JP5688744B2 - High strength and high toughness copper alloy forging - Google Patents
High strength and high toughness copper alloy forging Download PDFInfo
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- 229910000881 Cu alloy Inorganic materials 0.000 title claims description 27
- 238000005242 forging Methods 0.000 title claims description 9
- 239000000463 material Substances 0.000 claims description 17
- 229910052710 silicon Inorganic materials 0.000 claims description 10
- 229910052759 nickel Inorganic materials 0.000 claims description 9
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 239000010949 copper Substances 0.000 claims description 6
- 229910052726 zirconium Inorganic materials 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052725 zinc Inorganic materials 0.000 claims description 5
- 238000010521 absorption reaction Methods 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- 238000012360 testing method Methods 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 238000012545 processing Methods 0.000 description 11
- 238000011282 treatment Methods 0.000 description 11
- 239000000956 alloy Substances 0.000 description 10
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 9
- 229910052717 sulfur Inorganic materials 0.000 description 9
- 239000011593 sulfur Substances 0.000 description 9
- 230000032683 aging Effects 0.000 description 7
- 229910045601 alloy Inorganic materials 0.000 description 7
- 238000000034 method Methods 0.000 description 6
- 229910017876 Cu—Ni—Si Inorganic materials 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 239000011888 foil Substances 0.000 description 4
- 238000002347 injection Methods 0.000 description 4
- 239000007924 injection Substances 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- UREBDLICKHMUKA-CXSFZGCWSA-N dexamethasone Chemical compound C1CC2=CC(=O)C=C[C@]2(C)[C@]2(F)[C@@H]1[C@@H]1C[C@@H](C)[C@@](C(=O)CO)(O)[C@@]1(C)C[C@@H]2O UREBDLICKHMUKA-CXSFZGCWSA-N 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 229910052718 tin Inorganic materials 0.000 description 3
- 229910001369 Brass Inorganic materials 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 239000010951 brass Substances 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910000906 Bronze Inorganic materials 0.000 description 1
- 229910017518 Cu Zn Inorganic materials 0.000 description 1
- 229910017752 Cu-Zn Inorganic materials 0.000 description 1
- 229910017943 Cu—Zn Inorganic materials 0.000 description 1
- 239000010974 bronze Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000010622 cold drawing Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 1
- TVZPLCNGKSPOJA-UHFFFAOYSA-N copper zinc Chemical compound [Cu].[Zn] TVZPLCNGKSPOJA-UHFFFAOYSA-N 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 239000000428 dust Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000001988 toxicity Effects 0.000 description 1
- 231100000419 toxicity Toxicity 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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Description
この発明は、樹脂射出金型材を始めとした鍛造成形品に適用可能な高強度高靭性銅合金鍛造材に関するものである。 The present invention relates to a high-strength, high-toughness copper alloy forged material that can be applied to forged molded articles such as resin injection mold materials.
従来、導電性・熱伝導性に優れた合金として、黄銅（Ｃｕ−Ｚｎ系）、青銅（Ｃｕ−Ｓｎ系）、Ｂｅ銅やコルソン合金（Ｃｕ−Ｎｉ−Ｓｉ系）といった銅合金が用いられてきた。特に熱伝導とともに強度や硬度が要求されるようなプラスチック射出金型材や航空機部材などにはＢｅ銅やコルソン合金が用いられてきた。しかし、上記のＢｅ銅は溶解や加工時に生じる粉塵の有毒性が懸念され代替材が求められている。コルソン合金には更なる高熱伝導性、高強度、高硬度が求められている。また、鍛造材では鍛造後の熱処理時に材料に割れが生じることから、熱間加工性に加え、熱処理後の延性の向上が求められている。 Conventionally, copper alloys such as brass (Cu—Zn), bronze (Cu—Sn), Be copper, and Corson alloy (Cu—Ni—Si) have been used as alloys having excellent conductivity and thermal conductivity. It was. In particular, Be copper and Corson alloy have been used for plastic injection mold materials and aircraft members that require strength and hardness as well as heat conduction. However, the above-mentioned Be copper is concerned about the toxicity of dust generated during melting and processing, and an alternative material is required. Corson alloys are required to have higher thermal conductivity, higher strength, and higher hardness. In addition, since the forged material is cracked during heat treatment after forging, it is required to improve ductility after heat treatment in addition to hot workability.
