EP1023959A2 - Pulvermetallurgisch hergestellter Verbundwerkstoff und Verfahren zu dessen Herstellung - Google Patents
Pulvermetallurgisch hergestellter Verbundwerkstoff und Verfahren zu dessen Herstellung Download PDFInfo
- Publication number
- EP1023959A2 EP1023959A2 EP00101609A EP00101609A EP1023959A2 EP 1023959 A2 EP1023959 A2 EP 1023959A2 EP 00101609 A EP00101609 A EP 00101609A EP 00101609 A EP00101609 A EP 00101609A EP 1023959 A2 EP1023959 A2 EP 1023959A2
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- EP
- European Patent Office
- Prior art keywords
- composite material
- refractory
- material according
- refractory components
- melting point
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/047—Making non-ferrous alloys by powder metallurgy comprising intermetallic compounds
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01H—ELECTRIC SWITCHES; RELAYS; SELECTORS; EMERGENCY PROTECTIVE DEVICES
- H01H1/00—Contacts
- H01H1/02—Contacts characterised by the material thereof
- H01H1/0203—Contacts characterised by the material thereof specially adapted for vacuum switches
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01H—ELECTRIC SWITCHES; RELAYS; SELECTORS; EMERGENCY PROTECTIVE DEVICES
- H01H11/00—Apparatus or processes specially adapted for the manufacture of electric switches
- H01H11/04—Apparatus or processes specially adapted for the manufacture of electric switches of switch contacts
- H01H11/048—Apparatus or processes specially adapted for the manufacture of electric switches of switch contacts by powder-metallurgical processes
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12014—All metal or with adjacent metals having metal particles
- Y10T428/12028—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, etc.]
Definitions
- the invention relates to powder-metallurgically produced composite materials, comprising a matrix in which a granular additive is embedded, which consists of at least two refractory components, which as mixed crystals or there are intermetallic phases.
- the invention further relates to a Processes for their production and their use as contact materials, preferably in electrical vacuum interrupters.
- CuCr materials have very good current interruption properties and good dielectric strength (dielectric reconsolidation). At the in this required performance range is the small number of 10,000 switching cycles the erosion resistance of CuCr materials is sufficient.
- Vacuum contactors In the low voltage range ⁇ 1,000 V, the use of Vacuum contactors are becoming increasingly important. The used in this area Sagittarius have to withstand 1,000,000 or more switching cycles, and that Tear current should be as low as possible. To those used here As a result, vacuum materials have additional main requirements.
- High-performance materials for this area are pure W / Cu, WC / Ag, WC / Cu Form or with other additives.
- the matrix component is particularly effective here Ag has a good current breaking behavior, while the high-melting component W or WC minimizes arcing under the influence of an arc.
- EP-A-0 083 245 which i.a. a CuCrW alloy disclosed, which in a manner known per se powder metallurgical way by pressing the metal powder mixture as well Sintering in solid or liquid Cu phase is produced.
- Purpose of this publication is the production of a fine-grained composite. This is supposed to be through the Formation of a complete solid solution of the refractory metals in one another Caused by the metals W and Cr crystallizing in a cubic system become.
- EP-A-0 668 599 similarly discloses a contact material made of CuCr with an additional auxiliary component from the group of tungsten, molybdenum, tantalum and niobium, which by diffusion of the refractory components in the liquid copper phase and subsequent quenching as a fine-grain distribution of the arc-resistant components in the Cu Matrix is generated.
- a contact material made of CuCr with an additional auxiliary component from the group of tungsten, molybdenum, tantalum and niobium, which by diffusion of the refractory components in the liquid copper phase and subsequent quenching as a fine-grain distribution of the arc-resistant components in the Cu Matrix is generated.
- a CuCrW material a mutual diffusion of Cr and W and an arc-resistant grain of Cr and W are described.
- the invention aims essentially at a fine-grained distribution of the individual refractory components in the metal matrix. The formation of mixed crystals or intermetallic phases of the
- Another object of the invention is to provide a method for Manufacture of such composite materials, which is carried out in an economical manner can be.
- the object of the invention is a composite material for use as a contact material, preferably as a switching contact for vacuum interrupters in Voltage range from 1,000 - 12,000V, to provide.
