JP4708833B2 - High strength copper alloy material for precision conductive spring with excellent sag resistance and its manufacturing method - Google Patents
High strength copper alloy material for precision conductive spring with excellent sag resistance and its manufacturing method Download PDFInfo
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- 229910000881 Cu alloy Inorganic materials 0.000 title claims description 47
- 239000000956 alloy Substances 0.000 title claims description 33
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- 238000010438 heat treatment Methods 0.000 claims description 51
- 239000010949 copper Substances 0.000 claims description 29
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- 229910052759 nickel Inorganic materials 0.000 claims description 18
- 229910052709 silver Inorganic materials 0.000 claims description 18
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- 238000001556 precipitation Methods 0.000 description 9
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- DMFGNRRURHSENX-UHFFFAOYSA-N beryllium copper Chemical compound [Be].[Cu] DMFGNRRURHSENX-UHFFFAOYSA-N 0.000 description 7
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- LPZOCVVDSHQFST-UHFFFAOYSA-N 2-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-3-ethylpyrazol-1-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C=1C(=NN(C=1)CC(=O)N1CC2=C(CC1)NN=N2)CC LPZOCVVDSHQFST-UHFFFAOYSA-N 0.000 description 2
- 229910000906 Bronze Inorganic materials 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
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- XXZCIYUJYUESMD-UHFFFAOYSA-N 2-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-3-(morpholin-4-ylmethyl)pyrazol-1-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C=1C(=NN(C=1)CC(=O)N1CC2=C(CC1)NN=N2)CN1CCOCC1 XXZCIYUJYUESMD-UHFFFAOYSA-N 0.000 description 1
- FYELSNVLZVIGTI-UHFFFAOYSA-N 2-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-5-ethylpyrazol-1-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C=1C=NN(C=1CC)CC(=O)N1CC2=C(CC1)NN=N2 FYELSNVLZVIGTI-UHFFFAOYSA-N 0.000 description 1
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- YCKOAAUKSGOOJH-UHFFFAOYSA-N copper silver Chemical compound [Cu].[Ag].[Ag] YCKOAAUKSGOOJH-UHFFFAOYSA-N 0.000 description 1
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Description
本発明は、例えば光ピックアップ用サスペンションワイヤなどの導電性ばね製品の用途において、特に耐へたり性に優れた高強度かつ高導電性の銅合金材料とその製造方法に関する。 The present invention relates to a high-strength and high-conductivity copper alloy material excellent in sag resistance, and a method for producing the same, particularly in the use of conductive spring products such as suspension wires for optical pickups.
銅は、電気抵抗が小さく導電性に優れることから、電気・電子用材料として多用され、その用途は種々電線からコネクタ、端子、スイッチなどの各種部品に至るまで多岐にわたって用いられている。しかしながら、一方で、銅は、軟質であるため、ばね製品のように高強度が要求される用途には本来不向きである。 Copper is widely used as an electrical / electronic material because of its low electrical resistance and excellent electrical conductivity, and its application is widely used from various electric wires to various parts such as connectors, terminals, and switches. However, on the other hand, since copper is soft, it is inherently unsuitable for applications that require high strength such as spring products.
そこで、高い導電性と高い強度が共に要求される導電性のばね製品、例えば、光ピックアップ用サスペンションワイヤなどの用途では、従来から高強度ステンレス鋼を芯材とし、その表面に銅をメッキもしくはクラッドした銅被覆材、あるいは、銅に他の元素を添加したリン青銅やベリリウム銅などの銅合金が使用されている。 Therefore, conductive spring products that require both high conductivity and high strength, such as suspension wires for optical pickups, have conventionally used high-strength stainless steel as the core and copper plated or clad on the surface. Copper alloys such as phosphor bronze and beryllium copper obtained by adding other elements to copper are used.
しかしながら、前者の銅被覆材は、芯材自体の強度によって高強度は維持できるものの、銅被覆した芯材からの剥離や銅の被覆状態の不均一により、品質特性にバラツキを生じやすいうえ、製造工程が複雑で品質の低下や製造コストの上昇が避けられないという問題があった。 However, although the former copper coating material can maintain high strength depending on the strength of the core material itself, it is likely to cause variations in quality characteristics due to peeling from the copper-coated core material and non-uniformity of the copper coating state. There is a problem in that the process is complicated, and deterioration in quality and increase in manufacturing cost are inevitable.
一方、後者の銅合金は、強度が大きいうえに導電性も比較的良好で、銅被覆材のような品質のバラツキといった問題も少ないことから広く用いられている。その特性として、例えばベリリウム銅では、引張強さが１４００ＭＰａ程度と高く（純銅は約２００ＭＰａ）、導電率も２０％ＩＡＣＳ程度と比較的良好であるが、Ｂｅは人体に有害であり、これを含む部品や装置を廃棄する場合には、別途処理工程を設けるなどの環境対策が必要となることから、最近ではその使用が制限されている。一方、前記リン青銅ではこのような問題はないものの、強度的にベリリウム銅には達しないことから、耐へたり性が求められる安定的なばね材としては満足し難いものである。 On the other hand, the latter copper alloy is widely used because it has high strength and relatively good electrical conductivity, and there are few problems such as variations in quality as in a copper coating material. As its properties, for example, beryllium copper has a high tensile strength of about 1400 MPa (pure copper is about 200 MPa) and conductivity is relatively good at about 20% IACS, but Be is harmful to the human body and includes this. In the case of discarding parts and devices, environmental measures such as providing a separate processing step are necessary, and their use has recently been limited. On the other hand, although the phosphor bronze does not have such a problem, it does not reach the strength of beryllium copper, so that it is not satisfactory as a stable spring material that requires sag resistance.
このような事情から、ベリリウム銅に代わる高強度、高導電性で、かつ、有害な元素を含まない銅合金材料が要望されており、このような特性を有する銅合金材料としては、例えば、Ｎｉを２．０〜４．８重量％、Ｓｉを０．２〜１．４重量％、Ｍｇを０．０５〜１．５重量％含有する銅合金において、その中に存在する析出物乃至介在物を特定したもの（特許文献１）、あるいは、Ｃｕに４〜３２原子％のＡｇを配合して鋳込んだ後に、急冷し、次いで冷間加工を行ったもの（特許文献２）などが提案されている。
しかしながら、前者はその強度（引張強さ）が７００〜１０００ＭＰａ程度に留まるものあり、導電性ばね用の材料としては到底満足できるものではなかった。また、後者の特許文献２についても、前者の特許文献１より高い強度（引張強さ）のものが示され、用途として、種々ケーブルや巻線、その他シャフト用補強材などの用途を示しているが、特にばね用製品では、単に強度が大きいだけでは不十分であって、例えば弾性特性や疲労特性、耐へたり性など種々特性を備えることが必要であり、特に耐へたり性については、ばね製品における寿命の面から重要であるものの、同文献はこの点について何ら示唆していない。 However, the former has a strength (tensile strength) of about 700 to 1000 MPa, which is not satisfactory as a material for the conductive spring. The latter patent document 2 also has a higher strength (tensile strength) than the former patent document 1, and shows applications such as various cables, windings, and other shaft reinforcing materials. However, in particular for spring products, it is not sufficient that the strength is simply high. For example, it is necessary to provide various characteristics such as elastic characteristics, fatigue characteristics, and sag resistance. Although important in terms of life in spring products, the document does not suggest anything about this point.
