JP2000017353A - Copper alloy excellent in hot workability - Google Patents
Copper alloy excellent in hot workabilityInfo
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- JP2000017353A JP2000017353A JP10179300A JP17930098A JP2000017353A JP 2000017353 A JP2000017353 A JP 2000017353A JP 10179300 A JP10179300 A JP 10179300A JP 17930098 A JP17930098 A JP 17930098A JP 2000017353 A JP2000017353 A JP 2000017353A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、熱間加工性に優れ
た銅合金に関し、特に、熱間加工時に割れを発生させる
ことのないＣｕ−Ｆｅ系銅合金に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a copper alloy having excellent hot workability, and more particularly to a Cu--Fe based copper alloy which does not crack during hot working.
【０００２】[0002]
【従来の技術】従来、半導体装置のリードフレーム、あ
るいは端子コネクター等に使用される銅合金として、た
とえば、Ｆｅを１．５〜３重量％、Ｐを０．０１〜０．
１５重量％、およびＺｎを０．０３〜１重量％含有した
Ｃｕ−Ｆｅ系銅合金が知られている。2. Description of the Related Art Conventionally, as a copper alloy used for a lead frame or a terminal connector of a semiconductor device, for example, 1.5 to 3% by weight of Fe and 0.01 to 0.
A Cu—Fe-based copper alloy containing 15% by weight and 0.03 to 1% by weight of Zn is known.
【０００３】通常、この銅合金からリードフレーム等を
製造するには、次の手順を経る。まず、銅合金を加熱し
て溶湯とし、これを連続または半連続的に鋳造してイン
ゴットを作り、次に、これを８００〜１０５０℃の温度
で熱間圧延し、水冷後、熱延板の両面を面削する。[0003] Usually, the following procedure is performed to manufacture a lead frame or the like from this copper alloy. First, a copper alloy is heated to form a molten metal, which is continuously or semi-continuously cast to produce an ingot. Then, the ingot is hot-rolled at a temperature of 800 to 1050 ° C., and water-cooled. Shave both sides.
【０００４】面削された板は、次いで、冷間圧延と時効
加熱処理と表面研磨を繰り返された後、最終圧延され、
歪みとり焼鈍を施されることによって、所定の銅合金条
とされる。[0004] The surface-cut sheet is then subjected to cold rolling, aging heat treatment, and surface polishing, and then to final rolling.
By performing the strain relief annealing, a predetermined copper alloy strip is formed.
【０００５】次に、この合金条は、金型でのプレス、打
ち抜き、曲げ加工などの諸加工を施された後、必要に応
じてメッキ処理をされ、所定のリードフレームあるいは
端子コネクターとされる。[0005] Next, the alloy strip is subjected to various processes such as pressing, punching, bending and the like in a mold, and then, if necessary, is plated to obtain a predetermined lead frame or terminal connector. .
【０００６】この銅合金は、Ｆｅを１．５〜３．０重量
％含有することによって特徴づけられており、優れた機
械的強度と導電性とを兼ね備えていることから、特に、
リードフレームの分野で広く活用されている。[0006] This copper alloy is characterized by containing 1.5 to 3.0% by weight of Fe, and has excellent mechanical strength and electrical conductivity.
Widely used in the field of lead frames.
【０００７】[0007]
【発明が解決しようとする課題】しかし、このＣｕ−Ｆ
ｅ系銅合金によると、熱間圧延の際に、熱延材の耳部に
エッジ割れを発生させやすい問題を有している。割れが
発生した熱延材は、内部に粒界割れを有するのが普通で
あり、このため、このような材料を使用してリードフレ
ームを製造すると、リード破損やメッキ膨れなどを多発
させることになる。However, this Cu-F
According to the e-based copper alloy, there is a problem that edge cracks are apt to be generated at the edge of the hot-rolled material during hot rolling. The hot rolled material that has cracked usually has internal grain boundary cracks.Therefore, when a lead frame is manufactured using such a material, lead breakage and plating swelling often occur. Become.
