【発明の詳細な説明】[Detailed description of the invention]
［産業上の利用分野］
本発明は銅細線又は磁気ヘツド用巻線芯線等と
して使用される銅合金線材に関し、特に、機械的
強度、導電性及び耐熱性が優れていると共に、伸
線加工時のダイスの摩耗が軽減され、線径が0.1
mm以下の極細線用として好適の銅合金線材に関す
る。
［従来の技術］
近時、電子機器の発達に伴い、銅細線及び磁気
ヘツド用巻線芯線（マグネツトワイヤ用芯線）の
分野においては、線径が0.1mm以下の極細銅線、
特に50μm以下の極細銅線に対する需要が急増し
ている。
ところで、銅線の極細線化に伴い、巻線時に断
線が発生しやすくなる。このため、極細銅線
（asdrawn）には通常の銅細線に要求される優れ
た導電性及び適度の軟かさ（伸び）に加え、破断
強度が高いことが要求されている。
従来、適度の伸びと高い破断強度を得るため
に、引抜後の極細銅線に半軟化処理を施してい
る。この場合、極細銅線の完全軟化温度が低い
と、後工程で極細銅線の周面にエナメルを焼き付
けるときに、極細銅線の組成が半軟化状態から完
全軟化状態に変化してしまう。従つて、所望の破
断強度を得ることができない。
このため、従来、極細銅線としてはZrを含有
した銅合金線材、Ag又はSb等を含有して銅合金
線材、Sn等を含有した銅合金線材及びCr銅等の
析出型銅合金線材等の完全軟化温度が高い銅合金
線材が使用されている。
［発明が解決しようとする課題］
しかしながら、上述の銅合金線材には下記に示
す問題点がある。
先ず、Zrを含有した銅合金線材の場合は、完
全軟化温度が高過ぎるため、半軟化特性を得るた
めの焼鈍が困難である。
また、Ag又はSb等を含有した銅合金線材の場
合は、適度の完全軟化温度ではあるが、半軟化状
態が得られる焼鈍温度域が狭いため、半軟化処理
後の半軟化特性にバラツキが発生しやすい。
更に、Sn等を含有した銅合金の場合は、所望
の導電性（95％IACS以上）を得ることが困難で
ある。
更にまた、Cr銅等の析出銅合金の場合は、完
全軟化させて伸びやすいものに改質しても、破断
強度は高いものの、伸線加工に使用するダイスの
摩耗が激しく、また、所望の導電性を得ることが
困難である。
本発明はかかる問題点に鑑みてなされたもので
あつて、半軟化処理が容易であり、処理後の破断
強度及び伸び等の機械的特性が優れていると共
に、導電性が優れており、更に、伸線加工時ダイ
スの摩耗を純銅の場合と同程度に抑制できる銅合
金線材を提供することを目的とする。
［課題を解決するための手段］
本発明に係る銅合金線材は、Agを0.05乃至0.2
重量％、Zrを0.003乃至0.01重量％の割合で含有
し、残部がCu及び不可避不純物であり、酸素含
有量を10ppm以下に規制する。
［作用］
前述の如く、Ag含有銅合金からなる極細銅線
は破断強度及び伸び等の機械的強度が優れている
と共に優れた導電性を有している。しかし、この
極細銅線は半軟化処理が可能な焼鈍条件の範囲が
極めて狭い。即ち、焼鈍温度を一定すると適正な
焼鈍時間範囲が極めて狭く、また、焼鈍時間を一
定にすると適正な焼鈍温度範囲が極めて狭くな
る。このため、半軟化処理のための焼鈍工程で品
質のバラツキが発生しやすい。
一方、Zr含有銅合金からなる極細銅線は半軟
化処理の適正焼鈍条件範囲は広いという利点を有
する。しかし、前述の如く完全軟化温度が高過ぎ
るため、半軟化処理のための焼鈍温度を高くする
か又は焼鈍時間を長くする必要がある。
本願発明者等は上述のAg含有銅合金を基に、
その欠点を解消すべく、適正焼鈍条件範囲を広く
する効果を有するZrを添加し、その添加量が異
なる各種の銅合金材から線径が30μmの極細銅線
を形成して、焼鈍実験を繰り返し行つた。その結
果、特許請求の範囲に記載の含有量でAgを含有
する銅合金に、同様に特許請求の範囲に記載の含
有量のZrを添加して得た合金は、Ag含有銅合金
の優れた機械的特性及び導電性を損うことなく、
半軟化処理のための適正焼鈍条件範囲が広くなる
ことを見出した。本発明はこのようにAg及びZr
の両元素を所定の組成で添加することにより両元
素のもつ特性を補完し合うようにしたものであ
る。
次に、本発明に係る銅合金材の各成分の組成限
定理由について説明する。
Ag
Agの含有量が0.05重量％未満の場合、完全軟
化温度の上昇効果を得ることができず、半軟化処
理後のエナメル焼付時に完全軟化状態になつてし
まうため、所望の破断強度を得ることができな
い。一方、Agの含有量が0.2重量％を超えると、
Agのコストが著しく上昇すると共に、極細銅線
の導電性が劣化する。このため、Agの含有量は
0.05乃至0.2重量％とする。
Zr
Zrの含有量が0.003重量％未満の場合は、Zrの
添加効果が得られず、適正焼鈍条件範囲を拡大で
きない。一方、Zrの含有量が0.01重量％を超える
と、極細銅線の導電性が劣化すると共に、焼鈍温
度が高くなつて焼鈍が困難になる。これにより、
Zrの含有量は0.003乃至0.01重量％とする。
酸素
酸素の含有量が10ppmを超えると、合金線材中
のZr等と結合してZrO2等の酸化物が多くなり、
極細銅線に伸線加工する工程で断線が発生しやす
くなる。このため、酸素の含有量は10ppm以下に
規制する。
［実施例］
次に、本発明の実施例について説明する。
下記第１表に示す成分の銅合金を真空中又は大
気中で溶解し、直径が20mmの銅合金ロツドを得
た。
[Industrial Application Field] The present invention relates to a copper alloy wire used as a thin copper wire or a winding core wire for a magnetic head, etc., and in particular, it has excellent mechanical strength, electrical conductivity, and heat resistance, and is easy to use during wire drawing. Reduces die wear and reduces wire diameter to 0.1
The present invention relates to a copper alloy wire material suitable for ultrafine wires of mm or less. [Prior Art] Recently, with the development of electronic equipment, in the field of fine copper wire and winding core wire for magnetic heads (core wire for magnet wire), ultra-fine copper wire with a wire diameter of 0.1 mm or less,