このように、近年、ベリリウム銅に代わる安全性の高い導電性ばね用の銅合金材料として、強度および導電性とともに、特に耐へたり性に優れたものが要望されているが、未だそのような要求に応え得るものは得られていない。そこで、本発明はこのような従来技術の課題に対処すべく鋭意研究の結果、特許文献２による銅銀合金にさらに所定量のＮｉ、Ｓｉを複合添加することで、組織内にＣｕとＡｇとの共晶相粒子およびＮｉとＳｉとのＮｉ２Ｓｉ相粒子を複合して含有することが有効との結論に至り本発明を完成した。 Thus, in recent years, as a copper alloy material for a highly safe conductive spring that replaces beryllium copper, a material that is particularly excellent in sag resistance as well as strength and conductivity has been demanded. No one can meet the demand. Therefore, as a result of earnest research to deal with such problems of the prior art, the present invention adds Cu and Ag in the structure by adding a predetermined amount of Ni and Si to the copper-silver alloy according to Patent Document 2 in combination. The present invention has been completed with the conclusion that it is effective to combine the eutectic phase particles of Ni and the Ni 2 Si phase particles of Ni and Si.
すなわち、本発明は、Ｂｅのような有害な元素を含まず、しかも、導電性ばね材料の用途に要求される十分な強度、耐へたり性および導電性を有する銅合金材料およびその製造方法の提供を目的とするものである。 That is, the present invention provides a copper alloy material that does not contain a harmful element such as Be and has sufficient strength, sag resistance, and conductivity required for the use of the conductive spring material, and a method for producing the same. It is for the purpose of provision.
前記目的を達成するため、本願の請求項１に記載の発明は、質量で、５．０〜１６．０％のＡｇ、１．０〜５．０％のＮｉおよび０．２〜１．２％のＳｉを含有し、残部がＣｕおよび不可避的不純物からなり、前記Ａｇ、ＮｉおよびＳｉの含有量をそれぞれａ（質量％）、ｂ（質量％）およびｃ（質量％）とするとき、８．０≦｛（１／４）×ａ＋ｂ｝／ｃ≦１４．０の関係にあり、組織内にＣｕとＡｇとの共晶相およびＮｉ２Ｓｉ粒子を複合して含有し、次式で求められるへたり率（γ）が１．２％以下であることを特徴とする耐へたり性に優れた電気・電子部品精密導電性ばね用高強度銅合金材料である。
γ（％）＝［（Ｌ ０ −Ｌ １ ）／Ｌ ０ ］×１００
（ここで、Ｌ １ およびＬ ０ は、当該材料から作製した線材または成形品にその０．２％耐力の４０％に相当する応力を３分間負荷した後、除荷した時の自由長および当初自由長である）
In order to achieve the object, the invention according to claim 1 of the present application is, by mass, 5.0 to 16.0% Ag, 1.0 to 5.0% Ni, and 0.2 to 1.2. % Si, the balance is Cu and inevitable impurities, and the contents of Ag, Ni and Si are a (mass%), b (mass%) and c (mass%), respectively. .0 ≦ have a relationship of {(1/4) × a + b } /c≦14.0, the eutectic phase and Ni 2 Si particles between Cu and Ag contained in the composite in a tissue, by the following equation It is a high-strength copper alloy material for precision conductive springs with excellent sag resistance, characterized in that the sag rate (γ) is 1.2% or less.
γ (%) = [(L 0 −L 1 ) / L 0 ] × 100
(Here, L 1 and L 0 are the free length when the load or the molded product made from the material is loaded for 3 minutes with the stress corresponding to 40% of its 0.2% proof stress, and the initial length when unloaded. Free length)
請求項２に記載の発明は、請求項１記載の銅合金材料において、前記合金組成は、さらに０．２〜１．０質量％のＳｎおよび／または０．３〜１．２質量％のＺｎを含有することを特徴とするものである。 The invention according to claim 2 is the copper alloy material according to claim 1, wherein the alloy composition further includes 0.2 to 1.0 mass% of Sn and / or 0.3 to 1.2 mass% of Zn. It is characterized by containing.
請求項３に記載の発明は、請求項１または２記載の銅合金材料において、０．２％耐力が９００ＭＰａ以上で、かつ、導電率が２５％ＩＡＣＳ以上であることを特徴とするものである。 The invention according to claim 3 is the copper alloy material according to claim 1 or 2, wherein the 0.2% proof stress is 900 MPa or more and the conductivity is 25% IACS or more. .
また、請求項４に記載の発明は、質量で、５．０〜１６．０％のＡｇ、１．０〜５．０％のＮｉおよび０．２〜１．２％のＳｉを含有し、残部がＣｕおよび不可避的不純物からなり、前記Ａｇ、ＮｉおよびＳｉの含有量をそれぞれａ（質量％）、ｂ（質量％）およびｃ（質量％）とするとき、８．０≦｛（１／４）×ａ＋ｂ｝／ｃ≦１４．０の関係にある銅合金材料に、温度３００〜６００℃で１〜１００時間の１次熱処理を施した後、加工率５０％以上で冷間加工を行い、前記冷間加工後に、前記１次熱処理温度以下の温度で所定時間熱処理する２次熱処理を施すことを特徴とする耐へたり性に優れた電気・電子部品精密導電性ばね用高強度銅合金材料の製造方法である。 The invention described in Claim 4 is the mass, containing 5.0 to 16.0% of Ag, 1.0 to 5.0 percent of Ni and 0.2 to 1.2% of Si, balance Ri Do Cu and inevitable impurities, wherein Ag, Ni and Si content, respectively a (mass%), when and b (wt%) and c (mass%), 8.0 ≦ {(1 a near Ru copper alloy material relation /4)×Atasub}/c≦14.0, cold working after subjected to primary heat treatment 1-100 hours at a temperature 300 to 600 ° C., working ratio of 50% or more gastric row, the later cold working, the first heat treatment temperature below the temperature at predetermined time heat treatment to second heat treatment sexual excellent electric and electronic parts precision conductive spring for high sag resistance, characterized in that applying It is a manufacturing method of a strength copper alloy material.
