JP2003288831A - Cadmium-free electrical contacts and breakers using the same - Google Patents
Cadmium-free electrical contacts and breakers using the sameInfo
- Publication number
- JP2003288831A JP2003288831A JP2002088015A JP2002088015A JP2003288831A JP 2003288831 A JP2003288831 A JP 2003288831A JP 2002088015 A JP2002088015 A JP 2002088015A JP 2002088015 A JP2002088015 A JP 2002088015A JP 2003288831 A JP2003288831 A JP 2003288831A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- contact
- thickness
- breaker
- mass
- 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.)
- Granted
Links
- 229910001316 Ag alloy Inorganic materials 0.000 claims abstract description 38
- 229910052738 indium Inorganic materials 0.000 claims abstract description 20
- 239000000203 mixture Substances 0.000 claims abstract description 20
- 229910052718 tin Inorganic materials 0.000 claims abstract description 20
- 239000000126 substance Substances 0.000 claims abstract description 13
- 230000005611 electricity Effects 0.000 claims abstract 2
- 238000007254 oxidation reaction Methods 0.000 claims description 32
- 230000003647 oxidation Effects 0.000 claims description 29
- 239000012298 atmosphere Substances 0.000 claims description 12
- 238000005266 casting Methods 0.000 claims description 10
- 239000002184 metal Substances 0.000 claims description 9
- 229910052751 metal Inorganic materials 0.000 claims description 9
- 239000000956 alloy Substances 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 8
- 229910045601 alloy Inorganic materials 0.000 claims description 7
- 239000011261 inert gas Substances 0.000 claims description 4
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 230000001590 oxidative effect Effects 0.000 claims description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 2
- 229910052787 antimony Inorganic materials 0.000 claims description 2
- 229910001873 dinitrogen Inorganic materials 0.000 claims description 2
- 229910052745 lead Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 229910052725 zinc Inorganic materials 0.000 claims description 2
- 238000002156 mixing Methods 0.000 claims 1
- 238000009826 distribution Methods 0.000 abstract description 2
- 238000012360 testing method Methods 0.000 description 23
- 238000003466 welding Methods 0.000 description 22
- 238000000034 method Methods 0.000 description 19
- 238000000137 annealing Methods 0.000 description 12
- 239000000463 material Substances 0.000 description 12
- 238000011282 treatment Methods 0.000 description 11
- 239000011159 matrix material Substances 0.000 description 8
- 238000011156 evaluation Methods 0.000 description 6
- 238000001513 hot isostatic pressing Methods 0.000 description 6
- 239000010953 base metal Substances 0.000 description 5
- 230000007547 defect Effects 0.000 description 5
- 238000005259 measurement Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 229910052793 cadmium Inorganic materials 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 230000003287 optical effect Effects 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 230000000712 assembly Effects 0.000 description 2
- 238000000429 assembly Methods 0.000 description 2
- 238000012790 confirmation Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000007731 hot pressing Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 102220253765 rs141230910 Human genes 0.000 description 2
- 229910052709 silver Inorganic materials 0.000 description 2
- 229910016569 AlF 3 Inorganic materials 0.000 description 1
- 229910000809 Alumel Inorganic materials 0.000 description 1
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- 239000010425 asbestos Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 238000005219 brazing Methods 0.000 description 1
- 229910001179 chromel Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 229910052733 gallium Inorganic materials 0.000 description 1
- 229910052732 germanium Inorganic materials 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 231100000956 nontoxicity Toxicity 0.000 description 1
- 238000000879 optical micrograph Methods 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 229910052895 riebeckite Inorganic materials 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 238000004611 spectroscopical analysis Methods 0.000 description 1
- 229910001887 tin oxide Inorganic materials 0.000 description 1
- 230000001988 toxicity Effects 0.000 description 1
- 231100000419 toxicity Toxicity 0.000 description 1
Landscapes
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Breakers (AREA)
- Contacts (AREA)
Abstract
(57)【要約】
【課題】ＣｄフリーのＡｇ合金にて、配線遮断器、ノー
ヒューズブレーカー、漏電遮断器、サーキットブレーカ
ー、安全ブレーカー、または分電盤に用いられるブレー
カー等に適用できる優れた電気接点を提供する。
【解決手段】ＳｎおよびＩｎをともに３〜９質量％含む
化学組成のＡｇ合金からなる接点であり、Ａｇ合金に含
まれる酸化物のアスペクト比の平均値が２．５以上、
５．０以下であり、酸化物の希薄な層の厚みが、接点の
厚みの０％を超え、３．０％未満の範囲内にある電気接
点。(57) [Summary] An excellent electricity that can be applied to a circuit breaker, a no-fuse breaker, an earth leakage breaker, a circuit breaker, a safety breaker, a breaker used for a distribution board, or the like by using a Cd-free Ag alloy. Provide contacts. A contact made of an Ag alloy having a chemical composition containing both Sn and In of 3 to 9% by mass has an average oxide aspect ratio of 2.5 or more contained in the Ag alloy.
An electrical contact having a thickness of less than 5.0, wherein the thickness of the dilute layer of oxide is greater than 0% and less than 3.0% of the thickness of the contact.
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、主として配線遮断
器、ノーヒューズブレーカー、漏電遮断器、サーキット
ブレーカー、安全ブレーカー、または分電盤に用いられ
るブレーカー（以下本発明では、これらをまとめて単に
ブレーカーと言う。）に有用な電気接点およびそれを用
いたブレーカーに関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention mainly relates to a circuit breaker, a no-fuse breaker, an earth leakage circuit breaker, a circuit breaker, a safety breaker, or a breaker used for a distribution board (hereinafter, these are collectively referred to simply as breakers. The present invention relates to a useful electrical contact and a breaker using the same.
【０００２】[0002]
【従来の技術】ブレーカー用の電気接点の材料には、従
来からＣｄ、Ｓｎ、Ｉｎなどの酸化物が分散されたＡｇ
合金が広く使われてきた。特にＣｄ酸化物が分散された
ものは、この種の電気接点に好適であり、ブレーカーに
広く使われてきた。しかしながらＣｄ化合物には毒性の
問題がある。このためこれに代わる電気接点の材料とし
てＳｎ、Ｉｎなどの酸化物が分散された、いわゆるＣｄ
フリーのＡｇ合金の開発が、近年になって強く望まれる
ようになり、数多くの材料が開発され、数多くの電気機
器に使われるようになっている。2. Description of the Related Art As a material for an electrical contact for a breaker, there has been conventionally used Ag in which oxides such as Cd, Sn and In are dispersed.
Alloys have been widely used. In particular, the one in which Cd oxide is dispersed is suitable for this type of electrical contact and has been widely used for breakers. However, Cd compounds have toxicity problems. For this reason, so-called Cd, in which oxides of Sn, In, etc. are dispersed, is used as an alternative electrical contact material.
In recent years, the development of free Ag alloys has been strongly desired, and many materials have been developed and used in many electric devices.