近年、銅合金の箔帯で強度を増大し、かつ曲げ加工性を向上させる方策として、Ｃｕ−Ｎｉ−Ｓｉ系銅合金にＭｇ、Ｓｎ、Ｔｉ、Ｚｒ、Ａｌ、Ｍｎなどを添加した銅合金が製造されている（特許文献１、特許文献２、特許文献３、特許文献４、特許文献５参照）。
Ｍｇ、Ｓｎはマトリックスに固溶して強度を向上させる。Ｔｉ、Ｚｒ、Ａｌ、Ｍｎは硫黄との親和性が強いため硫黄と化合物を形成し、熱間加工割れの原因である粒界への硫黄の偏析を軽減する。
In recent years, copper alloys obtained by adding Mg, Sn, Ti, Zr, Al, Mn, etc. to a Cu—Ni—Si based copper alloy as a measure to increase the strength and improve the bending workability with a copper alloy foil strip. It is manufactured (see Patent Document 1, Patent Document 2, Patent Document 3, Patent Document 4, and Patent Document 5).
Mg and Sn are dissolved in the matrix to improve the strength. Ti, Zr, Al, and Mn have a strong affinity for sulfur, so they form a compound with sulfur, reducing the segregation of sulfur to the grain boundaries, which is the cause of hot work cracking.
特許文献２、特許文献３、特許文献５に示すような銅合金箔帯はＳｎ、Ｍｎ、Ｚｒなどを添加して、固溶化処理と時効処理の前後で、熱間圧延、冷間圧延や熱間引抜、冷間引抜を繰り返し行うことで従来の銅合金箔帯を上回る曲げ加工性と強度を有している。
また、特許文献６に示すように、シェル中子用金型材に適用できる銅合金も発明されている。
Copper alloy foil strips as shown in Patent Document 2, Patent Document 3, and Patent Document 5 are added with Sn, Mn, Zr, etc., and before and after solution treatment and aging treatment, hot rolling, cold rolling or hot rolling. By repeatedly performing thinning and cold drawing, it has bending workability and strength that exceed those of conventional copper alloy foil strips.
Moreover, as shown in Patent Document 6, a copper alloy that can be applied to a shell core mold material has also been invented.
しかし、鍛造成型品を製造する場合は、主に熱間鍛造で加工成型を行う。箔帯製造で行うような圧延や引抜加工を行うことができないので特許文献２、特許文献３、特許文献５に示すような成分で鍛造成型品を製造しても高強度が得られない。
また、特許文献６で提案されている銅合金の引張強さは最大５８８ＭＰａであり、金型の鏡面性が要求される場合や、熱サイクルの振幅が大きい場合のような、強度が必要な用途においては不十分である。
また、高強度を得るためにはＮｉとＳｉの添加量の増加が有効であるが、凝固中に生成する晶出物や熱処理中に生成する析出物が増加し、熱伝導率が低下したり熱間加工性や熱処理後の延性が低下する可能性がある。
However, when manufacturing a forged molded product, processing molding is mainly performed by hot forging. Since the rolling and drawing processes that are performed in the production of foil strips cannot be performed, high strength cannot be obtained even if forged products are manufactured with the components shown in Patent Document 2, Patent Document 3, and Patent Document 5.
In addition, the tensile strength of the copper alloy proposed in Patent Document 6 is 588 MPa at the maximum, and when the mirror surface property of the mold is required or when the amplitude of the thermal cycle is large, the application requiring strength Is insufficient.