上記組成の銅合金材料に１次熱処理を施すことで、材料組織内にＣｕとＡｇとの共晶相（ＣｕＡｇ相）およびＮｉ２Ｓｉ相粒子とが複合化した形で形成される。そして加工率５０％以上で冷間加工を行うことで、組織が繊維化され、高い強度と耐へたり性が得られる。 By subjecting the copper alloy material having the above composition to a primary heat treatment, a Cu / Ag eutectic phase (CuAg phase) and Ni 2 Si phase particles are formed in a composite form in the material structure. And by carrying out cold working at a working rate of 50% or more, the structure is fibrillated, and high strength and sag resistance are obtained.
２次熱処理は、銅合金材料がばねとしての製品形状に成形された後に施されることが望ましい。２次熱処理を行うことで、さらにＮｉ２Ｓｉ相粒子が析出し、耐へたり性が向上することとなる。 The secondary heat treatment is desirably performed after the copper alloy material is formed into a product shape as a spring. By performing the secondary heat treatment, Ni 2 Si phase particles are further precipitated and the sag resistance is improved.
ここで、1次熱処理は、もっぱらＣｕＡｇ相の析出を主眼とし、Ｎｉ２Ｓｉ相粒子の析出は副次的であるのに対し、２次熱処理は、Ｎｉ２Ｓｉ相粒子の析出を主眼としている。ＣｕＡｇ相は冷間加工性に優れ、析出後に冷間加工を施すことで繊維化し高い強度が得られる。一方、Ｎｉ２Ｓｉ相粒子は金属間化合物であり、塑性加工性に乏しく、過度に析出させると加工性に悪影響を与える反面、Ｎｉ２Ｓｉ相粒子が多く析出することで塑性変形が生じにくくなり、耐へたり性が向上する。そこで、１次熱処理では比較的高い温度で熱処理を行い、ＣｕＡｇ相を多く析出させる。その後、冷間加工を行い、ばねとしての製品形状に成形された後に、比較的低い温度で２次熱処理を行い、Ｎｉ２Ｓｉ相粒子の析出を図り、加工性と耐へたり性の両立を図っている。２次熱処理の温度が高すぎると再結晶が起こり、ＣｕＡｇ相による繊維強化の効果が失われてしまうこととなる。 Here, primary heat treatment mainly focuses on precipitation of CuAg phase, and precipitation of Ni 2 Si phase particles is secondary, whereas secondary heat treatment mainly focuses on precipitation of Ni 2 Si phase particles. . The CuAg phase is excellent in cold workability, and is fiberized by applying cold work after precipitation to obtain high strength. On the other hand, Ni 2 Si phase particles are an intermetallic compound and have poor plastic workability. If they are excessively precipitated, the workability is adversely affected. On the other hand, a large amount of Ni 2 Si phase particles precipitate, so that plastic deformation hardly occurs. Improves sag resistance. Therefore, in the first heat treatment by heat at relatively high temperatures, thereby often precipitate CuAg phase. After that, after cold working and forming into a product shape as a spring, secondary heat treatment is performed at a relatively low temperature, Ni 2 Si phase particles are precipitated, and both workability and sag resistance are achieved. I am trying. If the temperature of the secondary heat treatment is too high, recrystallization occurs and the effect of fiber reinforcement by the CuAg phase is lost.
本発明によれば、環境上の問題がなく、しかも、ＣｕＡｇ相粒子とＮｉ２Ｓｉ相粒子とを複合生成させた微細粒子によって、高強度で高導電性を有し、また、耐へたり性を改善した銅合金材料を得ることができ、また、これを用いて、耐へたり性に優れ、長寿命の導電性ばね材料を得ることができる。 According to the present invention, there is no environmental problem, and the fine particles obtained by complex formation of CuAg phase particles and Ni 2 Si phase particles have high strength and high conductivity, and are also resistant to sag. A copper alloy material having improved resistance can be obtained, and by using this, a conductive spring material having excellent sag resistance and a long life can be obtained.
以下、本発明の実施形態について説明するが、各構成元素の含有量の単位「％」は「質量％」を示す。 Hereinafter, although embodiment of this invention is described, the unit "%" of content of each structural element shows "mass%".
本発明の銅合金材料は、Ｃｕに、５．０〜１６．０％のＡｇを含有させることにより、ＣｕとＡｇの共晶相を晶出させて、良好な導電性を維持しつつ強度を増大させ、さらに、１．０〜５．０％のＮｉおよび０．２〜１．２％のＳｉを含有させることによって、Ｃｕ母材中にさらにＮｉとＳｉの化合物粒子（Ｎｉ２Ｓｉ相）を析出させ、これらの共晶相とＮｉ２Ｓｉ粒子との複合生成によって、導電性の低下を抑制しながら、強度のいっそうの増大を図るとともに、前記ばね用として用いる場合における耐へたり性の向上を図るものである。 The copper alloy material of the present invention contains 5.0 to 16.0% Ag in Cu, thereby crystallizing a eutectic phase of Cu and Ag, and maintaining strength while maintaining good conductivity. By increasing and further containing 1.0 to 5.0% Ni and 0.2 to 1.2% Si, further compound particles of Ni and Si (Ni 2 Si phase) in the Cu base material In addition, the composite formation of these eutectic phases and Ni 2 Si particles is intended to further increase the strength while suppressing the decrease in conductivity, and to improve the sag resistance when used for the spring. It is intended to improve.
ここで「へたり性」とは、例えば「ばね技術研究会会報」ｐ．２８２８（２００１年１０月発行）にも説明されているように、「弾性限度内の低い応力下において、塑性歪みが発生する現象」で、一般的には「弾性領域で、歪みを繰り返して与えたり、長時間歪みを与えたままにすると、実際に加えられた歪みより大きい歪みが加えられたときと同じ挙動を示し、除荷しても戻らない歪みが生じる現象」をいう。 Here, “sagging” means, for example, “Spring Technology Workshop Bulletin” p. 2828 (issued in October 2001), “Phenomenon in which plastic strain occurs under low stress within the elastic limit”. Generally, “strain is repeatedly applied in the elastic region. If the strain is applied for a long period of time, it means the same phenomenon as when a strain larger than the strain actually applied is applied and a strain that does not return even when unloaded is generated.
そして、その測定は、例えば所定形状を有する試験線材に、その線材の弾性領域内での応力を負荷して所定時間放置した後に開放したときの歪みについて、応力負荷前と応力除去後の形状乃至寸法変化の比率で示されるものであって、本願発明では、負荷応力として対象線材またはその成形品の０．２％耐力値の４０％に相当する応力を３分間負荷した後、除荷した時の残留歪み量として［（Ｌ０−Ｌ１）／Ｌ０］×１００の計算式から求めることができる。なお、この場合、線材がトーションばねのような曲げ応力が加わる状態で使用されるものでは、前記４０％相当応力を加え、除荷した後の線材の弦長比について前記式から求められる。 The measurement is performed, for example, on a test wire having a predetermined shape by applying a stress in the elastic region of the wire and leaving it for a predetermined time, and then releasing the strain before or after stress loading. In the present invention, when a load corresponding to 40% of the 0.2% proof stress value of the target wire or its molded product is loaded for 3 minutes and then unloaded. The residual strain amount of [(L 0 −L 1 ) / L 0 ] × 100 can be obtained from the calculation formula. In this case, when the wire is used in a state where a bending stress such as a torsion spring is applied, the chord length ratio of the wire after unloading by applying the 40% equivalent stress is obtained from the above formula.
