JP6196435B2 - Titanium copper and method for producing the same - Google Patents

Titanium copper and method for producing the same Download PDF

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JP6196435B2
JP6196435B2 JP2012220659A JP2012220659A JP6196435B2 JP 6196435 B2 JP6196435 B2 JP 6196435B2 JP 2012220659 A JP2012220659 A JP 2012220659A JP 2012220659 A JP2012220659 A JP 2012220659A JP 6196435 B2 JP6196435 B2 JP 6196435B2
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JP2014074193A (en
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波多野 隆紹
隆紹 波多野
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JX Nippon Mining and Metals Corp
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Description

本発明は、コネクタ、端子、リレー、スイッチ等の導電性ばね材やトランジスタ、集積回路(IC)等の半導体機器のリ−ドフレーム材として好適な、優れた強度、疲労特性、曲げ加工性、耐応力緩和特性、導電性等を備えたチタン銅及びその製造方法に関する。   The present invention has excellent strength, fatigue characteristics, bending workability, suitable as a lead frame material for semiconductor devices such as conductive spring materials such as connectors, terminals, relays, switches, transistors, integrated circuits (ICs), etc. The present invention relates to titanium copper having stress relaxation resistance, conductivity, and the like, and a method for producing the same.

電子機器の各種端子、コネクタ、リレー、スイッチ等の電気伝導性及びばね性が必要な材料として、製造コストを重視する場合には低廉な黄銅が用いられ、ばね性が重視される場合にはりん青銅が用いられ、ばね性及び耐食性が重視される場合には洋白が用いられてきた。しかしながら、近年の電子機器類及びその部品の軽量化、薄肉化および小型化に伴い、これらの材料では強度を十分に向上させることが難しいため、チタン銅等のいわゆる高級ばねの需要が増大している。
JIS合金番号C1990に規定されるチタン銅は、溶体化処理の後に時効処理を行うことにより製造される。溶体化処理では、鋳造や熱間圧延の際に生成した粗大なCu−Ti化合物をCu母地に固溶させると同時にCu母地を再結晶させ、再結晶粒の結晶粒径を調整する。時効処理においてはCu3TiまたはCu4Tiの微細粒子を析出させ、これらの微細粒子が引張り強さ、耐力、ばね限界値等の強度特性の向上に寄与する。
As a material that requires electrical conductivity and springiness for various terminals, connectors, relays, switches, etc. of electronic equipment, inexpensive brass is used when manufacturing costs are important, and phosphorous is used when springiness is important. Bronze is used, and when whiteness and corrosion resistance are important, Western white has been used. However, with the recent reduction in weight, thickness and size of electronic devices and their components, it is difficult to sufficiently improve the strength of these materials, so the demand for so-called high-grade springs such as titanium copper has increased. Yes.
Titanium copper prescribed | regulated to JIS alloy number C1990 is manufactured by performing an aging treatment after solution treatment. In the solution treatment, the coarse Cu—Ti compound generated during casting or hot rolling is dissolved in the Cu matrix and simultaneously the Cu matrix is recrystallized to adjust the crystal grain size of the recrystallized grains. In the aging treatment, Cu 3 Ti or Cu 4 Ti fine particles are precipitated, and these fine particles contribute to improvement of strength properties such as tensile strength, proof stress, and spring limit value.

例えば、コネクタはメス端子及びオス端子から構成され、両端子を勘合することにより電気的接続が得られる。電気接点では、メス端子がそのばね力によりオス端子を保持し、所望の接触力を得ている。
メス端子材料の強度が低いと、オス端子を挿入した際にメス端子に永久変形(へたり)が発生する。へたりが生じると、電気接点部での接触力が低下し、電気抵抗が増大する。そこで、へたりの発生を抑制するため、耐力やばね限界値の高い銅合金材料が開発されてきた(例えば特許文献1等)。
For example, the connector is composed of a female terminal and a male terminal, and electrical connection can be obtained by fitting both terminals. In the electrical contact, the female terminal holds the male terminal by its spring force and obtains a desired contact force.
If the strength of the female terminal material is low, permanent deformation (sagging) occurs in the female terminal when the male terminal is inserted. When the sagging occurs, the contact force at the electrical contact portion decreases and the electrical resistance increases. Therefore, in order to suppress the occurrence of sagging, copper alloy materials having high proof stress and spring limit values have been developed (for example, Patent Document 1).

また、特許文献2では、コネクタの設計を容易にするために、圧延方向の曲げたわみ係数を80〜110GPaに調整したチタン銅を提案している。しかしながら、この材料のへたり特性は、特にばねに繰り返したわみを与える場合において充分とはいえず、さらに、ばねの接触力の著しい低下を引き起こすという問題もあった。   Patent Document 2 proposes titanium copper in which the bending deflection coefficient in the rolling direction is adjusted to 80 to 110 GPa in order to facilitate the design of the connector. However, the sag characteristics of this material are not sufficient particularly when the spring is repeatedly bent, and there is also a problem in that the contact force of the spring is significantly reduced.

特開2004−076091号公報JP 2004-076091 A WO2012/029717号WO2012 / 029717

銅合金材料のへたり特性を改善するためには、耐力、ばね限界値等の強度特性を高めることが有効である。しかしながら、高強度化に伴い曲げ加工性が悪化する等の理由により、高強度化だけによるへたり改善には限界があった。
そこで、本発明では、高強度化以外の手段も用いることにより、へたりの発生が著しく抑制されたチタン銅及びその製造方法を提供することを課題とする。
In order to improve the sag characteristics of the copper alloy material, it is effective to increase strength characteristics such as proof stress and spring limit values. However, there is a limit to the improvement in the sag due to the increase in the strength only because the bending workability deteriorates with the increase in the strength.
Accordingly, an object of the present invention is to provide titanium copper in which the occurrence of sag is remarkably suppressed by using means other than increasing the strength, and a method for producing the same.

コネクタのばね部を片持ちはりとして単純化し、へたりが発生する原理を説明する。図1に示すように、一端を固定した板ばねの固定端から長さLの位置にたわみdを与えると、下記の式1で示される接触力Pが得られ、板ばねの固定端表面に下記の式2で示される最大応力Sが発生する。
P=dEwt3/4L3 (式1)
S=3tEd/2L2 (式2)
ここでEはヤング率、wは板幅、tは板厚である。
Sが板ばねの素材である銅合金の耐力を超えると、板ばねが永久変形し、板ばねにへたりが生じる。式2より、素材のヤング率が低いほど、へたりの発生が始まるたわみが大きい、すなわちへたりが発生し難いと考えられる。
通常、コネクタ等のばね部はその長手方向が、圧延平面において圧延方向と直交するように設計されている(図2の90度方向)。従って、圧延方向と90度の角度を成す方向のヤング率が低いことが重要といえる。
一方、コネクタ等のばね部に与えられるたわみは一回だけではなく、端子の挿抜等により数千回以上のたわみが与えられることが多い。特にリレー等ではたわみ回数が著しく多い。
本発明者は、圧延方向と90度の角度を成す方向に繰り返したわみを与えた場合のへたりに対しては、圧延方向と90度の角度を成す方向のヤング率だけではなく、圧延方向と45度の角度を成す方向のヤング率も大きな影響を及ぼすことを知見した。
The principle of the occurrence of sag will be described by simplifying the spring part of the connector as a cantilever. As shown in FIG. 1, when a deflection d is given to the position of length L from the fixed end of the leaf spring with one end fixed, a contact force P expressed by the following equation 1 is obtained, and the surface of the leaf spring is fixed to the fixed end surface. The maximum stress S shown by the following formula 2 is generated.
P = dEwt 3 / 4L 3 (Formula 1)
S = 3tEd / 2L 2 (Formula 2)
Here, E is Young's modulus, w is the plate width, and t is the plate thickness.
When S exceeds the proof stress of the copper alloy that is the material of the leaf spring, the leaf spring is permanently deformed and the leaf spring is sag. From Formula 2, it is considered that the lower the Young's modulus of the material, the greater the deflection at which the occurrence of sag starts, that is, the sag does not easily occur.
Usually, a spring portion such as a connector is designed such that its longitudinal direction is perpendicular to the rolling direction in the rolling plane (90-degree direction in FIG. 2). Therefore, it can be said that it is important that the Young's modulus in the direction that forms an angle of 90 degrees with the rolling direction is low.
On the other hand, the deflection given to the spring portion of the connector or the like is not limited to one time, but is often given several thousand times or more by inserting and removing terminals. Especially in relays, the number of deflections is remarkably large.
The present inventor has not only the Young's modulus in the direction that forms an angle of 90 degrees with the rolling direction, but also the rolling direction for the sag in the case where repeated deflection is given in the direction that forms an angle of 90 degrees with the rolling direction. It has been found that the Young's modulus in the direction of an angle of 45 degrees has a great influence.

以上の知見を基礎として完成した本発明は一側面において、1.5〜5.0質量%のTiを含有し、残部が銅及び不可避的不純物からなり、90度方向(度は銅箔の圧延平面における圧延方向と成す角度、以下同様)のヤング率(曲げたわみ係数)が100〜120GPaであり、45度方向のヤング率(曲げたわみ係数)が140GPa以下であるチタン銅である。   The present invention completed on the basis of the above knowledge, in one aspect, contains 1.5 to 5.0% by mass of Ti, the balance is made of copper and inevitable impurities, and is in the direction of 90 degrees (degree is the rolling of copper foil) Titanium copper having a Young's modulus (bending deflection coefficient) of the angle formed with the rolling direction in the plane, the same applies hereinafter, of 100 to 120 GPa and a Young's modulus (bending deflection coefficient) in the 45 degree direction of 140 GPa or less.