【０００８】従って、本発明の目的は、熱間圧延時に割
れを発生させることのない加工性に優れたＣｕ−Ｆｅ系
銅合金を提供することにある。Accordingly, an object of the present invention is to provide a Cu-Fe-based copper alloy which is excellent in workability without causing cracks during hot rolling.
【０００９】[0009]
【課題を解決するための手段】本発明は、上記の目的を
達成するため、Ｆｅを１．５〜２．４重量％、Ｐを０．
００１〜０．１重量％、Ｚｎを０．０１〜０．５重量
％、Ｍｇを０．００１〜０．１２重量％、Ａｌを０．０
０１〜０．１重量％、およびＳｉ、Ｍｎ、Ｔｉのうちの
１種以上を０．００１〜０．１重量％含有し、残部がＣ
ｕから成ることを特徴とする熱間加工性に優れた銅合金
を提供するものである。According to the present invention, 1.5 to 2.4% by weight of Fe and 0.
001-0.1% by weight, Zn 0.01-0.5% by weight, Mg 0.001-0.12% by weight, Al 0.0%
0.01 to 0.1% by weight, and 0.001 to 0.1% by weight of at least one of Si, Mn, and Ti, and the remainder is C
It is intended to provide a copper alloy excellent in hot workability characterized by being made of u.
【００１０】一般に、銅合金等の連続または半連続鋳造
においては、鋳塊表層の数ｍｍを除いた部分は徐々に冷
却される形で凝固する。このため、凝固後の冷却過程で
は、固溶限界を超えて固溶した合金元素が、結晶粒界お
よび結晶粒内に析出するようになる。Generally, in continuous or semi-continuous casting of a copper alloy or the like, a portion of the surface layer of the ingot other than a few mm is solidified while being gradually cooled. For this reason, in the cooling process after solidification, the alloy element that has dissolved beyond the solid solution limit precipitates in the crystal grain boundaries and crystal grains.
【００１１】一方、Ｃｕ−Ｆｅ系合金における５５０℃
以下でのＣｕ中へのＦｅの固溶は、０．１５％が限界で
あり、このため、０．１５％を超える部分のＦｅは、結
晶粒界と結晶粒内に析出することになるが、結晶粒内に
多量のＦｅが析出すると、高温下での粒界すべりが起こ
りにくくなることから、粒界の強度が低下するようにな
り、結果として、熱間圧延時に割れが発生するようにな
る。On the other hand, 550 ° C. in a Cu—Fe alloy
The limit of the solid solution of Fe in Cu below is 0.15%, and therefore, the portion of Fe exceeding 0.15% precipitates in the crystal grain boundaries and crystal grains. When a large amount of Fe precipitates in the crystal grains, the grain boundary slip at high temperatures is unlikely to occur, so that the strength of the grain boundaries decreases, and as a result, cracks occur during hot rolling. Become.
【００１２】本発明は、特定の合金元素を添加すること
により、結晶粒界へのＦｅの析出を抑制して粒界の中高
温強度を改善し、これにより熱間加工性を向上させよう
とするものであるが、これにはＦｅの含有量も重要な要
素として関与してくることになる。The present invention is intended to suppress the precipitation of Fe at the crystal grain boundaries by adding a specific alloying element to improve the medium to high temperature strength of the grain boundaries, thereby improving the hot workability. However, the content of Fe also plays an important factor in this.
【００１３】上記したＦｅの含有上限値２．４重量％
は、以上の効果を得るための不可欠の要件であり、これ
を超えての含有は、熱間加工時の割れ発生につながるこ
とから避ける必要がある。The upper limit of the content of Fe is 2.4% by weight.
Is an indispensable requirement for obtaining the above-mentioned effects, and a content exceeding this is necessary to avoid cracks during hot working, and thus must be avoided.