また、圧縮コイルばねなどの成形品の場合についても、例えば以下の要領でへたり率を求めることができる。すなわち、そのばねについて、予め応力負荷した応力−歪み線図を求め、その線図のなかで０．２％耐力に相当する応力の４０％を加えた状態で所定時間放置し、除荷した時の自由長（Ｌ１）と当初自由長（Ｌ０）との変化を前記式に入れて求めるものである。これらの関係から明らかなように、値の小さいほど耐へたり性に優れていることを意味する。前記用途光ピックアップ用ばねやその他精密機器用ばねに用いるものでは、より好ましい耐へたり性は１．２％以下である。 Moreover, also in the case of molded articles, such as a compression coil spring, a sag rate can be calculated | required in the following ways, for example. That is, when a stress-strain diagram pre-stressed with respect to the spring is obtained, and left unloaded for a predetermined time in a state where 40% of the stress corresponding to 0.2% proof stress is added in the diagram. The change between the free length (L 1 ) and the initial free length (L 0 ) is calculated in the above equation. As is clear from these relationships, the smaller the value, the better the sag resistance. For those used for the optical pickup spring and other precision device springs, the more preferred sag resistance is 1.2% or less.
したがって、本発明では、こうした現象を改善するためには、線の高強度化とともに弾性限度内での変形挙動に耐え得る形態にするのが有効との判断から、前記ＣｕＡｇ共晶相およびＮｉ２Ｓｉ化合物を複合して生成させることとした。また、そのなかで、これら共晶相および化合物がその長手方向に沿って連続的に点在配置した分布状態乃至繊維状に引き伸ばされた状態で複合させることで、たわみ応力などに対して大きな抵抗を有するものとなる。 Therefore, in the present invention, in order to improve such a phenomenon, it is effective to make a form that can withstand the deformation behavior within the elastic limit as well as increasing the strength of the wire, so that the CuAg eutectic phase and Ni 2 are effective. It was decided to form a composite of Si compounds . Among these, by combining these eutectic phases and compounds in a distributed state in which the eutectic phase and the compound are continuously arranged along the longitudinal direction or in a state of being stretched into a fiber shape, a large resistance to a bending stress or the like is obtained. It will have.
こうした析出物の発生を図る観点から、本発明では各元素の含有量を前述の範囲にするものとした。すなわち、Ａｇ含有量が５．０％に満たないと、強度が不十分となり、１６．０％を超えると、強度が高くなりすぎ冷間加工（伸線加工）が困難になる。好ましいＡｇ含有量は８．０〜１４．０％の範囲であり、より好ましくは９．５〜１２．０％の範囲である。また、Ｎｉ含有量が１．０％に満たないと、上記Ｎｉ ２ Ｓｉの形成が少なくなり、強度を十分に向上させることができない。また、５．０％を超えると、強度は高くなるものの冷間加工が困難になる。好ましいＮｉ含有量は１．５〜３．２％の範囲である。 From the viewpoint of generating such precipitates, in the present invention, the content of each element is set to the above-described range. That is, if the Ag content is less than 5.0%, the strength is insufficient, and if it exceeds 16.0%, the strength becomes too high and cold working (drawing) becomes difficult. The preferable Ag content is in the range of 8.0 to 14.0%, more preferably in the range of 9.5 to 12.0%. On the other hand, if the Ni content is less than 1.0%, the formation of the Ni 2 Si is reduced and the strength cannot be sufficiently improved. On the other hand, if it exceeds 5.0%, the strength increases, but cold working becomes difficult. A preferable Ni content is in the range of 1.5 to 3.2%.
さらに、Ｓｉは、Ｎｉとの金属間化合物、Ｎｉ２Ｓｉを生成させるものであるため、Ｎｉ含有量が決まると最適なＳｉ含有量も決まってくる。すなわち、Ｓｉ含有量が０．２％に満たないと、Ｎｉ２Ｓｉの析出量が少なくなり、強度を十分に向上させることができない。また、１．２％を超えると、強度は変わらず、導電性が低下する。好ましいＳｉ含有量は０．３〜０．８％の範囲である。 Furthermore, since Si is an intermetallic compound with Ni and produces Ni 2 Si, the optimum Si content is determined when the Ni content is determined. That is, when the Si content is less than 0.2%, the amount of Ni 2 Si deposited decreases, and the strength cannot be sufficiently improved. On the other hand, if it exceeds 1.2%, the strength does not change and the conductivity is lowered. A preferable Si content is in the range of 0.3 to 0.8%.
また、本発明においては、Ａｇ、ＮｉおよびＳｉの含有量をそれぞれａ（％）、ｂ（％）およびｃ（％）としたとき、８．０≦｛（１／４）×ａ＋ｂ｝／ｃ≦１４．０となるようにすることが好ましい。これは、Ａｇ、ＮｉおよびＳｉの各含有量のバランスをとることにより、冷間加工や析出処理などを行う場合に、加工硬化、析出硬化を促進して、強度を増大させることができ、かつ、良好な導電性も維持することができるという知見に基づくものである。 In the present invention, when the contents of Ag, Ni, and Si are a (%), b (%), and c (%), respectively, 8.0 ≦ {(1/4) × a + b} / c It is preferable to satisfy ≦ 14.0 . It is possible to increase the strength by promoting work hardening and precipitation hardening when performing cold working and precipitation treatment by balancing the contents of Ag, Ni and Si, and Based on the knowledge that good conductivity can be maintained.
すなわち、図１は、Ａｇ、ＮｉおよびＳｉのそれぞれの含有量を前述した範囲で種々変化させ、［｛（１／４）×ａ＋ｂ｝／ｃ］値（Ａ値）と、強度（耐力、引張強さ）および導電率の関係を調べた結果を示したもので、［｛（１／４）×ａ＋ｂ｝／ｃ］値と強度は正の比例関係にあり、また、［｛（１／４）×ａ＋ｂ｝／ｃ］値と導電率は負の比例関係にあり、［｛（１／４）×ａ＋ｂ｝／ｃ］値を特定することにより、安定した特性が得られることを示している。
［（１／４ａ＋ｂ）／ｃ］値が８．０未満では、強度を十分に増大させることができず、一方、［（１／４ａ＋ｂ）／ｃ］値が１４．０を超えると、十分な耐へたり性が得られない。
That is, FIG. 1 shows various changes in the contents of Ag, Ni and Si within the above-mentioned range, and [{(1/4) × a + b} / c] value (A value) and strength (proof strength, tensile strength). The relationship between the strength and the conductivity is shown. [{(1/4) × a + b} / c] value and the strength are in a positive proportional relationship, and [{(1/4) ) × a + b} / c] value and conductivity are in a negative proportional relationship, and specifying the [{(1/4) × a + b} / c] value indicates that stable characteristics can be obtained. .
