C.
【００１２】[0012]
【作用】上述のコルソン合金に関連した公知の材料とし
て、コルソン合金にＡｌを添加したものがあるが、本目
標の機械的強度を満足せず、高温硬さが物足りないもの
となっている。そこで本発明者等は前記課題を解決する
ため、種々実験を行った結果、コルソン合金相当にＡｌ
のほかＦｅ，Ｍｎを加え、これに溶体化処理および時効
処理を加えることにより、上述の条件を満足させたもの
である。As a known material related to the above-mentioned Corson alloy, there is a material in which Al is added to the Corson alloy, but it does not satisfy the target mechanical strength, and the high temperature hardness is insufficient. Therefore, as a result of various experiments conducted by the present inventors in order to solve the above-mentioned problems, as a result, Corson alloy is equivalent to Al.
In addition to Fe and Mn, the solution treatment and the aging treatment were added thereto to satisfy the above conditions.
【００１３】次にＣｕ以外の本合金の組成に関して説明
する。Ｎｉは、機械的強度を上げる目的で用いられると
共に、高温硬さを上げるのに効果がある。その含有量が
３．５ｗｔ％より少ないと、機械的強度や高温硬さを上
げる効果が少ない。また、５ｗｔ％よりも含有量が多い
と導電率が落ち、熱伝導率が悪くなる。Next, the composition of the present alloy other than Cu will be described. Ni is used for the purpose of increasing the mechanical strength and is effective in increasing the high temperature hardness. When the content is less than 3.5 wt%, the effect of increasing mechanical strength and high temperature hardness is small. Further, if the content is more than 5 wt%, the electric conductivity decreases and the thermal conductivity deteriorates.
【００１４】また、ＳｉはＮｉと化合しニッケル珪化物
を作り、溶体化処理をすることにより過飽和固溶体が得
られる。その後、時効処理をすることにより微粒析出に
よって硬くなる性質をもっている。その結果導電性のあ
る熱伝導率の良い材料となる。そして、Ｓｉの一部はＭ
ｎと化合しマンガン珪化物を作り、耐摩耗性に寄与す
る。また、Ｓｉの含有量が０．５ｗｔ％より少ないと上
記の効果がなく、２ｗｔ％よりも多いと、機械的性質の
伸びを悪くする。Further, Si combines with Ni to form nickel silicide, and a solution treatment is performed to obtain a supersaturated solid solution. After that, it has a property of being hardened by precipitation of fine particles by aging treatment. As a result, it becomes a material having conductivity and good thermal conductivity. And a part of Si is M
It combines with n to form manganese silicide and contributes to wear resistance. Further, if the Si content is less than 0.5 wt%, the above effect is not obtained, and if it is more than 2 wt%, the elongation of mechanical properties is deteriorated.
【００１５】また、Ａｌは、機械的性質の引張強さを上
げると共に、耐摩耗性を向上させる。そのため、含有量
が３．０ｗｔ％よりも少ないと目標の引張強さを出すこ
とができない。また、含有量が５．５ｗｔ％よりも多い
と、他の添加元素との関係もあって、機械的性質の伸び
が悪くなると同時に、耐熱性にも影響を及ぼして高温硬
さが悪くなる。Further, Al raises the mechanical properties such as tensile strength and wear resistance. Therefore, if the content is less than 3.0 wt%, the target tensile strength cannot be obtained. On the other hand, if the content is more than 5.5 wt%, the elongation of mechanical properties is deteriorated due to the relationship with other additive elements, and at the same time, the heat resistance is affected and the high temperature hardness is deteriorated.