In order to obtain high strength, it is effective to increase the amount of Ni and Si. However, the amount of crystallized substances generated during solidification and precipitates generated during heat treatment increase, and the thermal conductivity decreases. Hot workability and ductility after heat treatment may be reduced.
本発明は、上記事情を背景としてなされたものであり、Ｃｕ−Ｎｉ−Ｓｉ系銅合金に適量のＺｒを添加し硬度、強度、靭性を向上し、プラスチック射出金型材を始めとした鍛造成形品に使用可能な高硬度、高強度、高靭性を有する高強度高靭性銅合金鍛造材を提供することを目的としている。 The present invention has been made against the background of the above circumstances. Forging molded products such as plastic injection mold materials are improved by adding an appropriate amount of Zr to a Cu-Ni-Si based copper alloy to improve hardness, strength and toughness. An object of the present invention is to provide a high-strength, high-toughness copper alloy forging material having high hardness, high strength, and high toughness that can be used in the present invention.
本発明は、上記の課題を解決するためにＣｕ−Ｎｉ−Ｓｉ系銅合金にＺｒを０．００５〜０．２％添加して粒界へのＮｉ２Ｓｉの析出を低減して靭性を高めつつ、Ｎｉ、Ｓｉ、Ｚｒの化合物を形成して強度と硬度を高めるものである。 In order to solve the above problems, the present invention adds 0.005 to 0.2% of Zr to a Cu—Ni—Si based copper alloy to reduce precipitation of Ni 2 Si on the grain boundary and increase toughness. However, Ni, Si, and Zr compounds are formed to increase the strength and hardness.
すなわち、本発明の高強度高靭性銅合金鍛造材のうち第１の本発明は、質量％で、Ｎｉ：３．８を越えて１０％まで、Ｓｉ：０．８を越えて２．４％まで、Ｚｒ：０．００５〜０．１５％を含有し、Ｎｉ／Ｓｉが３．８〜４．８７５である組成を有し、残部がＣｕおよび不可避不純物からなり、ＪＩＳＺ２２４１に準拠して常温で測定された引張強さが７５０ＭＰａ以上、ＪＩＳＺ２２４２に準拠してＵノッチ試験片を用いて測定された衝撃吸収エネルギーが１０Ｊ以上、常温で測定された導電率が３０％ＩＡＣＳ以上であることを特徴とする。 That is, among the high-strength, high-toughness copper alloy forgings according to the present invention, the first present invention has a mass% of Ni: more than 3.8 to 10%, Si: more than 0.8 and 2.4%. Zr: 0.005 to 0.15 % , Ni / Si has a composition of 3.8 to 4.875, the balance is made of Cu and inevitable impurities , and at room temperature according to JISZ2241 The measured tensile strength is 750 MPa or more, the impact absorption energy measured using a U-notch test piece in accordance with JISZ2242 is 10 J or more, and the conductivity measured at room temperature is 30% IACS or more. To do.
第２の本発明の高強度高靭性銅合金鍛造材は、前記第１の本発明において、さらに、Ｃｒ、Ｍｎ、Ｚｎの１種または２種以上を合計で１．５％以下含有することを特徴とする。 The high-strength, high-toughness copper alloy forged material of the second aspect of the present invention further comprises one or more of Cr, Mn, and Zn in the first aspect of the present invention, containing 1.5% or less in total. Features.
以下、本発明の高強度高靱性銅合金鍛造材における各成分の組成限定理由を説明する。なお、以下の成分含有量は、いずれも質量％で示される。 Hereinafter, the reasons for limiting the composition of each component in the high-strength, high-toughness copper alloy forged material of the present invention will be described. In addition, all the following component content is shown by the mass%.