【００１４】Ｆｅの含有下限値を１．５重量％に設定す
る理由は、Ｃｕ中にＦｅを析出させることによって得ら
れる強度および耐熱性向上の効果を確保するためであ
り、もし、Ｆｅの含有量がこれを下廻るときには、充分
な強度と耐熱性とが得られなくなる。The reason for setting the lower limit of Fe content to 1.5% by weight is to secure the effect of improving the strength and heat resistance obtained by precipitating Fe in Cu. If the amount is less than this, sufficient strength and heat resistance cannot be obtained.
【００１５】本発明におけるＭｇは、結晶粒界へのＦｅ
の析出を防止すると同時に、原料や炉材、あるいは雰囲
気等から不可避的に混入するＳをトラップし、これを安
定なＭｇ化合物の形にして母相中に固定し、これによっ
て熱間加工性を向上させるために混入されるものである
が、この目的のためには、含有量を０．００１〜０．１
２重量％に設定する必要がある。[0015] In the present invention, Mg represents Fe
At the same time as trapping S that is inevitably mixed in from the raw material, furnace material, atmosphere, etc., and fixing it in the form of a stable Mg compound in the mother phase, thereby improving hot workability. It is added to improve the content. For this purpose, the content is 0.001 to 0.1.
It must be set to 2% by weight.
【００１６】Ｍｇの含有量が０．００１重量％未満にな
ると、Ｓが結晶粒界中を移動して粒界割れを助長するよ
うになり、熱間加工性の向上効果が不充分なものとな
る。一方、逆に、Ｍｇが０．１２重量％を超過する場合
には、導電性の低下を招くばかりか、溶湯が酸化して湯
流れが悪くなり、鋳造困難な状態を招くようになる。If the Mg content is less than 0.001% by weight, S moves in the crystal grain boundaries to promote grain boundary cracking, and the effect of improving hot workability is insufficient. Become. On the other hand, when Mg exceeds 0.12% by weight, not only the conductivity is lowered, but also the molten metal is oxidized and the flow of the molten metal is deteriorated, so that the casting becomes difficult.
【００１７】Ａｌの含有量を０．００１〜０．１重量％
に限定する理由は、熱間加工性の向上と導電性確保のた
めである。０．００１重量％未満では、Ｍｇと共存して
の結晶粒界へのＦｅ析出防止効果と、それによる熱間加
工性改善が不充分なものとなり、逆に、０．１重量％を
超えると、熱間加工性の改善効果が飽和するようになる
とともに、導電性が低下するようになる。The content of Al is 0.001 to 0.1% by weight.
The reason for limiting to is to improve hot workability and ensure conductivity. If the content is less than 0.001% by weight, the effect of preventing Fe precipitation at the crystal grain boundaries in the presence of Mg and the improvement in hot workability thereby become insufficient. In addition, the effect of improving hot workability is saturated, and the conductivity is reduced.
【００１８】Ｚｎの添加は、脱酸および脱ガス効果を得
るためであり、これらの効果に充分なものを得るために
は、含有量を０．０１〜０．５重量％とする必要があ
る。含有量を０．０１重量％未満に設定すると、脱酸、
脱ガス効果に充分な結果が得られず、逆に、０．５重量
％を超えると、導電性の低下をもたらすことになるの
で、避ける必要がある。The addition of Zn is for obtaining deoxidizing and degassing effects, and in order to obtain sufficient effects for these effects, the content needs to be 0.01 to 0.5% by weight. . When the content is set to less than 0.01% by weight, deoxidation,
Sufficient results cannot be obtained for the degassing effect. Conversely, if the content exceeds 0.5% by weight, a decrease in conductivity will be caused, and thus it is necessary to avoid such a problem.
【００１９】Ｐは、溶湯を鋳造するときの脱酸のために
不可欠であり、その含有量は０．００１〜０．１重量％
の範囲に設定される。０．００１重量％未満では充分な
脱酸効果が得られず、また、０．１重量％を超過しても
脱酸効果のさらなる向上はなく、むしろ、かえって導電
性の低下と加工性の悪化を招くようになることから、避
ける必要がある。P is indispensable for deoxidation when casting a molten metal, and its content is 0.001 to 0.1% by weight.
