EP3198048B1 - Electrical clamps - Google Patents

Electrical clamps Download PDF

Info

Publication number
EP3198048B1
EP3198048B1 EP15756842.9A EP15756842A EP3198048B1 EP 3198048 B1 EP3198048 B1 EP 3198048B1 EP 15756842 A EP15756842 A EP 15756842A EP 3198048 B1 EP3198048 B1 EP 3198048B1
Authority
EP
European Patent Office
Prior art keywords
alloy
connection element
electrical connection
copper
leg
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.)
Active
Application number
EP15756842.9A
Other languages
German (de)
French (fr)
Other versions
EP3198048A1 (en
Inventor
Timo ALLMENDINGER
Kai Weber
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Wieland Werke AG
Original Assignee
Wieland Werke AG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Wieland Werke AG filed Critical Wieland Werke AG
Priority to PL15756842T priority Critical patent/PL3198048T3/en
Publication of EP3198048A1 publication Critical patent/EP3198048A1/en
Application granted granted Critical
Publication of EP3198048B1 publication Critical patent/EP3198048B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon

Definitions

  • the invention relates to an electrical clamp containing a copper-zinc alloy according to the preamble of claim 1.
  • CN103589903A discloses the tubes made of a copper alloy, consisting of (in% by weight): 63.0-66.0% Cu, 0.6-1.2% Al, ⁇ 0.7% Ni, 1.6-2.4% Mn, ⁇ 0.5% Fe, 0.8-1.3% Si , ⁇ 0.1% Pb and balance Cu.
  • bronze materials are used, which are characterized by a fine microstructure with a grain size of maximum 3 ⁇ m.
  • significantly high mechanical strengths are achieved with greatly improved forming properties.
  • processors can achieve correspondingly tight bending radii.
  • the improved flexibility also means that the roughness in the forming zones is significantly less than when using standard bronze. Subsequent coatings with a lower layer thickness can thus be carried out, which can result in considerable cost savings in further processing.
  • the electrical conductivity is identical to that of standard bronzes and is approximately 7.5 to 12 MS / m.
  • Another precipitation-hardening CuNi1CoSi alloy with Ni-Co mixed silicides is also very suitable for economical miniaturization of connectors.
  • the material is high-strength, has a comparatively good electrical and thermal conductivity at 29 MS / m and is easy to process.
  • the materials described are particularly suitable for processing on punching / bending machines and can only be machined with great effort.
  • CuPb1P is another easily machinable machine material that also has a high electrical conductivity of around 50 MS / m. It is particularly suitable for connectors and other electronic applications.
  • the range of alloys is rounded off by further precipitation hardening materials.
  • These include, for example, CuNi1Pb1P and CuNiPb0.5P as a low-alloy copper material with high strength, good conductivity of at least 32 MS / m and good machinability.
  • the Pb component makes the material particularly suitable for machined plug contacts in electrical engineering and electronics.
  • the invention has for its object to develop an electrical clamp from a low-lead or lead-free copper alloy.
  • iron-nickel-manganese-containing mixed silicides are embedded in the matrix.
  • the structure consists of an ⁇ matrix, which contains deposits of 5 to 45% by volume of the ⁇ phase and mixed silicides containing iron-nickel-manganese of up to 20% by volume.
  • the structure contains the iron-nickel-manganese-containing mixed silicides with a stem-like form and iron-nickel-enriched mixed silicides with a globular shape.