【０００３】ＣｄフリーのＡｇ合金からなる電気接点
は、温度特性が重視される比較的低負荷の電気機器や接
触抵抗を問題とするコンタクターのような軽負荷の機器
には適している。しかしながら定格電流が１０Ａ以上を
要求されるブレーカー用の電気接点として用いる場合に
は、Ｃｄ入りのものに比べその性能が劣っているのが現
状である。例えば本発明の主たる対象である定格電流が
１０Ａ以上、遮断電流１．５ｋＡ以上のブレーカーの多
くが現在でもＣｄを１０質量％以上含有した電気接点を
使用している。Ｃｄ入り接点は、含有するＣｄの酸化物
が約９００℃以上になると昇華し、ブレーカーの短絡遮
断時に発生する熱量を奪い去り、溶着を未然に防止する
という優れた効果があるためである。これに対しＣｄフ
リー接点の場合には、Ｃｄ元素が有するこのような現象
は存在しない。従って、短絡遮断時に発生する大きな熱
量によって、接点が溶着し易いからである。このためＣ
ｄフリーのＡｇ合金からなる電気接点は、ブレーカー用
途にはなじまず、主にマグネットスイッチやリレーなど
に通常使われてきた。The electrical contacts made of a Cd-free Ag alloy are suitable for relatively low-load electrical equipment in which temperature characteristics are important and light-load equipment such as contactors having a problem of contact resistance. However, when used as an electrical contact for a breaker that requires a rated current of 10 A or more, the current situation is that the performance is inferior to that of the one containing Cd. For example, most breakers with a rated current of 10 A or more and a breaking current of 1.5 kA or more, which are the main objects of the present invention, still use electrical contacts containing 10% by mass or more of Cd. This is because the Cd-containing contact has an excellent effect of sublimating the contained Cd oxide when the temperature rises to about 900 ° C. or higher, removing the amount of heat generated when the breaker is short-circuited and preventing welding. On the other hand, in the case of a Cd-free contact, such a phenomenon that the Cd element has does not exist. Therefore, the contacts are easily welded by a large amount of heat generated when the short circuit is interrupted. Therefore C
Electric contacts made of d-free Ag alloy have not been used for breaker applications, and have been usually used mainly for magnet switches and relays.
【０００４】ブレーカー用電気接点に要求される特性に
は、（１）耐溶着特性、（２）初期段階での温度特性、
（３）過負荷試験後の温度特性、（４）耐久試験後の温
度特性、（５）遮断試験後の絶縁特性、（６）耐消耗特
性などが挙げられる。これらの要求特性の中で、Ｃｄフ
リーのＡｇ合金からなる電気接点が、ブレーカー向けの
Ｃｄ入り電気接点にとって変わるために、レベルアップ
しなければならない特性の第一は耐溶着特性である。そ
こでＳｎ、Ｉｎを含んだＡｇ合金にＣｄ、Ｓｎ、Ｉｎ以
外の元素を添加することによって、Ｃｄフリー接点の耐
溶着性を向上させる試みがなされてきた。The characteristics required for the electrical contacts for breakers include (1) welding resistance characteristics, (2) initial temperature characteristics,
(3) Temperature characteristics after overload test, (4) Temperature characteristics after endurance test, (5) Insulation characteristics after interruption test, (6) Wear resistance characteristics and the like. Among these required properties, the first property that must be upgraded in order to replace the Cd-free Ag alloy electrical contacts with the Cd-containing electrical contacts for breakers is the welding resistance property. Therefore, attempts have been made to improve the welding resistance of Cd-free contacts by adding an element other than Cd, Sn, and In to an Ag alloy containing Sn and In.
【０００５】例えば特開昭５１−１３８８９５号公報に
は、Ｓｎを３〜４．５ａｔ％、Ｉｎを５〜７．５ａｔ％
含み、その他の不純物含有量が０．５ａｔ％以下の銀−
酸化物系電気接点材料が開示されている。しかしなが
ら、これらのＣｄフリー接点材料は、低負荷または中負
荷用途に開発されたものであり、例えば本発明の主たる
対象である定格電流１０Ａ以上、遮断電流１．５ｋＡ以
上のブレーカー用途に用いるには、その性能が十分では
ないのが現状である。For example, in JP-A-51-138895, Sn is 3 to 4.5 at% and In is 5 to 7.5 at%.
Silver containing other impurities in an amount of 0.5 at% or less-
Oxide-based electrical contact materials are disclosed. However, these Cd-free contact materials have been developed for low-load or medium-load applications, and for example, for use in breaker applications with a rated current of 10 A or more and a breaking current of 1.5 kA or more, which are the main objects of the present invention. The current situation is that the performance is not sufficient.
【０００６】[0006]
【発明が解決しようとする課題】これらの接点は、まず
Ａｇ、Ｓｎ、Ｉｎ等の構成元素で合金を形成し、その後
これを内部酸化させて、Ａｇマトリックス中にＳｎ、Ｉ
ｎなどの酸化物を分散させることによって作製される。
この方法を後酸化法ともいう。しかしながら、このよう
に作製された接点は、その製造方法上の制約から、接点
のほぼ中央部に希薄層と呼ばれる酸化物濃度の少ない領
域が存在する。これは、内部酸化時にＳｎやＩｎ等の溶
質成分が接点の表面方向へ移動した結果存在するもので
ある。本件の希薄層とは、EDX分析（エネルギー分散型X
線分光分析）の点分析から得られるＳｎまたはＩｎのい
ずれかの元素のピーク高さが、周囲の正常組織から得ら
れるそれの９５％未満となる領域のことである。また、
この希薄層は、周囲の正常組織より明度が高くなってい
るため、図２に示したように５００倍程度の光学顕微鏡
観察により容易にその領域を認識することができ、希薄
層の厚みを測定することができる。この希薄層部分は、
接点の表面部に比べ酸化物の量が少ないために耐熱強度
が低く、特に耐溶着性能を劣化させるという問題があ
る。またこれら従来の接点では、内部酸化工程でＳｎ、
Ｉｎなどが酸化される際に、これらの酸化物とＡｇマト
リックスとの間に格子欠陥が多く発生し、その格子欠陥
が接点の耐熱強度を低下させ、特に耐溶着性能を劣化さ
せるという問題もある。なお、前述の希薄層を形成させ
ない製造方法として粉末冶金による方法が有る。この方
法は、Ｓｎ、Ｉｎなどの元素を含有した粉末状の金属を
予め酸化し、これらの酸化物を含んだＡｇ合金粉末を固
化して作製する。この方法を前酸化法とも言う。しかし
前酸化法によって得られる接点では、確かに希薄層は形
成されないが、酸化によってＡｇ合金中に格子欠陥が無
数に発生するため耐熱強度が弱く、本発明の目的とする
接点の製造方法としては適切でない。These contacts are formed by first forming an alloy with constituent elements such as Ag, Sn, In, etc., and then internally oxidizing this to form Sn, I in the Ag matrix.
It is made by dispersing an oxide such as n.
This method is also called a post-oxidation method. However, in the contact thus produced, due to the limitation of the manufacturing method, there is a region having a low oxide concentration, which is called a dilute layer, in the substantially central portion of the contact. This exists as a result of solute components such as Sn and In moving toward the surface of the contact during internal oxidation. The thin layer in this case is an EDX analysis (energy dispersive X
It is the region where the peak height of either Sn or In element obtained from the point analysis of (line spectroscopy) is less than 95% of that obtained from the surrounding normal tissue. Also,
Since this diluted layer has higher brightness than the surrounding normal tissue, the region can be easily recognized by observing with an optical microscope at about 500 times as shown in FIG. 2, and the thickness of the diluted layer can be measured. can do. This thin layer part is
Since the amount of oxide is smaller than that on the surface of the contact, the heat resistance is low, and there is a problem that the welding resistance is deteriorated. Also, in these conventional contacts, Sn,
When In or the like is oxidized, many lattice defects occur between these oxides and the Ag matrix, and the lattice defects lower the heat resistance strength of the contact, and particularly deteriorate the welding resistance performance. . Incidentally, there is a method by powder metallurgy as a manufacturing method which does not form the above-mentioned thin layer. This method is prepared by previously oxidizing a powdery metal containing an element such as Sn or In, and solidifying an Ag alloy powder containing these oxides. This method is also called a pre-oxidation method. However, in the contact obtained by the pre-oxidation method, a dilute layer is certainly not formed, but the heat resistance is weak because a large number of lattice defects are generated in the Ag alloy due to the oxidation, and the contact manufacturing method aimed at by the present invention is as follows. not appropriate.