Is set in the range. If the amount is less than 0.001% by weight, a sufficient deoxidizing effect cannot be obtained. If the amount exceeds 0.1% by weight, the deoxidizing effect is not further improved. Need to be avoided.
【００２０】本発明においては、Ｓｉ、Ｍｎ、Ｔｉのう
ちの１種以上が０．００１〜０．１重量％の範囲内で添
加されるが、これを添加する理由は、やはり熱間加工性
を向上させるためであり、その量が設定値未満になる
と、熱間圧延時の割れ防止に充分な結果が得られない。
また、これらの含有量が０．１重量％を超えるときに
は、溶湯が酸化しやすくなり、良質の鋳塊が得られなく
なる。In the present invention, one or more of Si, Mn, and Ti are added in a range of 0.001 to 0.1% by weight. When the amount is less than the set value, a sufficient result for preventing cracking during hot rolling cannot be obtained.
On the other hand, when the content exceeds 0.1% by weight, the molten metal is easily oxidized, and a high quality ingot cannot be obtained.
【００２１】これら３種成分の含有量としては、３種同
時含有のときは、重量％においてＭｎ＞Ｓｉ＞Ｔｉとな
るように設定することが望ましく、また、２種含有時に
は、同じく重量％においてＭｎ＞Ｓｉ、Ｓｉ＞Ｔｉ、あ
るいはＭｎ＞Ｔｉとなるように設定することが望まし
い。The content of these three components is desirably set so that Mn>Si> Ti in wt% when the three components are simultaneously contained, and in the case of two components, the content is also the same in wt%. It is desirable to set so that Mn> Si, Si> Ti, or Mn> Ti.
【００２２】以上、各成分の添加理由と含有量設定理由
について説明したが、Ｆｅ ２．０〜２．３重量％、Ｐ
０．０１５〜０．０５重量％、Ｚｎ ０．０５〜０．
１５重量％、Ｍｇ ０．００５〜０．０８重量％、Ａｌ
０．００５〜０．０５重量％、Ｓｉ、Ｍｎ、Ｔｉの１
種以上を０．００１〜０．１重量％、および残部銅から
成る組成を、本発明の目的を達成するためのより好まし
く、より限定された組成として推奨することができる。The reason for adding each component and the reason for setting the content have been described above.
0.015-0.05% by weight, Zn 0.05-0.
15% by weight, Mg 0.005 to 0.08% by weight, Al
0.005 to 0.05% by weight, 1 of Si, Mn, Ti
Compositions comprising at least 0.001 to 0.1% by weight of the seed and the balance copper can be recommended as more preferred and more limited compositions to achieve the objects of the present invention.
【００２３】なお、本発明による銅合金の中には、不可
避的に混入する不純物は当然含まれ、また、発明の目的
を阻害しないかぎり、他の成分の添加は可能である。The copper alloy according to the present invention naturally contains impurities unavoidably mixed therein, and other components can be added as long as the object of the present invention is not impaired.
【００２４】[0024]
【発明の実施の形態】次に、本発明による銅合金の実施
の形態について説明する。Next, an embodiment of a copper alloy according to the present invention will be described.
【実施例】電気銅を木炭で被覆することにより大気から
遮断し、低周波誘導溶解炉を使用して溶解した溶湯に、
表１に示された種類と量の元素成分を添加して各実施例
および比較例毎の溶湯を調合した。[Examples] Electrolytic copper is covered with charcoal to block it from the atmosphere, and is melted using a low-frequency induction melting furnace.
The types and amounts of elemental components shown in Table 1 were added to prepare molten metals for each of the examples and comparative examples.