  • alloy composition according to the invention is suitable for electrical terminals. So far, such alloys have been used in accordance with the German published patent application DE 10 2007 029 991 A1 the applicant is only intended for use for sliding elements in internal combustion engines, transmissions or hydraulic units.
  • the invention is based on the consideration of providing an electrical clamp with a copper-zinc alloy with embedded iron-nickel-manganese-containing mixed silicides, which can be produced in particular with the aid of the continuous or semi-continuous continuous casting process. Due to the mixed silicide formation and microstructure formation, the copper-zinc alloy has a very high electrical conductivity for this group of materials.
  • the alloy also has high hardness and strength values, nevertheless a necessary degree of ductility, expressed by the elongation at break during a tensile test, is guaranteed.
  • the subject of the invention proves to be particularly suitable for electrical terminals, optionally also with screw connections.
  • iron and nickel-rich mixed silicides are first separated out. With further growth, these precipitates can grow into mixed silicides containing iron-nickel-manganese of considerable size, often in the form of stalks. Furthermore, a considerable proportion remains rather small with a globular shape, which is finely distributed in the matrix. The finely divided silicides are seen as the reason that the ⁇ phase is stabilizing.
  • the alloy has a high ductility during cold forming. In the case of electrical clamps, this is particularly important in crimping, in which the material is usually subjected to severe plastic deformation. This enables the material to be flanged, squeezed or folded with almost any degree of deformation, without the formation of cracks in the material.
  • the material is also particularly suitable for machined electrical terminals.
  • the good machinability is already achieved with a beta phase of 5% by volume. Up to 45 vol.% Of the ⁇ -phase, the chip formation during the machining process also improves at higher contents, by desirably forming short chips. With a ⁇ -phase content of less than 5% by volume, machinability is no longer satisfactory when used as an automatic material for high machining rates. With a ⁇ -phase content of over 45% by volume, it can be seen that the toughness of the material and the temperature resistance of the structure deteriorate. The final state of the alloy from the respective manufacturing process leads to a ⁇ phase, which is embedded in an island structure in an ⁇ matrix. Such ⁇ -phase islands are particularly favorable for the machinability and the corrosion resistance of the alloy.
  • the particular advantage of the alloy according to the invention is thus based on a combination of properties optimized for the intended use in the form of an increase in the strength, the temperature resistance of the structure and the electrical conductivity with sufficient toughness properties at the same time.
  • the material solution claimed takes into account the need for an environmentally friendly lead-free alloy alternative due to the lead content substituted for conventional alloys.
  • this material is predestined for special applications where, despite high demands on hardness and strength, a necessary degree of plasticizability is required.
  • the final relaxation annealing is preferably carried out at 300 ° C. to 400 ° C. for 3 to 4 hours.
  • the copper-zinc alloy can contain 33.5 to 36.0% Zn. With these higher zinc contents, the toughness properties and good electrical conductivity required for electrical clamps can still be achieved.
  • the proportion of further elements, in particular the copper proportion, is correspondingly reduced by the highest possible zinc content. With the consequence that the alloy results in a correspondingly lower metal price due to a higher proportion of cheaper zinc.