Ｎｉ：３．８を越えて１０％まで
Ｓｉ：０．８を越えて２．４％まで
Ｎｉ及びＳｉは、時効処理を行うことによりＮｉとＳｉが微細なＮｉ２Ｓｉを主とした金属間化合物の析出粒子を形成し、合金の強度を著しく増加させる。また、時効処理でのＮｉ２Ｓｉの析出に伴い、導電性が向上する。ただし、Ｎｉ濃度が３．８％以下で、かつＳｉ濃度が０．８％以下の場合は、所望とする強度が得られない。また、Ｎｉ濃度が１０％を超え、かつＳｉ濃度が２．４％を超える場合は、鋳造時にＮｉ２Ｓｉ、Ｎｉ５Ｓｉ２などが大量に晶出又は析出し、加工や熱処理時に割れやすくなる。加えて、Ｎｉ濃度が１０％を超えると導電率も低下する。
製造性や特性のバランスを考慮すると、より好ましくはＮｉ濃度の下限が４．０％（さらに好ましくは５．０％）、上限が８．０％で、かつＳｉ濃度の下限が０．９％、上限が１．９％である。なお、Ｎｉ／Ｓｉ比は３．８〜４．６が望ましく、この比から大きく外れると、過剰となったＮｉ又はＳｉがＣｕマトリックス中に固溶して熱伝導率を低下させる。
Ni: more than 3.8 up to 10% Si: more than 0.8 up to 2.4% Ni and Si are formed by aging treatment between Ni and Si, mainly Ni 2 Si. Forms precipitated particles of the compound and significantly increases the strength of the alloy. Further, the conductivity is improved with the precipitation of Ni 2 Si in the aging treatment. However, when the Ni concentration is 3.8% or less and the Si concentration is 0.8% or less, the desired strength cannot be obtained. Further, when the Ni concentration exceeds 10% and the Si concentration exceeds 2.4%, a large amount of Ni 2 Si, Ni 5 Si 2 or the like crystallizes or precipitates during casting, and is easily cracked during processing or heat treatment. . In addition, when the Ni concentration exceeds 10%, the conductivity also decreases.
In consideration of the balance of manufacturability and characteristics, the lower limit of the Ni concentration is more preferably 4.0% (more preferably 5.0%), the upper limit is 8.0%, and the lower limit of the Si concentration is 0.9%. The upper limit is 1.9%. The Ni / Si ratio is preferably 3.8 to 4.6. If the Ni / Si ratio deviates greatly from this ratio, excess Ni or Si is dissolved in the Cu matrix to lower the thermal conductivity.
Ｚｒ：０．００５〜０．２％
Ｚｒは硫黄との親和性が強いため硫黄と化合物を形成し、熱間加工割れの原因であるインゴット粒界への硫黄の偏析を軽減することで熱間加工性が改善する。一方で、本発明者らが鋭意調査した結果、Ｚｒ添加によりＮｉやＳｉの拡散が抑制されて粒界に析出するＮｉ２Ｓｉが減少し、時効後の靭性が改善されることが見い出された。この効果を得るためにＺｒを０．００５％以上添加する。しかし、０．２％以上添加すると酸化物や晶出物が増加して製造性、靭性や導電率が劣化するため、上限を０．２％とする。製造性や特性のバランスを考慮すると、より好ましくは下限が０．０１％、上限が０．１％である。
Zr: 0.005 to 0.2%
Since Zr has a strong affinity with sulfur, it forms a compound with sulfur, and the hot workability is improved by reducing the segregation of sulfur to the ingot grain boundary, which is the cause of hot work cracking. On the other hand, as a result of intensive investigations by the present inventors, it was found that Ni 2 Si deposited on grain boundaries is reduced by the addition of Zr and Ni 2 Si is reduced and the toughness after aging is improved. . In order to obtain this effect, 0.005% or more of Zr is added. However, if 0.2% or more is added, the oxides and crystallized substances increase and the manufacturability, toughness and electrical conductivity deteriorate, so the upper limit is made 0.2%. Considering the balance between manufacturability and characteristics, the lower limit is more preferably 0.01% and the upper limit is 0.1%.