【００２５】[0025]
【表１】 [Table 1]
【００２６】次いで、これらの溶湯をそれぞれ鋳型に鋳
造し、厚さ１５０ｍｍ、幅４５０ｍｍ、長さ３５００ｍ
ｍの銅合金インゴットを製造した後、これを９５０℃の
温度下で熱間圧延することにより、厚さ１１ｍｍの熱延
板を製造した。この間の熱間圧延作業は、１パス毎の圧
下率を約２１％、圧延最終温度が６５０℃以下となるよ
うに条件を設定して行われた。Next, each of these melts is cast into a mold, and has a thickness of 150 mm, a width of 450 mm, and a length of 3500 m.
After manufacturing a copper alloy ingot having a thickness of 11 mm, a hot-rolled sheet having a thickness of 11 mm was manufactured by hot rolling at a temperature of 950 ° C. During this hot rolling, the conditions were set such that the rolling reduction per pass was about 21% and the final rolling temperature was 650 ° C. or less.
【００２７】次に、このようにして得られた熱延板の上
下面を面削することにより厚さ１１ｍｍの板とし、さら
に、これを冷間圧延することによって厚さ２ｍｍに圧延
し、６００℃で１時間の時効熱処理を施した。Next, the upper and lower surfaces of the hot-rolled sheet thus obtained were chamfered into a sheet having a thickness of 11 mm, and the sheet was cold-rolled to be rolled to a thickness of 2 mm. An aging heat treatment at 1 ° C. for 1 hour was performed.
【００２８】次に、熱処理した板の表面から酸化膜を除
去し、２次冷間圧延を行って厚さ０．８ｍｍのシート材
とした後、圧下率７５％で最終圧延を行い、０．２ｍｍ
厚さのＣｕ−Ｆｅ系銅合金薄帯を完成した。Next, the oxide film was removed from the surface of the heat-treated sheet, and the sheet was subjected to secondary cold rolling to form a sheet material having a thickness of 0.8 mm. Then, final rolling was performed at a rolling reduction of 75%. 2mm
A Cu—Fe-based copper alloy ribbon having a thickness was completed.
【００２９】表１に、以上のようにして遂行された実施
例と比較例の熱間圧延における割れ発生についての観察
結果を示した。観察は圧延パス毎に行い、何回目のパス
のときに割れが発生したかを表示した。参考のため、表
２には、鋳造時の割れの有無と完成品（薄帯）における
表面欠陥の有無についても示す。Table 1 shows the results of observations on the occurrence of cracks in hot rolling of the examples and comparative examples performed as described above. The observation was performed for each rolling pass, and the number of passes in which the crack occurred was displayed. For reference, Table 2 also shows the presence or absence of cracks during casting and the presence or absence of surface defects in the finished product (ribbon).
【００３０】[0030]
【表２】 [Table 2]
【００３１】この観察結果によれば、実施例１〜４の場
合が熱間圧延時に全く割れを発生させていないのに比
べ、比較例はいずれも耳部エッジに割れを発生させてお
り、特に、比較例４の場合には３回目で表面が割れ、５
回目には崩壊にまで至っている。According to the results of the observation, in the case of Examples 1 to 4, no cracks were generated at the time of hot rolling, whereas in the comparative examples, cracks were generated at the edge of the ear. In the case of Comparative Example 4, the surface cracked at the third
The second time has led to collapse.
【００３２】また、鋳造割れや完成品の表面欠陥の面で
も、実施例が全く問題がないのに比べ、比較例の場合に
は４例中２例に鋳造割れを発生させ、さらに、４例中４
例に完成品の表面欠陥を発生させており、実施例と比較
例の間には明確な差が認められる。In the case of casting cracks and surface defects of the finished product, there is no problem in the embodiment, but in the case of the comparative example, casting cracks occurred in two out of four cases. Medium 4
In the examples, surface defects of the finished product were generated, and a clear difference was observed between the examples and the comparative examples.