  • the electrical conductivity of the alloy can advantageously be at least 5.8 MS / m. Particularly preferred conductivities are at least 10 MS / m to over 13 MS / m. These values are not achieved by comparable materials, such as the brass containing lead. Even values above 13 MS / m can be set by suitable further processing steps.
  • the structure consisting of an ⁇ matrix, which contains deposits of 5 to 45% by volume in the ⁇ phase and mixed silicides containing iron-nickel-manganese up to 20% by volume after further processing, which includes at least one hot forming and / or cold forming and optionally further annealing steps.
  • this alloy ensures an advantageous temperature resistance of the structure with sufficient toughness properties for the manufacture of the electrical clamp.
  • the relationship between the level and distribution of the proportion of the ⁇ phase and the temperature resistance of the structure is the relationship between the level and distribution of the proportion of the ⁇ phase and the temperature resistance of the structure.
  • this cubic, body-centered type of crystal has an indispensable strength-increasing function in the copper-zinc alloys, the minimization of the ⁇ content should not be the only focus.
  • the structure of the copper-zinc alloy can be modified in such a way that, in addition to high strength, it also has sufficient temperature resistance, ductility and good electrical conductivity.
  • At least one relaxation annealing in a temperature range from 250 to 450 ° C. and preferably an annealing time of 2 to 5 hours can follow in the further processing after the shaping.
  • Cast bolts of the copper-zinc alloy according to the invention were produced by continuous casting or permanent mold casting.
  • the chemical composition of the continuous casting of alloy 1 and the die casting of alloys 2 and 3 is shown in Table 1.
  • Table 1 Chemical composition of the casting bolts or casting blocks (in% by weight) without indication of possible impurities Cu [%] Zn [%] Si [%] Mn [%] Ni [%] Sn [%] Al [%] Fe [%] Leg. 1 64.0 31.1 1.0 2.0 0.6 ⁇ 0.01 0.9 0.4 Leg. 2 64.0 30.8 1.1 2.1 0.6 - 0.9 0.5 Leg. 3 61.6 34.8 0.7 1.7 0.3 - 0.5 0.4
  • Table 2 Structure parameters, electrical conductivity and mechanical properties at two positions of the pipes in the final state (Leg. 1) ⁇ content [%] Grain size [ ⁇ m] Electrical conductivity [MS / m] Rm [MPa] R p0.2 [MPa] Elongation at break A5 [%] Hardness HB 5 15-20 11.4 640 560 14.5 201 15-20 20-25 11.2 647 572 13.2 199
  • Table 3 Structure parameters, electrical conductivity and mechanical properties of the round bars in the final state (Leg. 1) Round rod ⁇ [mm] ⁇ content [%] Grain size [ ⁇ m] Electrical conductivity [MS / m] R m [MPa] R p0.2 [MPa] Elongation at break A5 [%] Hardness HB 13.40 5 20-25 11.4 607 512 12.4 191 16.35 15-20 25 10.9 638 549 12.0 199 45.50 10-15 25 10.7 570 420 20.1 172
  • the characteristic value for the electrical conductivity can be further increased for the formats of alloys 2 and 3 produced according to production sequence 5 by an additional stress relief annealing carried out at a temperature of 250 to 450 ° C.
  • the ⁇ content is between 5-20% in all 5 production sequences. Further investigations show that the ⁇ contents are preferably between 5-30%.
  • the island-like formation of the ⁇ phase in the final state of production, embedded in a structure of an ⁇ matrix, can appear in somewhat different forms. With increasingly lower contents of the ⁇ -phase, islands that are isolated from each other appear, which in the limit case can form a kind of gusset filling compared to the crystallites of the ⁇ -matrix.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Conductive Materials (AREA)