【０００７】本願の課題は、この様な現実を鑑みて、上
記問題点を解消し、毒性に問題の無いＣｄフリーのＡｇ
合金からなる、耐溶着特性の優れた電気接点、特に定格
電流１０Ａ以上、遮断電流１．５ＫＡ以上のブレーカー
に有用な電気接点および同接点を用いたブレーカーを提
供することである。In view of such a reality, the problem of the present application is to solve the above-mentioned problems and to provide a Cd-free Ag which has no toxicity problem.
An object of the present invention is to provide an electrical contact made of an alloy having excellent welding resistance, particularly useful for a breaker having a rated current of 10 A or more and a breaking current of 1.5 KA or more, and a breaker using the same.
【０００８】[0008]
【課題を解決するための手段】本発明は、ＳｎおよびＩ
ｎをともに３〜９質量％含む化学組成のＡｇ合金からな
る電気接点であり、前記Ａｇ合金に含まれる酸化物のア
スペクト比の平均値が２．５以上、５．０以下で、前記
接点の中央部に形成される酸化物の希薄な層の厚みが、
前記接点の厚みの０％を超え、３．０％未満である電気
接点である。さらに本発明は、この電気接点を用いたブ
レーカーである。The present invention provides Sn and I
An electrical contact made of an Ag alloy having a chemical composition containing n in the range of 3 to 9% by mass, wherein the average aspect ratio of oxides contained in the Ag alloy is 2.5 or more and 5.0 or less. The thickness of the thin oxide layer formed in the center is
The electrical contact is more than 0% and less than 3.0% of the thickness of the contact. Further, the present invention is a breaker using this electric contact.
【０００９】[0009]
【発明の実施の形態】本発明の電気接点は、Ｓｎおよび
Ｉｎをともに３〜９質量％含む化学組成を有し、残部は
Ａｇおよび不可避的不純物からなる。なお通常これらの
成分は、Ａｇマトリックス中に化合物、特に酸化物の形
態で分散される。Ｓｎの含有量を３〜９質量％とするの
は、３質量％未満では接点の耐溶着特性が劣化し、９質
量％を超えると接点の製造が困難になり温度特性も劣化
するからである。 好ましくは３．５〜６質量％であ
る。またＩｎの含有量を３〜９質量％とするのは、この
範囲外の含有量の場合には耐溶着特性や温度特性が劣化
するからであり、さらに９質量％を超えると、Ｓｎの含
有量にもよるが、接点の製造が困難になるからである。
好ましくは４〜６質量％である。BEST MODE FOR CARRYING OUT THE INVENTION The electrical contact of the present invention has a chemical composition containing both Sn and In in an amount of 3 to 9% by mass, and the balance is Ag and inevitable impurities. Incidentally, these components are usually dispersed in the Ag matrix in the form of a compound, particularly an oxide. The Sn content is set to 3 to 9% by mass because when the content is less than 3% by mass, the welding resistance of the contact deteriorates, and when it exceeds 9% by mass, the manufacturing of the contact becomes difficult and the temperature property also deteriorates. . It is preferably 3.5 to 6% by mass. Further, the reason for setting the In content to 3 to 9 mass% is that if the content is outside this range, the welding resistance characteristics and the temperature characteristics deteriorate, and if it exceeds 9 mass%, the Sn content is further increased. Although it depends on the quantity, it becomes difficult to manufacture the contact.
It is preferably 4 to 6% by mass.
【００１０】Ａｇ合金中の酸化物のアスペクト比の平均
値を２．５以上５以下とするのは、この範囲外では、酸
化物とＡｇマトリックスとの間に格子欠陥が多く生成す
るため、Ａｇ合金の耐熱強度が劣化するからである。ア
スペクト比の平均値が２．５未満では接点の耐溶着特性
が劣化し、５を越えても耐溶着特性や耐消耗特性が劣化
する。なお、本件のアスペクト値の平均値は、以下の方
法で算出される。接点の任意の切断面から任意に選んだ
５０００倍の光学顕微鏡視野に含まれる酸化物粒子につ
いて、その長径／短径、すなわちアスペクト比を測定す
る。この測定を１００個の酸化物粒子のアスペクト比が
得られるまで繰り返し、それら１００個の平均値をこの
接点の酸化物のアスペクト比の平均値とする。The average value of the aspect ratios of the oxides in the Ag alloy is set to 2.5 or more and 5 or less. Outside this range, many lattice defects are generated between the oxides and the Ag matrix. This is because the heat resistance strength of the alloy deteriorates. When the average value of the aspect ratio is less than 2.5, the welding resistance property of the contact deteriorates, and when it exceeds 5, the welding resistance property and wear resistance property deteriorate. In addition, the average value of the aspect values of the present case is calculated by the following method. The major axis / minor axis, that is, the aspect ratio of oxide particles contained in a 5000-fold optical microscope field arbitrarily selected from an arbitrary cut surface of a contact is measured. This measurement is repeated until the aspect ratio of 100 oxide particles is obtained, and the average value of these 100 particles is taken as the average value of the oxide aspect ratio of this contact.
【００１１】更に、接点中央部に形成される希薄層の厚
みが、接点の厚みの０％を超え、３．０％未満であると
する理由は以下の通りである。ブレーカー用の電気接点
は、所定の大電流を通電させたときの耐溶着性が必要で
あるとともに、大量の消耗が生じた場合でも繰り返しの
使用が可能でなければならない。従って、接点が実用上
優れた耐溶着性を有するためには、その厚み方向の全体
に渡って優れた耐溶着性を持つことが必要であり、耐熱
強度の低い希薄層の厚さは極力小さくする必要が有る。
特にそれが接点の厚みの３．０％以上になると、実用上
優れた耐溶着性を維持することができない。より好まし
くは、接点の厚みの０％を超え、１．５％以下である。
なお、本発明は、前述のように後酸化法によって得られ
る電気接点に関するものであり、その製法上、必然的に
希薄層が形成される。なお、本件の希薄層の厚みは、以
下の方法で算出される。接点の厚さ方向に平行な面で、
その接点を二等分するように切断する。その切断面の中
央部に現れている希薄層の、接点の厚さ方向と同じ方向
を希薄層の厚さ方向とし、接点の厚さ方向と垂直な方向
を希薄層の長さ方向とする。その希薄層の長さ方向の中
央から希薄層の長さの両側各３０％の範囲に当たる部分
を測定範囲とする。その測定範囲から任意の１０個所を
５００倍の光学顕微鏡で観察し、それぞれの観察個所に
対し、図２に示したように希薄層と周囲の正常組織との
上下の境界に線を引き、それらの線間（図２の矢印部
分）の長さを測定する。得られた１０個所の測定結果の
平均値をこの接点の希薄層の厚さとする。Further, the reason why the thickness of the thin layer formed at the center of the contact is more than 0% and less than 3.0% of the thickness of the contact is as follows. The electrical contacts for breakers must have resistance to welding when a predetermined large current is passed through them, and must be able to be used repeatedly even when a large amount of wear occurs. Therefore, in order for the contact to have excellent welding resistance in practical use, it is necessary to have excellent welding resistance throughout the thickness direction, and the thickness of the dilute layer with low heat resistance is as small as possible. Need to do.