If the [(1 / 4a + b) / c] value is less than 8.0, the strength cannot be increased sufficiently. On the other hand, if the [(1 / 4a + b) / c] value exceeds 14.0, the strength is sufficient. sag resistance is not be obtained.
本発明の銅合金には、耐へたり性をさらに向上させるため、必要に応じてＳｎおよび／またはＺｎを含有させることができる。その含有量は、Ｓｎが０．２〜１．０％、Ｚｎが０．３〜１．２％の範囲が好ましい。Ｓｎが０．２％未満では、添加による効果が得られず、１．０％を超えると加工性が低下する。また、Ｚｎが０．３％未満では、添加による効果が得られず、１．２％を超えるとＳｎの場合と同様に加工性が低下する。 In order to further improve the sag resistance, the copper alloy of the present invention can contain Sn and / or Zn as necessary. The content of Sn is preferably in the range of 0.2 to 1.0% and Zn in the range of 0.3 to 1.2%. If Sn is less than 0.2%, the effect of addition cannot be obtained, and if it exceeds 1.0%, the workability decreases. Moreover, if Zn is less than 0.3%, the effect by addition cannot be obtained, and if it exceeds 1.2%, the workability deteriorates as in the case of Sn.
また、本発明の銅合金には、例えば合計３％以下の不可避的不純物が含まれていてもよい。不可避的不純物としては、Ｍｇ、Ｍｎ、Ｃｒ、Ｃｏ、Ｔｉ、Ａｌ、Ｓｂ、Ａｓ、Ｐｂ、Ｂｉ、Ｏ、Ｐ、Ｓ、Ｓｅ、Ｔｅなどが挙げられる。 The copper alloy of the present invention may contain, for example, 3% or less of inevitable impurities in total. Inevitable impurities include Mg, Mn, Cr, Co, Ti, Al, Sb, As, Pb, Bi, O, P, S, Se, Te, and the like.
本発明の銅合金は、０．２％耐力が９００ＭＰａ以上であり、導電率が２５％ＩＡＣＳ以上であることが好ましく、０．２％耐力が９００ＭＰａ未満では、ばね用材料としての強度が十分でなく、また、導電率が２５％ＩＡＣＳ未満では、導電材料としたときの損失が大きくなる。より好ましくは、０．２％耐力が１０００〜１５００ＭＰａ程度で、導電率が３０％ＩＡＣＳ以上である。 The copper alloy of the present invention preferably has a 0.2% yield strength of 900 MPa or more and an electrical conductivity of 25% IACS or more. If the 0.2% yield strength is less than 900 MPa, the strength as a spring material is sufficient. In addition, when the conductivity is less than 25% IACS, the loss when the conductive material is used increases. More preferably, the 0.2% proof stress is about 1000 to 1500 MPa, and the conductivity is 30% IACS or more.
ここで、０．２％耐力は、ＪＩＳ Ｚ ２２４１「金属材料引張試験法」に準拠して引張試験を行った場合の、０．２％の永久歪みを生ずるときの応力をいい、また、導電率は、ＪＩＳ Ｃ ３００２に準拠して、２０℃の恒温槽中での４端子法（試料長さ１００ｍｍ）により測定することができる。特に耐力は硬質線材において、弾性特性が向上してより大きな応力に耐えることができ、用途の拡大を図ることができる。 Here, 0.2% proof stress refers to the stress when a permanent strain of 0.2% is produced when a tensile test is performed in accordance with JIS Z 2241 “Metal Material Tensile Test Method”. The rate can be measured by a four-terminal method (sample length: 100 mm) in a constant temperature bath at 20 ° C. in accordance with JIS C 3002. In particular, in the case of a hard wire, the elastic characteristics are improved, and it is possible to withstand a greater stress, and the application can be expanded.
本発明の銅合金材料は、このような特性とともに、組織内に前記析出物を複合し、また、該析出物は硬質かつ微細であることから、分散強化または繊維強化特性を備えるものとなり、それによって耐へたり性を高めることができる。特に、これら析出物をその長手方向に沿って方向性を持って配置した場合により顕著となる。なお、このような析出物によって導電性は若干低下する場合があるものの、本発明ではなお２５％ＩＡＣＳ以上の導電性を有することから実質的な影響はない。 The copper alloy material of the present invention combines the above precipitates in the structure with such characteristics, and since the precipitates are hard and fine, they have dispersion strengthening or fiber reinforced characteristics. Can improve the sag resistance. In particular, it becomes more prominent when these precipitates are arranged with directionality along the longitudinal direction. Although the conductivity may be slightly lowered by such a precipitate, the present invention has no substantial influence since it has a conductivity of 25% IACS or more.
上記のような銅合金材料は、次のような方法で製造することが好ましい。 The copper alloy material as described above is preferably manufactured by the following method.
すなわち、質量で、５．０〜１６．０％のＡｇ、１．０〜５．０％のＮｉおよび０．２〜１．２％のＳｉと、必要に応じて０．２〜１．０％のＳｎおよび／または０．３〜１．２％のＺｎを含有し、残部がＣｕおよび不可避的不純物からなる銅合金材料に、温度３００〜６００℃で１〜１００時間の１次熱処理を施すことで、組織内にＣｕとＡｇとの共晶相（ＣｕＡｇ相）およびＮｉ２Ｓｉ相粒子とを複合形成させ、その後、加工率５０％以上で冷間加工を行うものである。冷間加工は、最終形状に応じて、伸線、圧延またはその他の加工方法が採用される。 That is, by mass, 5.0 to 16.0% Ag, 1.0 to 5.0% Ni and 0.2 to 1.2% Si, and 0.2 to 1.0 if necessary. A copper alloy material containing 1% Sn and / or 0.3 to 1.2% Zn, the balance being Cu and inevitable impurities, is subjected to a primary heat treatment at a temperature of 300 to 600 ° C. for 1 to 100 hours. Thus, the eutectic phase (CuAg phase) of Cu and Ag and Ni 2 Si phase particles are formed in the structure in a composite, and then cold working is performed at a working rate of 50% or more. For cold working, wire drawing, rolling, or other processing methods are employed depending on the final shape.