- the invention thus relates to a powder metallurgy Composite material comprising a matrix of a metal with a Melting point of at most 1,200 ° C and one embedded in this matrix
- a powder metallurgy Composite material comprising a matrix of a metal with a Melting point of at most 1,200 ° C and one embedded in this matrix
- Comical addition of at least two refractory components is characterized in that the refractory components in the form of mixed crystals or intermetallic phases.
- Preferred embodiments of the composite material of the invention are The subject matter of claims 2-8. Among them, one is particularly preferred Composite material in which a or a first group of refractory components a melting point of 1,500 to 2,400 ° C and a second or a second Group of refractory components has a melting point of over 2,400 ° C.
- a method for producing the composite material mentioned provided which is characterized in that one powdery mixture of at least two refractory components Heating converts to a mixed crystal or an intermetallic phase and that powder obtained therefrom by cooling and crushing powder metallurgical route with a matrix metal with a melting point of connects at most 1,200 ° C.
- Another object of the invention is the use of the above Composite material as an electrical contact material, preferably as a switch contact for vacuum interrupters, especially in the voltage range from 1,000 to 12,000 V.
- the powder metallurgy composite of the present invention comprises a matrix of a metal with a melting point of at most 1200 ° C, in which a granular addition of at least two refractory components is embedded, the refractory components mixed crystals or include intermetallic phases from each other.
- Relatively low-melting ones are suitable as the matrix of the composite material
- Metals with good electrical conductivity, as they are usually used for Vacuum contact pads are used.
- Cu is preferred as matrix material, Ag or Al. Alloys of these metals can also be used without that the proportions are critical.
- refractory components that are suitable for use in the Compounds of the invention are suitable, namely the metals of groups V b V, Nb and Ta, and Vl b of the periodic table, namely Cr, Mo and W.
- the metals in elemental form can also be nitrides, carbides, silicides or borides these metals (hereinafter referred to as "hard materials") and mixtures thereof or mixtures of the hard materials with the metals.
- hard materials can change the properties of the Composite material, such as its weight, positively affect.
- the metals Cr and W are preferred as refractory components.
- the quantity ratio of the refractory metals or hard materials used is not critical as long as it is guaranteed that by heating these components a Mixed crystal or an intermetallic phase is obtained. Within that The quantitative ratios of the metals or hard materials in certain limits wide ranges fluctuate. It is also within the scope of the invention if the ratio is such that only partly mixed crystals or intermetallic phases arise while an excess Metal component remains partially as a pure substance.
- the refractory component is preferably at least 1, preferably at least 5, more preferably at least 10 and in particular at least 50% by weight from mixed crystals and intermetallic phases.
- The is particularly preferably Refractory portion to more than 90% and especially completely as a mixed crystal or intermetallic phase.
- mixed crystals are homogeneous solid solutions
- refractory metals or hard materials their places in the crystal lattice the atoms of the different metals are occupied.
- the atoms forming hard materials with a small radius, can be placed on metal interstitial spaces Host grid be stored; see. Römpp Lexikon Chemie, 10th edition 1998, p. 2705.
- Intermetallic phases are chemical compounds of two or more metallic elements whose structure is distinct from that of the metals differs. In addition to phases with a stoichiometric composition according to the existing valences, there are also those in which these exact composition just a special case in a broad Represents area of homogeneity. Specific examples of the intermetallic phases are the Laves phases, Hume Rothery phases and Zintl phases; see. Rompp Lexicon Chemie, 10th edition 1998, p. 1943.
- the share of the refractory components in the total mass of the Composite is not particularly critical, but is typically 15 to 80, preferably 25 to 50 wt .-%.
- the proportion is accordingly Matrix metals usually 20 to 85, preferably 50 to 75 wt .-%.
- the composite of the invention contains at least one refractory component with a melting point in the relatively low range of 1,500 to 2,400 ° C and at least one second refractory component with a relatively high melting point in the range of over 2,400 ° C.
- refractory components with a The melting point in the former range are Cr and Nb, while examples of the usable refractory components with a melting point above 2,400 ° C Metals are Ta, Mo and W.