In particular, if it is 3.0% or more of the thickness of the contact, practically excellent welding resistance cannot be maintained. More preferably, it is more than 0% and 1.5% or less of the thickness of the contact.
The present invention relates to an electrical contact obtained by the post-oxidation method as described above, and a dilute layer is inevitably formed due to its manufacturing method. The thickness of the dilute layer in this case is calculated by the following method. With a surface parallel to the thickness direction of the contact,
Cut the contact into two halves. The thin layer appearing at the center of the cut surface has the same direction as the thickness direction of the contact as the thickness direction of the thin layer, and the direction perpendicular to the thickness direction of the contact as the length direction of the thin layer. The measurement range is a portion corresponding to a range of 30% on both sides of the length of the diluted layer from the center in the lengthwise direction of the diluted layer. From the measurement range, 10 arbitrary spots were observed with a 500 × optical microscope, and a line was drawn at the upper and lower boundaries between the dilute layer and the surrounding normal tissue as shown in FIG. The length between the lines (the arrow in FIG. 2) is measured. The average value of the obtained measurement results at 10 points is taken as the thickness of the thin layer of this contact.
【００１２】本発明の電気接点には、上記の基本成分に
加え、さらにＳｂ、Ｃａ、Ｂｉ、Ｎｉ、Ｃｏ、Ｚｎまた
はＰｂの群から選ばれた少なくとも１種の元素が、従成
分として含まれていてもよい。通常これらの成分の大部
分は、Ａｇマトリックス中に化合物、特に酸化物の形態
で分散される。ただし個々の成分によって望ましい分散
量範囲が異なる。例えばいずれも元素換算された質量％
単位で０．０５〜２（Ｓｂ）、０．０３〜０．３（Ｃ
ａ）、０．０１〜１（Ｂｉ）、０．０２〜１．５（Ｎ
ｉ）、０．０２〜０．５（Ｃｏ）、０．０２〜８．５
（Ｚｎ）、０．０５〜５（Ｐｂ）である。なお括弧内は
対象元素である。以上の各成分種において、その量が上
記の範囲外になると、ブレーカーの種類によっては温度
特性が低下することがあり、特に上限を超えるとブレー
カーの種類によっては同時に耐溶着特性も低下すること
がある。In addition to the above-mentioned basic components, the electrical contact of the present invention further contains at least one element selected from the group of Sb, Ca, Bi, Ni, Co, Zn or Pb as a secondary component. May be. Usually most of these components are dispersed in the Ag matrix in the form of compounds, especially oxides. However, the desirable dispersion amount range differs depending on the individual components. For example, elemental mass%
0.05 to 2 (Sb), 0.03 to 0.3 (C
a), 0.01-1 (Bi), 0.02-1.5 (N
i), 0.02-0.5 (Co), 0.02-8.5
(Zn) and 0.05 to 5 (Pb). The elements in parentheses are target elements. In each of the above component types, if the amount is out of the above range, the temperature characteristics may be deteriorated depending on the type of breaker, and if it exceeds the upper limit, the welding resistance property may be decreased at the same time depending on the type of breaker. is there.
【００１３】通常は以上の従成分が接点の性能に若干影
響を及ぼすが、これ以外の成分としては、例えば以下の
ものが挙げられる。これらはいずれも本発明の目的の範
囲内で微量含まれても構わない。なお成分によって望ま
しい含有量が異なるが、括弧内数値の内元素記号で表示
されたものは、元素換算された質量％単位で、分子式で
表示のものは、同分子換算された質量％単位で表したそ
の許容上限値である。Ｃｅ、Ｌｉ、Ｃｒ、Ｌｉ、Ｓｒ、
Ｔｉ、Ｔｅ、Ｍｎ、ＡｌＦ３、ＣｒＦ３およびＣａＦ２
（５）、ＧｅおよびＧａ（３）、Ｓｉ（０．５）、Ｆｅ
およびＭｇ（０．１）。Usually, the above-mentioned subcomponents slightly affect the performance of the contact, but examples of the other components include the following. Any of these may be contained in a trace amount within the scope of the present invention. Although the desired content differs depending on the component, those indicated by the element symbol in the values in parentheses are expressed in element-converted mass% units, and those represented by molecular formulas are expressed in the same molecule-converted mass% units. It is the allowable upper limit value. Ce, Li, Cr, Li, Sr,
Ti, Te, Mn, AlF 3 , CrF 3 and CaF 2
(5), Ge and Ga (3), Si (0.5), Fe
And Mg (0.1).
【００１４】本発明者らは、電気接点に必要な前記した
いくつかの要求特性を満たす材料を探索してきた結果、
以上のような基本構成によれば、Ｃｄフリーの材料で従
来実現し得なかった優れた耐溶着特性と温度特性とを兼
ね備えた電気接点材料が提供可能であることを見出し
た。The present inventors have searched for materials satisfying the above-mentioned required characteristics required for electric contacts, and as a result,
It has been found that, with the above-described basic structure, it is possible to provide an electrical contact material having both excellent welding resistance characteristics and temperature characteristics that could not be realized conventionally with Cd-free materials.
【００１５】なお本発明の電気接点は、ブレーカーに組
み込むため台金などの他の部材と接続する必要がある。
したがって第二層の第一層とは反対側の面に他の部材と
の接続を容易にするため、純Ａｇ、ロウ材などの金属か
らなる薄い接続層を設けてもよい。なおこの層は、通常
この種の目的で配設される金属層と同じような形態であ
ればよい。The electric contact of the present invention must be connected to another member such as a base metal in order to be incorporated in the breaker.
Therefore, a thin connecting layer made of a metal such as pure Ag or a brazing material may be provided on the surface of the second layer opposite to the first layer to facilitate connection with other members. It should be noted that this layer may have a form similar to that of a metal layer usually provided for this type of purpose.
【００１６】次に本発明の電気接点の製造方法について
説明する。本発明の電気接点は、従来から行われてきた
この種のＡｇ合金と類似の後酸化法によって作られる。
例えば所望の化学組成となるように溶解・鋳造されたイ
ンゴットを粗圧延した後、必要により純Ａｇ圧延材を熱
間圧着する。これをさらに圧延して所定の厚みのフープ
にした後、同フープを打ち抜き、またはさらに成形し、
最終形状に近いサイズのＡｇ合金素材とし、さらにこの
素材を内部酸化してＳｎ、Ｉｎなどの金属成分を酸化物
に転換する。内部酸化は、大気から１００％酸素までの
酸素雰囲気中、１〜３０気圧、５００〜８５０℃、１０
〜１０００時間の範囲の条件で実施されることが好まし
い。なお溶解・鋳造に先立ち成分元素の酸化物以外の化
合物を含ませることもできる。また必要に応じて、圧延
等の塑性加工を施した後に適宜熱処理や形状を調整する
工程などを入れることもできる。Next, a method of manufacturing the electrical contact of the present invention will be described. The electrical contacts of the present invention are made by a post-oxidation method similar to the Ag alloys of this type that have been used conventionally.