Ｃｒ、Ｍｎ、Ｚｎ：ｌ種類以上を合計で１．５％以下
ＣｒはＳｉと金属間化合物を形成し、強度を向上させたり、結晶粒を微細化する効果がある。Ｍｎは硫黄との親和性が強いため硫黄と化合物を形成し、熱間加工割れの原因であるインゴット粒界への硫黄の偏析を低減することで熱間加工性が改善される。Ｚｎは固溶強化により強度を向上させる。また、溶解時に安価な黄銅スクラップを使用可能であれば製造コストを削減できる。
しかし、Ｃｒ、Ｍｎ、Ｚｎを過剰に添加すると熱伝導率が低下するため、上限をＣｒ、Ｍｎ、Ｚｎの１種類以上を合計で１．５％以下とする。
Cr, Mn, Zn: 1% or more in total 1.5% or less In total, Cr forms an intermetallic compound with Si, and has the effect of improving the strength and making the crystal grains fine. Since Mn has a strong affinity for sulfur, it forms a compound with sulfur, and the hot workability is improved by reducing the segregation of sulfur to the ingot grain boundaries, which is the cause of hot work cracking. Zn improves the strength by solid solution strengthening. Moreover, if an inexpensive brass scrap can be used at the time of melt | dissolution, a manufacturing cost can be reduced.
However, if Cr, Mn and Zn are added excessively, the thermal conductivity is lowered. Therefore, the upper limit is made 1.5% or less in total for one or more of Cr, Mn and Zn.
以上のように、本発明の高強度高靭性銅合金鍛造材はＺｒを適量含有することから、高熱伝導率を維持しつつ従来のＣｕ−Ｎｉ−Ｓｉ系銅合金よりも高強度、高硬度、高靭性を有することができる。この結果、本発明の高強度高靭性銅合金鍛造材は、プラスチック射出金型材や航空機部材などにも使用することができる。 As described above, since the high-strength, high-toughness copper alloy forged material of the present invention contains an appropriate amount of Zr, it has higher strength, higher hardness than conventional Cu-Ni-Si based copper alloys while maintaining high thermal conductivity, It can have high toughness. As a result, the high-strength, high-toughness copper alloy forged material of the present invention can be used for plastic injection mold materials, aircraft members, and the like.
本発明の高強度高靱性銅合金鍛造材は、常法によって製造することができる。
本発明に用いる銅合金は、常法により溶製することができ、真空雰囲気や不活性雰囲気、大気雰囲気などで材料を溶解し、鋳塊を得ることができる。雰囲気は真空雰囲気、不活性雰囲気が望ましいが例えば大気高周波炉で溶製することもできる。また、エレクトロスラグ再溶解炉などを用いた二次溶解を行ってもよい。連続鋳造法によって板材を得ることも可能である。
The high-strength, high-toughness copper alloy forged material of the present invention can be produced by a conventional method.
The copper alloy used in the present invention can be melted by a conventional method, and an ingot can be obtained by melting the material in a vacuum atmosphere, an inert atmosphere, an air atmosphere or the like. The atmosphere is preferably a vacuum atmosphere or an inert atmosphere, but it can also be melted in an atmospheric high frequency furnace, for example. Further, secondary melting using an electroslag remelting furnace or the like may be performed. It is also possible to obtain a plate material by a continuous casting method.
銅合金は必要に応じて加工が施される。加工の内容は本発明としては特に限定されるものではなく、プレス、ハンマー、圧延などの既知の鍛造方法を採用することができ、いかなる加工方法を用いても、本発明の特性を得ることが可能である。なお、加工は、製造性を考慮すると熱間加工が望ましく、さらには９００℃以上で行う熱間加工が望ましいが、室温での加工でも熱間加工と同様の特性を得ることが可能である The copper alloy is processed as necessary. The content of the processing is not particularly limited as the present invention, and a known forging method such as pressing, hammering, rolling or the like can be employed, and the characteristics of the present invention can be obtained by using any processing method. Is possible. The processing is preferably hot processing in consideration of manufacturability, and further, hot processing performed at 900 ° C. or higher is preferable, but it is possible to obtain the same characteristics as hot processing even at processing at room temperature.
