JPH07211143A - Low thermal expansion and high strength conductor for transmission line, and low loosening cable using same - Google Patents
Low thermal expansion and high strength conductor for transmission line, and low loosening cable using sameInfo
- Publication number
- JPH07211143A JPH07211143A JP589894A JP589894A JPH07211143A JP H07211143 A JPH07211143 A JP H07211143A JP 589894 A JP589894 A JP 589894A JP 589894 A JP589894 A JP 589894A JP H07211143 A JPH07211143 A JP H07211143A
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- JP
- Japan
- Prior art keywords
- less
- core wire
- transmission line
- low
- thermal expansion
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- Non-Insulated Conductors (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、特に既設送電線路の増
容量化に有効な低弛度電線及びこの電線の芯線に用いら
れる送電線用低熱膨張高強度芯線に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a low-slackness electric wire, which is particularly effective for increasing the capacity of an existing transmission line, and a low-thermal-expansion high-strength core wire for a transmission line used as a core wire of the electric wire.
【０００２】[0002]
【従来の技術】一般に、架空送電線用ＡＣＳＲ（鋼心ア
ルミ撚線）は芯線の周囲に、アルミ撚線を導体として撚
り合せてなるものであり、その送電容量は導体の断面積
に比例して増加する。そのため、架空送電線用ＡＣＳＲ
の外径が一定条件の下でその送電容量を増加させると、
その送電容量の増加に反比例して芯線が小径化するた
め、張力によってこれが伸びて架線時の弛度増大を招く
こととなる。また、この芯線を小径化させることなく、
このアルミ導体を耐熱性に優れたアルミ合金に代えるこ
とで送電容量を増やす方法も提案されているが、この方
法では芯線が送電時の温度上昇によって熱膨張して電線
伸びを招き、やはり弛度増大を防止することができな
い。従って、架空送電線用ＡＣＳＲの外径が一定の場
合、弛度増大を招くことなく送電容量を増大させるため
には、引張強度が高く、かつ線膨張係数の小さい芯線が
要求される。2. Description of the Related Art Generally, an overhead transmission line ACSR (steel core aluminum stranded wire) is formed by twisting an aluminum stranded wire as a conductor around a core wire, and its transmission capacity is proportional to the cross-sectional area of the conductor. Increase. Therefore, ACSR for overhead power transmission lines
If the outer diameter of the power transmission capacity increases under certain conditions,
Since the diameter of the core wire is reduced in inverse proportion to the increase in the power transmission capacity, the core wire is elongated by the tension, which causes an increase in slackness during overhead wire. Also, without reducing the diameter of this core wire,
A method has been proposed to increase the power transmission capacity by replacing the aluminum conductor with an aluminum alloy that has excellent heat resistance, but in this method, the core wire thermally expands due to the temperature rise during power transmission, which causes the wire to stretch, and the sag The increase cannot be prevented. Therefore, in the case where the outer diameter of the overhead power transmission line ACSR is constant, a core wire having a high tensile strength and a small linear expansion coefficient is required in order to increase the power transmission capacity without increasing the sag.
【０００３】このようなことから、線膨張係数の小さい
インバーを芯線として用いたインバーＡＣＳＲが開発さ
れ、既に一部実用化されている。例えば、このインバー
ＡＣＳＲとして、特公昭５７−１７９４２号（以下、従
来例１という）では１２０ｋｇｆ／ｍｍ2 以上の引張強
さを有するＡＣＳＲ用低膨張合金が、また、特公昭５７
−５６１６４号（以下、従来例２という）では線膨張係
数２×１０-5から６×１０-5／℃のＦｅ−Ｎｉ系のオー
ステナイト単相の合金線が提案されている。In view of the above, an Invar ACSR using an Invar having a small coefficient of linear expansion as a core wire has been developed and has been partially put into practical use. For example, as this Invar ACSR, in JP-B-57-17942 (hereinafter referred to as Conventional Example 1), a low expansion alloy for ACSR having a tensile strength of 120 kgf / mm 2 or more is also disclosed.
No. 56164 (hereinafter referred to as Conventional Example 2) proposes an Fe—Ni-based austenite single-phase alloy wire having a linear expansion coefficient of 2 × 10 −5 to 6 × 10 −5 / ° C.
【０００４】具体的に説明すると、従来例１は、実用面
では亜鉛メッキ後の引張強さが１０５から１１０ｋｇｆ
／ｍｍ2 以上の亜鉛メッキインバ線を芯線とし、その上
に丸形の超耐熱アルミ合金（ＺＴＡＬ）を導体として撚
り合せた亜鉛メッキインバ芯超耐熱アルミ合金撚り線
（ＺＴＡＣＩＲ）が従来のＡＣＳＲ１２０ｍｍ2 から１
５２０ｍｍ2 と同一構成で検討されており、一部サイズ
では実線路に使用されている。一方、従来例２は、アル
ミ被覆後の引張強さが９５から１０５ｋｇｆ／ｍｍ2 以
上のアルミ被覆インバ線を芯線とし、その上に扇形の圧
縮形特別耐熱アルミ合金線（ＸＴＡＬ）を導体として撚
り合せたアルミ被覆インバ心特別耐熱アルミ合金撚り線
（ＸＴＡＣＩＲ）であり、特に、このＸＴＡＣＩＲでは
既設線路の電線の張り替えを行う場合、電線の外径・撚
り線の引張荷重を従来電線と同等にするために、アルミ
被覆インバ線を太いサイズ化して引張荷重を確保し、Ｘ
ＴＡＬを扇形にすることで撚り線外径の増加を防いでい
る。More specifically, in the conventional example 1, the tensile strength after galvanizing is 105 to 110 kgf in practical use.
/ Mm 2 or more zinc Mekkiinba line to the core wire and, moreover zinc round super heat resistant aluminum alloy (ZTAL) twisted as conductor Mekkiinba core super heat resistant aluminum alloy stranded wire (ZTACIR) from conventional ACSR120mm 2 to 1
It has been studied with the same structure as 520 mm 2, and is used for an actual line in some sizes. On the other hand, in Conventional Example 2, an aluminum-coated invar wire having a tensile strength after aluminum coating of 95 to 105 kgf / mm 2 or more is used as a core wire, and a fan-shaped compression-type special heat-resistant aluminum alloy wire (XTAL) is twisted as a conductor on the core wire. Combined aluminum coated Invar core special heat resistant aluminum alloy stranded wire (XTACIR). Especially, in this XTACIR, when replacing the wire of the existing line, the outer diameter of the wire and the tensile load of the stranded wire are made equal to those of the conventional wire. In order to secure the tensile load by increasing the size of the aluminum-coated Invar wire,
By making the TAL fan-shaped, an increase in the outer diameter of the stranded wire is prevented.
【０００５】[0005]
【発明が解決しようとする課題】ところで、従来例１に
示されている送電線用低弛度電線では亜鉛メッキ後で芯
線の引張強さが１０５から１１０ｋｇｆ／ｍｍ2 アルミ
被覆後で９５から１１０ｋｇｆ／ｍｍ2 以上と一般にＡ
ＣＳＲに使用されている芯線の引張強さ（亜鉛メッキも
しくはアルミ被覆後で１２５から１３５ｋｇｆ／ｍ
ｍ2 ）に較べ強さが劣る。そのため、このＺＴＡＣＩＲ
構成品では撚り線の引張荷重が既設線より小さくなり、
安全率に余裕のない線路では電線の最大使用張力を既設
線の最大使用張力より小さくする必要があり、その結果
本構成電線の特長である低弛度特性が芯線の引張強さの
低下と相殺され、失われてしまう。By the way, in the low-slackness electric wire for power transmission line shown in Conventional Example 1, the tensile strength of the core wire after galvanizing is 105 to 110 kgf / mm 2 and the tensile strength of the core wire is 95 to 110 kgf after aluminum coating. / Mm 2 or more and generally A
Tensile strength of core wire used in CSR (125 to 135 kgf / m after galvanizing or aluminum coating)
The strength is inferior to that of m 2 ). Therefore, this ZTACIR
In the component, the tensile load of the stranded wire is smaller than that of the existing wire,
In a line with no margin of safety factor, it is necessary to make the maximum working tension of the wire smaller than the maximum working tension of the existing wire.As a result, the low slackness characteristic of this constituent wire offsets the decrease in the tensile strength of the core wire. Will be lost.
【０００６】一方、従来例２に示されているＸＴＡＣＩ
Ｒ構成の送電線用低弛度電線では、従来例１に示されて
いる撚り線の引張荷重の低下をインバ心の素線系を太く
することで防いでいるが、既設線の張り替えに当って
は、風圧荷重の増加を防ぐため、電線の外径を既設線と
同等にしなければならないため、電線の外径を既設線と
同じに押え、なおかつインバ心部を大きくしても導体部
であるアルミ合金の断面積を確保するため、アルミ合金
を扇形にし、断面に対する占積率を増やしている。この
場合において、撚り線層数の多い比較的太いサイズの撚
り線では、導体部アルミ合金部の断面積の絶対値が大き
いので、占積率が増えることで既設線なみの導体部断面
積を取り戻すことが可能となるが、この扇形のアルミ合
金を製造することは、導体材の伸線時にそのサイズ専用
の伸線ダイスを使用せねばならず、その上、伸線機も工
業的によく使用される、複数個の伸線ダイスを並び、各
ダイスの間に芯線材を貯める釜を配置したタイプのもの
が使用できないため、製造コストが高くなってしまう欠
点がある。さらに、より線層数が少ない細いサイズの電
線では、導体部の断面積の絶対値が少ないのでこの方法
での断面積の回復が非常に難しい。特に、アルミ部が１
５本、鋼心部が４本の構成の電線（小サイズＡＣＳＲ）
では、扇型導体を用いることによるアルミ導体断面積の
増加の程度が小さく、希望値を下回るためこの方法が取
れないので、アルミ被覆鋼または亜鉛メッキ鋼を用いた
既設線と等価の電線が製造できないという問題がある。On the other hand, the XTACI shown in Conventional Example 2
In the low-slackness electric wire for the transmission line of the R configuration, the decrease in the tensile load of the stranded wire shown in Conventional Example 1 is prevented by thickening the wire system of the Invar core, but it is necessary to replace the existing wire. In order to prevent an increase in wind pressure load, the outer diameter of the wire must be made equal to that of the existing wire.Therefore, even if the outer diameter of the wire is kept the same as that of the existing wire, and even if the invar core is enlarged, In order to secure the cross-sectional area of an aluminum alloy, the aluminum alloy is fan-shaped to increase the space factor for the cross section. In this case, for a relatively thick stranded wire with a large number of stranded wire layers, the absolute value of the cross-sectional area of the conductor aluminum alloy is large, so the space factor increases and the cross-sectional area of the conductor similar to that of the existing wire is increased. Although it is possible to recover it, the production of this fan-shaped aluminum alloy requires the use of a wire-drawing die for that size when drawing the conductor material. Since it is impossible to use a type in which a plurality of wire drawing dies are arranged and a pot for storing the core wire material is arranged between the dies, there is a drawback that the manufacturing cost becomes high. Furthermore, in the case of a thin electric wire having a smaller number of wire layers, it is very difficult to recover the cross-sectional area by this method because the absolute value of the cross-sectional area of the conductor portion is small. Especially, the aluminum part is 1
Electric wire with 5 wires and 4 steel cores (small size ACSR)
In this case, since the degree of increase in the aluminum conductor cross-sectional area due to the use of the fan-shaped conductor is small and it is less than the desired value, this method cannot be taken.Therefore, an electric wire equivalent to the existing wire using aluminum-coated steel or galvanized steel is manufactured. There is a problem that you cannot do it.