本発明に係るチタン銅の一実施形態においては、1.5〜5.0質量%のTiを含有し、残部が銅及び不可避的不純物からなり、90度方向のヤング率(曲げたわみ係数)が111〜120GPaであり、45度方向のヤング率(曲げたわみ係数)が111〜140GPaである。   In one embodiment of titanium copper according to the present invention, it contains 1.5 to 5.0% by mass of Ti, the balance is made of copper and unavoidable impurities, and the Young's modulus (bending deflection coefficient) in the direction of 90 degrees. The Young's modulus (bending deflection coefficient) in the 45 degree direction is 111 to 140 GPa.

本発明に係るチタン銅の別の一実施形態においては、Ag、B、Co、Cr、Fe、Mg、Mn、Mo、Ni、P、Si及びZrのうち1種以上を総量で0.005〜1.0質量%含有する。   In another embodiment of titanium copper according to the present invention, one or more of Ag, B, Co, Cr, Fe, Mg, Mn, Mo, Ni, P, Si, and Zr are 0.005 in total. 1.0% by mass is contained.

本発明は別の一側面において、1.5〜5.0質量%のTiを含有し、残部が銅及び不可避的不純物からなるインゴットを作製し、前記インゴットを、800〜1000℃で厚み5〜20mmまで熱間圧延した後、加工度30〜99%の冷間圧延を行い、400〜500℃の平均昇温速度を1〜50℃/秒として500〜650℃の温度帯に5〜80秒間保持することにより軟化度0.25〜0.75の予備焼鈍を施し、加工度7〜50%の冷間圧延を行い、次いで、700〜900℃で5〜300秒間の溶体化処理、及び、350〜550℃で2〜20時間の時効処理を行う方法であり、
前記軟化度が次式のSで示される、チタン銅の製造方法である:
S=(σ0−σ)/(σ0−σ900
ここで、σ0は予備焼鈍前の引張強さであり、σ及びσ900はそれぞれ予備焼鈍後及び900℃で焼鈍後の引張強さである。
In another aspect of the present invention, an ingot containing 1.5 to 5.0% by mass of Ti and the balance being made of copper and unavoidable impurities is prepared. After hot rolling to 20 mm, cold rolling with a workability of 30 to 99% is performed, and an average temperature increase rate of 400 to 500 ° C. is set to 1 to 50 ° C./second in a temperature range of 500 to 650 ° C. for 5 to 80 seconds. Pre-annealing with a softening degree of 0.25 to 0.75 by holding, performing cold rolling with a working degree of 7 to 50%, then solution treatment at 700 to 900 ° C. for 5 to 300 seconds, and It is a method of performing an aging treatment for 2 to 20 hours at 350 to 550 ° C.,
A method for producing titanium copper, wherein the softening degree is represented by S in the following formula:
S = (σ 0 −σ) / (σ 0 −σ 900 )
Here, σ 0 is the tensile strength before pre-annealing, and σ and σ 900 are the tensile strength after pre-annealing and after annealing at 900 ° C., respectively.

本発明に係るチタン銅の製造方法の一実施形態においては、前記インゴットがAg、B、Co、Cr、Fe、Mg、Mn、Mo、Ni、P、Si及びZrのうち1種以上を総量で0.005〜1.0質量%含有する。   In one embodiment of the method for producing titanium copper according to the present invention, the ingot is a total amount of at least one of Ag, B, Co, Cr, Fe, Mg, Mn, Mo, Ni, P, Si and Zr. It contains 0.005 to 1.0 mass%.

本発明は更に別の一側面において、本発明のチタン銅を備えた伸銅品である。   In yet another aspect, the present invention is a copper-stretched product including the titanium copper of the present invention.

本発明は更に別の一側面において、本発明のチタン銅を備えた電子機器部品である。   In still another aspect, the present invention is an electronic device component including the titanium copper of the present invention.

本発明によれば、圧延平面において圧延方向と直交する方向にばねを設計するコネクタ等の電子部品として用いた際に、ばねの稼動に伴うへたりの発生が著しく抑制された、チタン銅及びその製造方法を提供することができる。   According to the present invention, when used as an electronic component such as a connector for designing a spring in a direction perpendicular to the rolling direction in the rolling plane, the occurrence of sag associated with the operation of the spring is significantly suppressed, and titanium copper and its A manufacturing method can be provided.

へたりが発生する原理の説明図である。It is explanatory drawing of the principle which a sag occurs. チタン銅の圧延銅箔の圧延平面における圧延方向、圧延方向と45度をなす方向、圧延方向と90度をなす方向をそれぞれ示す図である。It is a figure which shows the rolling direction in the rolling plane of the rolled copper foil of titanium copper, the direction which makes 45 degree | times with a rolling direction, and the direction which makes 90 degree | times with a rolling direction, respectively. 本発明に係る合金を種々の温度で焼鈍したときの焼鈍温度と引張強さとの関係図である。It is a related figure of the annealing temperature when the alloy which concerns on this invention is annealed at various temperatures, and tensile strength. 実施例に係るたわみ試験の説明図である。It is explanatory drawing of the bending test which concerns on an Example.

(Ti濃度)
Ti濃度は1.5〜5.0質量%とする。チタン銅では、溶体化処理によりCuマトリックス中へTiを固溶させ、時効処理により微細な析出物を合金中に分散させることにより、強度及び導電率を向上させる。Ti濃度が1.5質量%未満になると、析出物の析出が不充分となり所望の強度が得られない。Ti濃度が5.0質量%を超えると、曲げ性が著しく劣化する。より好ましいTi濃度は2.9〜3.4質量%である。
(Ti concentration)
Ti concentration shall be 1.5-5.0 mass%. Titanium copper improves strength and conductivity by dissolving Ti in a Cu matrix by solution treatment and dispersing fine precipitates in the alloy by aging treatment. If the Ti concentration is less than 1.5% by mass, precipitation of precipitates is insufficient and desired strength cannot be obtained. When the Ti concentration exceeds 5.0% by mass, the bendability is remarkably deteriorated. A more preferable Ti concentration is 2.9 to 3.4% by mass.

(その他の添加元素)
Ag、B、Co、Cr、Fe、Mg、Mn、Mo、Ni、P、Si及びZrのうち1種以上を総量で0.005〜1.0質量%含有させることにより、強度を更に向上させることができる。合計含有量が0.005質量%未満であると上記効果は得られず、合計含有量が1.0質量%を超えると、曲げ加工性が劣化する。より好ましくは、上記元素のうち1種以上を総量で0.01〜0.5質量%含有させる。
(Other additive elements)
Strength is further improved by adding 0.005 to 1.0 mass% of Ag, B, Co, Cr, Fe, Mg, Mn, Mo, Ni, P, Si, and Zr in a total amount of one or more. be able to. If the total content is less than 0.005% by mass, the above effect cannot be obtained, and if the total content exceeds 1.0% by mass, the bending workability deteriorates. More preferably, one or more of the above elements are contained in a total amount of 0.01 to 0.5% by mass.

(ヤング率)
90度方向のヤング率を低く制御することにより、圧延直交方向に設計されたばねのへたりが小さくなる。通常のチタン銅の90度方向のヤング率は125〜130GPa程度である。このヤング率を120GPa以下に調整することにより、へたりが通常のチタン銅より著しく小さくなる。一方、ヤング率が低くなると、上記式1から明らかなように、電気接点における接触力が低下する。90度方向のヤング率が100GPa未満になると、接触力低下に伴う接触抵抗の増加が無視できなくなる。そこで、90度方向のヤング率を100〜120GPaに調整する。接触力の点からは、90度方向のヤング率は111GPa以上であることがより好ましい。さらに好ましいヤング率の範囲は、111〜115GPaである。
一方、90度方向のヤング率を100〜120GPaに調整したチタン銅では、45度方向のヤング率が140GPaを超え、150GPa以上にも達することがある。この45度方向のヤング率上昇を抑制し、45度方向のヤング率を140GPa以下、より好ましくは130GPa以下に調整することにより、一回のたわみを与えたときのへたりだけではなく、繰り返したわみを与えたときのへたりも改善される。
なお、90度方向のヤング率を100〜120GPaに調整したチタン銅では、その製造方法をいかに調整しても、45度方向のヤング率が111GPa未満になることは少なく、さらに120GPa未満になることも少ない。言い換えれば、90度方向のヤング率を100〜120GPa、45度方向のヤング率を140GPa以下に調整した本発明のチタン銅では、45度方向のヤング率は典型的には111GPa以上、より典型的には120GPa以上となる。なお、本発明のヤング率値は、片持ち梁による曲げたわみ係数として測定される値である。
(Young's modulus)
By controlling the Young's modulus in the 90-degree direction low, the settling of the spring designed in the direction perpendicular to the rolling is reduced. Normal titanium copper has a Young's modulus in the 90-degree direction of about 125 to 130 GPa. By adjusting this Young's modulus to 120 GPa or less, the sag is significantly smaller than that of ordinary titanium copper. On the other hand, when the Young's modulus decreases, as is apparent from the above formula 1, the contact force at the electrical contact decreases. When the Young's modulus in the 90-degree direction is less than 100 GPa, an increase in contact resistance accompanying a decrease in contact force cannot be ignored. Therefore, the Young's modulus in the 90-degree direction is adjusted to 100 to 120 GPa. From the point of contact force, the Young's modulus in the 90 degree direction is more preferably 111 GPa or more. A more preferable range of Young's modulus is 111 to 115 GPa.
On the other hand, with titanium copper whose Young's modulus in the 90 degree direction is adjusted to 100 to 120 GPa, the Young's modulus in the 45 degree direction exceeds 140 GPa and may reach 150 GPa or more. By suppressing the increase in Young's modulus in the 45 degree direction and adjusting the Young's modulus in the 45 degree direction to 140 GPa or less, more preferably 130 GPa or less, not only sag when a single deflection is applied, but also repeated deflection. The sagging when given is improved.
In addition, in the case of titanium copper whose 90 degree direction Young's modulus is adjusted to 100 to 120 GPa, the 45 degree direction Young's modulus is rarely less than 111 GPa and even less than 120 GPa no matter how the manufacturing method is adjusted. There are few. In other words, in the titanium copper of the present invention in which the Young's modulus in the 90 ° direction is adjusted to 100 to 120 GPa and the Young's modulus in the 45 ° direction is adjusted to 140 GPa or less, the Young's modulus in the 45 ° direction is typically 111 GPa or more. Is 120 GPa or more. The Young's modulus value of the present invention is a value measured as a bending deflection coefficient by a cantilever beam.