前記１次熱処理によって、Ｃｕマトリックス中に積極的にＡｇとＣｕからなる共晶相（ＣｕＡｇ相）を析出することを第一の特徴とする。このＣｕＡｇ相は、母相Ｃｕよりは硬質であるものの比較的延性を有し、その後の冷間加工によって、例えばその長手方向に沿って微細に伸びる繊維構造を有するものとする。なお、この場合、前記共晶相とともにＮｉ２Ｓｉ粒子を析出させることができる。熱処理温度が３００℃未満であるかもしくは熱処理時間が１時間に満たない場合は、前記析出が十分に行われず、逆に、熱処理温度が６００℃を超えるかもしくは熱処理時間が１００時間を越えると、ＣｕＡｇ相の固溶およびＮｉ２Ｓｉ粒子の粗大化が生じる。この析出熱処理は、より好ましくは３５０〜４５０℃の温度で５〜２０時間行う。 The first feature is that a eutectic phase (CuAg phase) composed of Ag and Cu is positively precipitated in the Cu matrix by the primary heat treatment. Although this CuAg phase is harder than the parent phase Cu, it has relatively ductility, and has a fiber structure that extends finely, for example, along its longitudinal direction by subsequent cold working. In this case, Ni 2 Si particles can be precipitated together with the eutectic phase. When the heat treatment temperature is less than 300 ° C. or the heat treatment time is less than 1 hour, the precipitation is not sufficiently performed. Conversely, when the heat treatment temperature exceeds 600 ° C. or the heat treatment time exceeds 100 hours, Solid solution of CuAg phase and coarsening of Ni 2 Si particles occur. This precipitation heat treatment is more preferably performed at a temperature of 350 to 450 ° C. for 5 to 20 hours.
ＣｕＡｇ相は、このような１次熱処理工程の後の冷間加工において、繊維状に引き伸ばされ、Ｎｉ２Ｓｉ粒子の析出とともに銅合金材料の強度を向上させる。 In the cold working after such a primary heat treatment step, the CuAg phase is stretched into a fiber shape and improves the strength of the copper alloy material together with the precipitation of Ni 2 Si particles.
本発明においては、このような冷間加工の途中で少なくとも１回の中間熱処理工程を行ってもよい。その際の熱処理条件としては、例えば真空中またはアルゴンもしくは窒素雰囲気中で、３００〜６００℃の温度で１分〜１時間未満程度が好ましく、４００〜５８０℃の温度で３〜３０分がより好ましい。このような中間熱処理を施すことにより、高い加工度で加工することが可能となる。温度が３００℃未満であるかもしくは時間が１分に満たないと加工性を十分に改善することができず、逆に、温度が６００℃を超えるかもしくは時間が１０時間を越えると、再結晶のために所定の強度が得られなくなる。 In the present invention, at least one intermediate heat treatment step may be performed during such cold working. As heat treatment conditions at that time, for example, in a vacuum or in an argon or nitrogen atmosphere, a temperature of 300 to 600 ° C. is preferably about 1 minute to less than 1 hour, and a temperature of 400 to 580 ° C. is more preferably 3 to 30 minutes. . By performing such an intermediate heat treatment, it is possible to perform processing with a high degree of processing. If the temperature is less than 300 ° C. or the time is less than 1 minute, the workability cannot be improved sufficiently. Conversely, if the temperature exceeds 600 ° C. or the time exceeds 10 hours, recrystallization occurs. Therefore, a predetermined strength cannot be obtained.
このようにして得られた銅合金材料を、その後、所定の製品形状に切断乃至加工することにより導電性ばね成形品が得られる。導電性ばね成形品の製品形状は、特に限定されるものではなく、コイル状（コイルばね）であっても、直線状（直線ばね）であっても、また、板状（板ばね）であってもよい。本発明においては、所定の製品形状に切断乃至加工した後、前記１次熱処理より低い温度、好ましくは１５０〜４００℃、より好ましくは２００〜３５０℃の２次熱処理を施すことが好ましい。このような２次熱処理を行うことにより、導電性ばね材料として用いる際の耐へたり性をさらに改善することができる。これは、主としてＮｉ２Ｓｉ粒子が析出したことによるものと推測される。２次熱処理温度が１次熱処理温度を超える温度条件では、再結晶が起こり、強度が低下することとなる。なお、この２次熱処理の時間は、熱処理温度に応じて耐へたり性の改善に必要な時間とされ、例えば大気中で、１分〜５時間、好ましくは３分〜１時間、より好ましくは５〜３０分間行われる。 The copper alloy material thus obtained is then cut or processed into a predetermined product shape to obtain a conductive spring molded product. The product shape of the conductive spring molded product is not particularly limited, and may be a coil shape (coil spring), a linear shape (linear spring), or a plate shape (leaf spring). May be. In the present invention, after cutting or processing into a predetermined product shape, it is preferable to perform a secondary heat treatment at a temperature lower than the primary heat treatment, preferably 150 to 400 ° C., more preferably 200 to 350 ° C. By performing such secondary heat treatment, it is possible to further improve the sag resistance when used as a conductive spring material. This is presumably due to the precipitation of Ni 2 Si particles. Under a temperature condition in which the secondary heat treatment temperature exceeds the primary heat treatment temperature, recrystallization occurs and the strength decreases. The time for the secondary heat treatment is a time required for improving the sag resistance according to the heat treatment temperature, and is, for example, 1 minute to 5 hours, preferably 3 minutes to 1 hour, more preferably in the air. 5 to 30 minutes.
本発明による銅合金材料は、高強度、高導電性で、かつ、耐へたり性に優れており、光ピックアップ用サスペンションワイヤ、ＬＳＩ検査用導電性ばね材など、かかる特性が要求される各種電気・電子部品の精密導電性ばね材として有用である。 The copper alloy material according to the present invention has high strength, high electrical conductivity, and excellent sag resistance. Various electrical properties such as suspension wires for optical pickups and conductive spring materials for LSI inspection are required. -Useful as a precision conductive spring material for electronic parts.
次に、本発明の実施例を記載するが、本発明は以下の実施例に何ら限定されるものではない。 Next, examples of the present invention will be described, but the present invention is not limited to the following examples.
実施例・比較例
外周に水冷ジャケットを設けた黒鉛鋳型を有する水平連続鋳造機を用いて、表１に示すような種々の組成を有する線径９．５ｍｍの鋳造ロッドを鋳造した。次いで、これらの鋳造ロッドに、表１に示した各種条件で熱処理および冷間加工を行い、線径０．７ｍｍの銅合金線材を得た。
Examples and Comparative Examples Using a horizontal continuous casting machine having a graphite mold provided with a water cooling jacket on the outer periphery, casting rods having various compositions as shown in Table 1 and having a wire diameter of 9.5 mm were cast. Next, these cast rods were heat-treated and cold worked under various conditions shown in Table 1 to obtain copper alloy wires having a wire diameter of 0.7 mm.
