JPH07188702A - Ag-base alloy powder and its production - Google Patents
Ag-base alloy powder and its productionInfo
- Publication number
- JPH07188702A JPH07188702A JP5329419A JP32941993A JPH07188702A JP H07188702 A JPH07188702 A JP H07188702A JP 5329419 A JP5329419 A JP 5329419A JP 32941993 A JP32941993 A JP 32941993A JP H07188702 A JPH07188702 A JP H07188702A
- Authority
- JP
- Japan
- Prior art keywords
- alloy powder
- based alloy
- particle size
- particles
- weight
- 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.)
- Withdrawn
Links
- 239000000843 powder Substances 0.000 title claims abstract description 98
- 239000000956 alloy Substances 0.000 title claims abstract description 91
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 91
- 238000004519 manufacturing process Methods 0.000 title claims description 21
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 32
- 239000001301 oxygen Substances 0.000 claims abstract description 32
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 32
- 239000011159 matrix material Substances 0.000 claims abstract description 26
- 229910052742 iron Inorganic materials 0.000 claims abstract description 23
- 229910052709 silver Inorganic materials 0.000 claims abstract description 14
- 238000009692 water atomization Methods 0.000 claims abstract description 14
- 230000001590 oxidative effect Effects 0.000 claims abstract description 5
- 239000002245 particle Substances 0.000 claims description 67
- 238000000034 method Methods 0.000 claims description 33
- 230000003647 oxidation Effects 0.000 abstract description 14
- 238000007254 oxidation reaction Methods 0.000 abstract description 14
- 238000007712 rapid solidification Methods 0.000 abstract description 5
- 239000000203 mixture Substances 0.000 abstract 2
- 230000001105 regulatory effect Effects 0.000 abstract 2
- 239000000155 melt Substances 0.000 description 15
- 229910052751 metal Inorganic materials 0.000 description 12
- 239000002184 metal Substances 0.000 description 12
- 238000010521 absorption reaction Methods 0.000 description 9
- 239000007789 gas Substances 0.000 description 8
- 238000002844 melting Methods 0.000 description 8
- 230000008018 melting Effects 0.000 description 8
- 239000011812 mixed powder Substances 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 238000009689 gas atomisation Methods 0.000 description 6
- 238000001816 cooling Methods 0.000 description 4
- 239000010419 fine particle Substances 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- 229910002701 Ag-Co Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 239000004020 conductor Substances 0.000 description 2
- 230000008520 organization Effects 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 238000000889 atomisation Methods 0.000 description 1
- 238000001354 calcination Methods 0.000 description 1
- 239000011362 coarse particle Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000005191 phase separation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01H—ELECTRIC SWITCHES; RELAYS; SELECTORS; EMERGENCY PROTECTIVE DEVICES
- H01H1/00—Contacts
- H01H1/02—Contacts characterised by the material thereof
- H01H1/021—Composite material
- H01H1/023—Composite material having a noble metal as the basic material
- H01H1/0237—Composite material having a noble metal as the basic material and containing oxides
- H01H2001/02378—Composite material having a noble metal as the basic material and containing oxides containing iron-oxide as major component
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、例えば電気接点、電
極、モータ用ブラシ等に使用される導電性材料を製造す
るための原料として好適なAg基合金粉末及びその製造方
法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an Ag-based alloy powder suitable as a raw material for producing a conductive material used in, for example, electric contacts, electrodes, brushes for motors, etc., and a method for producing the same.
【０００２】[0002]
【従来の技術】従来、電気接点、電極等に使用される導
電性材料用の原料として、Agマトリックス中にAgと二相
分離する金属からなる粒径0.01〜1.0 μｍの粒子が分散
されているAg基合金粉末が知られていて、このAg基合金
粉末を原料として製造された接点材料は耐溶着性に優れ
ている。（特開昭63-238229 参照）Agと二相分離する代
表的な金属としては、Fe、Co、Niが挙げられ、なかでも
FeまたはCoを含有したAg基合金粉末はFe及びCoの融点が
Niより高いために耐熱性が要求される用途への適用が期
待されている。しかし、従来のFeまたはCoの粒子が分散
されているAg基合金粉末に関しては、この粉末を成形、
焼結し、次いで伸線して得られる線材は電気伝導度は優
れるが、硬度が十分でなく、そのために例えば電気接点
としたときに耐消耗性が不十分であるという問題があっ
た。2. Description of the Related Art Conventionally, as a raw material for a conductive material used for electric contacts, electrodes, etc., particles having a particle diameter of 0.01 to 1.0 μm, which are made of a metal which is phase-separated from Ag, are dispersed in an Ag matrix. An Ag-based alloy powder is known, and a contact material produced from this Ag-based alloy powder as a raw material has excellent welding resistance. (See Japanese Patent Laid-Open No. 63-238229) Fe, Co, and Ni are typical metals that undergo two-phase separation from Ag.
Ag-based alloy powders containing Fe or Co have melting points of Fe and Co
Since it is higher than Ni, it is expected to be applied to applications requiring heat resistance. However, regarding the Ag-based alloy powder in which the particles of conventional Fe or Co are dispersed, this powder is molded,
The wire obtained by sintering and then drawing is excellent in electric conductivity, but has insufficient hardness, and therefore, there is a problem that the wear resistance is insufficient when it is used as an electrical contact, for example.