In particular, demand for ultra-fine copper wire of 50 μm or less is rapidly increasing. By the way, as copper wires become thinner, wire breakage becomes more likely to occur during winding. For this reason, ultrafine copper wires (asdrawn) are required to have high breaking strength in addition to the excellent conductivity and appropriate softness (elongation) required of ordinary thin copper wires. Conventionally, in order to obtain appropriate elongation and high breaking strength, ultrafine copper wire has been subjected to semi-softening treatment after being drawn. In this case, if the complete softening temperature of the ultra-fine copper wire is low, the composition of the ultra-fine copper wire will change from a semi-softened state to a completely softened state when enamel is baked on the circumferential surface of the ultra-fine copper wire in a subsequent process. Therefore, the desired breaking strength cannot be obtained. For this reason, conventional ultrafine copper wires include copper alloy wires containing Zr, copper alloy wires containing Ag or Sb, copper alloy wires containing Sn, etc., and precipitated copper alloy wires such as Cr copper. Copper alloy wire with a high complete softening temperature is used. [Problems to be Solved by the Invention] However, the above-mentioned copper alloy wire has the following problems. First, in the case of a copper alloy wire containing Zr, the complete softening temperature is too high, so annealing to obtain semi-softening characteristics is difficult. In addition, in the case of copper alloy wire rods containing Ag or Sb, although the complete softening temperature is appropriate, the annealing temperature range in which a semi-softened state can be obtained is narrow, resulting in variations in semi-softening characteristics after semi-softening treatment. It's easy to do. Furthermore, in the case of a copper alloy containing Sn or the like, it is difficult to obtain the desired conductivity (95% IACS or higher). Furthermore, in the case of precipitated copper alloys such as Cr copper, even if they are completely softened and modified to make them easier to stretch, their breaking strength is high, but the dies used for wire drawing are subject to severe wear, and it is difficult to achieve the desired results. It is difficult to obtain conductivity. The present invention has been made in view of these problems, and it is easy to perform semi-softening treatment, has excellent mechanical properties such as breaking strength and elongation after treatment, and has excellent electrical conductivity. An object of the present invention is to provide a copper alloy wire material that can suppress die wear during wire drawing to the same extent as pure copper. [Means for Solving the Problems] The copper alloy wire according to the present invention contains 0.05 to 0.2 Ag.