【０００７】以上の問題点は、いずれも電線の芯線が通
常のＡＣＳＲ系電線に用いる芯線よりも引張強さが低い
ことに起因するものである。これは、金属学的には、オ
ーステナイト単層組織の加工硬化能には、延性とのバラ
ンスの上で限界があることを示している。All of the above problems are due to the fact that the core wire of the electric wire has a lower tensile strength than the core wire used for a normal ACSR type electric wire. This indicates that metallurgically, the work hardening ability of the austenite single layer structure has a limit in terms of balance with ductility.
【０００８】また、降雪の予想される地域では、電線に
難着雪対策を施す必要があり、国内では多くの場合難着
雪リングを取付けている。これは雪が電線のより目に沿
って滑りながら筒雪になるのを、リングにより雪の滑り
を止めるものである。ここで、ＸＴＡＣＩＲ構成の電線
では、電線表面に雪が沿う程のより目がないため、難着
雪リングによる難着雪化ができない。Further, in areas where snowfall is expected, it is necessary to take measures against snowfall on electric wires, and in many cases, snowfall rings are attached in Japan. This is to prevent the snow from slipping along the eyes of the electric wire to become snow-covered snow, while the ring prevents the snow from sliding. Here, in the electric wire of the XTACIR configuration, since the surface of the electric wire has less eyes so that the snow is along the surface of the electric wire, the snow-hardening ring cannot make it hard to snow.
【０００９】さらに、従来の低弛度電線は、送電線用低
熱膨張芯線のキュリー点が２３０℃前後にあり、２３０
℃を境として熱膨張係数が急激に大きくなる特性をもっ
ている。そのために、ＸＴＡＣＩＲ構成の電線の導体に
用いられる特別耐熱合金線（ＸＴＡｌ）が３１０℃まで
の短時間耐熱性を有しているにもかかわらず、ＸＴＡＣ
ＩＲの短時間許容温度は運用上２９０℃に設計されてお
り、３１０℃までの熱膨張係数が従来の送電線用低膨張
芯線によりも低い低膨張芯線が求められている。この２
０℃の高温化が約５％の送電容量の増加になり、大変重
要なものである。ただし、Ｚｎメッキを施した送電線用
低膨張芯線の場合は、Ｚｎの耐熱温度が２４０℃である
ために、このような高温域での熱膨張係数の低下は意味
をなさず、Ａｌ被覆送電用低熱膨張芯線においてその効
果が発揮される。Further, in the conventional low sag wire, the Curie point of the low thermal expansion core wire for power transmission line is around 230 ° C.
It has the characteristic that the coefficient of thermal expansion rapidly increases at a temperature of ℃. Therefore, even though the special heat-resistant alloy wire (XTAl) used for the conductor of the XTACIR-structured wire has heat resistance up to 310 ° C for a short time, XTAC
The short-time allowable temperature of IR is designed to be 290 ° C. in operation, and a low expansion core wire having a coefficient of thermal expansion up to 310 ° C. lower than that of the conventional low expansion core wire for a transmission line is required. This 2
A high temperature of 0 ° C is a very important factor, as it increases the transmission capacity by about 5%. However, in the case of a Zn-plated low-expansion core wire for a power transmission line, since the heat-resistant temperature of Zn is 240 ° C., such a decrease in the thermal expansion coefficient in a high temperature range does not make sense, and Al-coated power transmission The effect is exhibited in the low thermal expansion core wire for use.
【００１０】そこで、本発明はこれら従来技術の問題点
を有効に解決するために案出されたものであり、その目
的は、従来の送電用低膨張芯線の高強度化と、さらに加
えて３１０℃までの低熱膨張化を図ることのできる新規
な送電線用低熱膨張高強度芯線及び、この送電線用低熱
膨張高強度芯線を用いて、既設線の外径を保ちつつ送電
容量の増大化を図ることができる新規な低弛度電線を提
供することである。Therefore, the present invention has been devised in order to effectively solve the problems of these conventional techniques, and its purpose is to increase the strength of the conventional low expansion core wire for power transmission, and in addition, 310 By using a new low-thermal-expansion high-strength core wire for transmission lines that can achieve low thermal expansion up to ℃, and this low-thermal-expansion high-strength core wire for transmission lines, the transmission capacity can be increased while maintaining the outer diameter of the existing wire. It is to provide a novel low sag wire that can be achieved.
【００１１】[0011]
【課題を解決するための手段】上記目的を達成するため
に、本発明者らは、Ｆｅ−Ｃｏ−Ｎｉ系合金に種々の合
金元素を添加した組成の合金の熱間圧延素材を用い、さ
らに冷間加工とＡｌ被覆またはＺｎメッキした状態の合
金線について引張特性、熱膨張係数、捻回特性および巻
付・巻戻し特性の調査を行った。ここで、捻回特性と
は、電線の撚り線作業の性能を評価するものであり、そ
の評価手段として、線材の一端を固定して他端をねじる
捻回試験を実施し、その破断に至る迄の回数を捻回値と
して測定するものである。また、巻付・巻戻し特性と
は、線材の曲げ加工性を評価するものであり、その評価
手法として、試験線材を自己径の１．５倍から２．０倍
程度の芯材に８回巻付けを行い、さらに同回数だけ巻戻
して線材の破断の有無を確認し性能を評価するものであ
る。そして、これらの評価の結果、従来のＦｅ−Ｎｉ系
低弛度送電用芯材ではオーステナイト相が強度の冷間加
工を加えても安定なため、加工硬化能に限界があり、Ａ
ＣＳＲ用鋼心材並の高強度を得ることができないことが
わかった。そこで、本発明が目的とするレベルの高強度
の低熱膨張芯線材を得るためには、強度の冷間加工によ
ってオーステナイト相の一部がマルテンサイト相に変態
するような合金組成を選び、さらにその時の冷間加工前
の合金組成が、もっとも低熱膨張係数が得られる組成に
最適化しておくことで、高強度と低熱膨張特性の両方が
可能であることを見出した。特に、このような加工誘起
変態を有する送電用低弛度芯線が高強度と低熱膨張特性
を両立するためには、Ｃは０．０６〜０．５０％含み、
かつ、添付した図１の実線で囲んだＮｉとＣｏを含む領
域において、残部の主な成分がＦｅからなる組成とする
ことで達成できる。In order to achieve the above object, the present inventors have used a hot-rolled material of an alloy having a composition in which various alloy elements are added to a Fe-Co-Ni-based alloy, and further, The tensile properties, the coefficient of thermal expansion, the twisting properties, and the winding / unwinding properties of the alloy wire in the state of cold working and Al coating or Zn plating were investigated. Here, the twisting characteristic is to evaluate the performance of the twisting operation of the electric wire, and as its evaluation means, a twisting test is carried out in which one end of the wire is fixed and the other end is twisted, which leads to its breakage. The number of times up to this is measured as a twist value. The wrapping / unwinding characteristics are used to evaluate the bending workability of a wire rod. As an evaluation method, a test wire rod is applied to a core wire having a diameter 1.5 times to 2.0 times the core diameter 8 times. The performance is evaluated by winding the wire and then rewinding the wire the same number of times to confirm whether or not the wire is broken. As a result of these evaluations, in the conventional Fe-Ni-based low-sagging power transmission core material, the austenite phase is stable even when subjected to high-strength cold working, so that there is a limit in work hardening ability.
It was found that it is not possible to obtain high strength comparable to that of steel core material for CSR. Therefore, in order to obtain a high-strength low-thermal-expansion core wire of a target level of the present invention, an alloy composition in which a part of the austenite phase is transformed into a martensite phase by the strength cold working is selected, and at that time. It was found that both the high strength and the low thermal expansion characteristics are possible by optimizing the alloy composition before cold working of the composition to the composition that gives the lowest thermal expansion coefficient. In particular, in order for the low sag core wire for power transmission having such a work-induced transformation to have both high strength and low thermal expansion characteristics, C is contained in an amount of 0.06 to 0.50%,
In addition, it can be achieved by using a composition in which the main component of the balance is Fe in the region containing Ni and Co surrounded by the solid line in FIG. 1 attached.
【００１２】より具体的には、主な合金組成としてＣを
０．０６〜０．５０％を含み、かつ図１の破線の枠で囲
んだ領域に示すようにＮｉとＣｏの関係を比例関係で結
ぶ領域と、ＮｉとＣｒ＋０．５４Ｍｏ＋０．２８Ｗの関
係を比例関係で結ぶ領域を共に満たす領域内でこれにＦ
ｅを加えた組成を主たる成分とすることで、より一層オ
ーステナイト相の加工硬化と加工誘起マルテンサイトの
強度向上を図ることができ、この組成にＡｌ被覆または
Ｚｎメッキ処理を施し、耐食性を加味することによっ
て、目的とするレベルの送電線用低熱膨張高強度芯線が
得られることがわかった。さらに、一部の組成の芯線
は、高強度化に加えて、従来の芯材では得られなかった
３１０℃までの低熱膨張化も達成できることがわかっ
た。More specifically, the main alloy composition contains C of 0.06 to 0.50%, and the relationship between Ni and Co is proportional as shown in the area surrounded by a broken line in FIG. F in the region that connects both the region connected by and the region connecting Ni and Cr + 0.54Mo + 0.28W in a proportional relationship
By using the composition containing e as the main component, it is possible to further improve the work hardening of the austenite phase and the improvement of the strength of the work-induced martensite. The composition is subjected to Al coating or Zn plating to add corrosion resistance. As a result, it was found that the desired level of low thermal expansion and high strength core wire for transmission line can be obtained. Further, it has been found that the core wire having a part of the composition can achieve not only high strength but also low thermal expansion up to 310 ° C., which cannot be obtained by the conventional core material.
【００１３】また、この送電線用低熱膨張高強度芯線を
用いれば、既設線の外径を保ちつつ増容量化を図ること
ができる低弛度送電線を提供することが可能となり、さ
らにはこの送電線を用いて従来の低弛度送電線では得ら
れなかった短時間最大使用温度が３１０℃まで使用可能
な低弛度送電線を提供できることが明らかになった。Further, by using this low thermal expansion high strength core wire for a power transmission line, it becomes possible to provide a low sag power transmission line capable of increasing the capacity while maintaining the outer diameter of the existing wire. It has been revealed that the transmission line can be used to provide a low-sag transmission line that can be used up to a maximum operating temperature of 310 ° C. for a short time, which cannot be obtained by the conventional low-sag transmission line.