加工された銅合金材では、加工後または加工途中に固溶化処理を行うことも可能である。固溶化処理の条件は、例えば８００〜１０００℃で１〜１０時間保持した後、Ｎｉ、Ｓｉを十分固溶させるために５００℃以上の温度域を５℃／秒以上の冷却速度で冷却するものが挙げられる。 The processed copper alloy material can be subjected to a solution treatment after processing or during processing. The conditions of the solid solution treatment are, for example, holding at 800 to 1000 ° C. for 1 to 10 hours, and then cooling a temperature range of 500 ° C. or higher at a cooling rate of 5 ° C./second or more in order to sufficiently dissolve Ni and Si. Is mentioned.
加工された銅合金材は、固溶化処理後または加工ままで時効処理を行うことができる。時効処理の条件は、例えば、４００〜５００℃で１〜３０時間保持するものが挙げられる。
得られた高強度高靱性銅合金材は、０．２％耐力が７５０ＭＰａ以上、衝撃吸収エネルギーが１０Ｊ以上、導電率が３０％ＩＡＣＳ以上の特性を有している。
The processed copper alloy material can be subjected to aging treatment after the solution treatment or as processed. As for the conditions of an aging treatment, what is hold | maintained at 400-500 degreeC for 1 to 30 hours is mentioned, for example.
The obtained high-strength, high-toughness copper alloy material has the characteristics that the 0.2% proof stress is 750 MPa or more, the impact absorption energy is 10 J or more, and the conductivity is 30% IACS or more.
以下に、本発明の実施例について説明する。
表１の成分組成になるように、原料を配合し真空誘導溶解炉で溶解してφ１００ｍｍ×２００ｍｍｈの合金を作製した。この合金を熱間鍛造して２５ｍｍ厚の板材とし、９７０℃で４時間保持した後に水冷する固溶化処理を実施した。本発明の溶解方法および鍛造方法は上記の方法に限定されるものではない。
Examples of the present invention will be described below.
Raw materials were blended so as to have the component composition shown in Table 1 and melted in a vacuum induction melting furnace to prepare an alloy of φ100 mm × 200 mmh. This alloy was hot-forged to obtain a plate having a thickness of 25 mm, and a solid solution treatment was carried out by holding it at 970 ° C. for 4 hours and then cooling it with water. The melting method and the forging method of the present invention are not limited to the above methods.
その後、時効処理を施して常温引張試験を実施し、ＪＩＳＺ２２４４に基づき、荷重５ｋｇでヴィッカース硬さと、ヴィーデマン＝フランツ則に示されるように熱伝導率とほぼ比例関係にある導電率を測定した。表２にその結果を示す。本発明の実施例は７００ＭＰａ以上の引張強さ（ＪＩＳＺ２２４１に準拠）、Ｕノッチ試験片で１０Ｊ以上の衝撃吸収エネルギー（ＪＩＳＺ２２４２に準拠）、３０％ＩＡＣＳ以上の導電率を有していた。また比較例と同等あるいはそれ以上の硬さを有していた。
以上のように、本発明は適量のＺｒを含有することにより、高導電率すなわち高熱伝導率を維持しつつ強度、靭性、硬度が高くなるという優れた性能を有する。
Thereafter, an aging treatment was performed, and a normal temperature tensile test was performed. Based on JISZ2244, a Vickers hardness was measured at a load of 5 kg, and an electrical conductivity approximately proportional to the thermal conductivity was measured as indicated by Wiedemann-Franz rule. Table 2 shows the results. The examples of the present invention had a tensile strength of 700 MPa or more (conforming to JISZ2241), an impact absorption energy of 10 J or more (conforming to JISZ2242), and a conductivity of 30% IACS or more using a U-notch test piece. Moreover, it had a hardness equal to or higher than that of the comparative example.
As described above, the present invention has an excellent performance that strength, toughness, and hardness are increased while maintaining high conductivity, that is, high thermal conductivity, by containing an appropriate amount of Zr.
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