(製造方法)
チタン銅の一般的な製造プロセスでは、まず溶解炉で電気銅、Ti等の原料を溶解し、所望の組成の溶湯を得る。そして、この溶湯をインゴットに鋳造する。チタンの酸化損耗を防止するため、溶解及び鋳造は真空中又は不活性ガス雰囲気中で行うことが好ましい。その後、熱間圧延、冷間圧延、溶体化処理、時効処理の順で所望の厚み及び特性を有する条や箔に仕上げる。熱処理後には、時効時に生成した表面酸化膜を除去するために、表面の酸洗や研磨等を行ってもよい。また、高強度化のために、溶体化処理と時効の間や時効後に冷間圧延を行ってもよい。
本発明では、上記ヤング率を得るために、溶体化処理の前に、熱処理(以下、予備焼鈍ともいう)及び比較的低加工度の冷間圧延(以下、軽圧延ともいう)を行う。
予備焼鈍では、材料を500〜650℃の温度帯、好ましくは500〜600℃の温度帯に、5〜80秒間保持することにより、熱間圧延後の冷間圧延により形成された圧延組織中に、部分的に再結晶粒を生成させる。圧延組織中の再結晶粒の割合には最適値があり、少なすぎてもまた多すぎても所望のヤング率が得られない。最適な割合の再結晶粒は、下記に定義する軟化度Sを0.25〜0.75に調整することで得られる。
図3に本発明合金に係る予備焼鈍前の材料を種々の温度で焼鈍したときの焼鈍温度と引張強さとの関係を例示する。熱電対を取り付けた試料を950℃の管状炉に挿入し、熱電対で測定される試料温度が所定温度に到達したときに、試料を炉から取り出して冷却し、引張強さを測定したものである。500〜700℃の間で再結晶が進行し、引張強さが急激に低下している。高温側での引張強さの緩やかな低下は、再結晶粒の成長によるものである。
予備焼鈍における軟化度Sを次式で定義する。
S=(σ0−σ)/(σ0−σ900
ここで、σ0は予備焼鈍前の引張強さであり、σ及びσ900はそれぞれ予備焼鈍後及び900℃で焼鈍後の引張強さである。900℃という温度は、本発明に係る合金を900℃で焼鈍すると安定して完全再結晶することから、再結晶後の引張強さを知るための基準温度として採用している。
Sが0.25未満又は0.75超になると、90度方向のヤング率が120GPaを超える。
Sを0.25〜0.75に調整するために、材料の最高到達温度を500〜650℃の範囲、好ましくは500〜600℃の範囲に調整した上で、材料温度が500℃以上の状態にて材料を5〜80秒間保持する。材料温度が650℃を超えると、または保持時間が80秒を超えると、Sを0.75以下に調整することが難しくなる。保持時間が5秒未満になると、Sを0.25以上に調整することが難しくなる。材料到達温度が500℃未満になると、500〜650℃における材料保持時間がゼロとなるため、該保持時間が5秒未満の場合と同様、Sを0.25以上に調整することが難しくなる。
なお、Sの0.25〜0.75への調整は、次の手順により行うことができる。
(1)予備焼鈍前の材料の引張り試験強さ(σ0)を測定する。
(2)予備焼鈍前の材料を900℃で焼鈍する。具体的には、熱電対を取り付けた材料を950℃の管状炉に挿入し、熱電対で測定される試料温度が900℃に到達したときに、試料を炉から取り出して水冷する。
(3)上記900℃焼鈍後の材料の引張強さ(σ900)を求める。
(4)例えば、σ0が800MPa、σ900が300MPaの場合、軟化度0.25及び0.75に相当する引張強さは、それぞれ675MPa及び425MPaである。
(5)焼鈍後の引張強さが425〜675MPaとなるように、焼鈍条件を決定する。
Sの制御に加え、予備焼鈍における材料の昇温速度を制御する。所望のヤング率を得るためには、400℃から500℃までの平均昇温速度を1〜50℃/秒の範囲、より好ましくは1.5〜40℃/秒の範囲、さらに好ましくは2〜20℃/秒の範囲に調整する必要がある。
上記平均昇温速度が1℃/秒を下回っても、また50℃/秒を超えても、45度方向のヤング率が140GPaを超える。さらに、上記平均昇温速度が1℃/秒を下回ると90度方向のヤング率が100GPa未満になることがあり、50℃/秒を超えると90度方向のヤング率が120GPaを超えることがある。
伸銅品の製造で工業的に用いられている焼鈍方式として、条を炉中に走行させ加熱する連続焼鈍、及び、条を巻き取ったコイルを炉中で挿入して加熱するバッチ焼鈍炉の二種類がある。一般的に、連続焼鈍における条の400〜500℃の昇温速度は50℃/秒超、バッチ焼鈍における条の400〜500℃の昇温速度は1℃/秒未満である。1〜50℃/秒の昇温速度は、例えば連続焼鈍において、炉内の温度分布に傾斜を付けるなどの対策により可能となる。
なお、上記工程(2)における「熱電対で測定される試料温度が900℃に到達したときに、試料を炉から取り出して水冷する」は、具体的には、例えば試料を炉内でワイヤーに吊しておき、900℃に到達した時点でワイヤーを切断して下方に設けておいた水槽内に落とすことで水冷するものや、試料温度が900℃に到達した直後に手作業により炉内から素早く取り出して水槽に漬けること等により行う。
(Production method)
In a general manufacturing process of titanium copper, first, raw materials such as electrolytic copper and Ti are melted in a melting furnace to obtain a molten metal having a desired composition. Then, this molten metal is cast into an ingot. In order to prevent oxidation wear of titanium, melting and casting are preferably performed in a vacuum or in an inert gas atmosphere. Thereafter, the strips and foils having desired thickness and characteristics are finished in the order of hot rolling, cold rolling, solution treatment, and aging treatment. After the heat treatment, surface pickling or polishing may be performed in order to remove the surface oxide film generated during aging. In order to increase the strength, cold rolling may be performed between the solution treatment and aging or after aging.
In the present invention, in order to obtain the above Young's modulus, heat treatment (hereinafter also referred to as pre-annealing) and cold rolling (hereinafter also referred to as light rolling) with a relatively low degree of work are performed before the solution treatment.
In the pre-annealing, the material is held in a temperature zone of 500 to 650 ° C., preferably in a temperature zone of 500 to 600 ° C. for 5 to 80 seconds, thereby forming a rolled structure formed by cold rolling after hot rolling. , Partially generate recrystallized grains. There is an optimum value for the ratio of recrystallized grains in the rolled structure, and if it is too little or too much, the desired Young's modulus cannot be obtained. The optimum proportion of recrystallized grains can be obtained by adjusting the softening degree S defined below to 0.25 to 0.75.
FIG. 3 illustrates the relationship between the annealing temperature and the tensile strength when the pre-annealing material according to the present invention alloy is annealed at various temperatures. A sample with a thermocouple attached was inserted into a tube furnace at 950 ° C., and when the sample temperature measured by the thermocouple reached a predetermined temperature, the sample was removed from the furnace and cooled, and the tensile strength was measured. is there. Recrystallization proceeds between 500 and 700 ° C., and the tensile strength is rapidly reduced. The gradual decrease in tensile strength on the high temperature side is due to the growth of recrystallized grains.
The softening degree S in the pre-annealing is defined by the following equation.
S = (σ 0 −σ) / (σ 0 −σ 900 )
Here, σ 0 is the tensile strength before pre-annealing, and σ and σ 900 are the tensile strength after pre-annealing and after annealing at 900 ° C., respectively. The temperature of 900 ° C. is adopted as a reference temperature for knowing the tensile strength after recrystallization because the alloy according to the present invention is stably completely recrystallized when annealed at 900 ° C.
When S is less than 0.25 or more than 0.75, the Young's modulus in the 90-degree direction exceeds 120 GPa.
In order to adjust S to 0.25 to 0.75, the maximum temperature of the material is adjusted to a range of 500 to 650 ° C., preferably 500 to 600 ° C., and the material temperature is 500 ° C. or higher. Hold material for 5 to 80 seconds. When the material temperature exceeds 650 ° C. or the holding time exceeds 80 seconds, it becomes difficult to adjust S to 0.75 or less. When the holding time is less than 5 seconds, it becomes difficult to adjust S to 0.25 or more. When the material arrival temperature is less than 500 ° C., the material holding time at 500 to 650 ° C. becomes zero, so that it is difficult to adjust S to 0.25 or more as in the case where the holding time is less than 5 seconds.
The adjustment of S to 0.25 to 0.75 can be performed by the following procedure.
(1) Measure the tensile test strength (σ 0 ) of the material before pre-annealing.
(2) The material before preliminary annealing is annealed at 900 ° C. Specifically, the material to which the thermocouple is attached is inserted into a tubular furnace at 950 ° C., and when the sample temperature measured by the thermocouple reaches 900 ° C., the sample is taken out of the furnace and cooled with water.
(3) Obtain the tensile strength (σ 900 ) of the material after annealing at 900 ° C.
(4) For example, when σ 0 is 800 MPa and σ 900 is 300 MPa, the tensile strengths corresponding to the softening degrees of 0.25 and 0.75 are 675 MPa and 425 MPa, respectively.
(5) The annealing conditions are determined so that the tensile strength after annealing is 425 to 675 MPa.
In addition to the control of S, the temperature rising rate of the material in the pre-annealing is controlled. In order to obtain a desired Young's modulus, the average rate of temperature increase from 400 ° C. to 500 ° C. is in the range of 1 to 50 ° C./second, more preferably in the range of 1.5 to 40 ° C./second, still more preferably 2 to 2. It is necessary to adjust to a range of 20 ° C./second.
Even if the average heating rate is less than 1 ° C./second or exceeds 50 ° C./second, the Young's modulus in the 45 degree direction exceeds 140 GPa. Further, when the average temperature rise rate is less than 1 ° C./second, the Young's modulus in the 90 ° direction may be less than 100 GPa, and when it exceeds 50 ° C./second, the Young's modulus in the 90 ° direction may exceed 120 GPa. .
As an annealing method that is industrially used in the manufacture of copper-drawn products, continuous annealing in which the strip is run and heated in the furnace, and a batch annealing furnace in which the coil wound with the strip is inserted and heated in the furnace There are two types. Generally, the rate of temperature increase from 400 to 500 ° C. for continuous strips in continuous annealing exceeds 50 ° C./second, and the rate of temperature increase from 400 to 500 ° C. for strips in batch annealing is less than 1 ° C./second. A temperature increase rate of 1 to 50 ° C./second can be achieved by measures such as inclining the temperature distribution in the furnace in continuous annealing, for example.
In the above step (2), “when the sample temperature measured by the thermocouple reaches 900 ° C., the sample is taken out of the furnace and water-cooled” is specifically, for example, the sample is wired in the furnace. When suspended, the wire is cut when it reaches 900 ° C. and dropped into a water tank provided below, or immediately after the sample temperature reaches 900 ° C. by hand from inside the furnace. Take it out quickly by immersing it in a water tank.