For example, after roughly rolling an ingot melted and cast to have a desired chemical composition, a pure Ag rolled material is subjected to hot pressure bonding if necessary. This is further rolled into a hoop of a predetermined thickness, then the hoop is punched or further molded,
An Ag alloy material having a size close to the final shape is used, and this material is internally oxidized to convert metal components such as Sn and In to oxides. Internal oxidation is carried out in an oxygen atmosphere from the atmosphere to 100% oxygen at 1 to 30 atm, 500 to 850 ° C., 10
It is preferable to carry out the treatment under a condition of a range of from about 1000 hours. A compound other than the oxides of the component elements may be included before the melting / casting. Further, if necessary, a step of appropriately performing heat treatment or shape adjustment after performing plastic working such as rolling may be included.
【００１７】酸化物のアスペクト比をコントロールする
には、内部酸化工程の後で、７５０℃以上の高温下にお
いてＡｇ合金を全体を僅かに塑性変形させる条件下で塑
性加工を行えば良い。例えば真空ホットプレスやＨＩＰ
（熱間静水圧成形）を行う。その場合、窒素ガスまたは
不活性ガス雰囲気中あるいは真空中、７５０℃以上９０
０℃以下の温度で、１００〜５，０００ｋｇｆ／ｃｍ２
の圧力を加えることが好ましい。Ａｇ合金の塑性変形が
発生するまで加圧を続ける必要があるが、通常は１分程
度の加圧でも十分である。真空ホットプレスやＨＩＰに
より、金属に変形が加えられ、その結果アスペクト比の
大きすぎる酸化物は分断され、アスペクト比の小さい酸
化物は分断されない状態で残るため、本発明に示された
範囲にそのアスペクト比をコントロールすることが可能
になる。同時に酸化物とマトリックス相との間の格子欠
陥が少ない状態に修復される。塑性加工条件にもよるが
７５０℃より温度が低いとＡｇマトリックスが塑性変形
し難いため、十分な効果を得ることは難しい。真空ホッ
トプレスやＨＩＰ以外の方法としては、金属に高温下で
塑性加工を加えることのできる方法であれば、どのよう
な方法を用いてもかまわない。例えば、上記の雰囲気中
での熱間圧延法を用いても良い。ただし熱間圧延法の場
合には圧延量の微調整が必要になる。In order to control the aspect ratio of the oxide, plastic working may be carried out after the internal oxidation step at a high temperature of 750 ° C. or higher under the condition that the entire Ag alloy is slightly plastically deformed. For example, vacuum hot press or HIP
(Hot isostatic pressing) is performed. In that case, in a nitrogen gas or inert gas atmosphere or in a vacuum, 750 ° C or higher 90
100 to 5,000 kgf / cm 2 at a temperature of 0 ° C. or lower
It is preferable to apply the pressure. Pressurization needs to be continued until the plastic deformation of the Ag alloy occurs, but usually a pressurization of about 1 minute is sufficient. The metal is deformed by vacuum hot pressing or HIP, and as a result, an oxide having an excessively large aspect ratio is divided, and an oxide having a small aspect ratio remains undivided. It becomes possible to control the aspect ratio. At the same time, the state where the number of lattice defects between the oxide and the matrix phase is small is restored. Depending on the plastic working conditions, if the temperature is lower than 750 ° C., it is difficult to plastically deform the Ag matrix, and it is difficult to obtain a sufficient effect. As a method other than vacuum hot pressing and HIP, any method may be used as long as it is a method capable of performing plastic working on a metal at a high temperature. For example, a hot rolling method in the above atmosphere may be used. However, in the case of the hot rolling method, it is necessary to finely adjust the rolling amount.
【００１８】希薄層の厚みをコントロールするには、酸
化物形成時に少なくとも２回以上の内部酸化処理を行
い、これら内部酸化処理間に、高純度Ｎ２ガスまたは高
純度不活性ガス雰囲気中あるいは真空雰囲気中の焼鈍を
施せば良い。前述したように、内部酸化工程において
は、ＳｎやＩｎのような溶質成分はＡｇ合金の表面側へ
移動するので、これを一旦元に戻してやるために、溶質
成分の拡散均一化を目的とした焼鈍を行うのである。こ
の焼鈍は、すべての溶質成分が酸化してしまう前に行う
ことが効果的であり、具体的には、内部酸化処理を開始
後、全内部酸化処理時間の２０％〜７０％の間で内部酸
化処理を少なくとも１度中断し、この焼鈍を施した後、
内部酸化処理を再開すれば良い。この焼鈍は、溶質成分
の酸化を進行させない雰囲気で行う必要が有る。通常、
密閉型の炉を用い炉内を一旦少なくとも１０−４torr以
下に脱気した後、９９．９％以上の純度のＮ２ガスまた
はＡｒやＨｅ等の不活性ガスで置換した後に焼鈍を開始
するのが好ましい。また、真空雰囲気中で焼鈍する場合
も同様に真空度が低いと所望の効果が得られにくいた
め、炉内を１０−５torr以下とすることが好ましい。ま
た、焼鈍の温度・時間は、溶質成分を十分に拡散させＡ
ｇ合金マトリックス中に均一に分散しうる条件であれば
よい。具体的には、５００〜８５０℃の温度範囲で５分
〜１００時間の焼鈍時間が好ましい。この焼鈍には、以
上の条件調整が可能な焼成炉を用いるが、例えば、前述
の真空ホットプレスやＨＩＰであってもかまわない。In order to control the thickness of the dilute layer, an internal oxidation treatment is performed at least twice during oxide formation, and a high purity N 2 gas or high purity inert gas atmosphere or vacuum is provided between these internal oxidation treatments. It may be annealed in the atmosphere. As described above, in the internal oxidation step, solute components such as Sn and In move to the surface side of the Ag alloy, so that the solute components are temporarily restored so that the solute components are uniformly diffused. It is annealed. It is effective to perform this annealing before all the solute components are oxidized. Specifically, after the internal oxidation treatment is started, the internal annealing is performed within 20% to 70% of the total internal oxidation treatment time. After interrupting the oxidation treatment at least once and performing this annealing,
The internal oxidation process may be restarted. This annealing needs to be performed in an atmosphere in which the solute components do not oxidize. Normal,
After degassing the inside of the furnace to at least 10 −4 torr or less using a closed furnace, and then replacing it with N 2 gas having a purity of 99.9% or more or an inert gas such as Ar or He, and then annealing. Is preferred. Similarly, when annealing is performed in a vacuum atmosphere, it is difficult to obtain the desired effect if the degree of vacuum is low. Therefore, it is preferable to set the inside of the furnace to 10 −5 torr or less. Also, the annealing temperature and time should be set so that the solute components are sufficiently diffused.
The condition is that it can be uniformly dispersed in the g-alloy matrix. Specifically, an annealing time of 5 minutes to 100 hours in a temperature range of 500 to 850 ° C. is preferable. A firing furnace capable of adjusting the above conditions is used for this annealing, but the above-mentioned vacuum hot press or HIP may be used, for example.