【００１６】また、Ｆｅは、この材料に関して重要な添
加元素で、組織を微細化し機械的強度を上げるととも
に、耐摩耗性を向上させる。そして、含有量が０．５ｗ
ｔ％より少ないと、組織を微細化したり、耐摩耗性を向
上させたり、機械的強度を上げる効果が少ないものとな
る。また。その含有量が２．５ｗｔ％より多いと、他の
添加元素との影響もあって、機械的性質の伸びが低下し
耐摩耗性が悪くなる。Further, Fe is an important additional element for this material, and refines the structure to increase the mechanical strength and wear resistance. And the content is 0.5w
If it is less than t%, the effect of refining the structure, improving the wear resistance, and increasing the mechanical strength will be small. Also. If the content is more than 2.5 wt%, the elongation of mechanical properties is lowered due to the influence of other additive elements, and the wear resistance is deteriorated.
【００１７】また、Ｍｎは、素地を強化し機械的強度を
上げる効果がある。そして、Ｓｉと化合し珪化物を作
り、耐摩耗性を向上させると共に熱間加工性を良くす
る。そのため、Ｍｎの含有量は厳密にすべきで、含有量
が０．５ｗｔ％より少ないと耐摩耗性を悪いものとす
る。また、含有量が１．５ｗｔ％よりも多いと耐熱性を
悪くすると共に、機械的性質の伸びも悪くする。Further, Mn has the effect of strengthening the base material and increasing the mechanical strength. Then, it combines with Si to form a silicide, which improves wear resistance and improves hot workability. Therefore, the content of Mn should be strict, and if the content is less than 0.5 wt%, the wear resistance becomes poor. Further, if the content is more than 1.5 wt%, the heat resistance is deteriorated and the elongation of mechanical properties is also deteriorated.
【００１８】以上のような配合で、鋳塊を作り熱間塑性
加工を施すか、または金型圧力鋳造により素材を作り、
更に本材質は熱処理により析出硬化させなければ、目標
の機械的強度および耐熱性、耐摩耗性を得ることができ
ない。そのため、溶体化処理温度および時効処理温度を
種々検討した結果、溶体化処理温度は８５０〜９７０℃
とし、時効処理温度は４７０〜６００℃とすることによ
り、目標の機械的強度および耐熱性、耐摩耗性を得るこ
とに成功したものである。With the above composition, an ingot is formed and hot plastic working is performed, or a material is formed by die pressure casting,
Furthermore, the target mechanical strength, heat resistance, and wear resistance cannot be obtained unless the material is precipitated and hardened by heat treatment. Therefore, as a result of various studies on the solution treatment temperature and the aging treatment temperature, the solution treatment temperature was 850 to 970 ° C.
By setting the aging treatment temperature to 470 to 600 ° C., the target mechanical strength, heat resistance, and wear resistance were successfully obtained.
【００１９】[0019]
【実施例】表１の配合で各材料をそろえた供試材を、高
周波誘導炉にて黒鉛るつぼ中で所定のフラックスを用い
大気溶解させた後、この溶湯を金型圧力鋳造にてφ８０
ｍｍ×２００ｍｍＬの試料Ａを得た。EXAMPLE A test material prepared by preparing each material in the composition shown in Table 1 was melted in a graphite crucible in a high frequency induction furnace in the atmosphere with a predetermined flux, and then the melt was pressure-molded with a die to obtain φ80.
A sample A of mm × 200 mmL was obtained.
【００２０】また、表１の配合で各材料をそろえた供試
材を、高周波誘導炉にて黒鉛るつぼ中で所定のフラック
スを用い大気溶解させた後、この溶湯を重力鋳造してφ
８０ｍｍ×２００ｍｍＬに注湯し試料Ｂの鋳塊を得た。Further, a test material prepared by preparing each material with the composition shown in Table 1 was melted in a graphite crucible in a high frequency induction furnace in the atmosphere with a predetermined flux, and then this molten metal was gravity cast to obtain φ.
It poured in 80 mm x 200 mmL, and obtained the ingot of the sample B.
【００２１】そして、上記の試料Ａをアズキャスト材と
してφ２１×２００Ｌ及びφ２５×２００Ｌに切り出し
た。Then, the above sample A was cut into φ21 × 200 L and φ25 × 200 L as an as cast material.