上記予備焼鈍の後、溶体化処理に先立ち、加工度7〜50%の軽圧延を行う。加工度R(%)は次式で定義する。
R=(t0−t)/t0×100(t0:圧延前の板厚、t:圧延後の板厚)
加工度がこの範囲から外れると、90度方向のヤング率が120GPaを超える。
After the preliminary annealing, prior to the solution treatment, light rolling with a working degree of 7 to 50% is performed. The processing degree R (%) is defined by the following equation.
R = (t 0 −t) / t 0 × 100 (t 0 : plate thickness before rolling, t: plate thickness after rolling)
If the degree of processing is out of this range, the Young's modulus in the 90 degree direction exceeds 120 GPa.

本発明に係る合金の製造方法を工程順に列記すると次のようになる。
(1)インゴットの鋳造
(2)熱間圧延(温度800〜1000℃、厚み5〜20mm程度まで)
(3)冷間圧延(加工度30〜99%)
(4)予備焼鈍(軟化度:S=0.25〜0.75、400〜500℃の平均昇温速度:1〜50℃/秒)
(5)軽圧延(加工度7〜50%)
(6)溶体化処理(700〜900℃で5〜300秒間)
(7)冷間圧延(加工度1〜60%)
(8)時効処理(350〜550℃で2〜20時間)
(9)冷間圧延(加工度1〜50%)
(10)歪取り焼鈍(300〜700℃で5秒〜10時間)
ここで、熱間圧延(2)は一般的なチタン銅の条件で行うことが可能であるが、材料温度を350℃以上に保った状態で所定の厚みまでの圧延を終え、その後直ちに水冷することが好ましい。これにより、熱間圧延後の冷却中における粗大析出物(製品の高強度化に寄与しない)の形成が抑制される。
冷間圧延(3)の加工度は30〜99%とすることが好ましい。予備焼鈍(4)で部分的に再結晶粒を生成させるためには、冷間圧延(3)で歪を導入しておく必要があり、30%以上の加工度で有効な歪が得られる。一方、加工度が99%を超えると、圧延材のエッジ等に割れが発生し、圧延中の材料が破断することがある。
冷間圧延(7)及び(9)は高強度化のために任意に行うものであり、圧延加工度の増加とともに強度が増加する反面、曲げ性が低下する。冷間圧延(7)及び(9)の有無及びそれぞれの加工度によらず、ヤング率の制御によりへたりが抑制されるという本発明の効果は得られる。冷間圧延(7)及び(9)は行ってもよいし行わなくてもよい。ただし、冷間圧延(7)及び(9)におけるそれぞれの加工度が上記上限値を超えることは曲げ性の点から好ましくなく、それぞれの加工度が上記下限値を下回ることは高強度化の効果の点から好ましくない。
歪取り焼鈍(10)は、冷間圧延(9)を行う場合にこの冷間圧延で低下するばね限界値等を回復させるために任意に行うものである。歪取り焼鈍(10)の有無に関わらず、ヤング率の制御によりへたりが抑制されるという本発明の効果は得られる。歪取り焼鈍(10)は行ってもよいし行わなくてもよい。
なお、工程(6)及び(8)については、チタン銅の一般的な製造条件を選択すればよい。
It is as follows when the manufacturing method of the alloy which concerns on this invention is listed in process order.
(1) Ingot casting (2) Hot rolling (temperature 800-1000 ° C, thickness 5-20mm)
(3) Cold rolling (working degree 30-99%)
(4) Pre-annealing (degree of softening: S = 0.25 to 0.75, average heating rate of 400 to 500 ° C .: 1 to 50 ° C./second)
(5) Light rolling (working degree 7-50%)
(6) Solution treatment (700 to 900 ° C. for 5 to 300 seconds)
(7) Cold rolling (working degree 1-60%)
(8) Aging treatment (2 to 20 hours at 350 to 550 ° C.)
(9) Cold rolling (working degree 1-50%)
(10) Strain relief annealing (at 300 to 700 ° C. for 5 seconds to 10 hours)
Here, the hot rolling (2) can be performed under the condition of general titanium copper, but the rolling to a predetermined thickness is finished in a state where the material temperature is maintained at 350 ° C. or higher, and then immediately cooled with water. It is preferable. Thereby, formation of coarse precipitates (not contributing to increase in strength of the product) during cooling after hot rolling is suppressed.
The degree of work in cold rolling (3) is preferably 30 to 99%. In order to generate recrystallized grains partially by pre-annealing (4), it is necessary to introduce strain by cold rolling (3), and effective strain can be obtained at a workability of 30% or more. On the other hand, if the degree of work exceeds 99%, cracks may occur at the edges of the rolled material and the material being rolled may break.
Cold rolling (7) and (9) is optionally performed to increase the strength, and the strength increases as the degree of rolling process increases, but the bendability decreases. The effect of the present invention that the sag is suppressed by controlling the Young's modulus can be obtained regardless of the presence or absence of cold rolling (7) and (9) and the degree of processing. Cold rolling (7) and (9) may or may not be performed. However, it is not preferable from the viewpoint of bendability that the respective working degrees in the cold rolling (7) and (9) exceed the above upper limit value, and the fact that each working degree is below the above lower limit effect of increasing the strength. From the point of view, it is not preferable.
The strain relief annealing (10) is optionally performed in order to recover the spring limit value and the like which are lowered by the cold rolling when the cold rolling (9) is performed. Regardless of the presence or absence of strain relief annealing (10), the effect of the present invention that the sag is suppressed by controlling the Young's modulus is obtained. The strain relief annealing (10) may or may not be performed.
In addition, what is necessary is just to select the general manufacturing conditions of titanium copper about process (6) and (8).

本発明のチタン銅は種々の伸銅品、例えば板、条及び箔に加工することができ、更に、本発明のチタン銅は、リードフレーム、コネクタ、ピン、端子、リレー、スイッチ、二次電池用箔材等の電子機器部品等に使用することができる。   The titanium copper of the present invention can be processed into various copper products, for example, plates, strips and foils. Furthermore, the titanium copper of the present invention is a lead frame, connector, pin, terminal, relay, switch, secondary battery. It can be used for electronic device parts such as foil materials.