It contains Zr at a ratio of 0.003 to 0.01% by weight, the remainder being Cu and unavoidable impurities, and the oxygen content is regulated to 10 ppm or less. [Function] As described above, the ultrafine copper wire made of an Ag-containing copper alloy has excellent mechanical strength such as breaking strength and elongation, and also has excellent electrical conductivity. However, the range of annealing conditions under which this ultra-fine copper wire can be semi-softened is extremely narrow. That is, when the annealing temperature is constant, the appropriate annealing time range is extremely narrow, and when the annealing time is constant, the appropriate annealing temperature range is extremely narrow. For this reason, variations in quality are likely to occur during the annealing process for semi-softening treatment. On the other hand, ultrafine copper wires made of Zr-containing copper alloys have the advantage that the range of appropriate annealing conditions for semi-softening treatment is wide. However, as mentioned above, the complete softening temperature is too high, so it is necessary to increase the annealing temperature or lengthen the annealing time for semi-softening treatment. The inventors of the present application, based on the above-mentioned Ag-containing copper alloy,
In order to eliminate this drawback, we added Zr, which has the effect of widening the range of appropriate annealing conditions, and repeated annealing experiments by forming ultra-fine copper wires with a wire diameter of 30 μm from various copper alloy materials with different addition amounts. I went. As a result, an alloy obtained by adding Zr in a content similarly stated in the claims to a copper alloy containing Ag in the content stated in the claims is superior to the Ag-containing copper alloy. without compromising mechanical properties and conductivity.
It has been found that the range of appropriate annealing conditions for semi-softening treatment is widened. The present invention thus deals with Ag and Zr.
By adding both elements in a predetermined composition, the characteristics of both elements complement each other. Next, the reasons for limiting the composition of each component of the copper alloy material according to the present invention will be explained. Ag If the Ag content is less than 0.05% by weight, the effect of increasing the complete softening temperature cannot be obtained and the enamel will be in a completely softened state when baked after semi-softening treatment, so it is difficult to obtain the desired breaking strength. I can't. On the other hand, when the Ag content exceeds 0.2% by weight,
The cost of Ag increases significantly and the conductivity of ultra-fine copper wire deteriorates. Therefore, the Ag content is
The amount should be 0.05 to 0.2% by weight. Zr If the Zr content is less than 0.003% by weight, the effect of Zr addition cannot be obtained and the range of appropriate annealing conditions cannot be expanded. On the other hand, when the Zr content exceeds 0.01% by weight, the conductivity of the ultrafine copper wire deteriorates and the annealing temperature becomes high, making annealing difficult. This results in
The content of Zr is 0.003 to 0.01% by weight. Oxygen When the oxygen content exceeds 10 ppm, it combines with Zr etc. in the alloy wire and oxides such as ZrO 2 increase.
Wire breakage is more likely to occur during the process of drawing ultra-fine copper wire. For this reason, the oxygen content is regulated to 10 ppm or less. [Example] Next, an example of the present invention will be described. A copper alloy having the components shown in Table 1 below was melted in vacuum or in the air to obtain a copper alloy rod having a diameter of 20 mm.