【０００３】[0003]
【発明が解決しようとする課題】上記の事情に鑑みて、
本発明は高電気伝導度であって、かつ、高硬度である線
材が得られる、FeまたはCoを含有した粒子が分散されて
いるAg基合金粉末を提供することを課題とし、このよう
な有用なAg基合金粉末を得ることのできる製造方法を提
供することを第２の課題とする。In view of the above circumstances,
It is an object of the present invention to provide an Ag-based alloy powder in which particles containing Fe or Co are dispersed, which is capable of obtaining a wire having high electrical conductivity and high hardness. A second object is to provide a manufacturing method capable of obtaining a stable Ag-based alloy powder.
【０００４】[0004]
【課題を解決するための手段】前記第１の課題を解決す
るために、請求項１記載の発明に係るAg基合金粉末は、
Agマトリックス中にFe及びFeの酸化物の少なくとも一方
からなる、粒径0.01〜1.0 μｍの粒子が分散されてお
り、さらに、酸素含有量が0.03重量％以上であり、か
つ、前記の粒径0.01〜1.0 μｍの粒子の含有量がFe元素
量換算で 0.5〜5.0重量％であることを特徴とし、請求
項２記載の発明に係るAg基合金粉末はAgマトリックス中
にCo及びCoの酸化物の少なくとも一方からなる、粒径0.
01〜1.0 μｍの粒子が分散されており、さらに、酸素含
有量が0.03重量％以上であり、かつ、前記の粒径0.01〜
1.0 μｍの粒子の含有量がCo元素量換算で 0.5〜5.0 重
量％であることを特徴としている。In order to solve the first problem, the Ag-based alloy powder according to the invention of claim 1 is
Particles having a particle size of 0.01 to 1.0 μm, which are composed of at least one of Fe and an oxide of Fe, are dispersed in an Ag matrix, and further, the oxygen content is 0.03% by weight or more, and the particle size is 0.01. The content of particles of 1.0 μm to 1.0 μm is 0.5 to 5.0% by weight in terms of the amount of Fe element. The Ag-based alloy powder according to the invention of claim 2 comprises Co and Co oxides in the Ag matrix. Particle size 0, consisting of at least one.
Particles of 01 to 1.0 μm are dispersed, the oxygen content is 0.03% by weight or more, and the particle diameter is 0.01 to
The content of 1.0 μm particles is 0.5 to 5.0% by weight in terms of Co element content.
【０００５】前記第２の課題を解決するために、請求項
３記載の発明に係るAg基合金粉末の製造方法は、請求項
１記載のAg基合金粉末の製造方法において、Ag及びFeの
混合溶湯を、水アトマイズ法で急冷凝固させてAg基合金
粉末を得ることを特徴とし、請求項４記載の発明に係る
Ag基合金粉末の製造方法は、請求項２記載のAg基合金粉
末の製造方法において、Ag及びCoの混合溶湯を、水アト
マイズ法で急冷凝固させてAg基合金粉末を得ることを特
徴とし、請求項５記載の発明に係るAg基合金粉末の製造
方法は、請求項１または請求項２記載のAg基合金粉末の
製造方法において、合金粉末を酸化雰囲気中で熱処理し
て内部酸化させる工程を経てAg基合金粉末を得ることを
特徴としている。In order to solve the second problem, the method for producing Ag-based alloy powder according to the invention of claim 3 is the same as the method for producing Ag-based alloy powder according to claim 1, in which Ag and Fe are mixed. According to the invention of claim 4, characterized in that the molten metal is rapidly solidified by a water atomizing method to obtain an Ag-based alloy powder.
The method for producing an Ag-based alloy powder is characterized in that, in the method for producing an Ag-based alloy powder according to claim 2, a mixed molten metal of Ag and Co is rapidly solidified by a water atomizing method to obtain an Ag-based alloy powder, A method for producing an Ag-based alloy powder according to a fifth aspect of the present invention is the method for producing an Ag-based alloy powder according to the first or second aspect, which comprises a step of heat-treating the alloy powder in an oxidizing atmosphere for internal oxidation. It is characterized in that the Ag-based alloy powder is obtained after that.
【０００６】以下本発明を詳細に説明する。本発明で粒
径0.01〜1.0 μｍの粒子の含有量がFe元素量換算で 0.5
〜5.0 重量％であること、または粒径0.01〜1.0 μｍの
粒子の含有量がCo元素量換算で 0.5〜5.0 重量％である
ことと限定しているのは、 0.5％未満では十分な硬度の
線材が得られなくなり、5.0 ％を越えて含有させること
は製造面で困難なためである。すなわち、FeまたはCo
の、Ag溶湯中への固溶限界が５％であり、５％を越える
とアトマイズ後にFeまたはCoの粗大粒子が生成してしま
う。また、本発明で酸素含有量が0.03重量％以上である
ことと限定しているのは、酸素含有量が0.03重量％未満
と少ないと、Ag基合金粉末を成形、焼結し、次いで伸線
して得られる線材における、FeまたはCoの酸化物の含有
量が少なくなり、その結果十分な硬度の線材が得られな
いためである。The present invention will be described in detail below. In the present invention, the content of particles having a particle size of 0.01 to 1.0 μm is 0.5 in terms of the amount of Fe element.