【００２２】また、上記の試料Ｂの黒皮を面削して除い
た後、熱間鍛造にてφ３０×Ｌに鍛伸した後、φ２１×
２００Ｌ及びφ２５×２００Ｌに切り出した。Further, after removing the black skin of the above-mentioned sample B by chamfering, it was hot forged to φ30 × L and then φ21 ×
It was cut into 200 L and φ25 × 200 L.
【００２３】そして、上記の切り出しを行った試料Ａ及
び試料Ｂを、各々熱処理温度８５０〜９７０℃にて溶体
化処理し、その後４７０〜６００℃で時効処理を施し
た。Then, the sample A and the sample B cut out as described above were subjected to solution treatment at a heat treatment temperature of 850 to 970 ° C., respectively, and then subjected to an aging treatment at 470 to 600 ° C.
【００２４】その後、各々の材料より、摩耗試験片５×
５×２５ｍｍ、引張試験用ＪＩＳ４号試験片、および高
温硬さ試験片としてφ２５×２０ｍｍを用意した。Then, wear test pieces 5 × were made from each material.
5 × 25 mm, JIS No. 4 test piece for tensile test, and φ25 × 20 mm were prepared as a high temperature hardness test piece.
【００２５】また、表１乃至表６に於いて、Ｎｏ１〜Ｎ
ｏ４は本発明合金の実施例である。また、表１乃至表６
に於いて、Ｎｏ５〜Ｎｏ１１は比較例である。この比較
例に於いて、Ｎｏ５は機械的性質および高温硬さは良好
だが、摩耗試験においては乾式および湿式とも本発明品
より悪い。Ｍｎを含有させていないので、マンガン珪化
物を形成していないためと考えられる。Further, in Tables 1 to 6, No1 to N
o4 is an example of the alloy of the present invention. Further, Tables 1 to 6
In No. 5, No. 5 to No. 11 are comparative examples. In this comparative example, No. 5 has good mechanical properties and high-temperature hardness, but in the abrasion test, both dry and wet are worse than those of the present invention. It is considered that this is because manganese silicide is not formed because Mn is not contained.
【００２６】また、比較例Ｎｏ６は、Ｆｅを無くしてＺ
ｒを添加したが、アズキャスト材の機械的性質が悪く、
耐摩耗性が本発明実施例よりも悪い。ただし耐熱性は良
好である。In Comparative Example No. 6, Fe was eliminated and Z
Although r was added, the mechanical properties of the as-cast material were poor,
The abrasion resistance is worse than that of the examples of the present invention. However, the heat resistance is good.
【００２７】また、比較例Ｎｏ７は、比較例Ｎｏ６と同
じくＦｅを含有させずにＺｒを添加し、更にＡｌを増や
した例であるが、Ａｌを増やした割にアズキャスト材で
の機械的性質が悪い。Ｚｒが酸化しやすい元素である影
響と、Ｆｅを添加していないことによって、耐摩耗性も
悪くなっている。Comparative Example No. 7 is an example in which Zr was added without containing Fe and Al was increased, as in Comparative Example No. 6, but the mechanical properties of the as-cast material were increased in spite of increasing Al. Is bad. Due to the effect that Zr is an element that is easily oxidized and the fact that Fe is not added, the wear resistance is also poor.
【００２８】また、比較例Ｎｏ８は、Ｎｉを本願発明よ
りも増やし、Ｆｅも本願発明よりも多く添加した例であ
る。また、Ａｌも上限近くに添加したため、機械的性質
の伸びが悪く、導電率も目標に到達していない。乾式で
の耐摩耗性は良いが湿式での耐摩耗性が少し悪い。Comparative Example No. 8 is an example in which Ni is increased more than in the present invention and Fe is also added more than in the present invention. Further, since Al is added near the upper limit, the elongation of mechanical properties is poor and the electrical conductivity does not reach the target. The dry type has good wear resistance, but the wet type has slightly poor wear resistance.
【００２９】また、比較例Ｎｏ９は、添加元素をＮｏ１
〜Ｎｏ８よりも少なくし、Ｍｎを含有させない例であ
る。当然機械的性質は悪く軟らかい材料となっている。
また、耐摩耗性は乾式では良いが湿式では少し悪くなっ
ている。In Comparative Example No. 9, the additive element was No.