【表】
この実施例１乃至３及び比較例１乃至６のロツ
ドを伸線加工して、極細銅線を形成した。その結
果、実施例１乃至３及び比較例１乃至５の銅合金
ロツドは断線することなく、１Kgのロツドから線
径が30μmの極細銅線を連続して伸線加工するこ
とができた。一方、比較例６の銅合金ロツドの場
合は、１Kgのロツドを線径が50μmの極細銅線に
伸線加工するときに４回断線が発生した。
また、このときの実施例１乃至３及び比較例１
乃至６の銅合金線材の伸線時におけるダイスの摩
耗は鈍銅の場合と同程度であつた。
次に、線径が30μmである実施例１乃至３及び
比較例１乃至５極細銅線に対して繰り返し焼鈍実
験を行い、破断強度が32Kgｆ／cm2以上であり、伸
び率が10％以上という機械的強度が得られる焼鈍
温度を調べた。
但し、このとき炉長が90cmの加熱炉を使用し、
この加熱炉内に実施例１乃至３及び比較例１乃至
５の極細銅線を60m／分の線速で挿通させた。
この結果、前述の所望の機械的強度が得られる
焼鈍温度範囲を下記第２表に示す。また、この焼
鈍により得た半軟化状態の極細銅線の導電率を第
２表に併せて示す。[Table] The rods of Examples 1 to 3 and Comparative Examples 1 to 6 were drawn to form ultrafine copper wires. As a result, the copper alloy rods of Examples 1 to 3 and Comparative Examples 1 to 5 could be continuously drawn into ultrafine copper wires with a wire diameter of 30 μm from 1 kg rods without breaking. On the other hand, in the case of the copper alloy rod of Comparative Example 6, wire breakage occurred four times when the 1 kg rod was drawn into an ultrafine copper wire with a wire diameter of 50 μm. In addition, Examples 1 to 3 and Comparative Example 1 at this time
The wear of the dies during drawing of the copper alloy wires Nos. 6 to 6 was comparable to that of the case of blunt copper. Next, repeated annealing experiments were conducted on the ultrafine copper wires of Examples 1 to 3 and Comparative Examples 1 to 5, each having a wire diameter of 30 μm, and the breaking strength was 32 Kgf/cm 2 or more and the elongation rate was 10% or more. The annealing temperature at which mechanical strength was obtained was investigated. However, at this time, use a heating furnace with a furnace length of 90 cm,
The ultrafine copper wires of Examples 1 to 3 and Comparative Examples 1 to 5 were inserted into this heating furnace at a wire speed of 60 m/min. As a result, the annealing temperature range in which the above-mentioned desired mechanical strength can be obtained is shown in Table 2 below. Further, the electrical conductivity of the semi-softened ultrafine copper wire obtained by this annealing is also shown in Table 2.
【表】
半軟化状態が得られる焼鈍温度は、低過ぎると
後工程において完全軟化状態となり、高過ぎると
処理が困難であるため、400乃至500℃の温度範囲
内で30℃以上の温度幅があることが好ましい。ま
た、導電率は95％IACS以上であることが好まし
い。実施例１乃至３はいずれもこの所望の条件を
満たしており、極めて優れた機械的特性及び電気
的特性を確実に得ることができた。
一方、本発明の特許請求の範囲から外れる比較
例１乃至６は、伸線加工性、適正焼鈍温度、処理
温度幅及び導電率のいずれか一項目以上が満足で
きるものではなかつた。
［発明の効果］
以上説明したように本発明に係る銅合金線材
は、0.05乃至0.2重量％以上のAg及び0.003乃至
0.01重量％のZrを含有し、酸素含有量を10ppm以
下に規制したから、半軟化処理を容易に行うこと
ができる。これにより、破断強度及び伸び等の機
械的強度並びに導電性が優れた極細銅線を得るこ
とができる。また、極細銅線ヲ伸線加工するため
のダイスの摩耗も極めて少ない。[Table] If the annealing temperature to obtain a semi-softened state is too low, it will become completely softened in the subsequent process, and if it is too high, it will be difficult to process. It is preferable that there be. Further, the conductivity is preferably 95% IACS or higher. Examples 1 to 3 all satisfied these desired conditions, and were able to reliably obtain extremely excellent mechanical and electrical properties. On the other hand, Comparative Examples 1 to 6, which fall outside the scope of the claims of the present invention, were not satisfactory in any one or more of wire drawability, appropriate annealing temperature, processing temperature range, and electrical conductivity. [Effect of the invention] As explained above, the copper alloy wire according to the present invention contains 0.05 to 0.2% by weight or more of Ag and 0.003 to 0.2% by weight.
Since it contains 0.01% by weight of Zr and the oxygen content is regulated to 10 ppm or less, semi-softening treatment can be easily performed. As a result, an ultrafine copper wire having excellent mechanical strength such as breaking strength and elongation as well as electrical conductivity can be obtained. In addition, the wear of dies for drawing ultra-fine copper wire is extremely low.