Description

Die Erfindung betrifft eine Elektroklemme enthaltend eine Kupfer-Zink-Legierung gemäß dem Oberbegriff des Anspruchs 1.The invention relates to an electrical clamp containing a copper-zinc alloy according to the preamble of claim 1.

DE 297 12 696 U1 offenbart Vorrichtungen zum Verbinden eines Kabels mit dem Körper einer Maschine mit Hilfe von Anschlussteilen. CN103589903A offenbart die Rohre aus einer Kupfer Legierung, bestehend aus (in Gew.%): 63.0-66.0% Cu, 0.6-1.2% Al, <0.7% Ni, 1.6-2.4% Mn, < 0.5% Fe, 0.8-1.3% Si, <0.1% Pb und Rest Cu. DE 297 12 696 U1 discloses devices for connecting a cable to the body of a machine using connectors. CN103589903A discloses the tubes made of a copper alloy, consisting of (in% by weight): 63.0-66.0% Cu, 0.6-1.2% Al, <0.7% Ni, 1.6-2.4% Mn, <0.5% Fe, 0.8-1.3% Si , <0.1% Pb and balance Cu.

Zahlreiche neue Automobilanwendungen für Sicherheit, Komfort und Leistung lassen sich nur durch den gezielten Einsatz von elektronischen Funktionen und Komponenten realisieren. Aufgrund der steigenden Anforderungen an die Steckverbinder und damit an die eingesetzten Werkstoffe ist in den letzten Jahren ein Trend hin zu Kupfer-Hochleistungslegierungen zu erkennen. Diese ausscheidungshärtenden Kupferwerkstoffe zeichnen sich durch hohe mechanische Festigkeit, hohe Leitfähigkeit und gute Verformbarkeit aus. Ausgehend von der ersten Generation der Cu-HP-Legierungen, beispielsweise CuNi3SiMg mit einer elektrischen Leitfähigkeit von etwas über 20 MS/m, musste die Eigenschaftskombination einer hohen Festigkeit und hohen Leitfähigkeit weiter optimiert werden.Numerous new automotive applications for safety, comfort and performance can only be realized through the targeted use of electronic functions and components. Due to the increasing demands on the connectors and thus on the materials used, a trend towards copper high-performance alloys can be seen in recent years. These precipitation hardening copper materials are characterized by high mechanical strength, high conductivity and good ductility. Starting from the first generation of Cu-HP alloys, for example CuNi3SiMg with an electrical conductivity of just over 20 MS / m, the combination of properties of high strength and high conductivity had to be further optimized.

Ein Schritt in diese Richtung war zunächst die Entwicklung von ausscheidungshärtenden Kupferlegierungen, beispielsweise basierend auf dem System CuCrAgFeTiSi mit 46 MS/m und Festigkeiten bis 610 MPa. Ein weiterer wesentlicher Vorteil dieser Legierung ist die sehr gute Relaxationsbeständigkeit des Werkstoffes im Einsatz bei erhöhten Temperaturen bis zu 200 °C. Mit diesem Legierungstyp können Anwendungen in den Bereichen Automotive, Industrieelektronik und Telekommunikation abgedeckt werden.One step in this direction was the development of precipitation-hardening copper alloys, for example based on the CuCrAgFeTiSi system with 46 MS / m and strengths up to 610 MPa. Another important advantage of this alloy is the very good relaxation resistance of the material when used at elevated temperatures up to 200 ° C. This type of alloy can be used to cover applications in the automotive, industrial electronics and telecommunications sectors.

Zudem kommen Bronzewerkstoffe zum Einsatz, die sich durch eine feine Gefügestruktur mit einer Korngröße von maximal 3 µm auszeichnen. Hierdurch werden bereits wesentlich hohe mechanische Festigkeiten bei zugleich stark verbesserten Umformeigenschaften erreicht. Infolge der deutlich verbesserten Umformbarkeit können Verarbeiter entsprechend enge Biegeradien realisieren. Ebenso bewirkt die verbesserte Biegbarkeit, dass die Rauheit in den Umformzonen wesentlich geringer ist als bei Verwendung von Standardbronzen. So können nachfolgende Beschichtungen mit geringerer Schichtdicke ausgeführt werden, womit sich beträchtliche Kosteneinsparungen bei der Weiterverarbeitung erzielen lassen. Die elektrische Leitfähigkeit ist identisch mit der von Standardbronzen und liegt bei ungefähr 7,5 bis 12 MS/m.In addition, bronze materials are used, which are characterized by a fine microstructure with a grain size of maximum 3 µm. As a result, significantly high mechanical strengths are achieved with greatly improved forming properties. As a result of the significantly improved formability, processors can achieve correspondingly tight bending radii. The improved flexibility also means that the roughness in the forming zones is significantly less than when using standard bronze. Subsequent coatings with a lower layer thickness can thus be carried out, which can result in considerable cost savings in further processing. The electrical conductivity is identical to that of standard bronzes and is approximately 7.5 to 12 MS / m.

Eine weitere ausscheidungshärtende CuNi1CoSi-Legierung mit Ni-Co-Mischsiliziden eignet sich ebenfalls sehr gut für eine wirtschaftliche Miniaturisierung von Steckverbindern. Der Werkstoff ist hochfest, besitzt mit 29 MS/m eine vergleichsweise gute elektrische und thermische Leitfähigkeit und lässt sich gut verarbeiten.Another precipitation-hardening CuNi1CoSi alloy with Ni-Co mixed silicides is also very suitable for economical miniaturization of connectors. The material is high-strength, has a comparatively good electrical and thermal conductivity at 29 MS / m and is easy to process.