~ 5.0 wt%, or the content of particles with a particle size of 0.01 ~ 1.0 μm is 0.5 ~ 5.0 wt% in terms of Co element amount is limited to less than 0.5% of sufficient hardness. This is because it becomes difficult to obtain a wire rod, and it is difficult to contain more than 5.0% in terms of manufacturing. Ie Fe or Co
However, the solid solution limit in the Ag melt is 5%, and if it exceeds 5%, coarse particles of Fe or Co will be formed after atomization. Further, the oxygen content is limited to 0.03 wt% or more in the present invention, the oxygen content is less than 0.03 wt%, the Ag-based alloy powder is molded, sintered, and then drawn. This is because the content of the oxide of Fe or Co in the wire rod thus obtained is small, and as a result, a wire rod having a sufficient hardness cannot be obtained.
【０００７】本発明における、Ag基合金粉末の平均粒径
については、特に限定はないが、２〜４５μｍであるこ
とが好ましい。この理由は２μｍ未満のAg基合金粉末を
製造することは製造面で困難であり、４５μｍを越える
と焼結性が劣化するという問題が生じるためである。The average particle size of the Ag-based alloy powder in the present invention is not particularly limited, but is preferably 2 to 45 μm. The reason for this is that it is difficult to manufacture Ag-based alloy powder of less than 2 μm in terms of manufacturing, and if it exceeds 45 μm, sinterability deteriorates.
【０００８】本発明の請求項３または請求項４記載の発
明に係るAg基合金粉末の製造方法では、混合溶湯を、水
アトマイズ法で急冷凝固させてAg基合金粉末を得る構成
になっている。この方法での融液温度としては１２００
〜１８００℃が好ましく、急冷凝固の冷却速度は１０2
〜１０8 ℃／秒が好ましい。冷却速度が１０2 ℃／秒未
満ではFeまたはCoの析出粒子径が大きくなり、１０8 ℃
／秒を越える冷却速度で行なうことは性能的には問題が
ないが、実用的には１０8 ℃／秒程度が冷却速度の限界
である。そして、水アトマイズ法で急冷凝固させて得ら
れるAg基合金粉末は、Agマトリックス中に酸素を含有し
ているので、Ag基合金粉末を焼結する工程において、含
有している酸素によりFeまたはCoの酸化物が形成され
る。すなわち、水アトマイズ法以外の他の方法に比べ水
アトマイズ法による方法は工程数を少なくして（Agマト
リックス中に酸素を含有させる工程が不要）本発明のAg
基合金粉末が製造できるという利点がある。In the method for producing the Ag-based alloy powder according to the third or fourth aspect of the present invention, the mixed molten metal is rapidly cooled and solidified by the water atomizing method to obtain the Ag-based alloy powder. . The melt temperature in this method is 1200
~ 1800 ° C is preferable, and the cooling rate for rapid solidification is 10 2
It is preferably 10 8 ° C / sec. If the cooling rate is less than 10 2 ° C / sec, the precipitated particle size of Fe or Co will be large and 10 8 ° C
Although there is no problem in terms of performance if the cooling rate is higher than 10 s / sec, the limit of the cooling rate is practically about 10 8 ° C / sec. Then, the Ag-based alloy powder obtained by rapid solidification by the water atomizing method contains oxygen in the Ag matrix, so in the step of sintering the Ag-based alloy powder, Fe or Co depending on the oxygen contained. Oxides are formed. That is, compared with other methods other than the water atomizing method, the method by the water atomizing method has a smaller number of steps (the step of incorporating oxygen in the Ag matrix is unnecessary).
There is an advantage that a base alloy powder can be manufactured.
【０００９】本発明の請求項５記載の発明に係るAg基合
金粉末の製造方法は、例えばガスアトマイズ法で得られ
た合金粉末を酸化雰囲気中で熱処理して内部酸化させて
Agマトリックス中に酸素を含有させるようにしている。
熱処理の温度については、特に限定するものではない
が、３００〜４５０℃で行なうのが好ましい。なぜなら
ば、３００℃未満では内部酸化速度が遅く、４５０℃を
越えると合金粉末の凝集が生じるという問題がある。A method for producing an Ag-based alloy powder according to a fifth aspect of the present invention is that the alloy powder obtained by, for example, a gas atomizing method is heat-treated in an oxidizing atmosphere to be internally oxidized.
Oxygen is contained in the Ag matrix.
The temperature of the heat treatment is not particularly limited, but it is preferably 300 to 450 ° C. This is because if the temperature is lower than 300 ° C, the internal oxidation rate is slow, and if the temperature exceeds 450 ° C, the alloy powder agglomerates.
【００１０】[0010]
【作用】Ag基合金粉末において、粒径0.01〜1.0 μｍの
FeまたはCo（またはこれらの酸化物）の粒子をできるだ
け多く均一に分散させることは、得られる線材を高電気
伝導度であって、高硬度なものにする働きをする。[Function] Ag-based alloy powder with a grain size of 0.01-1.0 μm
Evenly dispersing as many Fe or Co (or oxides thereof) particles as possible serves to make the resulting wire material have high electrical conductivity and high hardness.
【００１１】本発明に係るAg基合金粉末の製造方法で、
水アトマイズ法によって急冷凝固させることは、Feまた
はCo（またはこれらの酸化物）の粒子を微細に分散させ
る働きと共に、水の分解によってAgマトリックス中に酸
素を含有させる働きをする。In the method for producing an Ag-based alloy powder according to the present invention,
The rapid solidification by the water atomization method serves to finely disperse Fe or Co (or oxides thereof) particles, and also to cause oxygen to be contained in the Ag matrix due to water decomposition.