【００１４】従って、本発明はＦｅ−Ｃｏ−Ｎｉ系合金
からなる、少なくともオーステナイト相と加工誘起マル
テンサイト相との２相を有する合金の表面にＡｌ被覆を
施すことで、Ａｌ被覆芯線の常温の引張強さは、１３０
ｋｇｆ／ｍｍ2 以上、場合によっては１３５ｋｇｆ／ｍ
ｍ2 以上の高強度を発揮することができる。また、常温
から３１０℃までの平均熱膨張係数は６×１０-6／℃以
下であり、さらに自己径の１００倍の掴み間隔で捻った
時の捻回値が１５回以上および自己径の１．５倍の径の
軸棒に８回巻き付け後、８回巻戻しても破断を生じない
ことがわかった。また、このＡｌ被覆量は、線材の横断
面積の３０％以下であり、好適な範囲は１３〜２２％で
ある。Therefore, according to the present invention, by coating the surface of an alloy composed of an Fe-Co-Ni-based alloy having at least two phases of an austenite phase and a work-induced martensite phase with Al, the temperature of the Al-coated core wire at room temperature can be improved. Tensile strength is 130
kgf / mm 2 or more, 135 kgf / m in some cases
It can exhibit high strength of m 2 or more. Further, the average coefficient of thermal expansion from room temperature to 310 ° C. is 6 × 10 −6 / ° C. or less, and the twisting value when twisted at a gripping interval 100 times the self diameter is 15 times or more and the self diameter is 1 It was found that even if the shaft rod having a diameter of 5 times was wound 8 times and then rewound 8 times, no breakage occurred. Further, the Al coating amount is 30% or less of the cross-sectional area of the wire, and a suitable range is 13 to 22%.
【００１５】また、このＡｌ被覆に代えてＺｎメッキを
施しても同様な効果が得られる。すなわち、このメッキ
芯線の常温の引張強さは１３０ｋｇｆ／ｍｍ2 以上であ
り、より高強度を図ったものは１３５ｋｇｆ／ｍｍ2 以
上を発揮する。また、常温から２４０℃までの平均熱膨
張係数は６×１０-6／℃以下であり、さらに自己径の１
００倍の掴み間隔で捻った時の捻回値が１５回以上およ
び自己径の１．５倍の径の軸棒に８回巻き付け後、８回
巻戻しても破断を生じない。そして、この十分な耐食性
を得るためにはこのＺｎのメッキ量は２１５ｇ／ｍ2 以
上であることが望ましい。The same effect can be obtained by applying Zn plating instead of this Al coating. That is, the tensile strength at room temperature of this plated core wire is 130 kgf / mm 2 or more, and the one with higher strength exhibits 135 kgf / mm 2 or more. In addition, the average coefficient of thermal expansion from room temperature to 240 ° C is 6 × 10 -6 / ° C or less, and more than 1 of the self-diameter.
A twist value when twisted at a gripping interval of 00 times is 15 times or more, and after being wound 8 times around a shaft rod having a diameter 1.5 times the self diameter, no breakage occurs even when rewound 8 times. In order to obtain this sufficient corrosion resistance, it is desirable that the Zn plating amount be 215 g / m 2 or more.
【００１６】また、本発明に用いられるＦｅ−Ｃｏ−Ｎ
ｉ系合金の組成は、重量％でＣ０．０６〜０．５０％を
含み、Ｃｏ６５％以下、０またはＮｉ３０％未満の１種
または２種をＣｏ＋Ｎｉで２５〜６５％含有し、残部が
Ｆｅを主体とするものである。さらに詳しくは、重量％
でＣ０．０６〜０．５０％、Ｓｉ１．５％以下、Ｍｎ３
％以下、Ｃｏ２〜６５％、Ｎｉ０％または２９．９％以
下で、ＣｏとＮｉの関係が５２−（５／３）Ｎｉ≦Ｃｏ
≦６５−（５／３）Ｎｉを満足し、またはさらに１１％
以下のＣｒと６％以下のＷと６％以下のＭｏの１種また
は２種以上を、５−（１／４）Ｎｉ≦Ｃｒ＋０．５４Ｍ
ｏ＋０．２８Ｗ≦１１−（１／４）Ｎｉを満足する範囲
で含有し、残部が実質的にＦｅからなる組成であり、さ
らに個々の元素および元素の組合せにはより好適な範囲
が存在する。また、上記組成を基本として、さらに適
時、Ｂ，Ｍｇ，Ｃａ，Ｖ，Ｔｉ，Ｎｂ，Ｈｆ，Ｚｒ，Ａ
ｌ，ＲＥＭを組合せて添加することができる。Further, Fe-Co-N used in the present invention
The composition of the i-based alloy contains 0.06 to 0.50% by weight of C, 65% or less of Co, 0 or less than 30% of Ni, and 25 to 65% of Co + Ni, with the balance being Fe. It is the subject. More specifically, weight%
C0.06-0.50%, Si1.5% or less, Mn3
% Or less, Co 2 to 65%, Ni 0% or 29.9% or less, and the relationship between Co and Ni is 52− (5/3) Ni ≦ Co
≤65- (5/3) Ni is satisfied, or even 11%
One or two or more of the following Cr, W of 6% or less and Mo of 6% or less is used as 5- (1/4) Ni ≦ Cr + 0.54M
The composition contains o + 0.28W ≦ 11− (1/4) Ni in a range satisfying Ni, and the balance substantially consists of Fe, and more preferable ranges exist for individual elements and combinations of elements. Further, based on the above composition, B, Mg, Ca, V, Ti, Nb, Hf, Zr, A
1, REM can be added in combination.
【００１７】また、この芯材に用いられるＦｅ−Ｃｏ−
Ｎｉ系合金中に含まれる加工誘起マルテンサイト相の量
は２〜３５％の範囲が望ましい。Fe-Co- used for this core material
The amount of work-induced martensite phase contained in the Ni-based alloy is preferably in the range of 2 to 35%.
【００１８】また、本発明の低弛度電線は上述したよう
に、このアルミ被覆またはＺｎメッキを施した高強度膨
張高強度芯線をそれぞれ１本ないし複数本撚り合わせて
芯材とし、この芯材のまわりに１層ないし複数層のアル
ミ合金を導体として撚り合せたものであり、アルミ被覆
を施した芯線を用いた送電線の一部は、短時間最大使用
温度で３１０℃まで、一方Ｚｎメッキを施した芯線とを
用いた送電線の一部は短時間最大使用温度が２４０℃ま
で実用化できる。As described above, the low-slackness electric wire of the present invention is formed by twisting one or more high-strength expanded high-strength core wires coated with aluminum or Zn to form a core material. One or more layers of aluminum alloy are twisted together as a conductor, and some of the transmission lines that use an aluminum-coated core wire are heated up to 310 ° C for a short time, while Zn plating is performed. The maximum operating temperature of a part of the power transmission line using the core wire subjected to the above can be practically used up to 240 ° C for a short time.
【００１９】[0019]
【作用】本発明の送電線用低熱膨張高強度芯線が最も特
徴とする点は、加工誘起マルテンサイト相を含有してい
ることである。The feature of the low-thermal-expansion high-strength core wire for a power transmission line of the present invention is that it contains a work-induced martensite phase.
【００２０】従来、送電線用低熱膨張高強度芯線として
提案されてきたＦｅ−Ｎｉ系またはＦｅ−Ｃｏ−Ｎｉ系
低熱膨張芯線は、強度や捻回特性などの改良を目的と
し、組成や製造方法に特色を有しているが、その組織は
いずれもオーステナイト相が大部分を占めることを特徴
とするものである。Ｆｅ−Ｃｏ−Ｎｉ系合金をベースと
するオーステナイト単相合金の加工硬化能は、オーステ
ナイト相＋加工誘起マルテンサイト相の加工硬化能に及
ばず、本発明が意図するレベルの高強度の送電線低熱膨
張芯線が得られなくなるため、本発明送電線用低熱膨張
高強度芯線の組織は、Ｆｅ−Ｃｏ−Ｎｉ系合金をベース
としてオーステナイト相＋加工誘起マルテンサイト相の
少なくとも２相を有する必要がある。The Fe-Ni-based or Fe-Co-Ni-based low thermal expansion core wire, which has been heretofore proposed as a low thermal expansion and high strength core wire for a transmission line, has a composition and a manufacturing method for the purpose of improving strength and twisting characteristics. However, all of the structures are characterized by the austenite phase occupying most of them. The work hardening ability of the austenite single phase alloy based on the Fe-Co-Ni alloy does not reach the work hardening ability of the austenite phase + work-induced martensite phase, and the high strength transmission line low heat of the level intended by the present invention. Since the expanded core wire cannot be obtained, the structure of the low thermal expansion high strength core wire for the transmission line of the present invention needs to have at least two phases of the austenite phase and the work induction martensite phase based on the Fe—Co—Ni alloy.
【００２１】このＦｅ−Ｃｏ−Ｎｉ系２相合金の表面に
耐食性と導電性に寄与するＡ１被覆を実施すると、従来
のインバーＡＣＳＲよりも高強度の送電線用芯線が得ら
れ、従来の高強度鋼線を用いたＡＣＳＲと構造変更なし
に代替することができる。さらに一部の組成のＦｅ−Ｃ
ｏ−Ｎｉ系２相合金を芯線に用いれば、高強度化と低熱
膨張化が同時に達成され、ＸＴＡＬの耐熱限界である３
１０℃まで使用が可能となる。その際のＡｌ被覆送電線
用芯材の常温引張強さは、１３０ｋｇｆ／ｍｍ2 以上、
常温から３１０℃までの平均熱膨張係数は６×１０-6以
下、自己径の１００倍の掴み間隔で捻じった時の捻回値
は、１５回以上および自己径の１．５倍の径の軸棒に８
回巻き付け後、８回巻戻しても破断しないことが必要で
ある。それぞれの数値が１つでも満足できないと送電線
用芯材として従来の高強度鋼線と構造変更なしに代替で
きないので、これらの特性はすべて同時に満足する必要
がある。より望ましい常温の引張強さは１３５ｋｇｆ／
ｍｍ2 以上、より望ましい常温から３１０℃までの平均
熱膨張係数は５×１０-6以下である。When the surface of this Fe-Co-Ni type two-phase alloy is coated with A1 which contributes to corrosion resistance and conductivity, a core wire for a transmission line having a strength higher than that of the conventional Invar ACSR is obtained, and the conventional high strength core wire is obtained. It can be replaced with ACSR using steel wire without structural modification. In addition, Fe-C with some composition
If an o-Ni two-phase alloy is used for the core wire, high strength and low thermal expansion can be achieved at the same time, which is the heat resistance limit of XTAL.
It can be used up to 10 ° C. At that time, the tensile strength at room temperature of the Al-coated power transmission line core is 130 kgf / mm 2 or more,
The average coefficient of thermal expansion from room temperature to 310 ° C is 6 × 10 -6 or less, and the twist value when twisted at a gripping interval 100 times the self diameter is 15 times or more and 1.5 times the self diameter. To the shaft rod of
It is necessary that it does not break even after rewinding eight times after winding. If even one of each numerical value cannot be satisfied, it cannot be replaced with the conventional high-strength steel wire as a core material for a transmission line without structural modification. Therefore, all these characteristics must be satisfied at the same time. More desirable tensile strength at room temperature is 135 kgf /
The average thermal expansion coefficient from mm 2 or more, more preferably from room temperature to 310 ° C., is 5 × 10 −6 or less.
【００２２】また、Ａｌ被覆率が増加すると芯線として
の強度が低下し、上記の引張強さを維持することが困難
となるため、Ａｌ被覆率については３０％以下に限定す
る。より望ましいＡ１被覆率は１３〜２２％の範囲であ
る。Further, as the Al coverage increases, the strength of the core wire decreases and it becomes difficult to maintain the above tensile strength. Therefore, the Al coverage is limited to 30% or less. A more desirable A1 coverage is in the range of 13 to 22%.