すなわち、比較例１１−１、実施例１１−２では、鋳造ロッドに４５０℃で１０時間の１次熱処理を窒素雰囲気中で施した後、冷間加工した。冷間加工の途中、線径が３．０ｍｍまで伸線されたところで、４５０℃で６分の中間熱処理をアルゴン雰囲気中で行った。 That is, in Comparative Example 11-1 and Example 11-2 , the cast rod was subjected to primary heat treatment at 450 ° C. for 10 hours in a nitrogen atmosphere, and then cold worked. During the cold working, when the wire diameter was drawn to 3.0 mm, an intermediate heat treatment was performed at 450 ° C. for 6 minutes in an argon atmosphere.
比較例１１−３、実施例１１−４、比較例１２−１、実施例１２−２、比較例１３−１および実施例１３−２では、鋳造ロッドに４５０℃で１０時間の１次熱処理を施した後、冷間加工した。冷間加工の途中、線径が３．０ｍｍまで伸線されたところで、５５０℃で６分の中間熱処理を行った。 In Comparative Example 11-3, Example 11-4, Comparative Example 12-1, Example 12-2, Comparative Example 13-1, and Example 13-2 , the cast rod was subjected to primary heat treatment at 450 ° C. for 10 hours. After applying, it was cold worked. During the cold working, when the wire diameter was drawn to 3.0 mm, an intermediate heat treatment was performed at 550 ° C. for 6 minutes.
比較例１４−１、比較例1４−２では、鋳造ロッドに熱処理を施すことなく冷間加工した。冷間加工の途中、線径が３．０ｍｍまで伸線されたところで、５００℃で６分の中間熱処理を行った。 In Comparative Example 14-1 and Comparative Example 14-2 , the cast rod was cold worked without being subjected to heat treatment. During the cold working, when the wire diameter was drawn to 3.0 mm, an intermediate heat treatment was performed at 500 ° C. for 6 minutes.
比較例１４−３、実施例１４−４では、鋳造ロッドに３５０℃で１０時間の１次熱処理を施した後、冷間加工した。冷間加工の途中、線径が３．０ｍｍまで伸線されたところで、５５０℃で６分の中間熱処理を行った。 In Comparative Example 14-3 and Example 14-4 , the cast rod was subjected to primary heat treatment at 350 ° C. for 10 hours and then cold worked. During the cold working, when the wire diameter was drawn to 3.0 mm, an intermediate heat treatment was performed at 550 ° C. for 6 minutes.
比較例１４−５、実施例１４−６では、鋳造ロッドに４００℃で１０時間の１次熱処理を施した後、冷間加工した。冷間加工の途中、線径が３．０ｍｍまで伸線されたところで、５５０℃で６分の中間熱処理を行った。 In Comparative Example 14-5 and Example 14-6 , the cast rod was subjected to a primary heat treatment at 400 ° C. for 10 hours and then cold worked. During the cold working, when the wire diameter was drawn to 3.0 mm, an intermediate heat treatment was performed at 550 ° C. for 6 minutes.
なお、これらの各実施例・比較例の１次熱処理を施したものについては、ＣｕＡｇ共晶相とともに少量のＮｉ２Ｓｉ粒子が確認された。 A small amount of Ni 2 Si particles was confirmed together with the CuAg eutectic phase for those subjected to the primary heat treatment of each of the examples and comparative examples .
この後、得られた線径０．７ｍｍの銅合金線材をコイル状に加工して圧縮コイルばね（コイル外径：７．７０ｍｍ、コイル平均径：７．００ｍｍ、自由長（Ｌ０）：１３．５ｍｍ、総巻数：６．５巻、有効巻数：４．５巻）を作製した。実施例１１−２、実施例１１−４、実施例１２−２、実施例１３−２、比較例１４−２、実施例１４−４、実施例１４−６ではコイル状に加工後に、２５０℃で１時間の２次熱処理を行った。 Thereafter, the obtained copper alloy wire material having a wire diameter of 0.7 mm was processed into a coil shape, and a compression coil spring (coil outer diameter: 7.70 mm, coil average diameter: 7.00 mm, free length (L 0 ): 13 0.5 mm, total number of turns: 6.5, effective number of turns: 4.5). In Example 11-2, Example 11-4, Example 12-2, Example 13-2, Comparative Example 14-2, Example 14-4, and Example 14-6, after processing into a coil shape, 250 ° C. A secondary heat treatment was performed for 1 hour.
比較例２１−１、２１−２
１０．０質量％のＡｇと残部がＣｕからなる銅合金を、実施例と同様の水平連続鋳造機を用いて、線径９．５ｍｍの鋳造ロッドを鋳造し、次いで、この鋳造ロッドを冷間加工して、線径０．７ｍｍの銅合金線材を得た。この後、得られた線径０．７ｍｍの銅合金線材をコイル状に加工して実施例と同形状、同寸法の圧縮コイルばねを作製した。比較例２１−２ではコイル状に加工後に、２６０℃で３０分間の熱処理を行った。
Comparative Examples 21-1 and 21-2
A copper alloy composed of 10.0% by mass of Ag and the balance of Cu is cast using a horizontal continuous casting machine similar to that of the example to cast a casting rod having a wire diameter of 9.5 mm. Processing was performed to obtain a copper alloy wire having a wire diameter of 0.7 mm. Thereafter, the obtained copper alloy wire having a wire diameter of 0.7 mm was processed into a coil shape to produce a compression coil spring having the same shape and the same dimensions as those of the example. In Comparative Example 21-2 , heat treatment was performed at 260 ° C. for 30 minutes after processing into a coil shape.
比較例２２−１、２２−２
２質量％のＢｅと残部がＣｕからなる線径０．７ｍｍの銅合金線材を、コイル状に加工して実施例と同形状、同寸法の圧縮コイルばねを作製した。なお、比較例２２−１ではコイル状に加工後に、２６０℃で３０分間の熱処理を行った。また、比較例２２−２ではコイル状に加工後に、３００℃で１時間の熱処理を行った。
Comparative Examples 22-1 and 22-2
A copper alloy wire rod having a wire diameter of 0.7 mm made of 2 mass% Be and the balance Cu was processed into a coil shape to produce a compression coil spring having the same shape and the same dimensions as those of the example. In Comparative Example 22-1 , heat treatment was performed at 260 ° C. for 30 minutes after processing into a coil shape. Further, in Comparative Example 22-2 , heat treatment was performed at 300 ° C. for 1 hour after processing into a coil shape.