Die beschriebenen Werkstoffe eignen sich vor allem für die Verarbeitung auf Stanz-/Biegeautomaten und lassen sich nur mit großem Aufwand spanabhebend bearbeiten.The materials described are particularly suitable for processing on punching / bending machines and can only be machined with great effort.

Weitere Kupferwerkstoffe in Form von Stangen und Drähten, die sich hervorragend für spanend herzustellende Buchsen und Pins für Steckverbinder eignen, sind auch im Werkstoffportfolio der kostengünstigen Messingwerkstoffen mit den Legierungen CuZn37Pb0,5, CuZn35Pb1, CuZn35Pb2, CuZn37Pb2, CuZn36Pb3 und CuZn39Pb3 bekannt, die für anspruchsvolle Anwendungen in der Herstellung gedrehter Steckverbinder Einsatz finden.Other copper materials in the form of rods and wires, which are excellently suited for bushings and pins for connectors to be machined, are also known in the material portfolio of the inexpensive brass materials with the alloys CuZn37Pb0.5, CuZn35Pb1, CuZn35Pb2, CuZn37Pb2, CuZn36Pb3 and CuZn39Pb3 Applications are used in the manufacture of turned connectors.

Abhängig von den technischen Anforderungen kommen in diesen Fällen Werkstoffe mit hoher elektrischer Leitfähigkeit, hoher mechanischer Festigkeit sowie beide dieser Eigenschaften in Kombination zum Einsatz. So ist auch CuPb1P ein weiterer gut zerspanbarer Automatenwerkstoff, der zugleich eine hohe elektrische Leitfähigkeit von ungefähr 50 MS/m aufweist. Er eignet sich besonders für Steckverbinder und andere elektronische Anwendungen.In these cases, depending on the technical requirements, materials with high electrical conductivity and high mechanical strength are used as well as both of these properties in combination. CuPb1P is another easily machinable machine material that also has a high electrical conductivity of around 50 MS / m. It is particularly suitable for connectors and other electronic applications.

Neben den mischkristallhärtenden Legierungen wird das Legierungsspektrum durch weitere ausscheidungshärtende Werkstoffe abgerundet. Hierzu gehören beispielsweise CuNi1Pb1P und CuNiPb0,5P als niedriglegierter Kupferwerkstoff mit hoher Festigkeit, guter Leitfähigkeit von zumindest 32 MS/m sowie guter Zerspanbarkeit. Der Werkstoff eignet sich durch den Pb-Anteil besonders für zerspanend hergestellte Steckkontakte in der Elektrotechnik und Elektronik.In addition to the mixed crystal hardening alloys, the range of alloys is rounded off by further precipitation hardening materials. These include, for example, CuNi1Pb1P and CuNiPb0.5P as a low-alloy copper material with high strength, good conductivity of at least 32 MS / m and good machinability. The Pb component makes the material particularly suitable for machined plug contacts in electrical engineering and electronics.

Auch mit der Mehrstoff-Zinnbronze CuSn4Zn4Pb4P mit jeweils einem 4%-igen Zinn-, Zink- und Bleianteil lassen sich hohe Festigkeiten mit entsprechenden Federeigenschaften einstellen. Diese Zinnbronze ist gut kaltumformbar und lässt sich hervorragend zerspanen. Spezielle Einsatzgebiete sind federnde Elektronik-Kontakte.Even with the multi-component tin bronze CuSn4Zn4Pb4P, each with a 4% tin, zinc and lead content, high strengths with corresponding spring properties can be set. This tin bronze is easy to form cold and can be excellently machined. Special areas of application are resilient electronic contacts.

Bei einer Legierungsentwicklung mittlerweile immer zu berücksichtigen sind die verschiedenen Umweltdirektiven und Stoffbeschränkungen. Hierzu ergeben sich weitere Entwicklungspotentiale für alternative oder ergänzende Legierungen, welche für Steckverbinder geeignete Eigenschaftskombinationen auszeichnen. Dabei spielt neben den physikalischen Eigenschaften vor allem eine gute Bearbeitbarkeit eine entscheidende Rolle.The various environmental directives and substance restrictions must now always be taken into account when developing alloys. This results in further development potential for alternative or supplementary alloys, which distinguish combinations of properties suitable for connectors. In addition to the physical properties, good machinability plays a crucial role.