【００１９】（実施例１）表１の試料番号３〜８及び１
７、１８の「鋳造組成」欄に示す化学組成のＡｇ合金を
溶解・鋳造してインゴットを作製した。これらを粗加工
した後、このＡｇ合金と純Ａｇのインゴットを重ね合わ
せ、アルゴン雰囲気中８５０℃で圧着し、Ａｇ合金とそ
の１／１０の厚みの純Ａｇ層からなる複合素材を作製し
た。さらに冷間圧延してフープ状素材とし、これを打ち
抜いて、幅４．０ｍｍ、長さ６．５ｍｍ、厚み１．８ｍ
ｍの形状１と幅４．５ｍｍ、長さが６ｍｍ、厚み１ｍｍ
の形状２の二つの形状の接点チップを作製した。得られ
たチップを４気圧の酸素雰囲気中７５０℃で合計１７０
時間保持して内部酸化処理を行った。この内部酸化工程
において、内部酸化が所定時間の４０％完了した段階で
一旦降温し、これらの接点チップを１０−６torrの真空
中にて８００℃の温度で３０ｈ保持した。その後、再び
同一の条件で内部酸化を再開し、所定時間の内部酸化処
理を完了した。これら内部酸化処理後の接点チップを圧
力２，５００ｋｇｆ／ｃｍ ２の純Ａｒ雰囲気中７８０℃
において４時間のＨＩＰ処理を施し、表１の試料番号３
〜８及び１７，１８に示した接点試片とした。なお、表
１には、前述の測定方法により測定した、酸化物のアス
ペクト比の平均値と、希薄層の厚みを記した。(Example 1) Sample numbers 3 to 8 and 1 in Table 1
The Ag alloy of the chemical composition shown in the column 7 "Casting composition"
An ingot was prepared by melting and casting. Roughing these
After that, superimpose this Ag alloy and pure Ag ingot
And press-bond it in an argon atmosphere at 850 ° C.
A composite material consisting of a pure Ag layer with a thickness of 1/10 of
It was Further cold rolling into a hoop-shaped material, which is punched
Pull out, width 4.0mm, length 6.5mm, thickness 1.8m
m shape 1, width 4.5 mm, length 6 mm, thickness 1 mm
Two shape contact chips of shape 2 were manufactured. Obtained
170 chips in total at 750 ° C in an oxygen atmosphere of 4 atm.
The internal oxidation treatment was performed while holding the time. This internal oxidation process
At the stage when internal oxidation was completed 40% of the predetermined time
Once the temperature is lowered, these contact tips are-6torr vacuum
The temperature was kept at 800 ° C. for 30 hours. Then again
The internal oxidation is restarted under the same conditions, and the internal oxidation treatment is performed for a predetermined time.
Completed the reason. Press the contact tip after these internal oxidation treatments.
Power 2,500kgf / cm Two780 ℃ in pure Ar atmosphere
HIP treatment for 4 hours at
The contact test pieces shown in FIGS. The table
1 is the oxide asbestos measured by the above-mentioned measuring method.
The average value of the pect ratio and the thickness of the thin layer are shown.
【００２０】次いで図１のような形状の固定側および可
動側の電気銅製台金を準備し、形状１の電気接点を固定
側台金に、形状２の電気接点を可動側台金にそれぞれ銀
ロウ付けした。なお図において１は電気接点、２は台金
であり、ａが固定側、ｂが可動側のそれぞれのアッセン
ブリーを示す。その後、定格ＡＣ５０Ａフレームのブレ
ーカーに固定した。このようなブレーカーアッセンブリ
ーを各試料番号の接点チップ対毎に各３台用意した。ま
ず各試料の全てのアッセンブリーを使って、定格電流を
１００分間通電し初期の温度特性を確認した。温度特性
は、電源側端子部の室温からの昇温値を測定した。この
結果を表２の「初期の温度特性」欄に示した。次に２０
０Ｖ負荷状態において、３ｋＡの遮断電流で、３回の大
電流投入遮断試験を各々１台ずつのアッセンブリーを使
って行い、耐溶着性を確認した。次いで短絡試験を行っ
た後、再び定格電流を１００分間通電して、遮断試験後
の温度特性を確認した。この結果を表２の「短絡試験後
の温度特性」欄に示した。さらに、耐溶着性のみを確認
する目的で、引き続きＡＣ４４０Ｖにて、２．５ｋＡ、
及び２００Ｖで１．５ｋＡの条件での遮断試験をそれぞ
れ６回行った。この評価では、［全遮断回数×３（１ア
ッセンブリーの接点数）］を分母とし、［溶着した接点
数］を分子とした割合を求めた。ただし、試験途中で接
点の溶着が発生した場合は、それまでの遮断回数を採用
した。この結果を表２の「耐溶着特性」欄に示した。Next, a fixed side and a movable side electric copper base metal having a shape as shown in FIG. 1 are prepared, and the electric contact of the shape 1 is used for the fixed base metal, and the electric contact of the shape 2 is used for the movable base metal. I brazed it. In the figure, 1 is an electric contact, 2 is a base metal, a is a fixed side assembly, and b is a movable side assembly. Then, it was fixed to a breaker with a rated AC50A frame. Three such breaker assemblies were prepared for each contact tip pair of each sample number. First, using all the assemblies of each sample, a rated current was applied for 100 minutes to confirm the initial temperature characteristics. As the temperature characteristics, the temperature rise value from the room temperature of the power source side terminal portion was measured. The results are shown in the "Initial temperature characteristic" column of Table 2. Then 20
In a 0V load condition, a large-current breaking test was conducted three times at a breaking current of 3 kA using one assembly each, and welding resistance was confirmed. Then, after performing a short-circuit test, the rated current was again passed for 100 minutes to confirm the temperature characteristics after the interruption test. The results are shown in the "Temperature characteristics after short circuit test" column of Table 2. Further, for the purpose of confirming only the welding resistance, continuously at AC440V, 2.5 kA,
And the interruption | blocking test on condition of 200V and 1.5kA was performed 6 times, respectively. In this evaluation, the ratio of [total number of breaks × 3 (number of contacts in one assembly)] as the denominator and [number of welded contacts] as the numerator was obtained. However, if welding of the contacts occurred during the test, the number of interruptions up to that point was adopted. The results are shown in the "adhesion resistance" column of Table 2.
【００２１】過負荷試験は、初期温度特性を確認した別
のアッセンブリーを使い、５０Ａフレームの同定格電流
の６倍の電流を流した状態で、５秒のタイムスパンにて
開閉を５０回行い、その後上記初期確認時と同じ条件で
過負荷試験後の温度特性を確認した。この結果を表２の
「過負荷試験後の温度特性」欄に示した。耐久試験は、
初期温度特性を確認したアッセンブリーを使い、定格電
流を流した状態で、５秒のタイムスパンにて開閉を６０
００回行い、その後無負荷状態において更に４０００回
の開閉を行い、その後上記初期確認時と同じ条件で耐久
試験後の温度特性を確認した。この結果を表２の「耐久
試験後の温度特性」欄に示した。なお、温度特性は、ク
ロメルアルメル熱電対を用いて、ブレーカーの端子部の
室温からの温度上昇分を測定した。表２の「温度特性
（K）」欄の値は、上記測定による温度上昇分を[ K]単
位で示したものである。In the overload test, another assembly whose initial temperature characteristics were confirmed was used, and a switch was opened and closed 50 times in a time span of 5 seconds with a current of 6 times the rated current of 50 A frame being applied. Then, the temperature characteristics after the overload test were confirmed under the same conditions as in the initial confirmation. The results are shown in the "Temperature characteristics after overload test" column of Table 2. The durability test is
Using the assembly that confirmed the initial temperature characteristics, open and close 60 times in a time span of 5 seconds with the rated current flowing.