比較例２３−１、２３−２
３．０質量％のＡｇと残部がＣｕからなる銅合金を、実施例と同様の水平連続鋳造機を用いて、線径９．５ｍｍの鋳造ロッドを鋳造し、次いで、この鋳造ロッドを冷間加工して、線径０．７ｍｍの銅合金線材を得た。この後、得られた線径０．７ｍｍの銅合金線材をコイル状に加工して実施例と同形状、同寸法の圧縮コイルばねを作製した。比較例２３−２ではコイル状に加工後に、２６０℃で３０分間の熱処理を行った。
Comparative Examples 23-1 and 23-2
A copper alloy composed of 3.0% by mass of Ag and the balance of Cu is cast using a horizontal continuous casting machine similar to that of the example to cast a casting rod having a wire diameter of 9.5 mm. Processing was performed to obtain a copper alloy wire having a wire diameter of 0.7 mm. Thereafter, the obtained copper alloy wire having a wire diameter of 0.7 mm was processed into a coil shape to produce a compression coil spring having the same shape and the same dimensions as those of the example. In Comparative Example 23-2 , heat treatment was performed at 260 ° C. for 30 minutes after processing into a coil shape.
上記各実施例および各比較例で得られた圧縮コイルばねについて、へたり率（γ）を測定するとともに、同条件の処理を施した線材について０．２％耐力、引張強さおよび導電率を測定した。これらの結果を、冷間加工前に採取したサンプルについて測定した引張強さおよび導電率とともに表２に示す。なお、へたり率（γ）は、圧縮コイルばねに、ばね長さ１２ｍｍ、８ｍｍとする荷重を１０回繰り返して負荷した後の自由長（Ｌ１０）を測定し、次式より算出した。
γ（％）＝［（Ｌ０−Ｌ１０）／Ｌ０］×１００
また、０．２％耐力および引張強さはＪＩＳ Ｚ ２２４１に準拠し、導電率はＪＩＳ Ｃ ３００２に準拠して測定した。
For the compression coil springs obtained in each of the above Examples and Comparative Examples, the sag rate (γ) was measured, and 0.2% proof stress , tensile strength, and electrical conductivity were measured for the wire that had been processed under the same conditions. It was measured. These results are shown in Table 2 together with the tensile strength and conductivity measured for the samples taken before cold working. The sag rate (γ) was calculated from the following equation by measuring the free length (L 10 ) after a compression coil spring was loaded 10 times with a load having a spring length of 12 mm and 8 mm.
γ (%) = [(L 0 −L 10 ) / L 0 ] × 100
Further, 0.2% proof stress and tensile strength were measured according to JIS Z 2241, and conductivity was measured according to JIS C 3002.
表１および表２に示すように、実施例で得られた導電性ばねは、高強度、高導電性で、かつ、優れた耐へたり性を有するものである。比較例２１−１、２１−２のＣｕ−Ａｇ合金は導電率は７０％ＩＡＣＳ以上と良好であるものの、へたり率が約３．９％、約１．８％と大きく、ばね材料としては必ずしも十分ではない。一方、本発明の実施例はいずれもへたり率が小さい。特に、２次熱処理を施した実施例では、へたり率は１％以下となっており、比較例２２−１、２２−２のベリリウム銅合金と同等の耐へたり性を有し、かつ、導電率においてはそれらに勝るものとなっている。 As shown in Table 1 and Table 2, the conductive springs obtained in the examples have high strength, high conductivity, and excellent sag resistance. Although the Cu-Ag alloys of Comparative Examples 21-1 and 21-2 have good electrical conductivity of 70% IACS or higher, the sag ratio is large at about 3.9% and about 1.8%, and as a spring material, Not always enough. On the other hand, all of the embodiments of the present invention have a low settling rate . In particular, in the examples subjected to the secondary heat treatment, the sag rate is 1% or less, and has the same sag resistance as the beryllium copper alloys of Comparative Examples 22-1 and 22-2 , and In terms of conductivity, they are superior to them.
これらの測定結果から、本発明の銅合金材料は、ばね成形用として十分な特性を有することが確認された。したがって、導電性ばね材料の用途、特に精密分野において使用されるものとして、有害物質を含むベリリウム銅合金の代替材料として十分な性能を持つものである。 From these measurement results, it was confirmed that the copper alloy material of the present invention has sufficient characteristics for spring forming. Therefore, it has sufficient performance as a substitute material for beryllium copper alloys containing harmful substances as a conductive spring material, particularly in the precision field.
Claims (6)
γ（％）＝［（Ｌ ０ −Ｌ １ ）／Ｌ ０ ］×１００
（ここで、Ｌ １ およびＬ ０ は、当該材料から作製した線材または成形品にその０．２％耐力の４０％に相当する応力を３分間負荷した後、除荷した時の自由長および当初自由長である） Containing 5.0 to 16.0% Ag, 1.0 to 5.0% Ni and 0.2 to 1.2% Si by mass, with the balance consisting of Cu and inevitable impurities, When the contents of Ag, Ni and Si are a (mass%), b (mass%) and c (mass%), respectively, 8.0 ≦ {(1/4) × a + b} /c≦14.0 It is characterized by the fact that the structure contains a eutectic phase of Cu and Ag and Ni 2 Si particles in a composite, and the sag rate (γ) determined by the following formula is 1.2% or less. High strength copper alloy material for precision conductive springs with excellent sag resistance.
γ (%) = [(L 0 −L 1 ) / L 0 ] × 100
(Here, L 1 and L 0 are the free length when the load or the molded product made from the material is loaded for 3 minutes with the stress corresponding to 40% of its 0.2% proof stress, and the initial length when unloaded. Free length)
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|---|---|---|---|---|
| JPH0693399A (en) * | 1992-09-16 | 1994-04-05 | Showa Electric Wire & Cable Co Ltd | Production of cu-ag alloy conductor |
| JPH0693398A (en) * | 1992-09-16 | 1994-04-05 | Showa Electric Wire & Cable Co Ltd | Production of cu-ag alloy wire |
| JPH06145930A (en) * | 1992-11-02 | 1994-05-27 | Furukawa Electric Co Ltd:The | Production of precipitation type copper alloy |
| JPH08319527A (en) * | 1995-05-25 | 1996-12-03 | Kobe Steel Ltd | Copper alloy, excellent in adhesion of soft solder and plating suitability and easy of cleaning, and its production |
-
2005
- 2005-04-08 JP JP2005112190A patent/JP4708833B2/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0693399A (en) * | 1992-09-16 | 1994-04-05 | Showa Electric Wire & Cable Co Ltd | Production of cu-ag alloy conductor |
| JPH0693398A (en) * | 1992-09-16 | 1994-04-05 | Showa Electric Wire & Cable Co Ltd | Production of cu-ag alloy wire |
| JPH06145930A (en) * | 1992-11-02 | 1994-05-27 | Furukawa Electric Co Ltd:The | Production of precipitation type copper alloy |
| JPH08319527A (en) * | 1995-05-25 | 1996-12-03 | Kobe Steel Ltd | Copper alloy, excellent in adhesion of soft solder and plating suitability and easy of cleaning, and its production |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2006291271A (en) | 2006-10-26 |
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