It is an example in which the amount is less than No. 8 and Mn is not contained. Naturally, it is a soft material with poor mechanical properties.
Also, the wear resistance is good in the dry type, but a little worse in the wet type.
【００３０】また、比較例Ｎｏ１０は、本願発明の基本
となった材料であり、公知のものである。この材質は元
々冷間圧延を施して機械的強度を出すもので、本実施例
のようにアズキャスト材や熱間塑性加工のみ行い使用す
るものではないため、機械的強度も満足されず、高温硬
さは常温硬さと比較すれば良いが、やや物足りないもの
となっている。ただし、耐摩耗性はこの試験方法では良
い結果が出ている。Comparative Example No. 10 is a material which is the basis of the present invention and is a known material. This material is originally cold-rolled to provide mechanical strength, and as it is not used as an as-cast material or hot plastic working as in this example, mechanical strength is not satisfied, and high temperature The hardness is better than room temperature hardness, but it is somewhat unsatisfactory. However, wear resistance shows good results with this test method.
【００３１】また、比較例Ｎｏ１１は、ＪＩＳＣ６１９
１材に相当するアルミニウム青銅である。耐摩耗性は一
般の銅合金と比較すれば優秀な材料であるが、高温硬さ
は本実施材の中で最も悪い。Comparative Example No. 11 is JIS C619
Aluminum bronze corresponding to one material. Wear resistance is an excellent material compared with general copper alloys, but high temperature hardness is the worst among the materials of this embodiment.
【００３２】表１は成分組成値(ｗｔ％)を示している。Table 1 shows component composition values (wt%).
【表１】 [Table 1]
【００３３】表２は金型圧力鋳造した試料Ａの溶体化処
理および時効処理後の機械的性質および導電率を示して
いる。Table 2 shows the mechanical properties and electrical conductivity of the sample pressure-cast sample A after solution treatment and aging treatment.
【表２】 [Table 2]
【００３４】上記表２に於ける試料Ａの溶体化処理およ
び時効処理温度。 Ｎｏ１〜Ｎｏ９ 溶体化処理(９５０℃)、時効処理(５１０℃)。 Ｎｏ１０ 〃 (９００℃)、 〃 (５００℃)。 Ｎｏ１１ 焼入処理 (６３０℃)。Solution treatment and aging treatment temperatures of sample A in Table 2 above. No1 to No9 Solution treatment (950 ° C), aging treatment (510 ° C). No10 〃 (900 ℃), 〃 (500 ℃). No. 11 Quenching treatment (630 ° C).
【００３５】表３は鋳塊の試料Ｂを熱間鍛造後に溶体化
処理および時効処理を行った後の機械的性質及び導電率
を示している。Table 3 shows the mechanical properties and electrical conductivity of the ingot sample B after hot forging, solution treatment and aging treatment.
【表３】 [Table 3]
【００３６】上記表３に於いて溶体化処理および時効処
理方法は表２と同じにした。In Table 3 above, the solution treatment and aging treatment methods were the same as those in Table 2.
【００３７】表４は高温硬さ（測定単位 常温〜７００
℃ ＨＢ(１０／５００) ８００℃ＨＢ(１０／２７５)
を示している。Table 4 shows high temperature hardness (measurement unit: room temperature to 700).
℃ HB (10/500) 800 ℃ HB (10/275)
Is shown.
【表４】 [Table 4]
【００３８】上記表４に於いてＮｏの後のＡは試料Ａに
溶体化処理及び時効処理を行ったものであり、Ｂは試料
Ｂを熱間鍛造後に溶体化処理及び時効処理を行ったもの
である。In Table 4 above, A after No is the sample A subjected to solution treatment and aging treatment, and B is the sample B subjected to solution treatment and aging treatment after hot forging. Is.
【００３９】表５は乾式摩耗テスト（単位：ｍｇ／ｃｍ
2）を示している。Table 5 shows a dry abrasion test (unit: mg / cm
2 ) is shown.