【００１２】また、本発明に係るAg基合金粉末の製造方
法において、合金粉末を酸化雰囲気中で熱処理して内部
酸化させることは、Agマトリックス中に酸素を含有させ
る働きをする。水アトマイズ法以外の急冷凝固法、例え
ば、ガスアトマイズ法によって合金粉末を作製した場
合、合金粉末に酸素を含有させることができないが、こ
のような場合に、内部酸化によりAgマトリックス中にFe
またはCoの酸化物を生成させることによりAgマトリック
ス中に酸素成分を含有させることができるようになる。Further, in the method for producing an Ag-based alloy powder according to the present invention, heat treating the alloy powder in an oxidizing atmosphere to internally oxidize it functions to make oxygen contained in the Ag matrix. A rapid solidification method other than the water atomization method, for example, when the alloy powder is produced by the gas atomization method, it is not possible to contain oxygen in the alloy powder, in such a case, Fe in the Ag matrix due to internal oxidation.
Alternatively, the oxygen component can be contained in the Ag matrix by generating an oxide of Co.
【００１３】[0013]
【実施例】以下に、本発明の具体的な実施例及び比較例
を示す。 （実施例１）Ag及びFeを、Ag９６．５重量部、Fe３．５
重量部の割合で坩堝に入れ、高周波溶解によって融液温
度を１６５０℃とした。次にこの溶融物（混合溶湯）を
水圧８００kgf/cm2 で水アトマイズ法によって急冷凝固
させ、Ag基合金粉末を得た。このようにして得られたAg
基合金粉末は、表１に示す平均粒径であり、Agマトリッ
クス中に微細なFe粒子が均一に分散した組織であった。
そして、Agマトリックス中のFe粒子は表１に示す平均粒
径であり、その殆どが粒径0.01〜1.0 μｍの範囲内にあ
ることが確認された。また、得られたAg基合金粉末の含
有酸素量を燃焼−赤外吸収法により測定した結果を表１
に示す。EXAMPLES Specific examples and comparative examples of the present invention will be shown below. (Example 1) Ag and Fe, Ag 96.5 parts by weight, Fe3.5
Part by weight was placed in a crucible and the melt temperature was adjusted to 1650 ° C. by high frequency melting. Next, this melt (mixed molten metal) was rapidly solidified by a water atomizing method at a water pressure of 800 kgf / cm 2 to obtain Ag-based alloy powder. Ag obtained in this way
The base alloy powder had the average particle size shown in Table 1 and had a structure in which fine Fe particles were uniformly dispersed in the Ag matrix.
It was confirmed that the Fe particles in the Ag matrix had the average particle size shown in Table 1, and most of them were in the range of particle size 0.01 to 1.0 μm. The results of measuring the oxygen content of the obtained Ag-based alloy powder by the combustion-infrared absorption method are shown in Table 1.
Shown in.
【００１４】（実施例２）Ag及びFeを、Ag９５重量部、
Fe５重量部の割合で坩堝に入れ、高周波溶解によって融
液温度を１６５０℃とした。次にこの溶融物（混合溶
湯）を水圧８００kgf/cm2 で水アトマイズ法によって急
冷凝固させ、Ag基合金粉末を得た。このようにして得ら
れたAg基合金粉末は、表１に示す平均粒径であり、Agマ
トリックス中に微細なFe粒子が均一に分散した組織であ
った。そして、Agマトリックス中のFe粒子は表１に示す
平均粒径であり、その殆どが粒径0.01〜1.0 μｍの範囲
内にあることが確認された。また、得られたAg基合金粉
末の含有酸素量を燃焼−赤外吸収法により測定した結果
を表１に示す。(Example 2) Ag and Fe in an amount of 95 parts by weight of Ag,
5 parts by weight of Fe was put into the crucible, and the melt temperature was adjusted to 1650 ° C. by high frequency melting. Next, this melt (mixed molten metal) was rapidly solidified by a water atomizing method at a water pressure of 800 kgf / cm 2 to obtain Ag-based alloy powder. The Ag-based alloy powder thus obtained had the average particle size shown in Table 1 and had a structure in which fine Fe particles were uniformly dispersed in the Ag matrix. It was confirmed that the Fe particles in the Ag matrix had the average particle size shown in Table 1, and most of them were in the range of particle size 0.01 to 1.0 μm. In addition, Table 1 shows the results of measuring the oxygen content in the obtained Ag-based alloy powder by the combustion-infrared absorption method.
【００１５】（実施例３）Ag及びCoを、Ag９６．５重量
部、Co３．５重量部の割合で坩堝に入れ、高周波溶解に
よって融液温度を１６５０℃とした。次にこの溶融物
（混合溶湯）を水圧８００kgf/cm2 で水アトマイズ法に
よって急冷凝固させ、Ag基合金粉末を得た。このように
して得られたAg基合金粉末は、表１に示す平均粒径であ
り、Agマトリックス中に微細なCo粒子が均一に分散した
組織であった。そして、Agマトリックス中のCo粒子は表
１に示す平均粒径であり、その殆どが粒径0.01〜1.0 μ
ｍの範囲内にあることが確認された。また、得られたAg
基合金粉末の含有酸素量を燃焼−赤外吸収法により測定
した結果を表１に示す。Example 3 Ag and Co were put in a crucible at a ratio of 96.5 parts by weight of Ag and 3.5 parts by weight of Co, and the melt temperature was adjusted to 1650 ° C. by high frequency melting. Next, this melt (mixed molten metal) was rapidly solidified by a water atomizing method at a water pressure of 800 kgf / cm 2 to obtain Ag-based alloy powder. The Ag-based alloy powder thus obtained had the average particle size shown in Table 1 and had a structure in which fine Co particles were uniformly dispersed in the Ag matrix. The Co particles in the Ag matrix have the average particle size shown in Table 1, and most of them have a particle size of 0.01 to 1.0 μm.