以下に本発明の実施例を比較例と共に示すが、これらの実施例は本発明及びその利点をよりよく理解するために提供するものであり、発明が限定されることを意図するものではない。   Examples of the present invention will be described below together with comparative examples, but these examples are provided for better understanding of the present invention and its advantages, and are not intended to limit the invention.

(実施例1)
3.2質量%のTiを含有し残部が銅及び不可避的不純物からなる合金を実験材料とし、予備焼鈍及び軽圧延条件とヤング率との関係、さらにヤング率が製品のへたり特性に及ぼす影響を検討した。
高周波溶解炉にてアルゴン雰囲気中で内径60mm、深さ200mmの黒鉛るつぼを用い電気銅2.5kgを溶解した。上記合金組成が得られるよう合金元素を添加し、溶湯温度を1300℃に調整した後、鋳鉄製の鋳型に鋳込み、厚さ30mm、幅60mm、長さ120mmのインゴットを製造した。このインゴットを熱間圧延として、950℃で3時間加熱後、材料温度を350℃以上に保ったまま厚さ10mmまで圧延し、その後直ちに水冷した。熱間圧延板表面の酸化スケールをグラインダーで研削して除去した。研削後の厚みは9mmであった。その後、次の工程順で圧延及び熱処理を施し、板厚0.15mmの製品試料を作製した。
(1)冷間圧延:軽圧延の圧延加工度に応じ、所定の厚みまで冷間圧延した。
(2)予備焼鈍:所定温度に調整した電気炉に試料を挿入し、所定時間保持した後、試料を大気中に放置し冷却した。その間、試料に溶接した熱電対を用いて試料温度を測定し、到達温度、400〜500℃の平均昇温速度及び500〜650℃の保持時間を求めた。
(3)軽圧延:種々の圧延加工度で、厚み0.18mmまで冷間圧延を行った。
(4)溶体化処理:800℃に調整した電気炉に試料を挿入し、10秒間保持した後、試料を水槽に入れ冷却した。
(5)時効処理:電気炉を用い450℃で5時間、Ar雰囲気中で加熱した。
(6)冷間圧延:0.18mmから0.15mmまで加工度17%で冷間圧延した。
(7)歪取り焼鈍:400℃に調整した電気炉に試料を挿入し、10秒間保持した後、試料を大気中に放置し冷却した。
Example 1
3.2 Alloys containing 2% by mass of Ti and the balance being copper and inevitable impurities are used as experimental materials, the relationship between pre-annealing and light rolling conditions and Young's modulus, and the effect of Young's modulus on the sag characteristics of products It was investigated.
In a high frequency melting furnace, 2.5 kg of electrolytic copper was melted using a graphite crucible having an inner diameter of 60 mm and a depth of 200 mm in an argon atmosphere. Alloy elements were added to obtain the above alloy composition, the melt temperature was adjusted to 1300 ° C., and then cast into a cast iron mold to produce an ingot having a thickness of 30 mm, a width of 60 mm, and a length of 120 mm. This ingot was hot-rolled, heated at 950 ° C. for 3 hours, rolled to a thickness of 10 mm while maintaining the material temperature at 350 ° C. or higher, and then immediately cooled with water. The oxidized scale on the surface of the hot rolled plate was removed by grinding with a grinder. The thickness after grinding was 9 mm. Thereafter, rolling and heat treatment were performed in the following order of steps to produce a product sample having a thickness of 0.15 mm.
(1) Cold rolling: Cold rolling was performed to a predetermined thickness according to the rolling degree of light rolling.
(2) Pre-annealing: The sample was inserted into an electric furnace adjusted to a predetermined temperature and held for a predetermined time, and then the sample was left in the air and cooled. Meanwhile, the sample temperature was measured using a thermocouple welded to the sample, and the ultimate temperature, the average temperature rise rate of 400 to 500 ° C, and the holding time of 500 to 650 ° C were determined.
(3) Light rolling: Cold rolling to various thicknesses of 0.18 mm was performed.
(4) Solution treatment: The sample was inserted into an electric furnace adjusted to 800 ° C. and held for 10 seconds, and then the sample was placed in a water bath and cooled.
(5) Aging treatment: Heated in an Ar atmosphere at 450 ° C. for 5 hours using an electric furnace.
(6) Cold rolling: Cold rolled from 0.18 mm to 0.15 mm at a workability of 17%.
(7) Strain relief annealing: The sample was inserted into an electric furnace adjusted to 400 ° C. and held for 10 seconds, and then the sample was left in the air and cooled.

予備焼鈍後の試料及び製品試料(この場合は歪取り焼鈍上がり)について、次の評価を行った。
(予備焼鈍での軟化度評価)
予備焼鈍前及び予備焼鈍後の試料につき、引張試験機を用いてJIS Z 2241に準拠し、圧延方向と平行に引張強さを測定し、それぞれの値をσ0及びσとした。また、900℃で焼鈍試料を前記手順(950℃の炉に挿入し試料が900℃に到達したときに冷却)で作製し、圧延方向と平行に引張強さを同様に測定しσ900を求めた。σ0、σ、σ900から、下記式により軟化度Sを求めた。
S=(σ0−σ)/(σ0−σ900
The following evaluation was performed on the sample after the preliminary annealing and the product sample (in this case, the strain relief annealing was completed).
(Evaluation of softening degree in preliminary annealing)
With respect to the sample before pre-annealing and after pre-annealing, the tensile strength was measured in parallel with the rolling direction using a tensile tester in accordance with JIS Z 2241, and the respective values were taken as σ 0 and σ. In addition, an annealed sample at 900 ° C. was prepared by the above procedure (inserted into a 950 ° C. furnace and cooled when the sample reached 900 ° C.), and the tensile strength was measured in parallel with the rolling direction to obtain σ 900 . It was. The degree of softening S was determined from σ 0 , σ, and σ 900 by the following formula.
S = (σ 0 −σ) / (σ 0 −σ 900 )

(製品の引張り試験)
引張試験機を用いてJIS Z2241に準拠し、圧延方向と平行に0.2%耐力を測定した。
(Product tensile test)
A 0.2% proof stress was measured in parallel with the rolling direction in accordance with JIS Z2241 using a tensile tester.

(ヤング率測定)
ヤング率は、日本伸銅協会(JACBA)技術標準「銅及び銅合金板条の片持ち梁による曲げたわみ係数測定方法」に準じて測定した。
板厚t、幅w(=10mm)、長さ100mmの短冊形状の試料を、図2に示す試料の長手方向が圧延方向と90度の角度を成す方向及び45度の角度を成す方向に、それぞれ採取した。この試料の片端を固定し、固定端からL(=100t)の位置にP(=0.15N)の荷重を加え、このときのたわみdから、次式を用いヤング率Eを求めた。
E=4・P・(L/t)3/(w・d)
(Young's modulus measurement)
The Young's modulus was measured according to the Japan Copper and Brass Association (JACBA) technical standard “Method of measuring bending deflection coefficient of cantilevered copper and copper alloy strips”.
A strip-shaped sample having a plate thickness t, a width w (= 10 mm), and a length of 100 mm, in a direction in which the longitudinal direction of the sample shown in FIG. 2 forms an angle of 90 degrees with the rolling direction and an angle of 45 degrees, Each was collected. One end of this sample was fixed, a load of P (= 0.15 N) was applied to a position L (= 100 t) from the fixed end, and the Young's modulus E was determined from the deflection d at this time using the following equation.
E = 4 · P · (L / t) 3 / (w · d)

(たわみ試験)
幅5mmの短冊形状の試料を、図2に示す試料の長手方向が圧延方向と90度の角度を成す方向に採取した。
次に、図4のように、試料の片端を固定し、この固定端から距離Lの位置に、先端をナイフエッジに加工したポンチを押し当て、試料にたわみdを与えた後、ポンチを初期の位置に戻し除荷した。ポンチの移動速度は1mm/分とした。
まず1回のたわみを与え接触力P(ポンチに作用する荷重)を測定し、除荷後へたりδを求めた。また、5000回のたわみを与え、除荷した後のへたりδを求めた。
表1に評価結果を示す。ここで、たわみ試験は、t(板厚)=0.15mm、w(板幅)=5mm、L(ばね長)=9.3mm、d(たわみ)=3mmの条件で行った。また、へたりδは0.01mmの分解能で測定し、へたりδが検出されなかった場合は<0.01mmと表記している。
(Bending test)
A strip-shaped sample having a width of 5 mm was taken in a direction in which the longitudinal direction of the sample shown in FIG. 2 forms an angle of 90 degrees with the rolling direction.
Next, as shown in FIG. 4, one end of the sample is fixed, and a punch whose tip is processed into a knife edge is pressed to a position at a distance L from the fixed end to give a deflection d to the sample. Returned to position and unloaded. The moving speed of the punch was 1 mm / min.
First, a single deflection was applied and the contact force P (load acting on the punch) was measured to determine the sag δ after unloading. In addition, the sagging δ after unloading was determined by giving 5000 times of deflection.
Table 1 shows the evaluation results. Here, the deflection test was performed under the conditions of t (plate thickness) = 0.15 mm, w (plate width) = 5 mm, L (spring length) = 9.3 mm, and d (deflection) = 3 mm. Further, the sag δ is measured with a resolution of 0.01 mm, and when the sag δ is not detected, it is expressed as <0.01 mm.