【表５】 [Table 5]
【００４０】上記表５に於ける乾式摩耗テストは、摩耗
試験機を葉山式摩耗試験機により行った。 各々のテストピースを上記条件にて各３回テストした結
果の平均値を示したものである。また、上記の乾式摩耗
テストは試料Ａに溶体化処理及び時効処理を行ったもの
についてのみ行い、試料Ｂを熱間鍛造後に溶体化処理及
び時効処理を行ったものに付いては行っていない。The dry abrasion test in Table 5 above was carried out by using a Hayama abrasion tester as an abrasion tester. The average value of the results of testing each test piece three times under the above conditions is shown. Further, the above dry abrasion test was performed only on the sample A that was subjected to the solution treatment and the aging treatment, and was not performed on the sample B that was subjected to the solution treatment and the aging treatment after the hot forging.
【００４１】表６は湿式摩耗テスト（単位：ｍｇ／ｃｍ
2）を示している。Table 6 shows the wet wear test (unit: mg / cm
2 ) is shown.
【表６】 [Table 6]
【００４２】上記表６に於いて湿式摩耗テストは、摩耗
試験機を葉山式摩耗試験機により行った。 テスト条件 ６０ｋｇ／ｃｍ2圧 走行距離１０ｋｍ 走行スピード ３０ｍ／秒 相手材 ＳＣＭ４３５ 潤滑油 テトラオイルＮｏ．４６ ３０ｃｃ／ｈ供給 各々のテストピースを上記条件にて各３回以上テストし
た結果の平均値を示したものである。また、上記の湿式
摩耗テストは試料Ａに溶体化処理及び時効処理を行った
ものについてのみ行い、試料Ｂを熱間鍛造後に溶体化処
理及び時効処理を行ったものに付いては行っていない。In Table 6 above, the wet abrasion test was conducted by using a Hayama abrasion tester as an abrasion tester. Test conditions 60 kg / cm 2 pressure, traveling distance 10 km, traveling speed 30 m / sec, mating material SCM435, lubricating oil, tetra oil No. 46 30 cc / h supply This is an average value of the results of testing each test piece three times or more under the above conditions. Further, the above-mentioned wet wear test was performed only on the sample A that was subjected to the solution treatment and the aging treatment, and was not performed on the sample B that was subjected to the solution treatment and the aging treatment after hot forging.
【００４３】[0043]
【発明の効果】本発明は上述の如く、アルミニウム青銅
並みの機械的性質を備えながら、導電率(ＩＡＣＳ％)、
高温硬さ、耐摩耗性等に於いて優れた特性を得ることが
できるものである。As described above, the present invention has the electrical properties (IACS%) while having the mechanical properties of aluminum bronze.
It is possible to obtain excellent properties such as high temperature hardness and wear resistance.
Claims (2)
〜２．０ｗｔ％，Ａｌ３．０〜５．５ｗｔ％，Ｆｅ０．
５〜２．５ｗｔ％，Ｍｎ０．５〜１．５ｗｔ％及び残部
が不可避的な不純物を除く銅よりなる耐熱、耐摩耗性高
強度銅合金。1. Ni3.5 to 5.0 wt%, Si0.5
.About.2.0 wt%, Al3.0 to 5.5 wt%, Fe0.
A heat- and wear-resistant high-strength copper alloy comprising 5 to 2.5 wt%, Mn 0.5 to 1.5 wt%, and the balance being copper excluding inevitable impurities.
〜２．０ｗｔ％，Ａｌ３．０〜５．５ｗｔ％，Ｆｅ０．
５〜２．５ｗｔ％，Ｍｎ０．５〜１．５ｗｔ％及び残部
が不可避的な不純物を除く銅よりなり、これらに金型圧
力鋳造または、鋳塊に熱間塑性加工を加え、その後８５
０〜９７０℃にて溶体化処理し、次に処理温度４７０〜
６００℃にて時効処理を行うことを特徴とする耐熱、耐
摩耗性高強度銅合金の製造方法。2. Ni3.5 to 5.0 wt%, Si0.5
.About.2.0 wt%, Al3.0 to 5.5 wt%, Fe0.