【００２３】また、Ｆｅ−Ｃｏ−Ｎｉ系２相合金の表面
にＺｎメッキを実施すると安価でかつ耐食性に優れた送
電線用低熱膨張高強度芯線が得られる。Ｚｎメッキの場
合は、Ｚｎの耐熱温度が２４０℃であるため、送電線用
芯線の耐熱限度は２４０℃に限定されるが、従来の高強
度鋼線を用いたＡＣＳＲと構造変更なしに代替すること
ができる。その際のＺｎメッキ送電線用芯線の常温引張
強さは、１３０ｋｇ／ｍｍ2 以上、常温から２４０℃ま
での平均熱膨張係数は６×１０-6以下、自己径の１００
倍の掴み間隔で捻じった時の捻回値は、１５回以上およ
び自己径の１．５倍の径の軸棒に８回巻き付け後、８回
巻戻しても破断しないことが必要である。それぞれの数
値が１つでも満足できないと送電線用芯材として従来の
高強度鋼線と構造変更なしに代替できないので、これら
の特性はすべて同時に満足する必要がある。より望まし
い常温の引張強さは１３５ｋｇｆ／ｍｍ2 以上である。
また、Ｚｎメッキ量は、安定した耐食性を得るために２
１５ｇ／ｍ2 以上とする。If the surface of the Fe-Co-Ni-based two-phase alloy is plated with Zn, a low-thermal expansion and high-strength core wire for a transmission line which is inexpensive and has excellent corrosion resistance can be obtained. In the case of Zn plating, since the heat resistant temperature of Zn is 240 ° C., the heat resistant limit of the core wire for power transmission lines is limited to 240 ° C. However, it is replaced with the conventional ACSR using high strength steel wire without changing the structure. be able to. At that time, the room-temperature tensile strength of the Zn-plated transmission wire core wire is 130 kg / mm 2 or more, the average thermal expansion coefficient from room temperature to 240 ° C. is 6 × 10 −6 or less, and the self-diameter is 100.
The twisting value when twisted at a double gripping interval must be 15 times or more and must not break even after being wound 8 times around a shaft rod having a diameter 1.5 times the self diameter. . If even one of each numerical value cannot be satisfied, it cannot be replaced with the conventional high-strength steel wire as a core material for a transmission line without structural modification. Therefore, all these characteristics must be satisfied at the same time. A more desirable tensile strength at room temperature is 135 kgf / mm 2 or more.
The Zn plating amount is 2 in order to obtain stable corrosion resistance.
It should be 15 g / m 2 or more.
【００２４】次に、本発明の送電線用低熱膨張高強度芯
線に適する化学組成範囲について成分限界理由を説明す
る。なお、表１は、本発明の成分範囲を示したものであ
る。Next, the reasons for the compositional limits of the chemical composition range suitable for the low thermal expansion and high strength core wire for the transmission line of the present invention will be explained. Table 1 shows the component range of the present invention.
【００２５】Ｃは、高強度低熱膨芯線の冷間加工時にオ
ーステナイト相の加工硬化と加工誘起マルテンサイトの
強度向上に最も寄与する元素で、本発明の送電線用低熱
膨張高強度芯線の製造方法において成分上最も特色ある
元素である。また、オーステナイト安定化元素としてＮ
ｉやＣｏの一部を置換することもできる。このような効
果を得るために、Ｃは、重量％で最低０．０６％を必要
とするが、逆に０．５０％を越えると、オーステナイト
相を過度に安定化させて、マルテンサイト変態を起こし
にくくするとともに、熱膨張係数の増加を招くことにな
る。従って、Ｃの添加量は、０．０６〜０．５０％に限
定する。より望ましい範囲は表１に示す通りである。C is an element that contributes most to the work hardening of the austenite phase and the improvement of the strength of the work-induced martensite during cold working of the high-strength, low-thermal-expansion core wire, and the method for producing the low-thermal-expansion and high-strength core wire for a transmission line of the present invention Is the most distinctive element in terms of composition. Further, N is used as an austenite stabilizing element.
It is also possible to replace part of i or Co. In order to obtain such an effect, C needs to be at least 0.06% by weight. On the contrary, if it exceeds 0.50%, the austenite phase is excessively stabilized and the martensitic transformation is caused. In addition to making it difficult to cause, it causes an increase in the coefficient of thermal expansion. Therefore, the addition amount of C is limited to 0.06 to 0.50%. The more desirable range is as shown in Table 1.
【００２６】Ｓｉ，Ｍｎは脱酸元素として本発明合金に
含まれる。ただし、過度のＳｉ，Ｍｎは熱膨張係数の増
加を招くため、それぞれ重量％で１．５％以下および３
％以下の添加にとどめる。より望ましい範囲は表１に示
す通りである。Si and Mn are included in the alloy of the present invention as deoxidizing elements. However, since excessive Si and Mn cause an increase in the coefficient of thermal expansion, the weight% is 1.5% or less and 3% or less, respectively.
% Or less. The more desirable range is as shown in Table 1.
【００２７】ＣｏとＮｉは、本発明の送電線用低熱膨張
高強度芯線において、残部を構成するＦｅとともに合金
にインバー特性を与えるのに必要な元素である。広い成
分範囲として、Ｃｏ６５％以下、Ｎｉ３０％未満の１種
または２種をＣｏ−Ｎｉで２５〜６５％の範囲にあれ
ば、Ｆｅ−Ｎｉ−Ｃｏ−Ｃ系またはＦｅ−Ｎｉ−Ｃｏ−
Ｃ系にさらにＳｉ，Ｍｎ，Ｃｒ，Ｗ，Ｍｏ，Ｂ，Ｍｇ，
Ｃａ等の元素が加わった合金系を選ぶことで、本発明の
製造方法により所望する加工誘起変態能をもつ送電線用
芯線が得られる。Co and Ni are elements necessary for imparting Invar characteristics to the alloy together with Fe constituting the balance in the low-thermal-expansion and high-strength core wire for a power transmission line of the present invention. As a wide component range, if one or two of Co 65% or less and Ni less than 30% is contained in the range of 25 to 65% in Co-Ni, Fe-Ni-Co-C system or Fe-Ni-Co- system.
C, Si, Mn, Cr, W, Mo, B, Mg,
By selecting an alloy system to which an element such as Ca is added, a transmission wire core wire having a desired work-induced transformation ability can be obtained by the manufacturing method of the present invention.
【００２８】さらに、ＮｉとＣｏの成分範囲は、図１の
（Ｎｉ，Ｃｏ）の関係が、（２９．９，２．２）（２
９．９，１５．２），（０．６５），（０．５２）の４
点で囲まれた枠内において、特に最適な低熱膨張特性と
高強度化の両立が可能である。本発明において好ましい
領域とその右上の領域Ａは、Ｃｏ−６５−（５／３）Ｎ
ｉの関係式で隔てられ、領域Ａの合金組成になると、オ
ーステナイト相が強度の冷間加工を加えてもかなり安定
になり、領域Ａの中でも最適な組成を選ぶことで、熱膨
張係数を十分に低めることができるが、引張強さが不十
分となる。一方本発明において好ましい領域とその左下
の領域Ｂは、Ｃｏ−５２−（５／３）Ｎｉの関係式で隔
てられ、領域Ｂの合金組成になると、オーステナイト相
がもはや冷間加工の前段階で常温で安定に存在しにく
く、マルテンサイト相が生成しやすくなるために、低熱
膨張特性が失われるようになる。従って、本発明合金の
ＮｉとＣｏは、図１の実線で囲まれた枠内に示すごと
く、Ｃｏ２〜６５％、Ｎｉ２９．９％以下で、さらに以
下のＮｉとＣｏの関係を満たす範囲内が望ましい。Further, regarding the component ranges of Ni and Co, the relationship of (Ni, Co) in FIG. 1 is (29.9, 2.2) (2
9.9, 15.2), (0.65), (0.52) 4
Within the frame surrounded by the dots, it is possible to achieve both a particularly optimal low thermal expansion property and high strength. In the present invention, the preferable region and the region A on the upper right side are Co-65- (5/3) N.
When the alloy composition of the region A is separated by the relational expression of i, the austenite phase becomes considerably stable even if strong cold working is applied, and by selecting the optimal composition in the region A, the thermal expansion coefficient can be made sufficient. However, the tensile strength becomes insufficient. On the other hand, in the present invention, the preferable region and the lower left region B are separated by the relational expression of Co-52- (5/3) Ni, and when the alloy composition of the region B is reached, the austenite phase is no longer in the pre-stage of cold working. Since it is difficult to stably exist at room temperature and a martensite phase is easily generated, the low thermal expansion property is lost. Therefore, the Ni and Co of the alloy of the present invention are, as shown in the frame surrounded by the solid line in FIG. 1, 2 to 65% of Co and 29.9% or less of Ni, and within the range satisfying the following relationship between Ni and Co. desirable.
【００２９】５２−（５／３）Ｎｉ≦Ｃｏ≦６５−（５
／３）Ｎｉ……（１） また、Ｎｉを無添加とした場合、Ｃｏの望ましい成分範
囲は重量％で５２〜６５％である。そして、より望まし
いＮｉとＣｏの範囲は表１に示す通りである。52- (5/3) Ni≤Co≤65- (5
/ 3) Ni (1) When Ni is not added, the desirable range of Co content is 52 to 65% by weight. The more desirable ranges of Ni and Co are shown in Table 1.
【００３０】[0030]
【表１】 [Table 1]
【００３１】Ｃｒ，ＭｏおよびＷは同族の元素であり、
ともに基地であるオーステナイト相を安定化させるとと
もに、固溶強化元素及び一部は炭化物の析出強化元素と
して基地の加工硬化能を高めるので、必要に応じて１種
または２種以上を添加できる。また、これらの元素は、
低地度送電線の使用最高温度である３００℃付近の高温
強度を高める作用をもつ。しかし、これらの元素はとも
に変移点を低下させる元素であるため、Ｃｒの場合は１
１％、Ｍｏの場合は６％およびＷの場合は６％を越える
と変移点が過度に低下して、２００℃〜３００℃間の熱
膨張係数が急激に高くなってしまうため、Ｃｒの上限を
１１％、Ｍｏの上限を６％、およびＷの上限を６％にそ
れぞれ限定する。また、これらの元素は固溶強化ならび
に析出強化元素として原子比で同様の働きをするため、
Ｃｒ＋０．５４Ｍｏ＋０．２８Ｗについても上、下限を
規定する必要がある。Cr, Mo and W are elements of the same group,
Both stabilize the austenite phase, which is the base, and enhance the work hardening ability of the base as a solid solution strengthening element and partly as a precipitation strengthening element of carbide, so one or more kinds can be added if necessary. Also, these elements are
It has the effect of increasing the high temperature strength around 300 ° C, which is the maximum operating temperature of lowland transmission lines. However, since these elements are elements that lower the transition point, in the case of Cr, it is 1
If it exceeds 1%, 6% in the case of Mo and 6% in the case of W, the transition point is excessively lowered and the coefficient of thermal expansion between 200 ° C. and 300 ° C. is rapidly increased. Is limited to 11%, the upper limit of Mo is limited to 6%, and the upper limit of W is limited to 6%. Further, since these elements act similarly as solid solution strengthening and precipitation strengthening elements in the atomic ratio,
Also for Cr + 0.54Mo + 0.28W, it is necessary to specify the upper and lower limits.
【００３２】本発明において好ましい領域とその右上の
領域Ｃは、Ｃｒ−０．５４Ｍｏ＋０．２８Ｗ＝１１−
（１／４）Ｎｉの関係式で隔てられ、領域Ｃの合金組成
になると、オーステナイト相が強度の冷間加工を加えて
もかなり安定になって十分な引張強さが得られなくなる
と同時に変移点が低下して熱膨張係数が高くなってしま
う。In the present invention, the preferable region and the region C on the upper right of the region are Cr-0.54Mo + 0.28W = 11-.