- Preferred metal with lower melting point is Cr, preferred metal with a higher melting point is W.
- the embodiment is the quantitative ratio of the refractory components preferably such that when heated at least to a significant extent Mixed crystal or an intermetallic phase is formed.
- mixtures are made 10 to 90, preferably 30 to 70% by weight of the lower melting Refractory component, e.g. Chromium and 10 to 90, preferably 30-70 wt .-% of higher melting refractory component, e.g. Tungsten.
- Particularly suitable a mixture of about 70 wt .-% Cr and 30 wt .-% W.
- the amounts of the refractory components are selected such that the higher melting refractory in combination with the lower melting refractory component completely with formation of mixed crystals or intermetallic phases.
- the shaped bodies obtained from the sintering process are, due to the preferred high vacuum treatment, low in gas compared to parts conventionally sintered under protective gas, ie they contain reduced residual gas fractions of O 2 , N 2 or H 2 .
- These blanks are further processed by machining finishing in the form of disks, rings or the like into suitable contact pieces which are used in vacuum interrupters.
- the composite material of the present invention takes place as a contact material for example in vacuum interrupters.
- They are particularly suitable Composites of the invention for use in the stress range of 1,000 up to 12,000 V and here it is again the composite materials made of at least each a refractory component with a melting point in the range of 1,500 up to 2,400 ° C and at least one refractory component with a melting point of over 2,400 ° C, the mixed crystals or intermetallic phases of these Refractory components with melting points in each of the above Have areas.
- the melt cake is then broken up and ground.
- the Mixed crystal powder obtained is sieved to ⁇ 160 microns and in the solid phase sintered. For this purpose, 75% by weight of Cu metal powder and 25% by weight of that obtained CrW mixed crystal powder mixed, pressed and below the melting point sintered by copper under high vacuum.
- a CrW mixed crystal powder is prepared as described in Example 1, to ⁇ 160 ⁇ m sieved and sintered in the liquid phase.
- the CrW mixed crystal powder obtained pressed in the manner and under high vacuum with liquid Copper soaked that a fitting in the composition Cu 60 wt .-% Cr / W 40% by weight is obtained (FIG. 9).
- the analysis of the melt cake obtained shows polygonal, primarily precipitated grains of the intermetallic phase Cr 2 Ta in the composition CrTa 37/63% by weight (corresponding to 67 at.% Cr and 33 at.% Ta) (see FIG. 10). These are surrounded by a matrix of Cr metal ( Figure 11).
- This test result follows from the preselected composition of the green body from the metal components Cr and Ta close to the eutectic composition with ⁇ 34% by weight tantalum. (see Massalski et al., Binary Alloy Phase Diagrams, Second Edition Vol. 2, p. 1339).
- a Ta-rich starting composition up to a composition with 63-66% by weight Ta increases the proportion of the Cr 2 Ta phase at the expense of the Cr phase up to pure Cr 2 -Ta.
- the melt cake is, as stated in Example 1 or 2, crushed and with Cu or Ag using powder metallurgy to form a metal composite processed further.
- the carbon content in the mixed carbide can be increased if the pure Cr metal is replaced by the relatively low-melting Cr 3 C 2 (mp. 1,850 ° C). This corresponds to the condition of claim 3.
- the melt cake then solidifies with a nominal composition of 61% by weight Cr, 28% by weight W and 11% by weight C (FIG. 13).
- the original carbides have completely dissolved in favor of a new mixed carbide.
- the melt cake is, as stated in Example 1 or 2, crushed and with Cu or Ag using powder metallurgy to form a metal composite processed further.
- carbides such as VC, NbC, TaC, TiC, nitrides such as TiN and TaN, silicides such as Ta 2 Si and V 3 Si and borides such as TiB 2 can be used instead of the refractory components used here.
- melt cakes are made in the Compositions CrNb 50/50% by weight and CrMo 70/30% by weight mixed, pressed, melted, then crushed, sieved and added to the respective Processed combined with Cu or Ag.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- High-Tension Arc-Extinguishing Switches Without Spraying Means (AREA)
- Conductive Materials (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
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Abstract
Description
- geringer Materialabbrand,
- ausreichendes Schaltvermögen,
- geringe Schweißneigung,
- niedriger elektrischer Widerstand,
- gute Durchschlagfestigkeit (Spannungsfestigkeit),
- niedriger Abreißstrom.