発明例1〜16は、いずれも本発明が規定する条件で予備焼鈍及び軽圧延を行ったものであり、90度方向及び45度方向のヤング率が本発明の規定を満たし、たわみ1回後及び5000回後とも、へたりが検出されなかった。また、90度方向のヤング率の低下とともに接触力が低下する傾向があり、90度方向のヤング率が111GPa未満と低めであった発明例3、6、9、12、13は、他の発明例の接触力より若干低かったものの、全ての発明例において1.7Nを超える接触力を維持できた。
たわみ試験で得られる接触力(P)は、ヤング率(E)、耐力等の合金特性だけでなく、前記式1[P=dEwt3/4L3]から示唆されるように、試料形状(t,w)やたわみ条件(L,d)の影響も受ける。発明例で得られた上記接触力は、試料形状及びたわみ条件から期待される接触力に対し、充分なレベルといえた。
比較例1は、予備焼鈍及び軽圧延を行っていないものであり、一般的なチタン銅に相当する。90度方向のヤング率が120GPaを超えたため、一回のたわみでへたりが生じ、このへたりは5000回のたわみでやや増加した。
比較例2は、予備焼鈍及び軽圧延を行ったものの、予備焼鈍の際の到達温度が650℃を超え、軟化度が0.75を超えたものである。軟化度が過大であったため、90度方向のヤング率が120GPaを超えた。その結果、一回のたわみでへたりが生じ、このへたりは5000回のたわみでやや増加した。
比較例3は、予備焼鈍及び軽圧延を行ったものの、予備焼鈍の際の保持時間が5秒に満たず、軟化度が0.25を下回ったものである。軟化度が過小であったため、90度方向のヤング率が120GPaを超えた。その結果、一回のたわみでへたりが生じ、このへたりは5000回のたわみでやや増加した。
比較例4及び5では、予備焼鈍及び軽圧延を行ったものの、軽圧延の際の加工度がそれぞれ過小及び過大だったため、90度方向のヤング率が120GPaを超えた。その結果、一回のたわみでへたりが生じ、このへたりは5000回のたわみでやや増加した。
比較例6では、予備焼鈍の軟化度及び軽圧延の加工度が適正条件だったため、90度方向のヤング率が100〜120GPaに入った。しかし、予備焼鈍での400〜500℃の昇温速度が1℃/秒に満たなかったため、45度方向のヤング率が140GPaを超えた。その結果、1回のたわみではへたりが検出されなかったものの、5000回のたわみでへたりが発生した。
比較例7は、比較例6と同様、予備焼鈍での昇温速度が過小だったものだが、該昇温速度が特に遅かったため、45度方向のヤング率が140GPaを超え5000回のたわみでへたりが発生しただけでなく、90度方向のヤング率が100GPa未満になり、接触力が発明例の2/3程度まで低下した。このレベルまで接触力が低下すると、コネクタに加工し使用した際に、接点の接触電気抵抗が異常上昇する等の問題が生じる。
比較例8は、予備焼鈍の軟化度及び軽圧延の加工度が適正条件だったため、90度方向のヤング率が100〜120GPaに入った。しかし、予備焼鈍での400〜500℃の昇温速度が50℃/秒を超えたため、45度方向のヤング率が140GPaを超えた。その結果、1回のたわみではへたりが検出されなかったものの、5000回のたわみでへたりが発生した。
比較例9は、比較例8と同様、予備焼鈍での昇温速度が過大だったものであるが、該昇温速度が特に大きかったため、45度方向のヤング率が140GPaを超えただけでなく、90度方向のヤング率が120GPaを超えた。その結果、1回のたわみで既にへたりが生じ、このへたりは5000回のたわみで顕著に増加した。
比較例10は、予備焼鈍及び軽圧延を行ったものの、予備焼鈍の際の保持時間が80秒間を超え、軟化度が過大となり、また昇温速度が過小であったものである。90度方向のヤング率が120GPaを超え、一回のたわみでへたりが生じ、このへたりは5000回のたわみでやや増加した。
Inventive Examples 1 to 16 were pre-annealed and light-rolled under the conditions specified by the present invention. The Young's modulus in the 90 ° direction and 45 ° direction satisfied the specification of the present invention, and after one deflection. And after 5000 times, no sag was detected. Inventive Examples 3, 6, 9, 12, and 13 in which the Young's modulus in the 90-degree direction tends to decrease and the Young's modulus in the 90-degree direction is less than 111 GPa are other inventions. Although it was slightly lower than the contact force of the examples, the contact force exceeding 1.7 N could be maintained in all the inventive examples.
The contact force (P) obtained by the deflection test is not limited to the alloy properties such as Young's modulus (E) and proof stress, but also as shown by the above formula 1 [P = dEwt 3 / 4L 3 ]. , W) and deflection conditions (L, d). It can be said that the contact force obtained in the invention example was a sufficient level with respect to the contact force expected from the sample shape and the deflection condition.
Comparative Example 1 does not undergo pre-annealing and light rolling, and corresponds to general titanium copper. Since the Young's modulus in the 90-degree direction exceeded 120 GPa, a sag occurred with one deflection, and this sag increased slightly with a 5,000 deflection.
Although the comparative example 2 performed preliminary annealing and light rolling, the ultimate temperature in the case of preliminary annealing exceeded 650 degreeC and the softening degree exceeded 0.75. Since the degree of softening was excessive, the Young's modulus in the 90-degree direction exceeded 120 GPa. As a result, a sag occurred after a single deflection, and this sag increased slightly after 5000 deflections.
In Comparative Example 3, although pre-annealing and light rolling were performed, the holding time during pre-annealing was less than 5 seconds, and the softening degree was less than 0.25. Since the degree of softening was too small, the Young's modulus in the 90-degree direction exceeded 120 GPa. As a result, a sag occurred after a single deflection, and this sag increased slightly after 5000 deflections.
In Comparative Examples 4 and 5, although pre-annealing and light rolling were performed, the degree of processing during light rolling was too small and too large, so the Young's modulus in the 90 degree direction exceeded 120 GPa. As a result, a sag occurred after a single deflection, and this sag increased slightly after 5000 deflections.
In Comparative Example 6, since the softening degree of pre-annealing and the workability of light rolling were appropriate conditions, the Young's modulus in the 90 degree direction entered 100 to 120 GPa. However, since the temperature increase rate at 400 to 500 ° C. in the pre-annealing was less than 1 ° C./second, the Young's modulus in the 45 ° direction exceeded 140 GPa. As a result, no sag was detected in one deflection, but sag occurred in 5000 deflections.
In Comparative Example 7, as in Comparative Example 6, the rate of temperature increase during the pre-annealing was too low, but because the rate of temperature increase was particularly slow, the Young's modulus in the 45 degree direction exceeded 140 GPa and the deflection was 5000 times. In addition, the Young's modulus in the 90-degree direction was less than 100 GPa, and the contact force was reduced to about 2/3 of the inventive example. When the contact force decreases to this level, problems such as abnormal increase in contact electrical resistance of contacts occur when the connector is processed and used.
In Comparative Example 8, since the softening degree of pre-annealing and the workability of light rolling were appropriate conditions, the Young's modulus in the 90 degree direction entered 100 to 120 GPa. However, since the temperature increase rate at 400 to 500 ° C. in the pre-annealing exceeded 50 ° C./second, the Young's modulus in the 45 ° direction exceeded 140 GPa. As a result, no sag was detected in one deflection, but sag occurred in 5000 deflections.
In Comparative Example 9, as in Comparative Example 8, the rate of temperature increase during pre-annealing was excessive, but because the rate of temperature increase was particularly large, not only the Young's modulus in the 45 degree direction exceeded 140 GPa. The Young's modulus in the 90 degree direction exceeded 120 GPa. As a result, a sag has already occurred after one deflection, and this sag increased significantly after 5,000 deflections.
In Comparative Example 10, although pre-annealing and light rolling were performed, the holding time at the time of pre-annealing exceeded 80 seconds, the softening degree was excessive, and the heating rate was excessive. The Young's modulus in the 90-degree direction exceeded 120 GPa, and a sag occurred with one deflection, and this sag increased slightly with a 5,000 deflection.