【００３３】[0033]
【発明の効果】以上のように、本発明によれば、Ｆｅ、
Ｐ、Ｚｎ、Ｍｇ、Ａｌのそれぞれと、Ｓｉ、Ｍｎ、Ｔｉ
のうちの１種以上とをＣｕに添加し、さらに、これら成
分の含有量をそれぞれ特定の範囲内に設定することによ
って、熱間圧延時に割れが発生しない熱間加工性に優れ
たＣｕ−Ｆｅ系銅合金を提供するものであり、この種銅
合金の有用性を高めるうえにおいて、効果大である。As described above, according to the present invention, Fe,
P, Zn, Mg, Al and Si, Mn, Ti
By adding one or more of these to Cu, and further setting the content of each of these components in a specific range, Cu-Fe excellent in hot workability that does not generate cracks during hot rolling. The present invention provides a copper based alloy and is highly effective in enhancing the usefulness of this type of copper alloy.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 野本 詞之 茨城県土浦市木田余町3550番地 日立電線 株式会社システムマテリアル研究所内 (72)発明者 古徳 浩一 茨城県土浦市木田余町3550番地 日立電線 株式会社システムマテリアル研究所内 ──────────────────────────────────────────────────の Continuing from the front page (72) Inventor Yukiyuki Nomoto 3550 Kida Yomachi, Tsuchiura City, Ibaraki Prefecture Within Hitachi Cable System Materials Laboratory (72) Inventor Koichi Kotoku 3550 Kida Yomachi, Tsuchiura City, Ibaraki Prefecture Hitachi Cable Inside the System Materials Laboratory Co., Ltd.
Claims (3)
０１〜０．１重量％、Ｚｎを０．０１〜０．５重量％、
Ｍｇを０．００１〜０．１２重量％、Ａｌを０．００１
〜０．１重量％、およびＳｉ、Ｍｎ、Ｔｉのうちの１種
以上を０．００１〜０．１重量％含有し、残部がＣｕか
ら成ることを特徴とする熱間加工性に優れた銅合金。(1) 1.5 to 2.4% by weight of Fe and 0.0% of P
01-0.1% by weight, Zn 0.01-0.5% by weight,
0.001 to 0.12% by weight of Mg, 0.001% of Al
Copper having excellent hot workability, characterized in that the copper content is 0.001 to 0.1% by weight, and at least one of Si, Mn and Ti is 0.001 to 0.1% by weight, and the balance is Cu. alloy.
Ｍｎ＞Ｓｉ＞Ｔｉの割合で３種とも含有されることを特
徴とする請求項第１項記載の熱間加工性に優れた銅合
金。2. The copper alloy excellent in hot workability according to claim 1, wherein Si, Mn and Ti are contained in a proportion of Mn>Si> Ti in weight%. .
Ｍｎ＞Ｓｉ、Ｓｉ＞Ｔｉ、あるいはＭｎ＞Ｔｉの割合で
２種以上含有されることを特徴とする請求項第１項記載
の熱間加工性に優れた銅合金。3. The hot working method according to claim 1, wherein two or more kinds of Si, Mn and Ti are contained in a ratio of Mn> Si, Si> Ti or Mn> Ti in% by weight. Copper alloy with excellent workability.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10179300A JP2000017353A (en) | 1998-06-25 | 1998-06-25 | Copper alloy excellent in hot workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10179300A JP2000017353A (en) | 1998-06-25 | 1998-06-25 | Copper alloy excellent in hot workability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2000017353A true JP2000017353A (en) | 2000-01-18 |
Family
ID=16063425
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10179300A Pending JP2000017353A (en) | 1998-06-25 | 1998-06-25 | Copper alloy excellent in hot workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2000017353A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6632300B2 (en) * | 2000-06-26 | 2003-10-14 | Olin Corporation | Copper alloy having improved stress relaxation resistance |
-
1998
- 1998-06-25 JP JP10179300A patent/JP2000017353A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6632300B2 (en) * | 2000-06-26 | 2003-10-14 | Olin Corporation | Copper alloy having improved stress relaxation resistance |
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