When the alloy composition of the region C is separated by the relational expression of (1/4) Ni, the austenite phase becomes considerably stable even if it is subjected to high-strength cold working, and sufficient tensile strength cannot be obtained at the same time. The points decrease and the coefficient of thermal expansion increases.
【００３３】一方、本発明において好ましい領域とその
左下の領域Ｄは、Ｃｒ＋０．５４Ｍｏ＋２．２８Ｗ＝５
−（１／４）Ｎｉの関係式で隔てられ、領域Ｄの合金組
成になると、オーステナイト相がもはや冷間加工の前段
階で常温で安定に存在しにくく、マルテンサイト相が生
成しやすくなるために、低熱膨張特性が失われるように
なる。従って、本発明合金のＮｉとＣｒ＋０．５４Ｍｏ
＋０．２８Ｗ量の関係は、図１の破線の枠内に示すごと
く、Ｃｏ２〜６５％、Ｎｉ２９．９％以下で、さらに以
下の関係を満たす範囲内が望ましい。On the other hand, in the present invention, the preferable region and the lower left region D are Cr + 0.54Mo + 2.28W = 5.
When the alloy composition in the region D is separated by the relational expression of-(1/4) Ni, the austenite phase is less likely to exist stably at room temperature before the cold working, and the martensite phase is easily generated. In addition, the low thermal expansion characteristics will be lost. Therefore, the alloys of the present invention Ni and Cr + 0.54Mo
The relationship of the +0.28 W amount is, as shown in the frame of the broken line in FIG. 1, Co2 to 65%, Ni 29.9% or less, and it is preferable that the following relationship be further satisfied.
【００３４】５−（１／４）Ｎｉ≦Ｃｒ＋０．５４Ｍｏ
＋０．２８Ｗ≦１１−（１／４）Ｎｉ……（２） Ｂはオーステナイト結晶粒界に偏析して粒界を強化し、
本発明合金の熱間加工性の改善や常温の延性改善に役立
つ。また、ＭｇやＣａは、Ｓと結びついて粒状の硫化物
をつくり、Ｂと同様、熱間加工性の改善や常温の延性改
善に役立つ。このような効果のために、Ｂ、Ｍｇおよび
Ｃａは１種または２種以上を同時に添加することができ
るが、いずれも０．０２％を越える過度の添加は、合金
の融点を下げて、逆に熱間加工性を低下させるのでＢ、
ＭｇおよびＣａはいずれも０．０００１〜０．０２％の
添加とする。5- (1/4) Ni≤Cr + 0.54Mo
+ 0.28W ≦ 11− (1/4) Ni (2) B segregates at the austenite grain boundaries to strengthen the grain boundaries,
It is useful for improving the hot workability of the alloy of the present invention and improving the ductility at room temperature. Further, Mg and Ca combine with S to form a granular sulfide, and like B, are useful for improving hot workability and improving ductility at room temperature. For these effects, B, Mg, and Ca can be added singly or in combination of two or more, but excessive addition exceeding 0.02% lowers the melting point of the alloy and adversely affects B reduces the hot workability,
Both Mg and Ca are added at 0.0001 to 0.02%.
【００３５】なお、Ｆｅ−Ｎｉ−Ｃｏ系合金を強化する
添加元素は上記したＣやＣｒ、Ｍｏ以外に種々考えられ
るが、Ｖ，Ｔｉ，Ｎｂ，Ｔａ，ＨｆおよびＺｒはＣとの
親和力が強く、塊状の硬い１次炭水化物を生成し、少量
の添加であれば強度向上に寄与するため、Ｖ，Ｔｉ，Ｎ
ｂ，Ｔａ，ＨｆおよびＺｒは１種または２種以上を複合
に添加することができる。しかし、過度の添加は冷間加
工時に欠陥をつくりやすく、引張延びの低下や捻回値の
ばらつきの原因となるため、これらの元素の添加量は合
計で１．０％以下に限定する。Various additive elements for strengthening the Fe-Ni-Co alloy can be considered in addition to C, Cr and Mo described above, but V, Ti, Nb, Ta, Hf and Zr have a strong affinity with C. , It produces hard primary carbohydrates in a lump form, and if added in a small amount, it contributes to the improvement of strength, so V, Ti, N
b, Ta, Hf and Zr can be added singly or in combination of two or more. However, excessive addition easily causes defects during cold working and causes a decrease in tensile elongation and a variation in twist value. Therefore, the total addition amount of these elements is limited to 1.0% or less.
【００３６】また、Ａ１とＲＥＭは、脱酸や脱硫を目的
として添加することができ、それぞれ０．００１〜０．
２％の範囲で１種単独または２種の複合で添加できる。Further, A1 and REM can be added for the purpose of deoxidation and desulfurization, and 0.001 to 0.
Within the range of 2%, one kind can be added alone or two kinds can be added in combination.
【００３７】また、Ｏ、Ｎ等のガス成分は合金中で介在
物を生成し、捻回値のばらつき原因となるので、本発明
線においてはそれぞれ、０．０１％以下に制限するのが
良い。Further, since gas components such as O and N form inclusions in the alloy and cause variations in the twist value, it is preferable to limit each to 0.01% or less in the present invention line. .
【００３８】そして、本発明にかかわる組成は、上述し
た化学元素と残部Ｆｅから構成される。The composition according to the present invention is composed of the above chemical element and the balance Fe.
【００３９】上述の組成をもつ本発明の送電線用低熱膨
張高強度芯線は、熱間加工後あるいは固溶化熱処理後に
急冷しても常温ではオーステナイト相が主相として安定
であるが、伸線工程時に、十分な冷間加工を加えること
で、加工誘起マルテンサイト変態によって、優れた加工
硬化能が得られる。冷間加工による加工硬化は、Ｃ添加
によるオーステナイト基地の加工硬化能アップとＣを含
有するマルテンサイト相による効果が大きい。The low-thermal-expansion high-strength core wire for a transmission line of the present invention having the above-mentioned composition is stable as an austenite phase as a main phase at room temperature even if it is rapidly cooled after hot working or after solution heat treatment, but in the wire drawing step. At times, by sufficient cold working, excellent work hardening ability can be obtained by the work-induced martensitic transformation. The work hardening by cold working has a large effect by increasing the work hardening ability of the austenite base by adding C and the martensite phase containing C.
【００４０】また、本発明の合金組成からなる高強度低
熱膨張材料を線材に加工すると、特に冷間引抜の中間工
程で焼鈍処理を行なわなくても、４０回前後の安定した
捻回値が得られる。このレベルの捻回値は従来の高強度
鋼線の捻回値レベルと同等のものであり、これは、冷間
加工によってすでに存在する加工誘起マルテンサイト相
あるいは捻回中におきるオーステナイト相からマルテン
サイト相への変態による応力の緩和による効果が大きい
ものと推測される。When the high-strength, low-thermal-expansion material having the alloy composition of the present invention is processed into a wire, a stable twist value of about 40 times can be obtained without performing annealing treatment especially in the intermediate step of cold drawing. To be The twist value at this level is equivalent to the twist value level of conventional high-strength steel wire, which means that the work-induced martensite phase that already exists during cold working or the austenite phase that occurs during twisting to martensite It is presumed that the effect of stress relaxation due to the transformation to the site phase is large.
【００４１】インバー合金の基地が強度の冷間加工を加
えても、オーステナイト相が安定の場合は、熱膨張係数
は低いが引張強さが不十分であったり、線材に冷間加工
した際、単純な冷間引抜の工程では、捻回特性が不十分
になったりする。逆に、オーステナイト相が不安定にな
りすぎると、熱間加工後あるいは、固溶化処理後の冷却
過程で、マルテンサイト変態が過度に生じて、もはやイ
ンバ特性を得ることができなくなる。以上述べた理由に
より、本発明の送電線用低熱膨張高強度芯線が高い強度
と低い熱膨張係数および高い捻回値を同時に得るために
は、オーステナイト相と加工誘起変態によって生じるマ
ルテンサイト相との２相をあわせもつ必要がある。When the matrix of Invar alloy is subjected to strong cold working and the austenite phase is stable, the coefficient of thermal expansion is low but the tensile strength is insufficient, or when the wire is cold worked, In a simple cold drawing process, the twisting characteristics may become insufficient. On the other hand, if the austenite phase becomes too unstable, excessive martensite transformation will occur during the cooling process after hot working or after solution treatment, and it will no longer be possible to obtain Invar characteristics. For the reason described above, in order to simultaneously obtain a high strength, a low thermal expansion coefficient and a high twist value for the low thermal expansion high strength core wire for a transmission line of the present invention, the austenite phase and the martensite phase generated by the work induced transformation It is necessary to have two phases together.
【００４２】しかし、加工誘起変態によって生じるマル
テンサイト量は、Ｘ線回析によって求められるマルテン
サイト量／（マルテンサイト量＋オーステナイト量）比
において２〜３５％であることが強度と低熱膨張特性の
バランス上好ましい範囲である。なお、加工誘起変態に
よって得られるマルテンサイトの一部をドライアイス＋
アルコール中（−７５℃付近）や、それよりもさらに低
温での焼入れ処理による熱的なマルテンサイト変態で置
換することは可能であるが、変態量のバラツキと量産性
を考慮すると加工歪を駆動力とする変態を利用する方が
製造するうえで好ましい。However, the amount of martensite produced by the work-induced transformation is 2 to 35% in the ratio of the amount of martensite / (the amount of martensite + the amount of austenite) determined by X-ray diffraction, which indicates strength and low thermal expansion characteristics. This is a preferable range in terms of balance. In addition, part of the martensite obtained by the process-induced transformation is dry ice +
It is possible to replace it by thermal martensite transformation by quenching in alcohol (around -75 ° C) or at a lower temperature than that, but drive the processing strain considering variation in transformation amount and mass productivity. It is preferable to utilize the transformation that uses force for manufacturing.
【００４３】このような加工誘起マルテンサイトのオー
ステナイトへの逆変態温度５５０℃以上の温度であるた
め、送電線として使用される最高温度と言われている３
００℃前後の連続的な使用に対して本発明の送電線用低
熱膨張高強度芯線は特性上なんら問題はない。Since the reverse transformation temperature of such work-induced martensite to austenite is 550 ° C. or higher, it is said to be the highest temperature used as a transmission line 3.
The low-thermal-expansion and high-strength core wire for a power transmission line of the present invention has no problem in characteristics for continuous use at around 00 ° C.
【００４４】また、加工誘起マルテンサイトは、送電線
として使用される際の中間および仕上げ製造工程におけ
るＡ１被覆処理やＺｎメッキ処理のような４００〜５０
０℃の加熱で一部が炭化物とフェライトに分解すること
もあるが、本発明の送電線用低熱膨張高強度芯線におい
て、少量のフェライトの存在は、特性上なんら問題はな
い。また、実際には第３相として、析出強化作用をもつ
Ｃｒ、ＭｏやＷその他の炭化物が存在してもよい。Further, the work-induced martensite is 400 to 50 such as the A1 coating treatment and the Zn plating treatment in the intermediate and finish manufacturing steps when used as a power transmission line.
Although a part may be decomposed into carbide and ferrite by heating at 0 ° C, the presence of a small amount of ferrite causes no problem in characteristics in the low thermal expansion and high strength core wire for a power transmission line of the present invention. Further, actually, as the third phase, Cr, Mo, W or other carbides having a precipitation strengthening action may be present.