(実施例2)
実施例1で示した、へたり改善効果が、異なる成分及び製造条件のチタン銅で得られることを検証した。
実施例1と同様の方法で鋳造、熱間圧延及び表面研削を行い、表2の成分を有する厚み9mmの板を得た。この板に対し次の工程順で圧延及び熱処理を施し、表2に示す板厚の製品試料を得た。
(1)冷間圧延
(2)予備焼鈍:実施例1と同様の方法で実施。
(3)軽圧延
(4)溶体化処理:所定温度に調整した電気炉に試料を挿入し、10秒間保持した後、試料を水槽に入れ冷却した。該温度は再結晶粒の平均直径が5〜25μmの範囲になる範囲で選択した。
(5)冷間圧延(圧延1)
(6)時効処理:電気炉を用い所定温度で5時間、Ar雰囲気中で加熱した。該温度は時効後の引張強さが最大になるように選択した。
(7)冷間圧延(圧延2)
(8)歪取り焼鈍:所定温度に調整した電気炉に試料を挿入し、10秒間保持した後、試料を大気中に放置し冷却した。
予備焼鈍後の試料及び製品試料について、実施例1と同様の評価を行った。なお、たわみ試験ではw=5mmとし、後述する合金群毎に、本発明の効果が発現しやすいようL及びdを設定した。
表2及び3に評価結果を示す。圧延1、圧延2、歪取り焼鈍のいずれかを行わなかった場合は、それぞれの加工度または温度の欄に「なし」と表記している。
(Example 2)
It was verified that the effect of improving the sag shown in Example 1 was obtained with titanium copper having different components and production conditions.
Casting, hot rolling and surface grinding were performed in the same manner as in Example 1 to obtain a 9 mm thick plate having the components shown in Table 2. This plate was subjected to rolling and heat treatment in the following process order to obtain a product sample having a plate thickness shown in Table 2.
(1) Cold rolling (2) Pre-annealing: Performed in the same manner as in Example 1.
(3) Light rolling (4) Solution treatment: The sample was inserted into an electric furnace adjusted to a predetermined temperature and held for 10 seconds, and then the sample was placed in a water bath and cooled. The temperature was selected so that the average diameter of the recrystallized grains was in the range of 5 to 25 μm.
(5) Cold rolling (Rolling 1)
(6) Aging treatment: Heating was performed in an Ar atmosphere using an electric furnace at a predetermined temperature for 5 hours. The temperature was selected to maximize the tensile strength after aging.
(7) Cold rolling (Rolling 2)
(8) Strain relief annealing: The sample was inserted into an electric furnace adjusted to a predetermined temperature and held for 10 seconds, and then the sample was left in the air and cooled.
Evaluation similar to Example 1 was performed about the sample after pre-annealing, and a product sample. In the deflection test, w = 5 mm, and L and d were set for each alloy group described later so that the effects of the present invention are easily exhibited.
Tables 2 and 3 show the evaluation results. When any one of rolling 1, rolling 2, and strain relief annealing is not performed, “none” is written in the column of the degree of processing or temperature.

(合金A)
合金Aは、合金成分としてTiのみを含んでおり、残部が銅及び不可避的不純物から構成される。また、圧延1、圧延2、歪取り焼鈍のいずれもが行われている。発明例A−1では、ヤング率が規定を満たしたため、たわみ1回後及び5000回後とも、へたりが検出されなかった。
比較例A−1では、予備焼鈍での軟化度が0.75を超え、90度方向のヤング率が120GPaを超えたため、一回のたわみでへたりが生じた。
比較例A−2では、予備焼鈍の昇温速度が1℃/秒に満たず、45度方向のヤング率が140GPaを超えたため、5000回のたわみでへたりが発生した。
比較例A−3では、Ti濃度が過小であったため、製品の耐力が低下し、1回のたわみでへたりが生じた。
接触力について見ると、発明例A−1、比較例A−1及び比較例A−2では、90度方向のヤング率が100GPa以上となったため、試料形状及びたわみ条件から期待されるレベルの接触力が得られた。これに対し、90度方向のヤング率が100GPaを超えたものの耐力が著しく低い比較例A−3では、発明例A−1、比較例A−1及び比較例A−2に対し、2/3程度の接触力しか得られなかった。
(Alloy A)
The alloy A contains only Ti as an alloy component, and the balance is composed of copper and inevitable impurities. Moreover, all of rolling 1, rolling 2, and strain relief annealing are performed. In Invention Example A-1, since the Young's modulus satisfied the regulation, no sag was detected after one deflection and after 5,000 deflections.
In Comparative Example A-1, since the degree of softening in the pre-annealing exceeded 0.75 and the Young's modulus in the 90-degree direction exceeded 120 GPa, sag occurred due to a single deflection.
In Comparative Example A-2, the temperature increase rate of the pre-annealing was less than 1 ° C./second, and the Young's modulus in the 45 ° direction exceeded 140 GPa, so that sag occurred after 5000 deflections.
In Comparative Example A-3, since the Ti concentration was too low, the yield strength of the product was reduced, and sag occurred due to a single deflection.
As for the contact force, in Invention Example A-1, Comparative Example A-1 and Comparative Example A-2, the Young's modulus in the 90-degree direction was 100 GPa or more, and therefore the contact level expected from the sample shape and deflection conditions. Power was obtained. On the other hand, in Comparative Example A-3 in which the Young's modulus in the 90-degree direction exceeded 100 GPa but the proof stress was remarkably low, 2/3 of Invention Example A-1, Comparative Example A-1 and Comparative Example A-2 Only a moderate contact force was obtained.

(合金B)
合金Bは、合金成分として、3.5%Ti及び0.2%Fe(%は質量%、以下同様)を含有し、残部が銅及び不可避的不純物から構成される。また、圧延1が行われている。
発明例B−1では、ヤング率が規定を満たしたため、たわみ1回後及び5000回後とも、へたりが検出されなかった。
比較例B−1では、予備焼鈍及び軽圧延が行われず、90度方向のヤング率が120GPaを超えたため、一回のたわみでへたりが生じた。
比較例B−2では、予備焼鈍の昇温速度が50℃/秒を超え、45度方向のヤング率が140GPaを超えたため、5000回のたわみでへたりが発生した。
なお、発明例B−1、比較例B−1、比較例B−2とも、90度方向のヤング率が100GPa以上となったため、試料形状及びたわみ条件から期待されるレベルの接触力が得られた。
(Alloy B)
Alloy B contains 3.5% Ti and 0.2% Fe (% is mass%, the same applies hereinafter) as alloy components, and the balance is composed of copper and inevitable impurities. Moreover, rolling 1 is performed.
In Invention Example B-1, because the Young's modulus satisfied the regulation, no sag was detected after one deflection and after 5,000 deflections.
In Comparative Example B-1, pre-annealing and light rolling were not performed, and the Young's modulus in the 90-degree direction exceeded 120 GPa, so that sag occurred due to a single deflection.
In Comparative Example B-2, since the temperature increase rate of the pre-annealing exceeded 50 ° C./second and the Young's modulus in the 45 degree direction exceeded 140 GPa, sag occurred at 5000 times of deflection.
In each of Invention Example B-1, Comparative Example B-1, and Comparative Example B-2, the Young's modulus in the 90-degree direction was 100 GPa or more, so that the contact force at the level expected from the sample shape and the deflection condition was obtained. It was.

(合金C)
合金Cは、合金成分として、2.0%Ti、0.1%Ag、0.1%Coおよび0.1%Niを含有し、残部が銅及び不可避的不純物から構成される。また、圧延2及び歪取り焼鈍が行われている。
発明例C−1では、ヤング率が規定を満たしたため、たわみ1回後及び5000回後とも、へたりが検出されなかった。
比較例C−1では、予備焼鈍での軟化度が0.75を超え、90度方向のヤング率が120GPaを超えたため、一回のたわみでへたりが生じた。
比較例C−2では、予備焼鈍での軟化度が0.25に満たず、90度方向のヤング率が120GPaを超えたため、一回のたわみでへたりが生じた。
比較例C−3では、予備焼鈍の昇温速度が1℃/秒に満たず、45度方向のヤング率が140GPaを超えたため、5000回のたわみでへたりが発生した。
なお、発明例C−1、比較例C−1、比較例C−2、比較例C−3とも、90度方向のヤング率が100GPa以上となったため、試料形状及びたわみ条件から期待されるレベルの接触力が得られた。
(Alloy C)
Alloy C contains 2.0% Ti, 0.1% Ag, 0.1% Co and 0.1% Ni as alloy components, and the balance is composed of copper and inevitable impurities. Further, rolling 2 and strain relief annealing are performed.
In Invention Example C-1, because the Young's modulus satisfied the regulation, no sag was detected after one deflection and after 5,000 deflections.
In Comparative Example C-1, since the degree of softening during pre-annealing exceeded 0.75 and the Young's modulus in the 90-degree direction exceeded 120 GPa, sag occurred due to a single deflection.
In Comparative Example C-2, the degree of softening in the pre-annealing was less than 0.25, and the Young's modulus in the 90-degree direction exceeded 120 GPa, so that sag occurred with a single deflection.
In Comparative Example C-3, the temperature increase rate of the pre-annealing was less than 1 ° C./second, and the Young's modulus in the 45 ° direction exceeded 140 GPa, so that sag occurred after 5000 times of deflection.
In addition, since the Young's modulus in the 90-degree direction was 100 GPa or more in all of Invention Example C-1, Comparative Example C-1, Comparative Example C-2, and Comparative Example C-3, the level expected from the sample shape and deflection conditions The contact force was obtained.

(合金D)
合金Dは、合金成分として、4.5%Ti、0.05%Si、0.1%Ni、0.1%Zr及び0.1%Crを含有し、残部が銅及び不可避的不純物から構成される。また、圧延1が行われている。
発明例D−1では、ヤング率が規定を満たしたため、たわみ1回後及び5000回後とも、へたりが検出されなかった。
比較例D−1では、軽圧延の加工度が50%を超え、90度方向のヤング率が120GPaを超えたため、一回のたわみでへたりが生じた。
比較例D−2では、予備焼鈍の昇温速度が50℃/秒を超え、45度方向のヤング率が140GPaを超えたため、5000回のたわみでへたりが発生した。
なお、発明例D−1、比較例D−1、比較例D−2とも、90度方向のヤング率が100GPa以上となったため、試料形状及びたわみ条件から期待されるレベルの接触力が得られた。
(Alloy D)
Alloy D contains 4.5% Ti, 0.05% Si, 0.1% Ni, 0.1% Zr and 0.1% Cr as the alloy components, with the balance being composed of copper and inevitable impurities Is done. Moreover, rolling 1 is performed.
In Invention Example D-1, since the Young's modulus satisfied the regulation, no sag was detected after one deflection and after 5,000 deflections.
In Comparative Example D-1, since the workability of light rolling exceeded 50% and the Young's modulus in the 90-degree direction exceeded 120 GPa, sag occurred with a single deflection.
In Comparative Example D-2, since the temperature increase rate of the pre-annealing exceeded 50 ° C./second and the Young's modulus in the 45 degree direction exceeded 140 GPa, sag occurred after 5000 times of deflection.
In each of Invention Example D-1, Comparative Example D-1 and Comparative Example D-2, the Young's modulus in the 90-degree direction was 100 GPa or more, so that the contact force at the level expected from the sample shape and the deflection condition was obtained. It was.