It was confirmed to be within the range of m. Also, the obtained Ag
Table 1 shows the results of measuring the oxygen content in the base alloy powder by the combustion-infrared absorption method.
【００１６】（実施例４）Ag及びCoを、Ag９５重量部、
Co５重量部の割合で坩堝に入れ、高周波溶解によって融
液温度を１６００℃とした。次にこの溶融物（混合溶
湯）をガス圧１００kgf/cm2 でＮ2 ガスによる高圧ガス
アトマイズ法によって急冷凝固させて合金粉末を得た。
次いで得られた合金粉末を３５０℃で２４時間、３気圧
の酸素雰囲気中で加熱処理して、内部酸化させてAg基合
金粉末を得た。このようにして得られたAg基合金粉末
は、表１に示す平均粒径であり、Agマトリックス中にCo
及びCoの酸化物の微細な粒子が均一に分散した組織であ
った。そして、Agマトリックス中のCo及びCoの酸化物の
微細な粒子は表１に示す平均粒径であり、その殆どが粒
径0.01〜1.0 μｍの範囲内にあることが確認された。ま
た、内部酸化前のAg基合金粉末の含有酸素量及び内部酸
化後のAg基合金粉末の含有酸素量をそれぞれ燃焼−赤外
吸収法により測定した。内部酸化前のAg基合金粉末の含
有酸素量は０．０１重量％であり、内部酸化後のAg基合
金粉末の含有酸素量は表１に示すように１．５重量％で
あった。(Example 4) Ag and Co were added in an amount of 95 parts by weight of Ag,
5 parts by weight of Co was put in a crucible and the melt temperature was adjusted to 1600 ° C. by high frequency melting. Next, this melt (mixed molten metal) was rapidly cooled and solidified at a gas pressure of 100 kgf / cm 2 by a high pressure gas atomizing method using N 2 gas to obtain an alloy powder.
Next, the obtained alloy powder was heat-treated at 350 ° C. for 24 hours in an oxygen atmosphere of 3 atm and internally oxidized to obtain an Ag-based alloy powder. The Ag-based alloy powder thus obtained had the average particle size shown in Table 1 and contained Co in the Ag matrix.
And a structure in which fine particles of Co oxide were uniformly dispersed. It was confirmed that the fine particles of Co and Co oxide in the Ag matrix had the average particle diameter shown in Table 1, and most of them were in the particle diameter range of 0.01 to 1.0 μm. The oxygen content in the Ag-based alloy powder before internal oxidation and the oxygen content in the Ag-based alloy powder after internal oxidation were measured by the combustion-infrared absorption method. The oxygen content of the Ag-based alloy powder before internal oxidation was 0.01% by weight, and the oxygen content of the Ag-based alloy powder after internal oxidation was 1.5% by weight as shown in Table 1.
【００１７】（実施例５）Ag及びFeを、Ag９５重量部、
Fe５重量部の割合で坩堝に入れ、高周波溶解によって融
液温度を１６００℃とした。次にこの溶融物（混合溶
湯）をガス圧１００kgf/cm2 でＮ2 ガスによる高圧ガス
アトマイズ法によって急冷凝固させて合金粉末を得た。
次いで得られた合金粉末を３５０℃で２４時間、３気圧
の酸素雰囲気中で加熱処理して、内部酸化させてAg基合
金粉末を得た。このようにして得られたAg基合金粉末
は、表１に示す平均粒径であり、Agマトリックス中にFe
及びFeの酸化物の微細な粒子が均一に分散した組織であ
った。そして、Agマトリックス中のFe及びFeの酸化物の
微細な粒子は表１に示す平均粒径であり、その殆どが粒
径0.01〜1.0 μｍの範囲内にあることが確認された。ま
た、内部酸化前のAg基合金粉末の含有酸素量及び内部酸
化後のAg基合金粉末の含有酸素量をそれぞれ燃焼−赤外
吸収法により測定した。内部酸化前のAg基合金粉末の含
有酸素量は０．０１重量％であり、内部酸化後のAg基合
金粉末の含有酸素量は表１に示すように１．５重量％で
あった。Example 5 Ag and Fe were added in an amount of 95 parts by weight of Ag,
5 parts by weight of Fe was put into the crucible and the melt temperature was adjusted to 1600 ° C. by high frequency melting. Next, this melt (mixed molten metal) was rapidly cooled and solidified at a gas pressure of 100 kgf / cm 2 by a high pressure gas atomizing method using N 2 gas to obtain an alloy powder.
Next, the obtained alloy powder was heat-treated at 350 ° C. for 24 hours in an oxygen atmosphere of 3 atm and internally oxidized to obtain an Ag-based alloy powder. The Ag-based alloy powder thus obtained had the average particle size shown in Table 1 and Fe in the Ag matrix.
It had a structure in which fine particles of Fe oxide and Fe were uniformly dispersed. It was confirmed that the fine particles of Fe and Fe oxide in the Ag matrix had the average particle size shown in Table 1, and most of them were in the range of 0.01 to 1.0 μm. The oxygen content in the Ag-based alloy powder before internal oxidation and the oxygen content in the Ag-based alloy powder after internal oxidation were measured by the combustion-infrared absorption method. The oxygen content of the Ag-based alloy powder before internal oxidation was 0.01% by weight, and the oxygen content of the Ag-based alloy powder after internal oxidation was 1.5% by weight as shown in Table 1.