It was performed 00 times, and then opened and closed 4000 times more in the unloaded state, and then the temperature characteristics after the durability test were confirmed under the same conditions as in the initial confirmation. The results are shown in the "Temperature characteristics after durability test" column of Table 2. As for the temperature characteristics, a chromel alumel thermocouple was used to measure the temperature increase from the room temperature at the terminal of the breaker. The values in the “Temperature characteristics (K)” column of Table 2 indicate the temperature increase by the above measurement in [K] units.
【００２２】（比較例１）表１の試料番号１，２，９及
び１０の「鋳造組成」欄に示した化学組成以外は、実施
例１とまったく同様に接点試片の作製および評価を行っ
た。その結果を表２に示した。(Comparative Example 1) A contact test piece was prepared and evaluated in exactly the same manner as in Example 1 except for the chemical composition shown in the "Casting composition" column of sample numbers 1, 2, 9 and 10 in Table 1. It was The results are shown in Table 2.
【００２３】（実施例２）表１の試料番号１２及び１３
の「鋳造組成」欄に示した化学組成でＡｇ合金を作製
し、内部酸化後の塑性加工の条件を試料番号１２の試料
に対しては、８００℃において２，９００ｋｇｆ／ｃｍ
２、試料番号１３の試料に対しては、７６０℃において
１，５００ｋｇｆ／ｃｍ２とした以外は、実施例１とま
ったく同様に接点試片の作製および評価を行った。表１
に、作製した試料の酸化物のアスペクト比と希薄層の厚
みを示した。また、表２に評価結果を示した。Example 2 Sample Nos. 12 and 13 in Table 1
For the sample of Sample No. 12, an Ag alloy was prepared with the chemical composition shown in the column "Casting composition", and the plastic working condition after internal oxidation was 2,900 kgf / cm at 800 ° C.
2. With respect to the sample of Sample No. 13, a contact test piece was prepared and evaluated in exactly the same manner as in Example 1 except that the sample was 1,500 kgf / cm 2 at 760 ° C. Table 1
Fig. 2 shows the oxide aspect ratio and the thickness of the dilute layer of the prepared sample. The evaluation results are shown in Table 2.
【００２４】（比較例２）表１の試料番号１１及び１４
の「鋳造組成」欄に示した化学組成でＡｇ合金を作製
し、内部酸化後の塑性加工の条件を試料番号１１の試料
に対しては、９１０℃において２，０００ｋｇｆ／ｃｍ
２、試料番号１４の試料に対しては、７００℃において
２，０００ｋｇｆ／ｃｍ２とした以外は、実施例１とま
ったく同様に接点試片の作製および評価を行った。表１
に、作製した試料の酸化物のアスペクト比と希薄層の厚
みを示した。また、表２に評価結果を示した。Comparative Example 2 Sample Nos. 11 and 14 in Table 1
For the sample of Sample No. 11, an Ag alloy was prepared with the chemical composition shown in the "Casting composition" column, and the plastic working condition after internal oxidation was 2,000 kgf / cm at 910 ° C.
2. With respect to the sample of Sample No. 14, a contact test piece was prepared and evaluated in exactly the same manner as in Example 1 except that the sample was 2,000 kgf / cm 2 at 700 ° C. Table 1
Fig. 2 shows the oxide aspect ratio and the thickness of the dilute layer of the prepared sample. The evaluation results are shown in Table 2.
【００２５】（実施例３）表１の試料番号１５の「鋳造
組成」欄に示した化学組成でＡｇ合金を作製し、内部酸
化工程中の焼鈍の温度を６５０℃とした以外は、実施例
１とまったく同様に接点試片の作製および評価を行っ
た。表１に、作製した試料の酸化物のアスペクト比と希
薄層の厚みを示した。また、表２に評価結果を示した。(Example 3) Example 3 except that an Ag alloy was prepared with the chemical composition shown in the column "Casting composition" of sample No. 15 in Table 1 and the annealing temperature during the internal oxidation step was 650 ° C. A contact test piece was prepared and evaluated in exactly the same manner as in 1. Table 1 shows the aspect ratio of the oxide and the thickness of the dilute layer of the produced sample. The evaluation results are shown in Table 2.
【００２６】（比較例３）表１の試料番号１６の「鋳造
組成」欄に示した化学組成でＡｇ合金を作製し、内部酸
化工程中の焼鈍の温度を４５０℃とした以外は、実施例
１とまったく同様に接点試片の作製および評価を行っ
た。表１に、作製した試料の酸化物のアスペクト比と希
薄層の厚みを示した。また、表２に評価結果を示した。Comparative Example 3 An Ag alloy was prepared with the chemical composition shown in the "Casting composition" column of Sample No. 16 in Table 1 and the annealing temperature during the internal oxidation step was 450 ° C. A contact test piece was prepared and evaluated in exactly the same manner as in 1. Table 1 shows the aspect ratio of the oxide and the thickness of the dilute layer of the produced sample. The evaluation results are shown in Table 2.
【００２７】（比較例４）表１の試料番号１９、２０の
「鋳造組成」欄に示した化学組成でＡｇ合金を作製し、
内部酸化工程において、途中での焼鈍を行うことなく連
続して内部酸化処理を行い、内部酸化後の塑性加工も実
施せず、それら以外は実施例１と同様に試料を作成し
た。表１に、作製した試料の酸化物のアスペクト比と希
薄層の厚みを示した。また、得られた接点を実施例１と
同一の条件にて評価した。その結果を表２に示した。(Comparative Example 4) An Ag alloy having the chemical composition shown in the column "Casting composition" of sample numbers 19 and 20 in Table 1 was prepared.
In the internal oxidation step, a sample was prepared in the same manner as in Example 1 except that the internal oxidation treatment was continuously performed without performing the annealing in the middle and the plastic working after the internal oxidation was not performed. Table 1 shows the aspect ratio of the oxide and the thickness of the dilute layer of the produced sample. Further, the obtained contacts were evaluated under the same conditions as in Example 1. The results are shown in Table 2.
【００２８】[0028]
【表１】 [Table 1]
【００２９】[0029]
【表２】 [Table 2]
【００３０】以上の結果から以下のことが分かる。
（１）ＳｎおよびＩｎをともに３〜９質量％含む化学組
成のＡｇ合金からなる接点であり、Ａｇ合金に含まれる
酸化物のアスペクト比の平均値が２．５以上、５．０以
下であり、酸化物の希薄な層の厚みが、接点の厚みの０
％を超え、３．０％未満である本発明の接点を用いたブ
レーカーは、上記評価において充分実用可能な範囲内に
ある。一方本発明範囲外の接点を用いたブレーカーは、
実用レベルに達していない。即ち耐溶着性に関しては０
％よりも大きい値を示し、短絡試験後温度特性に関して
は、８０Ｋを越える実用レベルとしては望ましくない温
度を示し、それ以外の温度特性に関しても６０Ｋを越え
る実用レベルとしては望ましくない温度を示した。
（２）ＳｎおよびＩｎに加えＣｏなどの成分を少量含ん
だ場合でも同様のことが言える。From the above results, the following can be seen.
(1) A contact made of an Ag alloy having a chemical composition containing both 3 and 9 mass% of Sn and In, and an average aspect ratio of oxides contained in the Ag alloy is 2.5 or more and 5.0 or less. , The thickness of the oxide thin layer is 0 of the contact thickness.