- Bei zunehmender Spannung findet die Verwendung einer reinen Wolframkomponente ihre Begrenzung durch erhöhte Neigung zur Elektronenemission. Diese ist der Refraktärnatur des Wolframs (Smp 3.410 ° C) zuzuschreiben. Die Spannungsfestigkeit im Vakuum wird hierdurch geschwächt.
- Bei niedrigen Spannungen findet umgekehrt die Verwendung einer reinen Cr-Refraktär-Komponente ihre Begrenzung durch die mangelhafte Abbrandfestigkeit, die sich durch die aufsummierte Abbrandrate bei hohen Schaltspielen ergibt.
Für einen Werkstoff CuCrW wird eine wechselseitige Diffusion von Cr und W, sowie ein lichtbogenbeständiges Korn aus Cr und W beschrieben. Die Erfindung zielt im wesentlichen auf eine feinkörnige Verteilung der einzelnen Refraktärkomponenten in der Metallmatrix ab. Die Entstehung von Mischkristallen oder intermetallischen Phasen der Refraktäranteile untereinander wird nicht beschrieben.
- Figur 1:
- ein Schliffbild eines Cu Cr W-Verbundes gemäß EP-A-0 083 245;
- Figur 2:
- eine Röntgenfluoreszenz-Summenanalyse von Cr aus dem Cu Cr W-Verbund gemäß EP-A-0 083 245;
- Figur 3:
- eine Röntgenfluoreszenz-Punktanalyse von W aus dem Cu Cr W-Verbund gemäß EP-A-0 083 245;
- Figur 4:
- ein Schliffbild von Cr W 70/30-Mischkristallen aus Beispiel 1;
- Figur 5:
- ein Schliffbild von Cr W 70/30-Mischkristallen mit dendritischer Unterstruktur aus Beispiel 1;
- Figur 6:
- eine Röntgenfluoreszenz-Summenanalyse von Cr und W aus CrW 70/30-Mischkristallen aus Beispiel 1;
- Figur 7:
- eine Verteilungsanalyse für W aus Cr W 70/30-Mischkristallen aus Beispiel 1; die weißen Punkte bezeichnen W, die großen schwarzen Flecken sind Poren im Schmelzkuchen;
- Figur 8:
- eine Röntgenfluoreszenz-Summenanalyse von Cr und W aus CrW 70/30-Mischkristallen mit chromreicher Unterstruktur aus Beispiel 1;
- Figur 9:
- ein Schliffbild von Cr W-Mischkristallen in Cu-Matrix aus Beispiel 2;
- Figur 10:
- eine Röntgenfluoreszenz-Summenanalyse einer intermetallischen Cr2Ta-Phase aus Beispiel 3;
- Figur 11:
- eine REM-Aufnahme von Cr2Ta-Körnern in Cr-Matrix aus Beispiel 3;
- Figur 12:
- ein Schliffbild von Cr W C 70/28.2/1.8-Mischkarbid mit dendritischer Unterstruktur aus Beispiel 4;
- Figur 13:
- ein Schliffbild von Cr W C 61/28/11 Mischkarbid aus Beispiel 4
- Sintern in fester Phase:
Ein Metallpulver der niedrig schmelzenden Matrix und das erhaltene Mischkristallpulver werden gemischt, gepreßt und unterhalb des Schmelzpunktes des Matrixmetalls, bevorzugt unter Hochvakuum gesintert. - Sintern in flüssiger Phase:
Das erhaltene Mischkristallpulver wird gepreßt und bevorzugt unter Hochvakuum mit dem geschmolzenen Matrixmetall getränkt.
sowie 30 Gew.-% W-Metallpulver (W: ≥ 99,95 Gew.-%)
werden gemischt, gepreßt und unter Vakuum oder Schutzgas erschmolzen. Die Schmelze wird abgeschreckt und so rasch wie möglich zum Erstarren gebracht (Abkühlungsgeschwindigkeit > 100 K/min). Die erhaltenen Mischkristalle aus W und Cr sind nahezu homogen in der Zusammensetzung und zeigen nur schwache Inhomogenitäten bezüglich der gegenseitigen Verteilung der Einzelkomponenten. Die erstarrte Schmelze zeigt eine einheitlich ausgebildete polygonale Kornstruktur (Figur 4). Die ursprünglich eingesetzten Metallkörnungen W bzw. Cr haben sich in der Schmelze vollständig aufgelöst und sind im Schmelzkuchen nicht mehr nachzuweisen.