【００４５】[0045]
【実施例】以下、本発明について具体的実施例を説明す
る。EXAMPLES Specific examples of the present invention will be described below.
【００４６】［実施例１］表２に示す組成のＦｅ−Ｃｏ
−Ｎｉ−（Ｃｒ−Ｍｏ−Ｗ）系合金を溶製し、熱間鍛造
および熱間圧延によって直径１０ｍｍのコイル状に仕上
げた後、これを８５０℃から９８０℃の温度で３０分保
持後水冷の固溶化処理と表面の皮剥を行い、直径９．４
ｍｍの試料を作製し、その後、この試料を用いて、冷間
引抜によりトータルの加工率８２〜９５％の範囲で、送
電線用芯線材を作製した。なお、芯線材にＡｌを被覆す
る場合は、直径４．６ｍｍの段階まで引き抜いた段階で
Ａｌ被覆を実施し、さらに仕上げ線径まで引き抜き、さ
らに安定化処理として３１０℃で２時間加熱を行なっ
た。Ｚｎメッキの場合は、最終引き抜き径の段階でメッ
キ浴中への浸漬処理により、Ｚｎメッキを実施した。[Example 1] Fe-Co having the composition shown in Table 2
-Ni- (Cr-Mo-W) -based alloy was melted and finished into a coil shape with a diameter of 10 mm by hot forging and hot rolling, which was then held at a temperature of 850 ° C to 980 ° C for 30 minutes and then water-cooled. Solution treatment and surface peeling were performed to obtain a diameter of 9.4
A sample having a size of mm was prepared, and thereafter, using this sample, a core wire material for a transmission line was prepared by cold drawing in a range of a total processing rate of 82 to 95%. In the case of coating the core wire with Al, Al coating was carried out at the stage of drawing up to a diameter of 4.6 mm, further drawing to the finished wire diameter, and further heating at 310 ° C. for 2 hours as a stabilizing treatment. . In the case of Zn plating, Zn plating was performed by immersion in a plating bath at the final drawing diameter.
【００４７】そして、これらの試料を用いて熱膨張試
験、引張試験、捻回試験、巻付・巻戻し試験および合金
中のマルテンサイト量の測定を実施した。この結果を表
２に示す。なお、表２には芯線材に用いたＦｅ−Ｃｏ−
Ｎｉ−（Ｃｒ−Ｍｏ−Ｗ）系合金のトータルの冷間加工
率、Ａｌ被覆およびＺｎメッキがついた状態での仕上げ
直径、Ａｌ被覆率およびＺｎメッキ量も併せ示す。ま
た、表２に示すように、熱膨張測定は示差熱膨張計によ
り、Ａｌ被覆の場合は３０℃から３１０℃まで、Ｚｎメ
ッキの場合は３０℃から２４０℃までの平均熱膨張係数
を測定した。引張試験の伸びは標点間２５０ｍｍで測定
し、引張強さと絞りについていずれも５本の平均値を求
めた。また捻回試験は、掴み間を自己径の１００倍と
し、回転数６０ｒｐｍで破断までの捻回値をそれぞれ１
０本測定し、平均値を求めた。巻付・巻戻し試験につい
ては、自己径の１．５倍の芯線に各８回巻付・巻戻しし
た際に試験片が破断するか否かを調査し、割れのない場
合は合格として○印を、割れが発生した場合は不合格と
して×印を表２に記載することにした（実際には割れの
出た試料はなし）。さらに、本発明芯線および従来芯線
のＡｌ被覆またはＺｎメッキをＮａＯＨ水溶液で溶解除
去した後、Ｆｅ−Ｃｏ−Ｎｉ−（Ｃｒ−Ｍｏ−Ｗ）系合
金の試料横断面のＸ線回析を行ない、以下の式によりオ
ーステナイト相との比を求めた。Then, using these samples, a thermal expansion test, a tensile test, a twisting test, a winding / unwinding test and a measurement of the amount of martensite in the alloy were carried out. The results are shown in Table 2. In Table 2, Fe-Co- used for the core wire
The total cold workability of the Ni- (Cr-Mo-W) alloy, the finish diameter with the Al coating and the Zn plating, the Al coverage, and the Zn plating amount are also shown. Further, as shown in Table 2, the thermal expansion was measured by a differential thermal dilatometer by measuring the average thermal expansion coefficient from 30 ° C. to 310 ° C. for Al coating and from 30 ° C. to 240 ° C. for Zn plating. . The elongation in the tensile test was measured at a gauge length of 250 mm, and an average value of 5 was obtained for both tensile strength and drawing. Further, in the twisting test, the gripping distance was set to 100 times the self-diameter, and the twisting value up to breaking was 1 at a rotation speed of 60 rpm.
0 pieces were measured and the average value was calculated. Regarding the wrapping / rewinding test, it was investigated whether or not the test piece broke when the core wire having 1.5 times the self-diameter was wound / rewound 8 times each, and if there was no crack, it was judged as pass. When a crack was generated, the mark was rejected and a cross was decided to be shown in Table 2 (actually, no sample was cracked). Furthermore, after the Al coating or Zn plating of the core wire of the present invention and the conventional core wire is dissolved and removed with an aqueous NaOH solution, X-ray diffraction of a cross section of a sample of the Fe—Co—Ni— (Cr—Mo—W) alloy is performed. The ratio with the austenite phase was calculated by the following formula.
【００４８】マルテンサイト相（％）＝｛Ｉα／（Ｉγ
＋Ｉα）｝×１００ Ｉγ＝Ｉγ（１１１）＋Ｉγ（２００）＋Ｉγ（２２
０）−Ｉγ（３１１） Ｉγ（１１１）等はオーステナイトのＸ線回折強度 Ｉα＝Ｉα（１１０）＋Ｉα（２００）＋Ｉα（２２
０）＋Ｉα（２１１） Ｉα（１１０）等はマルテンサイトのＸ線回折強度 表２に示す合金のうち、Ｎｏ．１〜１８は本発明の送電
線用低熱膨張高強度芯線に用いられる合金であり、Ｎ
ｏ．４１は、特開平３−１１５５４３号に開示される高
強度低熱膨張合金である。また、これらの合金のＮｉと
Ｃｏの関係およびＮｉとＣｒ＋０．５４Ｍｏ＋０．２８
Ｗ量の関係を図１に示している。Martensite phase (%) = {Iα / (Iγ
+ Iα)} × 100 Iγ = Iγ (111) + Iγ (200) + Iγ (22
0) -Iγ (311) Iγ (111) and the like are X-ray diffraction intensities of austenite Iα = Iα (110) + Iα (200) + Iα (22
0) + Iα (211) Iα (110) and the like are X-ray diffraction intensities of martensite. 1 to 18 are alloys used for the low thermal expansion and high strength core wire for the power transmission line of the present invention, and N
o. 41 is a high strength low thermal expansion alloy disclosed in Japanese Patent Laid-Open No. 3-115543. Further, the relationship between Ni and Co of these alloys and Ni and Cr + 0.54Mo + 0.28
The relationship of the W amount is shown in FIG.
【００４９】[0049]
【表２】 [Table 2]
【００５０】[0050]
【表３】 [Table 3]
【００５１】この結果、表２に示すように、本発明は８
２〜９５％の冷間加工後に１３０〜１６７ｋｇｆ／ｃｍ
2 の引張強さと３０℃から２４０℃間および３０℃から
３１０℃間の平均熱膨張係数で５．９×１０-6℃以下の
性能を併せもち、従来のピアノ線と同等あるいはそれに
近い引張強さとピアノ線の１／２以下の熱膨張係数が得
られることが判る（ピアノ線の熱膨張係数α３０−３１
０℃：１１．５〜１３×１０-6／℃）。As a result, according to the present invention, as shown in Table 2,
130-167 kgf / cm after 2 to 95% cold working
It has the tensile strength of 2 and the average thermal expansion coefficient of 5.9 × 10 -6 ° C or less between 30 ° C and 240 ° C and between 30 ° C and 310 ° C. It can be seen that a coefficient of thermal expansion of 1/2 or less than that of a piano wire can be obtained (coefficient of thermal expansion of piano wire α30-31
0 ° C .: 11.5 to 13 × 10 −6 / ° C.).
【００５２】また、これらの特性は従来芯線Ｎｏ．４１
と較べると、引張強度に各段の差が見られる。さらに、
本発明芯線Ｎｏ．１，２，２７および２８は、従来芯線
よりもさらに３０〜３１０℃間の熱膨張係数が低く、導
電体であるＸＴＡｌの設計耐熱限界（３１０℃）までの
使用が可能となる。また、その他の本発明芯線について
も、既設鉄塔の建て替えなしに、送電線を張り替えるた
めには、ピアノ線と同等の強度を持つことが絶対条件と
なるので、弛度の点では、従来芯線に同等あるいはやや
劣る程度であり、３１０℃までの使用が困難な点もある
が、それよりも設計上低い送電温度の場合は、張り替え
が可能となる。Further, these characteristics are the same as those of the conventional core wire No. 41
Compared with the above, there are differences in tensile strength at each step. further,
The present invention core wire No. 1, 2, 27 and 28 have a lower coefficient of thermal expansion between 30 and 310 ° C. than the conventional core wire, and can be used up to the design heat resistance limit (310 ° C.) of XTAl which is a conductor. Also, regarding the other core wires of the present invention, in order to replace the transmission line without rebuilding the existing steel tower, it is absolutely necessary that the core wire have the same strength as the piano wire. However, it is difficult to use it up to 310 ° C, but if the transmission temperature is lower than that, the replacement is possible.
【００５３】また、表３より、本発明芯線は高い捻回値
と優れた巻付・巻戻し特性を有することがわかる。この
ような結果は、冷間加工時に存在する加工誘起マルテン
サイトおよびこれらの各種試験の組成変形中に生じるオ
ーステナイト相から、マルテンサイト相への変態によっ
てもたらされる。表３より本発明は、オーステナイト相
とマルテンサイト相の相比において、５〜２５％のマル
テンサイト相を含むことがわかる。Further, it can be seen from Table 3 that the core wire of the present invention has a high twist value and excellent winding / unwinding characteristics. Such results are brought about by the transformation from the work-induced martensite present during cold working and the austenitic phase that occurs during the compositional deformation of these various tests to the martensitic phase. It can be seen from Table 3 that the present invention includes the martensite phase in an amount of 5 to 25% in the phase ratio of the austenite phase and the martensite phase.
【００５４】これに対し、従来芯線Ｎｏ．４１は、皮剥
後に単純に冷間加工を行うだけで、捻回値が５回以下の
低い値となり、送電線の芯材の用途に対しては適さなく
なる。On the other hand, the conventional core wire No. No. 41 has a low twist value of 5 times or less by simply performing cold working after stripping, which makes it unsuitable for use as a core material of a transmission line.
【００５５】［実施例２］本発明のＡＣＳＲ構成での表
３のＮｏ．２８の線材を用いてできる送電線性能及び弛
度の計算例を、従来電線の性能と比較して表４に示す。
尚、弛度は線路の最大使用張力を電線の引張荷重の１／
３（安全率３）として径間長を２００ｍ、電線温度をそ
の電線の許容温度で計算した。[Embodiment 2] No. 2 in Table 3 in the ACSR configuration of the present invention. Table 4 shows an example of calculation of transmission line performance and slack that can be made using 28 wire rods in comparison with the performance of conventional electric wires.