(合金E)
合金Eは、合金成分として、3.0%Ti、0.05%Mg、0.1%Mn及び0.1%Moを含有し、残部が銅及び不可避的不純物から構成される。また、圧延2と歪取り焼鈍が行われている。
発明例E−1では、ヤング率が規定を満たしたため、たわみ1回後及び5000回後とも、へたりが検出されなかった。
比較例E−1では、軽圧延の加工度が7%に満たず、90度方向のヤング率が120GPaを超えたため、一回のたわみでへたりが生じた。
発明例E−1、比較例E−1とも、90度方向のヤング率が100GPa以上となったため、試料形状及びたわみ条件から期待されるレベルの接触力が得られた。
比較例E−2では、予備焼鈍の昇温速度が非常に小さかった。このため、45度方向のヤング率が140GPaを超えて5000回のたわみでへたりが発生した。さらに、90度方向のヤング率が100GPa未満となり、接触力が発明例E−1及び比較例E−1の半分以下まで低下した。
(Alloy E)
Alloy E contains 3.0% Ti, 0.05% Mg, 0.1% Mn, and 0.1% Mo as alloy components, and the balance is composed of copper and inevitable impurities. Further, rolling 2 and strain relief annealing are performed.
In Invention Example E-1, since the Young's modulus satisfied the regulation, no sag was detected after one deflection and after 5,000 deflections.
In Comparative Example E-1, the degree of work in light rolling was less than 7%, and the Young's modulus in the 90-degree direction exceeded 120 GPa, so that sag occurred with a single deflection.
In both Invention Example E-1 and Comparative Example E-1, the Young's modulus in the 90-degree direction was 100 GPa or more, so that the contact force at the level expected from the sample shape and deflection conditions was obtained.
In Comparative Example E-2, the temperature increase rate of the preliminary annealing was very small. For this reason, the Young's modulus in the 45 degree direction exceeded 140 GPa, and sag occurred after 5000 times of deflection. Furthermore, the Young's modulus in the 90-degree direction was less than 100 GPa, and the contact force decreased to less than half that of Invention Example E-1 and Comparative Example E-1.

(合金F)
合金Fは、合金成分として、2.2%Ti、0.05%Pおよび0.05%Bを含有し、残部が銅及び不可避的不純物から構成される。また、圧延2が行われている。
発明例F−1では、ヤング率が規定を満たしたため、たわみ1回後及び5000回後とも、へたりが検出されなかった。
比較例F−1では、予備焼鈍の昇温速度が非常に大きかったため、45度方向のヤング率が140GPaを超えると同時に、90度方向のヤング率が120GPaを超えた。その結果、1回のたわみでへたりが生じ、このへたりが5000回のたわみで増大した。
なお、発明例F−1、比較例F−1とも、90度方向のヤング率が100GPa以上となったため、試料形状及びたわみ条件から期待されるレベルの接触力が得られた。
(Alloy F)
Alloy F contains 2.2% Ti, 0.05% P and 0.05% B as alloy components, and the balance is composed of copper and inevitable impurities. Further, rolling 2 is performed.
In Invention Example F-1, because the Young's modulus satisfied the regulation, no sag was detected after one deflection and after 5,000 deflections.
In Comparative Example F-1, since the temperature increase rate of the pre-annealing was very large, the Young's modulus in the 45 degree direction exceeded 140 GPa, and at the same time, the Young's modulus in the 90 degree direction exceeded 120 GPa. As a result, sag occurred with one deflection, and this sag increased with 5000 deflections.
In addition, since the Young's modulus in the 90-degree direction was 100 GPa or more in both Invention Example F-1 and Comparative Example F-1, a contact force at a level expected from the sample shape and deflection conditions was obtained.

Claims (7)

1.5〜5.0質量%のTiを含有し、残部が銅及び不可避的不純物からなり、90度方向(度は銅箔の圧延平面における圧延方向と成す角度、以下同様)のヤング率(曲げたわみ係数)が100〜120GPaであり、45度方向のヤング率(曲げたわみ係数)が140GPa以下であるチタン銅。   It contains 1.5 to 5.0 mass% of Ti, the balance is made of copper and unavoidable impurities, and the Young's modulus in the direction of 90 degrees (degree is the angle formed with the rolling direction in the rolling plane of the copper foil, the same applies hereinafter) Titanium copper having a bending deflection coefficient) of 100 to 120 GPa and a Young's modulus (bending deflection coefficient) in the 45 degree direction of 140 GPa or less. 1.5〜5.0質量%のTiを含有し、残部が銅及び不可避的不純物からなり、90度方向のヤング率(曲げたわみ係数)が111〜120GPaであり、45度方向のヤング率(曲げたわみ係数)が111〜140GPaである請求項1に記載のチタン銅。   It contains 1.5 to 5.0% by mass of Ti, the balance is made of copper and inevitable impurities, the Young's modulus in the 90 degree direction (bending deflection coefficient) is 111 to 120 GPa, and the Young's modulus in the 45 degree direction ( Titanium copper according to claim 1, wherein the bending deflection coefficient is 111 to 140 GPa. Ag、B、Co、Cr、Fe、Mg、Mn、Mo、Ni、P、Si及びZrのうち1種以上を総量で0.005〜1.0質量%含有する請求項1又は2に記載のチタン銅。   The content of 0.005 to 1.0 mass% in total of one or more of Ag, B, Co, Cr, Fe, Mg, Mn, Mo, Ni, P, Si, and Zr, according to claim 1 or 2. Titanium copper. 1.5〜5.0質量%のTiを含有し、残部が銅及び不可避的不純物からなるインゴットを作製し、前記インゴットを、800〜1000℃で厚み5〜20mmまで熱間圧延した後、加工度30〜99%の冷間圧延を行い、400〜500℃の平均昇温速度を1〜50℃/秒として500〜650℃の温度帯に5〜80秒間保持することにより軟化度0.25〜0.75の予備焼鈍を施し、加工度7〜50%の冷間圧延を行い、次いで、700〜900℃で5〜300秒間の溶体化処理、加工度1〜60%の冷間圧延、350〜550℃で2〜20時間の時効処理、加工度1〜50%の冷間圧延、300〜700℃で5秒〜10時間の任意に行う歪取り焼鈍をこの順で行う方法であり、
前記軟化度が次式のSで示される、請求項1に記載のチタン銅の製造方法:
S=(σ0−σ)/(σ0−σ900
ここで、σ0は予備焼鈍前の引張強さであり、σ及びσ900はそれぞれ予備焼鈍後及び900℃で焼鈍後の引張強さである。
An ingot containing 1.5 to 5.0% by mass of Ti and the balance being made of copper and inevitable impurities was manufactured, and the ingot was hot rolled to a thickness of 5 to 20 mm at 800 to 1000 ° C., and then processed. The degree of softening is 0.25 by performing cold rolling at a temperature of 30 to 99% and holding the temperature in the temperature range of 500 to 650 ° C. for 5 to 80 seconds with an average temperature increase rate of 400 to 500 ° C. being 1 to 50 ° C./second. ˜0.75 pre-annealing, cold rolling with a working degree of 7 to 50%, then solution treatment at 700 to 900 ° C. for 5 to 300 seconds, cold rolling with a working degree of 1 to 60%, It is a method of performing aging treatment for 2 to 20 hours at 350 to 550 ° C., cold rolling at a working degree of 1 to 50%, and strain relief annealing arbitrarily performed at 300 to 700 ° C. for 5 seconds to 10 hours in this order,
The method for producing titanium copper according to claim 1, wherein the degree of softening is represented by S of the following formula:
S = (σ 0 −σ) / (σ 0 −σ 900 )
Here, σ 0 is the tensile strength before pre-annealing, and σ and σ 900 are the tensile strength after pre-annealing and after annealing at 900 ° C., respectively.
前記インゴットがAg、B、Co、Cr、Fe、Mg、Mn、Mo、Ni、P、Si及びZrのうち1種以上を総量で0.005〜1.0質量%含有する請求項4に記載のチタン銅の製造方法。   5. The ingot according to claim 4, wherein the ingot contains 0.005 to 1.0 mass% in total of one or more of Ag, B, Co, Cr, Fe, Mg, Mn, Mo, Ni, P, Si, and Zr. Manufacturing method of titanium copper. 請求項1〜3のいずれかに記載のチタン銅を備えた伸銅品。   The copper-stretched article provided with the titanium copper in any one of Claims 1-3. 請求項1〜3のいずれかに記載のチタン銅を備えた電子機器部品。   The electronic device component provided with the titanium copper in any one of Claims 1-3.
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