Claims (14)
- Pulvermetallurgisch hergestellter Verbundwerkstoff, umfassend eine Matrix aus einem Metall mit einem Schmelzpunkt von höchstens 1.200° C und einem in dieser Matrix eingebetteten körnigen Zusatz aus mindestens zwei Refraktärkomponenten, dadurch gekennzeichnet, daß die Refraktärkomponenten Mischkristalle oder intermetallische Phasen voneinander umfassen.
- Verbundwerkstoff nach Anspruch 1, dadurch gekennzeichnet, daß der Anteil der Refraktärkomponenten 15 - 80, vorzugsweise 25 - 50 Gew.-%, und der Anteil der Matrix 20 - 85, vorzugsweise 50 - 75 Gew.-%, bezogen auf die Gesamtmasse des Verbundwerkstoffes, beträgt.
- Verbundwerkstoff nach einem der Ansprüche 1 bis 2, dadurch gekennzeichnet, daß eine bzw. eine erste Gruppe der Refraktärkomponenten einen Schmelzpunkt im Bereich von 1.500 bis 2.400° C und eine zweite bzw. eine zweite Gruppe der Refraktärkomponenten einen Schmelzpunkt über 2.400° C aufweisen.
- Verbundwerkstoff nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, daß die höher schmelzende Refraktärkomponente sich in Verbindung mit der niedriger schmelzenden Refraktärkomponente vollständig in Form von der Bildung von Mischkristallen oder intermetallischen Phasen auflöst.
- Verbundwerkstoff nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, daß die Matrix aus mindestens einem der Metalle Cu, Ag und Al besteht.
- Verbundwerkstoff nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, daß die Refraktärkomponenten aus Metallen der Gruppen V b, (V, Nb, Ta) und Vl b (Cr, Mo, W) des Periodensystems sowie deren Nitriden, Carbiden, Siliciden, Boriden und Gemischen davon ausgewählt sind.
- Verbundwerkstoff nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, daß die niedriger schmelzende Refraktärkomponente in einer Menge von 10 - 90, vorzugsweise 30 - 70 Gew.-% bezogen auf die Gesamtheit der Refraktärkomponenten vorliegt.
- Verbundwerkstoff nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, daß eine niedriger schmelzende Refraktärkomponente Cr und eine höher schmelzende Refraktärkomponente W ist.
- Verfahren zur Herstellung eines Verbundwerkstoffes nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, daß man ein pulverförmiges Gemisch von mindestens zwei Refraktärkomponenten durch Erhitzen in einen Mischkristall oder eine intermetallische Phase umwandelt und das daraus durch Abkühlen und Zerkleinern gewonnene Pulver auf pulvermetallurgischem Weg mit einem Matrixmetall mit einem Schmelzpunkt von höchstens 1.200° C verbindet.
- Verfahren nach Anspruch 9, dadurch gekennzeichnet, daß man ein Gemisch eines bzw. einer ersten Gruppe an Refraktärkomponenten mit einem Schmelzpunkt von 1.500 bis 2.400°C und eines zweiten bzw. einer zweiten Gruppe an Refraktärkomponenten mit einem Schmelzpunkt von über 2.400° C einsetzt.
- Verfahren nach Anspruch 9 oder 10, dadurch gekennzeichnet, daß die Herstellung unter Schutzgas oder Hochvakuum erfolgt.
- Verwendung eines Verbundwerkstoffes nach einem der Ansprüche 1 bis 8 als elektrischer Kontaktwerkstoff.