%, Less than 3.0%, the breaker using the contact of the present invention is in a practically sufficient range in the above evaluation. On the other hand, a breaker using a contact outside the scope of the present invention,
Not at a practical level. That is, the welding resistance is 0
%, The temperature characteristics after the short circuit test showed an undesired temperature as a practical level exceeding 80K, and the other temperature characteristics showed an undesirable temperature as a practical level exceeding 60K.
(2) The same can be said when a small amount of a component such as Co is contained in addition to Sn and In.
【００３１】[0031]
【発明の効果】以上述べたように、本発明の電気接点
は、ＳｎとＩｎをともに３〜９質量％含むＡｇ合金から
なり、Ａｇ合金に含まれる酸化物のアスペクト比の平均
値が２．５以上、５．０以下であり、酸化物の希薄な層
の厚みが、接点の厚みの０％を超え、３．０％未満であ
るため、従来Ｃｄ入りのＡｇ合金でしか到達し得なかっ
た優れた耐溶着特性と温度特性を兼ね備えた接点電気特
性を有する。したがってＣｄフリー入りのＡｇ合金から
なる電気接点に代わって、ブレーカー用の接点として利
用できる。さらに本発明によれば、以上の電気接点を用
いたブレーカーを提供することができる。As described above, the electric contact of the present invention is made of an Ag alloy containing both Sn and In in an amount of 3 to 9 mass%, and the average aspect ratio of oxides contained in the Ag alloy is 2. It is 5 or more and 5.0 or less, and the thickness of the oxide thin layer is more than 0% and less than 3.0% of the thickness of the contact, and thus can be reached only by the conventional Ag alloy containing Cd. It also has excellent electrical characteristics of contacts that have excellent welding resistance and temperature characteristics. Therefore, it can be used as a contact for a breaker in place of the electrical contact made of Ag alloy containing Cd free. Further, according to the present invention, it is possible to provide a breaker using the above electrical contacts.
【図１】本発明の実施例の電気試験に用いた接点アッセ
ンブリーを模式的に示す図である。FIG. 1 is a diagram schematically showing a contact assembly used in an electrical test of an example of the present invention.
【図２】本発明の電気接点の中央部切断面にある希薄層
部分を示した光学顕微鏡写真である。FIG. 2 is an optical micrograph showing a thin layer portion on a cut surface of a central portion of an electric contact of the present invention.
１、電気接点 ２、台金 1, electrical contact 2, base money
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｆ 1/00 ６６１ Ｃ２２Ｆ 1/00 ６６１Ａ ６８３ ６８３ ６８５ ６８５Ｚ ６８６ ６８６Ｂ ６９１ ６９１Ｂ ６９１Ｃ ６９４ ６９４Ｂ 1/02 1/02 Ｈ０１Ｈ 1/02 Ｈ０１Ｈ 1/02 Ｂ Ｆターム(参考） 4K020 AA21 AB01 AC05 BB31 BC01 5G030 AA04 AA08 XX00 5G050 AA01 AA08 AA11 AA19 AA29 AA33 AA40 AA45 AA53 BA01 CA05 DA04 ─────────────────────────────────────────────────── ─── Continuation of front page (51) Int.Cl. 7 Identification code FI theme code (reference) C22F 1/00 661 C22F 1/00 661A 683 683 685 685Z 686 686B 691 691B 691C 694 694B 1/02 1/02 H01H 1/02 H01H 1/02 BF term (reference) 4K020 AA21 AB01 AC05 BB31 BC01 5G030 AA04 AA08 XX00 5G050 AA01 AA08 AA11 AA19 AA29 AA33 AA40 AA45 AA53 BA01 CA05 DA04
Claims (5)
化学組成のＡｇ合金からなる電気接点であり、前記Ａｇ
合金に含まれる酸化物のアスペクト比の平均値が２．５
以上、５．０以下であり、前記接点の中央部に形成され
る酸化物の希薄な層の厚みが、前記接点の厚みの０％を
超え、３．０％未満であることを特徴とする電気接点。1. An electrical contact comprising an Ag alloy having a chemical composition containing both Sn and In in an amount of 3 to 9% by mass.
The average aspect ratio of the oxides contained in the alloy is 2.5
As described above, the thickness is 5.0 or less, and the thickness of the oxide thin layer formed in the central portion of the contact is more than 0% and less than 3.0% of the thickness of the contact. Electrical contacts.
量％、Ｉｎ含有量が４〜６質量％である請求項１に記載
の電気接点。2. The electrical contact according to claim 1, wherein the Ag alloy has a Sn content of 3.5 to 6 mass% and an In content of 4 to 6 mass%.
にＳｂ、Ｃａ、Ｂｉ、Ｎｉ、Ｃｏ 、ＺｎまたはＰｂの
群から選ばれた少なくとも１種の元素を含む請求項１に
記載の電気接点。3. The electricity according to claim 1, wherein the Ag alloy further contains at least one element selected from the group of Sb, Ca, Bi, Ni, Co, Zn or Pb in addition to Sn and In. contact.
金属を配合し、溶解、鋳造することによって、Ｓｎおよ
びＩｎをともに３〜９質量％含有するＡｇ合金のインゴ
ットを形成する工程と、前記インゴットを塑性加工する
工程と、前記塑性加工されたＡｇ合金を成形する工程
と、Ａｇ合金中のＳｎ及びＩｎを酸化させる内部酸化工
程を含む電気接点の製造方法であり、前記内部酸化工程
が少なくとも２回以上に分割され、それらの間に、Ａｇ
合金を高純度窒素ガスまたは高純度不活性ガス雰囲気中
あるいは真空雰囲気中で焼鈍し、前記内部酸化工程完了
後のＡｇ合金に７５０℃以上の温度で塑性加工を施すこ
とを特徴とする電気接点の製造方法。4. Ag metal and at least Sn metal and In
A step of forming an ingot of an Ag alloy containing Sn and In in an amount of 3 to 9 mass% by blending a metal, melting and casting, a step of plastically working the ingot, and the plastically worked Ag alloy And an internal oxidation step of oxidizing Sn and In in an Ag alloy, wherein the internal oxidation step is divided into at least two or more times, and Ag
The alloy is annealed in a high-purity nitrogen gas or a high-purity inert gas atmosphere or in a vacuum atmosphere, and the Ag alloy after the completion of the internal oxidation step is subjected to plastic working at a temperature of 750 ° C. or higher. Production method.
接点を用いたブレーカー。5. A breaker using the electrical contact according to any one of claims 1 to 4.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002088015A JP4045826B2 (en) | 2002-03-27 | 2002-03-27 | Kadomi-free electrical contacts and breakers using the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002088015A JP4045826B2 (en) | 2002-03-27 | 2002-03-27 | Kadomi-free electrical contacts and breakers using the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2003288831A true JP2003288831A (en) | 2003-10-10 |
| JP4045826B2 JP4045826B2 (en) | 2008-02-13 |
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ID=29234013
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2002088015A Expired - Fee Related JP4045826B2 (en) | 2002-03-27 | 2002-03-27 | Kadomi-free electrical contacts and breakers using the same |
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| Country | Link |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2009041246A1 (en) * | 2007-09-25 | 2009-04-02 | A.L.M.T.Corp. | Process for producing contact member, contact member, and switch |
-
2002
- 2002-03-27 JP JP2002088015A patent/JP4045826B2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2009041246A1 (en) * | 2007-09-25 | 2009-04-02 | A.L.M.T.Corp. | Process for producing contact member, contact member, and switch |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4045826B2 (en) | 2008-02-13 |
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