Note that the sag is the maximum usable tension of the line 1 / the tensile load of the wire.
3 (safety factor 3), the span length was 200 m, and the wire temperature was calculated by the allowable temperature of the wire.
【００５６】[0056]
【表４】 [Table 4]
【００５７】本発明の小サイズＡＣＳＲ構成での表３の
Ｎｏ．１の線材を用いてできる送電線性能及び弛度の計
算例を、従来電線と比較して表５に示す。尚、計算条件
は表４と同じとした。No. 3 in Table 3 in the small size ACSR configuration of the present invention. Table 5 shows an example of calculation of power transmission line performance and sag that can be made using the wire rod of No. 1 in comparison with the conventional electric wire. The calculation conditions were the same as in Table 4.
【００５８】[0058]
【表５】 [Table 5]
【００５９】［実施例３］上記実施例は、導体部・鋼線
材とも丸形の素線を使用した例であるが、ＸＴＡＣＩＲ
のように、太目の鋼芯と扇形の導体部を採用すれば同一
外径のＡＣＳＲより高い引張荷重の電線を作ることがで
きる。このような電線は河川横断や海峡横断等の比較的
径間長の長い径間に有効である。[Embodiment 3] The above embodiment is an example in which round conductor wires are used for both the conductor portion and the steel wire rod.
As described above, if a thick steel core and a fan-shaped conductor are used, an electric wire having a tensile load higher than that of the ACSR having the same outer diameter can be manufactured. Such an electric wire is effective for relatively long spans such as river crossings and strait crossings.
【００６０】[0060]
【発明の効果】本発明の送電線用低熱膨張高強度芯線
は、従来鋼線並の引張強さを発揮するため、従来の低熱
膨張芯線に比べて数段高い強度を有する。その結果、従
来の鋼心より線（ＡＣＳＲ）を用いた送電線を本発明の
低弛度芯線に張り替えるだけで送電容量の大幅な増加を
図ることができる。さらに、一部の本発明芯線をもちい
れば、従来の低熱膨張芯線よりもさらに電線の弛度を抑
制できるため、導電体である特別耐熱Ａｌ合金（ＸＴＡ
ｌ）の設計限界温度（３１０℃）まで送電線の耐用温度
を高めることが可能となり、さらなる送電容量の増加が
望める。The low-thermal-expansion and high-strength core wire for a power transmission line of the present invention exhibits tensile strength equivalent to that of a conventional steel wire, and therefore has a strength several times higher than that of a conventional low-thermal-expansion core wire. As a result, it is possible to significantly increase the transmission capacity simply by replacing the conventional transmission line using the steel core strand (ACSR) with the low sag core wire of the present invention. Further, since the use of a part of the core wire of the present invention can further suppress the sagging of the electric wire as compared with the conventional low thermal expansion core wire, the special heat-resistant Al alloy (XTA
It is possible to increase the service temperature of the power transmission line up to the design limit temperature (310 ° C.) of l), and further increase the power transmission capacity.
【図１】本発明及び従来の送電用低弛度芯線の組成関係
をプロットして示した状態図である。FIG. 1 is a state diagram in which a composition relation of a low sag core wire for power transmission of the present invention and a conventional power transmission is plotted.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２３Ｃ 30/00 Ｂ (72)発明者 三本杉 潔 茨城県日立市川尻町４丁目10番１号 日立 電線株式会社豊浦工場内 (72)発明者 志賀 博一 茨城県日立市川尻町４丁目10番１号 日立 電線株式会社豊浦工場内 (72)発明者 佐藤 光司 島根県安来市安来町2107番地２ 日立金属 株式会社冶金研究所内 (72)発明者 舛形 芳樹 島根県安来市安来町2107番地２ 日立金属 株式会社安来工場内 (72)発明者 大野 丈博 島根県安来市安来町2107番地２ 日立金属 株式会社冶金研究所内─────────────────────────────────────────────────── ─── Continuation of front page (51) Int.Cl. 6 Identification number Reference number within the agency FI Technical indication C23C 30/00 B (72) Inventor Kiyoshi Sanbonsugi 4-10-1 Kawajiri-cho, Hitachi-shi, Ibaraki Hitachi Cable Co., Ltd. Toyoura Plant (72) Inventor Hirokazu Shiga 4-10-1 Kawajiri-cho, Hitachi City, Ibaraki Prefecture Hitachi Cable Co., Ltd. Toyoura Plant (72) Inventor Koji Sato 2107-2 Yasugi-cho, Yasugi City, Shimane Prefecture Inside the Metallurgical Laboratory, Hitachi Metals Co., Ltd. (72) 2107, Yasugi-cho, Yasugi-shi, Shimane 2 Inventor Yoshiki Masuga Inside the Yasugi Plant, Hitachi Metals Co., Ltd. (72) Takehiro Ohno 2107, Yasugi-cho, Yasugi-shi, Shimane 2 Hitachi Metals Co., Ltd. Company Metallurgy Research Center
Claims (19)
つ、その組成が少なくともオーステナイト相と加工誘起
マルテンサイト相との２相を有する鋼線材の表面に、Ａ
ｌ被覆を施したことを特徴とする送電線用低熱膨張高強
度芯線。1. A steel wire comprising a Fe--Co--Ni alloy and having a composition of at least two phases, an austenite phase and a work-induced martensite phase, is
A low-thermal-expansion and high-strength core wire for a transmission line, characterized by being coated with l.
つ、その組成が少なくともオーステナイト相と加工誘起
マルテンサイト相との２相を有する鋼線材の表面に、Ｚ
ｎメッキを施したことを特徴とする送電線用低熱膨張高
強度芯線。2. A surface of a steel wire rod made of a Fe—Co—Ni alloy and having a composition of at least two phases, an austenite phase and a work-induced martensite phase, has a Z
A low-thermal-expansion and high-strength core wire for a transmission line, characterized by being plated with n.
系合金中に含まれる加工誘起マルテンサイト相の量が２
〜３５％の範囲であることを特徴とする請求項１または
２に記載の送電線用低熱膨張高強度芯線。3. Fe—Co—Ni forming the steel wire rod.
The amount of work-induced martensite phase contained in the Al-based alloy is 2
It is the range of -35%, The low thermal expansion high strength core wire for transmission lines of Claim 1 or 2 characterized by the above-mentioned.
断面積の３０％以下であることを特徴とする請求項１ま
たは３に記載の送電線用低熱膨張高強度芯線。4. The low-thermal-expansion high-strength core wire for a transmission line according to claim 1, wherein the coverage of the Al coating is 30% or less of the cross-sectional area of the steel wire rod.
断面積の１３〜２２％の範囲であることを特徴とする請
求項１または３に記載の送電線用低熱膨張高強度芯線。5. The low-thermal-expansion high-strength core wire for a transmission line according to claim 1, wherein the coverage of the Al coating is in the range of 13 to 22% of the cross-sectional area of the steel wire rod.
であることを特徴とする請求項２または３に記載の送電
線用低熱膨張高強度芯線。6. The low thermal expansion high strength core wire for a transmission line according to claim 2, wherein the Zn plating amount is 215 g / m 2 or more.
系合金の組成が、重量％でＣが０．０６〜０．５０％、
Ｃｏが６５％以下、Ｎｉが３０％未満の１種または２種
をＣｏ＋Ｎｉで２５〜６５％、残部がＦｅであることを
特徴とする請求項１〜６いずれかに記載の送電線用低熱
膨張高強度芯線。7. Fe—Co—Ni forming the steel wire rod
The composition of the alloy is 0.06 to 0.50% by weight,
The low thermal expansion for a transmission line according to any one of claims 1 to 6, wherein Co is 65% or less, Ni is less than 30%, one or two is 25% to 65% of Co + Ni, and the balance is Fe. High strength core wire.
系合金の組成が、重量％でＣが０．０６〜０．５０％、
Ｓｉが１．５％以下、Ｍｎが３％以下、Ｃｏが２〜６５
％、Ｎｉが０または２９．９％以下で、かつこのＣｏと
Ｎｉの関係が５２−（５／３）Ｎｉ≦Ｃｏ≦６５−（５
／３）Ｎｉ、またはさらに１１％以下のＣｒと６％以下
のＷと６％以下のＭｏのいずれか１種または２種以上を
５−（１／４）Ｎｉ≦Ｃｒ＋０．５４Ｍｏ＋０．２８Ｗ
≦１１−（１／４）Ｎｉであり、残部がＦｅであること
を特徴とする請求項１〜６いずれかに記載の送電線用低
熱膨張高強度芯線。8. The Fe—Co—Ni constituting the steel wire rod.
The composition of the alloy is 0.06 to 0.50% by weight,
Si 1.5% or less, Mn 3% or less, Co 2 to 65
%, Ni is 0 or 29.9% or less, and the relationship between Co and Ni is 52− (5/3) Ni ≦ Co ≦ 65− (5
/ 3) Ni, or 11% or less of Cr, 6% or less of W and 6% or less of Mo, and one or more of them is 5- (1/4) Ni ≦ Cr + 0.54Mo + 0.28W
≦ 11- (1/4) Ni, the balance being Fe, The low thermal expansion and high strength core wire for a power transmission line according to any one of claims 1 to 6.
系合金の組成が、重量％でＣが０．０６〜０．５０％、
Ｓｉが１．５％以下、Ｍｎが３％以下、Ｃｏが８．１〜
３２％以下、Ｎｉが１２％以上２９．９％以下で、かつ
このＣｏとＮｉの関係が５２−（５／３）Ｎｉ≦Ｃｏ≦
６５−（５／３）Ｎｉであり、またはさらに８％以下の
Ｃｒと６％以下のＷと６％以下のＭｏの１種または２種
以上を、５−（１／４）Ｎｉ≦Ｃｒ＋０．５４Ｍｏ＋
０．２８Ｗ≦１１−（１／４）Ｎｉ、残部がＦｅである
ことを特徴とする請求項１〜６いずれかに記載の送電線
用低熱膨張高強度芯線。9. Fe—Co—Ni forming the steel wire rod.
The composition of the alloy is 0.06 to 0.50% by weight,
Si is 1.5% or less, Mn is 3% or less, and Co is 8.1 to 1.
32% or less, Ni 12% or more and 29.9% or less, and the relationship between Co and Ni is 52- (5/3) Ni ≦ Co ≦
65- (5/3) Ni, or one or more of Cr of 8% or less, W of 6% or less and Mo of 6% or less is added to 5- (1/4) Ni ≦ Cr + 0. 54Mo +
0.28 W <= 11- (1/4) Ni and the balance is Fe, The low thermal expansion high strength core wire for transmission lines in any one of Claims 1-6 characterized by the above-mentioned.
ｉ系合金の組成が、重量％でＣが０．１５〜０．５０
％、Ｓｉが１．５％以下、Ｍｎが３％以下、Ｃｏが８．
１〜２２％以下、Ｎｉが１８％以上２９．９％以下で、
ＣｏとＮｉの関係が５２−（５／３）Ｎｉ≦Ｃｏ≦６５
−（５／３）Ｎｉであり、またはさらに６．５％以下の
Ｃｒと５％以下のＷと５％以下のＭｏの１種または２種
以上を５−（１／４）Ｎｉ≦Ｃｒ＋０．５４Ｍｏ＋０．
２８Ｗ≦１１−（１／４）Ｎｉであり、残部がＦｅであ
ることを特徴とする請求項１〜６いずれかに記載の送電
線用低熱膨張高強度芯線。10. Fe-Co-N constituting the steel wire rod.