【００１８】（比較例１）平均粒径１０μｍのAg粉末及
び平均粒径１０μｍのCo粉末をAg９５重量部、Co５重量
部の割合で混合し、Ag−Co混合粉末を得た。このAg−Co
混合粉末中のCo粉末は表２に示すように平均粒径は１０
μｍであり、その殆どが粒径１〜２０μｍの範囲内であ
ることが確認された。また、Ag−Co混合粉末の含有酸素
量を燃焼−赤外吸収法により測定した結果を表２に示
す。Comparative Example 1 Ag powder having an average particle size of 10 μm and Co powder having an average particle size of 10 μm were mixed at a ratio of 95 parts by weight of Ag and 5 parts by weight of Co to obtain an Ag-Co mixed powder. This Ag-Co
The Co powder in the mixed powder has an average particle size of 10 as shown in Table 2.
It was confirmed that the average particle size was in the range of 1 to 20 μm. Table 2 shows the results of measuring the oxygen content of the Ag-Co mixed powder by the combustion-infrared absorption method.
【００１９】（比較例２）平均粒径１０μｍのAg粉末及
び平均粒径１０μｍのFe粉末をAg９５重量部、Fe５重量
部の割合で混合し、Ag−Fe混合粉末を得た。このAg−Fe
混合粉末中のFe粉末は表２に示すように平均粒径は１０
μｍであり、その殆どが粒径１〜２０μｍの範囲内であ
ることが確認された。また、Ag−Fe混合粉末の含有酸素
量を燃焼−赤外吸収法により測定した結果を表２に示
す。Comparative Example 2 Ag powder having an average particle size of 10 μm and Fe powder having an average particle size of 10 μm were mixed at a ratio of 95 parts by weight of Ag and 5 parts by weight of Fe to obtain an Ag-Fe mixed powder. This Ag-Fe
The Fe powder in the mixed powder has an average particle size of 10 as shown in Table 2.
It was confirmed that the average particle size was in the range of 1 to 20 μm. Table 2 shows the results of measuring the oxygen content of the Ag-Fe mixed powder by the combustion-infrared absorption method.
【００２０】（比較例３）Ag及びCoを、Ag９５重量部、
Co５重量部の割合で坩堝に入れ、高周波溶解によって融
液温度を１６００℃とした。次にこの溶融物（混合溶
湯）をガス圧１００kgf/cm2 でＮ2 ガスによる高圧ガス
アトマイズ法によって急冷凝固させてAg基合金粉末を得
た。（実施例４の内部酸化前の合金粉末に同じ）このよ
うにして得られたAg基合金粉末は、表２に示す平均粒径
であり、Agマトリックス中に微細なCo粒子が均一に分散
した組織であった。そして、Agマトリックス中のCo粒子
は表２に示す平均粒径であり、その殆どが粒径0.01〜1.
0 μｍの範囲内にあることが確認された。また、Ag基合
金粉末の含有酸素量を燃焼−赤外吸収法により測定した
結果を表２に示す。Comparative Example 3 Ag and Co were added in an amount of 95 parts by weight of Ag,
5 parts by weight of Co was put in a crucible and the melt temperature was adjusted to 1600 ° C. by high frequency melting. Next, this melt (mixed molten metal) was rapidly solidified by a high pressure gas atomization method using N 2 gas at a gas pressure of 100 kgf / cm 2 to obtain Ag-based alloy powder. (The same as the alloy powder before internal oxidation in Example 4) The thus obtained Ag-based alloy powder had the average particle size shown in Table 2, and the fine Co particles were uniformly dispersed in the Ag matrix. It was an organization. The Co particles in the Ag matrix have the average particle size shown in Table 2, and most of them have a particle size of 0.01 to 1.
It was confirmed to be in the range of 0 μm. Table 2 shows the results of measuring the oxygen content of the Ag-based alloy powder by the combustion-infrared absorption method.
【００２１】（比較例４）Ag及びFeを、Ag９５重量部、
Fe５重量部の割合で坩堝に入れ、高周波溶解によって融
液温度を１６００℃とした。次にこの溶融物（混合溶
湯）をガス圧１００kgf/cm2 でＮ2 ガスによる高圧ガス
アトマイズ法によって急冷凝固させてAg基合金粉末を得
た。（実施例５の内部酸化前の合金粉末に同じ）このよ
うにして得られたAg基合金粉末は、表２に示す平均粒径
であり、Agマトリックス中に微細なFe粒子が均一に分散
した組織であった。そして、Agマトリックス中のFe粒子
は表２に示す平均粒径であり、その殆どが粒径0.01〜1.
0 μｍの範囲内にあることが確認された。また、Ag基合
金粉末の含有酸素量を燃焼−赤外吸収法により測定した
結果を表２に示す。(Comparative Example 4) Ag and Fe were added in an amount of 95 parts by weight of Ag,
5 parts by weight of Fe was put into the crucible and the melt temperature was adjusted to 1600 ° C. by high frequency melting. Next, this melt (mixed molten metal) was rapidly solidified by a high pressure gas atomization method using N 2 gas at a gas pressure of 100 kgf / cm 2 to obtain Ag-based alloy powder. (The same as the alloy powder before internal oxidation of Example 5) The Ag-based alloy powder thus obtained had the average particle size shown in Table 2, and the fine Fe particles were uniformly dispersed in the Ag matrix. It was an organization. The Fe particles in the Ag matrix have the average particle size shown in Table 2, and most of them have a particle size of 0.01 to 1.