- Verwendung eines Verbundwerkstoffes nach einem der Ansprüche 1 bis 8 als Schaltkontakt für Vakuumschaltkammern.
- Verwendung eines Verbundwerkstoffes nach Anspruch 13 im Spannungsbereich von 1.000 bis 12.000 V.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE19903619A DE19903619C1 (de) | 1999-01-29 | 1999-01-29 | Pulvermetallurgisch hergestellter Verbundwerkstoff und Verfahren zu dessen Herstellung sowie dessen Verwendung |
DE19903619 | 1999-01-29 |
Publications (3)
Publication Number | Publication Date |
---|---|
EP1023959A2 true EP1023959A2 (de) | 2000-08-02 |
EP1023959A3 EP1023959A3 (de) | 2004-03-24 |
EP1023959B1 EP1023959B1 (de) | 2007-03-14 |
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ID=7895834
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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EP00101609A Expired - Lifetime EP1023959B1 (de) | 1999-01-29 | 2000-01-28 | Pulvermetallurgisch hergestellter Verbundwerkstoff und Verfahren zu dessen Herstellung |
Country Status (5)
Country | Link |
---|---|
US (1) | US6350294B1 (de) |
EP (1) | EP1023959B1 (de) |
JP (1) | JP2000219923A (de) |
DE (2) | DE19903619C1 (de) |
ES (1) | ES2283251T3 (de) |
Families Citing this family (17)
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DE10261303B3 (de) * | 2002-12-27 | 2004-06-24 | Wieland-Werke Ag | Verbundmaterial zur Herstellung elektrischer Kontakte und Verfahren zu dessen Herstellung |
DE10318890B4 (de) * | 2003-04-17 | 2014-05-08 | Ami Doduco Gmbh | Elektrische Steckkontakte und ein Halbzeug für deren Herstellung |
DE102005003812A1 (de) * | 2005-01-27 | 2006-10-05 | Abb Technology Ag | Verfahren zur Herstellung eines Kontaktstückes, sowie Kontaktstück für eine Vakuumschaltkammer selbst |
SE528908C2 (sv) * | 2005-07-15 | 2007-03-13 | Abb Research Ltd | Kontaktelement och kontaktanordning |
EP1934995B1 (de) * | 2005-07-15 | 2014-04-02 | Impact Coatings AB (Publ.) | Kontaktelement und kontaktanordnung |
DE102006027821A1 (de) * | 2006-06-16 | 2007-12-27 | Siemens Ag | Elektrischer Schaltkontakt |
DE102008015464A1 (de) * | 2008-03-18 | 2009-09-24 | Siemens Aktiengesellschaft | Bauteil mit einer elektrischen Kontaktfläche für ein elektrisches Kontaktelement, insbesondere Stromschiene |
CN102618773B (zh) * | 2012-04-05 | 2013-06-19 | 浙江大学 | Ag/La1-xSrxCoO3电接触复合材料的制备方法 |
CN105359241A (zh) * | 2013-06-24 | 2016-02-24 | 三菱电机株式会社 | 电触点材料及其制造方法 |
WO2015133262A1 (ja) * | 2014-03-04 | 2015-09-11 | 株式会社明電舎 | 電極材料 |
JP5861807B1 (ja) * | 2014-03-04 | 2016-02-16 | 株式会社明電舎 | 電極材料の製造方法 |
WO2015133264A1 (ja) * | 2014-03-04 | 2015-09-11 | 株式会社明電舎 | 合金 |
CN107532237B (zh) * | 2015-05-01 | 2019-11-01 | 株式会社明电舍 | 用于制造电极材料的方法和电极材料 |
WO2017039200A1 (ko) * | 2015-08-28 | 2017-03-09 | 부경대학교 산학협력단 | 에너지변환 경사기능복합체 및 그의 제조방법 및 이를 이용한 센서 |
KR101782107B1 (ko) * | 2015-08-28 | 2017-09-26 | 부경대학교 산학협력단 | 에너지변환 경사기능복합체 및 그의 제조방법 |
JP6075423B1 (ja) * | 2015-09-03 | 2017-02-08 | 株式会社明電舎 | 真空遮断器 |
KR101860852B1 (ko) | 2016-06-30 | 2018-05-25 | 부경대학교 산학협력단 | 고방열 금속-형광체 경사기능복합체 및 이를 이용한 고효율 에너지 순환 레이저 라이팅 시스템 |