The composition of the i-based alloy has a C content of 0.15 to 0.50 in weight%.
%, Si 1.5% or less, Mn 3% or less, Co 8.
1 to 22% or less, Ni is 18% or more and 29.9% or less,
The relationship between Co and Ni is 52− (5/3) Ni ≦ Co ≦ 65
-(5/3) Ni, or one or more of 6.5% or less of Cr, 5% or less of W and 5% or less of Mo is added to 5- (1/4) Ni≤Cr + 0. 54Mo + 0.
28W ≦ 11− (1/4) Ni, the balance being Fe, The low thermal expansion high strength core wire for a power transmission line according to claim 1.
ｉ系合金の組成が、重量％でＣが０．１５〜０．４０
％、Ｓｉが０．５％以下、Ｍｎが１％以下、Ｃｏが８．
１〜１７％以下、Ｎｉが２１〜２９．５％で、このＣｏ
とＮｉの関係が５２−（５／３）Ｎｉ≦Ｃｏ≦６５−
（５／３）Ｎｉであり、またはさらに５．７５％以下の
Ｃｒと４％以下のＷと４％以下のＭｏの１種または２種
以上が５−（１／４）Ｎｉ≦Ｃｒ＋０．５４Ｍｏ＋０．
２８Ｗ≦１１−（１／４）Ｎｉであり、残部がＦｅであ
ることを特徴とする請求項１〜６いずれかに記載の送電
線用低熱膨張高強度芯線。11. Fe-Co-N constituting the steel wire rod.
The composition of the i-based alloy is 0.15 to 0.40 in C by weight%.
%, Si 0.5% or less, Mn 1% or less, Co 8.
1 to 17% or less, Ni 21 to 29.5%, and this Co
And Ni are 52- (5/3) Ni≤Co≤65-
(5/3) Ni, or one or more of 5.75% or less of Cr, 4% or less of W and 4% or less of Mo is 5- (1/4) Ni ≦ Cr + 0.54Mo + 0. ．
28W ≦ 11− (1/4) Ni, the balance being Fe, The low thermal expansion high strength core wire for a power transmission line according to claim 1.
ｉ系合金の組成が、重量％でＣが０．１５〜０．４０
％、Ｓｉが０．５％以下、Ｍｎが１％以下、Ｃｏが８．
１〜１７％以下、Ｎｉが２１〜２９．５％で、このＣｏ
とＮｉの関係が５２−（５／３）Ｎｉ≦Ｃｏ≦６５−
（５／３）Ｎｉを満足し、残部がＦｅであることを特徴
とする請求項１〜６いずれかに記載の送電線用低熱膨張
高強度芯線。12. The Fe—Co—N constituting the steel wire rod.
The composition of the i-based alloy is 0.15 to 0.40 in C by weight%.
%, Si 0.5% or less, Mn 1% or less, Co 8.
1 to 17% or less, Ni 21 to 29.5%, and this Co
And Ni are 52- (5/3) Ni≤Co≤65-
The low thermal expansion and high strength core wire for a transmission line according to any one of claims 1 to 6, wherein (5/3) Ni is satisfied and the balance is Fe.
ｉ系合金の組成が、重量％でＣが０．２０〜０．３０
％、Ｓｉが０．５％以下、Ｍｎが０．５％以下、Ｃｏが
１２〜１３．５％、Ｎｉが２７．７〜２９．５％を含有
し、残部がＦｅであることを特徴とする請求項１〜６い
ずれかに記載の送電線用低熱膨張高強度芯線。13. An Fe—Co—N constituting the steel wire rod.
The composition of the i-based alloy is such that C is 0.20 to 0.30 in% by weight.
%, Si is 0.5% or less, Mn is 0.5% or less, Co is 12 to 13.5%, Ni is 27.7 to 29.5%, and the balance is Fe. The low-thermal expansion and high-strength core wire for a power transmission line according to any one of claims 1 to 6.
ｉ系合金のＦｅの一部を、重量％でＢ０．０００１〜
０．０２％、Ｍｇ０．０００１〜０．０２％、Ｃａ０．
０００１〜０．０２％の１種または２種以上で置換した
ことを特徴とする請求項７〜１３いずれかに記載の送電
線用低熱膨張高強度芯線。14. Fe—Co—N constituting the steel wire rod.
A part of Fe of the i-based alloy is B0.0001 by weight%.
0.02%, Mg 0.0001 to 0.02%, Ca 0.
It replaced by 1 type (s) or 2 or more types of 0001-0.02%, The low thermal expansion high strength core wire for transmission lines in any one of the Claims 7-13 characterized by the above-mentioned.
ｉ系合金のＦｅの一部を、Ｖ，Ｔｉ，Ｎｂ，Ｔａ，Ｈ
ｆ，Ｚｒの１種または２種以上合計１％以下の範囲で置
換したことを特徴とする請求項７〜１４いずれかに記載
の送電線用低熱膨張高強度芯線。15. Fe—Co—N constituting the steel wire rod.
Part of Fe in the i-based alloy is replaced with V, Ti, Nb, Ta, H
The low-thermal-expansion high-strength core wire for a power transmission line according to any one of claims 7 to 14, wherein one or more of f and Zr are substituted in the range of 1% or less in total.
ｉ系合金のＦｅの一部を、重量％でＡｌ０．００１〜
０．２％、ＲＥＭ０．００１〜０．２％の１種または２
種で置換したことを特徴とする請求項７〜１５いずれか
に記載の送電線用低熱膨張高強度芯線。16. An Fe—Co—N constituting the steel wire rod.
A part of Fe in the i-based alloy is 0.001% by weight of Al.
0.2%, REM 0.001-0.2% 1 type or 2
The low-thermal-expansion high-strength core wire for a power transmission line according to any one of claims 7 to 15, wherein the core wire is replaced with a seed.
2 以上、常温から３１０℃までの平均熱膨張係数が６×
１０-6／℃以下、自己径の１００倍の掴み間隔で捻った
時の捻回値が１５回以上及び自己径の１．５倍の径の軸
棒に８回巻き付けた後、８回巻き戻しても破断が生じな
いことを特徴とする請求項１〜１６いずれかに記載の送
電線用低熱膨張高強度芯線。17. The tensile strength at room temperature is 130 kgf / mm.
2 or more, average thermal expansion coefficient from room temperature to 310 ° C is 6 ×
10 -6 / ℃ or less, the twist value when twisted at a gripping interval of 100 times its own diameter is 15 times or more, and 8 times after it is wound around a shaft rod with a diameter of 1.5 times its own diameter. The low-thermal-expansion high-strength core wire for a power transmission line according to any one of claims 1 to 16, wherein the core wire does not break even when returned.
2 以上、常温から２４０℃までの平均熱膨張係数が６×
１０-6／℃以下、自己径の１００倍の掴み間隔で捻った
時の捻回値が１５回以上及び自己径の１．５倍の径の軸
棒に８回巻き付けた後、８回巻き戻しても破断が生じな
いことを特徴とする請求項１〜１６いずれかに記載の送
電線用低熱膨張高強度芯線。18. The tensile strength at room temperature is 130 kgf / mm.
2 or more, average thermal expansion coefficient from room temperature to 240 ° C is 6 ×
10 -6 / ℃ or less, the twist value when twisted at a gripping interval of 100 times its own diameter is 15 times or more, and 8 times after it is wound around a shaft rod with a diameter of 1.5 times its own diameter. The low-thermal-expansion high-strength core wire for a power transmission line according to any one of claims 1 to 16, wherein the core wire does not break even when returned.
の送電線用低熱膨張高強度芯線をそれぞれ１本ないし複
数本撚り合わせて芯材とし、この芯材のまわりに１層な
いし複数層のアルミ合金を導体として撚り合せてなるこ
とを特徴とする低弛度電線。19. One or a plurality of low thermal expansion high strength core wires for a power transmission line according to any one of claims 1 to 18 are twisted together to form a core material, and one or a plurality of layers are provided around the core material. A low-slack wire that is made by twisting together the aluminum alloy as a conductor.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6005898A JP3011596B2 (en) | 1994-01-24 | 1994-01-24 | Low thermal expansion high strength core wire for transmission line and low sag wire using the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6005898A JP3011596B2 (en) | 1994-01-24 | 1994-01-24 | Low thermal expansion high strength core wire for transmission line and low sag wire using the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07211143A true JPH07211143A (en) | 1995-08-11 |
| JP3011596B2 JP3011596B2 (en) | 2000-02-21 |
Family
ID=11623718
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6005898A Expired - Fee Related JP3011596B2 (en) | 1994-01-24 | 1994-01-24 | Low thermal expansion high strength core wire for transmission line and low sag wire using the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3011596B2 (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100361969B1 (en) * | 2000-07-20 | 2002-11-23 | 한국전기연구원 | Extra high-strength invar alloys with low thermal expansion |
| JP2010174350A (en) * | 2009-01-30 | 2010-08-12 | Res Inst Electric Magnetic Alloys | High elastic and constant-modulus alloy, method for producing the same, and precise mechanical equipment |
| JP2012255212A (en) * | 2012-07-11 | 2012-12-27 | Research Institute For Electromagnetic Materials | High-elasticity and constant-modulus alloy and manufacturing method therefor, and precision instrument |
| JP2015061932A (en) * | 2013-08-23 | 2015-04-02 | 大同特殊鋼株式会社 | Maraging steel having excellent fatigue characteristic |
| JP2017225205A (en) * | 2016-06-13 | 2017-12-21 | 古河電気工業株式会社 | Electric power network and laying method of electric power network |
| JP2019011515A (en) * | 2013-08-23 | 2019-01-24 | 大同特殊鋼株式会社 | Maraging steel excellent in fatigue characteristic |
| WO2022030090A1 (en) * | 2020-08-06 | 2022-02-10 | 住友電気工業株式会社 | Iron alloy, iron alloy wire, and iron alloy stranded wire |
-
1994
- 1994-01-24 JP JP6005898A patent/JP3011596B2/en not_active Expired - Fee Related
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100361969B1 (en) * | 2000-07-20 | 2002-11-23 | 한국전기연구원 | Extra high-strength invar alloys with low thermal expansion |
| JP2010174350A (en) * | 2009-01-30 | 2010-08-12 | Res Inst Electric Magnetic Alloys | High elastic and constant-modulus alloy, method for producing the same, and precise mechanical equipment |
| JP2012255212A (en) * | 2012-07-11 | 2012-12-27 | Research Institute For Electromagnetic Materials | High-elasticity and constant-modulus alloy and manufacturing method therefor, and precision instrument |
| JP2015061932A (en) * | 2013-08-23 | 2015-04-02 | 大同特殊鋼株式会社 | Maraging steel having excellent fatigue characteristic |
| US10119186B2 (en) | 2013-08-23 | 2018-11-06 | Daido Steel Co., Ltd. | Maraging steel excellent in fatigue characteristics |
| JP2019011515A (en) * | 2013-08-23 | 2019-01-24 | 大同特殊鋼株式会社 | Maraging steel excellent in fatigue characteristic |
| JP2017225205A (en) * | 2016-06-13 | 2017-12-21 | 古河電気工業株式会社 | Electric power network and laying method of electric power network |
| WO2022030090A1 (en) * | 2020-08-06 | 2022-02-10 | 住友電気工業株式会社 | Iron alloy, iron alloy wire, and iron alloy stranded wire |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3011596B2 (en) | 2000-02-21 |
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