It was confirmed to be in the range of 0 μm. Table 2 shows the results of measuring the oxygen content of the Ag-based alloy powder by the combustion-infrared absorption method.
【００２２】上記実施例１〜５及び比較例１〜４で得ら
れたAg基合金粉末または混合粉末を、加圧力３０kgf/mm
2 で加圧して成形し、次いで８５０℃−２時間の焼成
（真空雰囲気中）と４２０℃−９０kgf/mm2 の熱間圧縮
を２回繰り返して焼結体を得た。次に、焼結体予熱温度
８００℃、金型温度４２０℃で熱間押し出しにより、直
径８ｍｍに押し出した後、スウェージング加工、引抜き
加工によって直径２ｍｍの線材を得た。得られた線材の
硬度をマイクロビッカース硬度計を用いて、３００ｇの
荷重を１５秒間加える条件で測定し、その結果を表１及
び表２に示した。また、得られた線材の電気伝導度を直
流四端子法によって測定し、その結果を同じく表１及び
表２に示した。The Ag-based alloy powder or the mixed powder obtained in Examples 1 to 5 and Comparative Examples 1 to 4 was applied with a pressure of 30 kgf / mm.
Pressurized with 2 by molding, and then to obtain a 850 ° C. calcination -2 hours (vacuum atmosphere) and 420 ℃ -90kgf / mm 2 of the hot compressed twice repeated sintered body. Next, a sintered body was preheated at a temperature of 800 ° C. and a mold temperature of 420 ° C. and hot extruded to a diameter of 8 mm, and then swaged and drawn to obtain a wire having a diameter of 2 mm. The hardness of the obtained wire rod was measured using a micro Vickers hardness meter under the condition that a load of 300 g was applied for 15 seconds, and the results are shown in Tables 1 and 2. The electric conductivity of the obtained wire was measured by the DC four-terminal method, and the results are also shown in Tables 1 and 2.
【００２３】[0023]
【表１】 [Table 1]
【００２４】[0024]
【表２】 [Table 2]
【００２５】表１及び表２の結果で明らかなように、実
施例１〜５のAg基合金粉末を用いた線材の硬度は高く、
また電気伝導度も高い値となっている。As is clear from the results of Tables 1 and 2, the hardness of the wire rods using the Ag-based alloy powders of Examples 1 to 5 is high,
The electric conductivity is also high.
【００２６】[0026]
【発明の効果】請求項１または請求項２記載の発明に係
るAg基合金粉末は、上記のように構成されているため、
このAg基合金粉末を用いることにより、高電気伝導度で
あって、かつ、高硬度である線材が得られる。The Ag-based alloy powder according to the invention of claim 1 or 2 is constituted as described above,
By using this Ag-based alloy powder, a wire having high electrical conductivity and high hardness can be obtained.
【００２７】また、請求項３〜請求項５記載の発明に係
るAg基合金粉末の製造方法によれば、高電気伝導度であ
って、かつ、高硬度である線材が得られる有用なAg基合
金粉末を製造することが可能になる。Further, according to the method for producing an Ag-based alloy powder according to the inventions of claims 3 to 5, a useful Ag-based material which can obtain a wire having high electric conductivity and high hardness. It becomes possible to produce alloy powder.
Claims (5)
少なくとも一方からなる、粒径0.01〜1.0 μｍの粒子が
分散されており、さらに、酸素含有量が0.03重量％以上
であり、かつ、前記の粒径0.01〜1.0 μｍの粒子の含有
量がFe元素量換算で 0.5〜5.0 重量％であるAg基合金粉
末。1. Particles having a particle size of 0.01 to 1.0 μm, which are composed of at least one of Fe and an oxide of Fe, are dispersed in an Ag matrix, and further have an oxygen content of 0.03% by weight or more, and An Ag-based alloy powder in which the content of the particles having a particle size of 0.01 to 1.0 μm is 0.5 to 5.0% by weight in terms of the amount of Fe element.
少なくとも一方からなる、粒径0.01〜1.0 μｍの粒子が
分散されており、さらに、酸素含有量が0.03重量％以上
であり、かつ、前記の粒径0.01〜1.0 μｍの粒子の含有
量がCo元素量換算で 0.5〜5.0 重量％であるAg基合金粉
末。2. Ag particles in which particles of at least one of Co and Co oxide and having a particle size of 0.01 to 1.0 μm are dispersed, and the oxygen content is 0.03% by weight or more, and An Ag-based alloy powder in which the content of the particles having a particle size of 0.01 to 1.0 μm is 0.5 to 5.0% by weight in terms of the amount of Co element.
において、Ag及びFeの混合溶湯を、水アトマイズ法で急
冷凝固させてAg基合金粉末を得ることを特徴とするAg基
合金粉末の製造方法。3. The Ag-based alloy powder according to claim 1, wherein the mixed molten Ag and Fe is rapidly solidified by a water atomizing method to obtain Ag-based alloy powder. Manufacturing method.
において、Ag及びCoの混合溶湯を、水アトマイズ法で急
冷凝固させてAg基合金粉末を得ることを特徴とするAg基
合金粉末の製造方法。4. The Ag-based alloy powder according to claim 2, wherein the molten alloy of Ag and Co is rapidly solidified by a water atomizing method to obtain Ag-based alloy powder. Manufacturing method.