5 to 2.5 wt%, Mn 0.5 to 1.5 wt%, and the balance being copper excluding unavoidable impurities, and die pressure casting or hot plastic working of the ingot, and then 85
Solution heat treatment at 0-970 ° C., then treatment temperature 470-
A method for producing a heat-resistant and wear-resistant high-strength copper alloy, which comprises performing an aging treatment at 600 ° C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP30137795A JPH09143596A (en) | 1995-11-20 | 1995-11-20 | High strength copper alloy with resistance to heat and wear, and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP30137795A JPH09143596A (en) | 1995-11-20 | 1995-11-20 | High strength copper alloy with resistance to heat and wear, and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH09143596A true JPH09143596A (en) | 1997-06-03 |
Family
ID=17896148
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP30137795A Pending JPH09143596A (en) | 1995-11-20 | 1995-11-20 | High strength copper alloy with resistance to heat and wear, and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH09143596A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003097886A1 (en) * | 2002-05-17 | 2003-11-27 | Metglas, Inc. | Copper-nickel-silicon two phase quench substrate |
| US7291231B2 (en) | 2002-05-17 | 2007-11-06 | Metglas, Inc. | Copper-nickel-silicon two phase quench substrate |
| WO2012081571A1 (en) * | 2010-12-13 | 2012-06-21 | 日本精線株式会社 | Copper alloy wire and copper alloy spring |
| CN103320731A (en) * | 2013-06-18 | 2013-09-25 | 浙江朋诚科技有限公司 | Heating processing technology of aluminum bronze alloy taper sleeve |
| CN103320643A (en) * | 2013-06-18 | 2013-09-25 | 浙江朋诚科技有限公司 | Aluminum bronze alloy taper sleeve |
-
1995
- 1995-11-20 JP JP30137795A patent/JPH09143596A/en active Pending
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003097886A1 (en) * | 2002-05-17 | 2003-11-27 | Metglas, Inc. | Copper-nickel-silicon two phase quench substrate |
| US6764556B2 (en) | 2002-05-17 | 2004-07-20 | Shinya Myojin | Copper-nickel-silicon two phase quench substrate |
| US7291231B2 (en) | 2002-05-17 | 2007-11-06 | Metglas, Inc. | Copper-nickel-silicon two phase quench substrate |
| WO2012081571A1 (en) * | 2010-12-13 | 2012-06-21 | 日本精線株式会社 | Copper alloy wire and copper alloy spring |
| CN103261460A (en) * | 2010-12-13 | 2013-08-21 | 日本精线株式会社 | Copper alloy wire and copper alloy spring |
| EP2653575A1 (en) * | 2010-12-13 | 2013-10-23 | Nippon Seisen Co., Ltd. | Copper alloy wire and copper alloy spring |
| EP2653575A4 (en) * | 2010-12-13 | 2014-09-03 | Nippon Seisen Co Ltd | Copper alloy wire and copper alloy spring |
| JP2014196564A (en) * | 2010-12-13 | 2014-10-16 | 日本精線株式会社 | High strength and high conductivity copper alloy fine wire, copper alloy spring and manufacturing method of copper alloy spring |
| JP5711764B2 (en) * | 2010-12-13 | 2015-05-07 | 日本精線株式会社 | Copper alloy wire and copper alloy spring |
| US9476474B2 (en) | 2010-12-13 | 2016-10-25 | Nippon Seisen Co., Ltd. | Copper alloy wire and copper alloy spring |
| CN103320731A (en) * | 2013-06-18 | 2013-09-25 | 浙江朋诚科技有限公司 | Heating processing technology of aluminum bronze alloy taper sleeve |
| CN103320643A (en) * | 2013-06-18 | 2013-09-25 | 浙江朋诚科技有限公司 | Aluminum bronze alloy taper sleeve |
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