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US4066451A (en) * | 1976-02-17 | 1978-01-03 | Erwin Rudy | Carbide compositions for wear-resistant facings and method of fabrication |
US4915902A (en) * | 1984-10-19 | 1990-04-10 | Martin Marietta Corporation | Complex ceramic whisker formation in metal-ceramic composites |
EP0668599A2 (de) * | 1994-02-21 | 1995-08-23 | Kabushiki Kaisha Toshiba | Kontaktmaterial für Vakuumschalter und Verfahren zu dessen Herstellung |
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JPS58115728A (ja) * | 1981-12-28 | 1983-07-09 | 三菱電機株式会社 | 真空しや断器用接点 |
US4517033A (en) * | 1982-11-01 | 1985-05-14 | Mitsubishi Denki Kabushiki Kaisha | Contact material for vacuum circuit breaker |
DE3428276A1 (de) * | 1984-08-01 | 1986-02-06 | Doduco KG Dr. Eugen Dürrwächter, 7530 Pforzheim | Werkstoff fuer elektrische kontakte auf der basis von silber mit wolframkarbid und verfahren zu seiner herstellung |
EP0181149B1 (de) * | 1984-10-30 | 1990-01-03 | Mitsubishi Denki Kabushiki Kaisha | Kontaktmaterial für Vakuumschalter |
US4677264A (en) * | 1984-12-24 | 1987-06-30 | Mitsubishi Denki Kabushiki Kaisha | Contact material for vacuum circuit breaker |
US4784829A (en) | 1985-04-30 | 1988-11-15 | Mitsubishi Denki Kabushiki Kaisha | Contact material for vacuum circuit breaker |
DE58904983D1 (de) * | 1988-04-20 | 1993-08-26 | Siemens Ag | Sinterkontaktwerkstoff auf silberbasis zur verwendung in schaltgeraeten der energietechnik, insbesondere fuer kontaktstuecke in niederspannungsschaltern. |
DE3829250A1 (de) * | 1988-08-29 | 1990-03-01 | Siemens Ag | Verfahren zur herstellung eines kontaktwerkstoffes fuer vakuumschalter |
DE4205763A1 (de) | 1992-02-25 | 1993-08-26 | Siemens Ag | Sinterkontaktwerkstoff auf silberbasis zur verwendung in schaltgeraeten der energietechnik |
-
1999
- 1999-01-29 DE DE19903619A patent/DE19903619C1/de not_active Expired - Fee Related
-
2000
- 2000-01-21 JP JP2000013117A patent/JP2000219923A/ja active Pending
- 2000-01-25 US US09/490,659 patent/US6350294B1/en not_active Expired - Fee Related
- 2000-01-28 ES ES00101609T patent/ES2283251T3/es not_active Expired - Lifetime
- 2000-01-28 DE DE50014151T patent/DE50014151D1/de not_active Expired - Lifetime
- 2000-01-28 EP EP00101609A patent/EP1023959B1/de not_active Expired - Lifetime
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4066451A (en) * | 1976-02-17 | 1978-01-03 | Erwin Rudy | Carbide compositions for wear-resistant facings and method of fabrication |
US4915902A (en) * | 1984-10-19 | 1990-04-10 | Martin Marietta Corporation | Complex ceramic whisker formation in metal-ceramic composites |
EP0668599A2 (de) * | 1994-02-21 | 1995-08-23 | Kabushiki Kaisha Toshiba | Kontaktmaterial für Vakuumschalter und Verfahren zu dessen Herstellung |
Also Published As
Publication number | Publication date |
---|---|
DE50014151D1 (de) | 2007-04-26 |
JP2000219923A (ja) | 2000-08-08 |
EP1023959B1 (de) | 2007-03-14 |
DE19903619C1 (de) | 2000-06-08 |
EP1023959A3 (de) | 2004-03-24 |
US6350294B1 (en) | 2002-02-26 |
ES2283251T3 (es) | 2007-11-01 |
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