粉末の製造方法において、合金粉末を酸化雰囲気中で熱
処理して内部酸化させる工程を経てAg基合金粉末を得る
Ag基合金粉末の製造方法。5. The method for producing an Ag-based alloy powder according to claim 1 or 2, wherein the Ag-based alloy powder is obtained through a step of heat-treating the alloy powder in an oxidizing atmosphere to internally oxidize it.
Manufacturing method of Ag-based alloy powder.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5329419A JPH07188702A (en) | 1993-12-27 | 1993-12-27 | Ag-base alloy powder and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5329419A JPH07188702A (en) | 1993-12-27 | 1993-12-27 | Ag-base alloy powder and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07188702A true JPH07188702A (en) | 1995-07-25 |
Family
ID=18221191
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5329419A Withdrawn JPH07188702A (en) | 1993-12-27 | 1993-12-27 | Ag-base alloy powder and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07188702A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0774524A1 (en) * | 1995-11-20 | 1997-05-21 | Degussa Aktiengesellschaft | Silver-iron material for electrical switch contacts |
| WO1997033288A1 (en) * | 1996-03-05 | 1997-09-12 | Siemens Aktiengesellschaft | Contact material of silver and active components, moulded piece produced therefrom and process for the production of said moulded piece |
| WO2017073057A1 (en) * | 2015-10-30 | 2017-05-04 | Ｄｏｗａエレクトロニクス株式会社 | Silver powder and method for producing same |
| JP2017082327A (en) * | 2015-10-30 | 2017-05-18 | Ｄｏｗａエレクトロニクス株式会社 | Silver powder and method for producing the same |
-
1993
- 1993-12-27 JP JP5329419A patent/JPH07188702A/en not_active Withdrawn
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0774524A1 (en) * | 1995-11-20 | 1997-05-21 | Degussa Aktiengesellschaft | Silver-iron material for electrical switch contacts |
| WO1997033288A1 (en) * | 1996-03-05 | 1997-09-12 | Siemens Aktiengesellschaft | Contact material of silver and active components, moulded piece produced therefrom and process for the production of said moulded piece |
| WO2017073057A1 (en) * | 2015-10-30 | 2017-05-04 | Ｄｏｗａエレクトロニクス株式会社 | Silver powder and method for producing same |
| JP2017082327A (en) * | 2015-10-30 | 2017-05-18 | Ｄｏｗａエレクトロニクス株式会社 | Silver powder and method for producing the same |
| KR20180075582A (en) * | 2015-10-30 | 2018-07-04 | 도와 일렉트로닉스 가부시키가이샤 | Silver powder and method for producing the same |
| US20180326497A1 (en) * | 2015-10-30 | 2018-11-15 | Dowa Electronics Materials Co., Ltd. | Silver powder and method for producing same |
| US10828702B2 (en) | 2015-10-30 | 2020-11-10 | Dowa Electronics Materials Co., Ltd. | Silver powder and method for producing same |
| JP2021075799A (en) * | 2015-10-30 | 2021-05-20 | Ｄｏｗａエレクトロニクス株式会社 | Silver powder and method for producing the same |
| TWI734710B (en) * | 2015-10-30 | 2021-08-01 | 日商同和電子科技有限公司 | Silver powder and method for producing same |
| US11407030B2 (en) | 2015-10-30 | 2022-08-09 | Dowa Electronics Materials Co., Ltd. | Silver powder and method for producing same |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| AU598815B2 (en) | Circuit breaker contact containing silver and graphite fibers | |
| JP2843900B2 (en) | Method for producing oxide-particle-dispersed metal-based composite material | |
| JP3763006B2 (en) | Copper tungsten alloy and method for producing the same | |
| US4999050A (en) | Dispersion strengthened materials | |
| US4752333A (en) | Alloys having high electrical and mechanical characteristics, the production thereof and the uses thereof in particular in the electrical, electronic and connection arts | |
| US4452651A (en) | Electrical contact materials and their production method | |
| US3438753A (en) | Tungsten-copper composites | |
| JPH07188702A (en) | Ag-base alloy powder and its production | |
| JP2531701B2 (en) | Manufacturing method of dispersion strengthened copper alloy | |
| US3505065A (en) | Method of making sintered and infiltrated refractory metal electrical contacts | |
| US3525609A (en) | Copper alloy material | |
| KR970001558B1 (en) | Method for composite powder | |
| JPS6148573B2 (en) | ||
| JPH01180901A (en) | Silver nickel composite powder for electric contact material and manufacture thereof | |
| JPS621835A (en) | Manufacture of ag-nio electric contact point material | |
| US6056916A (en) | Process for producing a product made of a contact material based on silver, contact material and product made of the contact material | |
| JPH10195556A (en) | Production of electric contact material | |
| JP3168635B2 (en) | Manufacturing method of electrode material | |
| US4427625A (en) | Silver cadmium oxide electrical contacts | |
| JPH08127829A (en) | Electric contact material and its production | |
| JPH01164730A (en) | Superconducting material and its production | |
| JP3106609B2 (en) | Manufacturing method of electrode material | |
| JPS6026621A (en) | Manufacture of heat resistant molybdenum material | |
| KR910002952B1 (en) | Making process for contact of air circuit breaker | |
| JP2000319734A (en) | Composite material produced by powder metallurgy, and its production |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Application deemed to be withdrawn because no request for examination was validly filed |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 20010306 |