Der Erfindung liegt die Aufgabe zugrunde, eine Elektroklemme aus einer bleiarmen bzw. bleifreien Kupfer-Legierung weiterzubilden.The invention has for its object to develop an electrical clamp from a low-lead or lead-free copper alloy.

Die Erfindung wird durch die Merkmale des Anspruchs 1 wiedergegeben. Die weiteren rückbezogenen Ansprüche geben vorteilhafte Aus- und Weiterbildungen der Erfindung wieder.The invention is represented by the features of claim 1. The further back-related claims reflect advantageous developments and developments of the invention.

Die Erfindung schließt die technische Lehre zum Aufbau einer Elektroklemme enthaltend eine Kupfer-Zink-Legierung ein. Die Kupfer-Zink-Legierung besteht aus (in Gew.-%):

  • 28,0 bis 36,0 % Zn,
  • 0,5 bis 1,5 % Si,
  • 1,5 bis 2,5 % Mn,
  • 0,2 bis 1,0 % Ni,
  • 0,5 bis 1,5 % Al,
  • 0,1 bis 1,0 % Fe,
  • wahlweise noch bis maximal 0,1 % Pb,
  • wahlweise noch bis maximal 0,1 % P,
  • wahlweise noch bis 0,08 % S,
  • Rest Cu und unvermeidbare Verunreinigungen.
The invention includes the technical teaching for the construction of an electrical clamp containing a copper-zinc alloy. The copper-zinc alloy consists of (in% by weight):
  • 28.0 to 36.0% Zn,
  • 0.5 to 1.5% Si,
  • 1.5 to 2.5% Mn,
  • 0.2 to 1.0% Ni,
  • 0.5 to 1.5% Al,
  • 0.1 to 1.0% Fe,
  • optionally up to a maximum of 0.1% Pb,
  • optionally up to a maximum of 0.1% P,
  • optionally up to 0.08% S,
  • Balance Cu and unavoidable impurities.

Erfindungsgemäß sind in der Matrix Eisen-Nickel-Mangan-haltige Mischsilizide eingelagert. Das Gefüge besteht aus einer α-Matrix, in der Einlagerungen an β-Phase von 5 bis zu 45 Vol.-% sowie an Eisen-Nickel-Mangan-haltigen Mischsiliziden bis zu 20 Vol.-% enthalten sind. Des Weiteren liegen im Gefüge die Eisen-Nickel-Mangan-haltigen Mischsilizide mit stängeliger Form sowie an Eisen-Nickel-angereicherte Mischsilizide mit globularer Gestalt vor.According to the invention, iron-nickel-manganese-containing mixed silicides are embedded in the matrix. The structure consists of an α matrix, which contains deposits of 5 to 45% by volume of the β phase and mixed silicides containing iron-nickel-manganese of up to 20% by volume. In addition, the structure contains the iron-nickel-manganese-containing mixed silicides with a stem-like form and iron-nickel-enriched mixed silicides with a globular shape.

Überraschend hat sich gezeigt, dass sich die erfindungsgemäße Legierungszusammensetzung für Elektroklemmen eignet. Bisher war ein Einsatz derartiger Legierungen gemäß der deutschen Offenlegungsschrift DE 10 2007 029 991 A1 der Anmelderin nur für eine Verwendung für Gleitelemente in Verbrennungsmotoren, Getrieben oder hydraulischen Aggregaten vorgesehen.Surprisingly, it has been shown that the alloy composition according to the invention is suitable for electrical terminals. So far, such alloys have been used in accordance with the German published patent application DE 10 2007 029 991 A1 the applicant is only intended for use for sliding elements in internal combustion engines, transmissions or hydraulic units.

Derartige abweichende Anwendungen verfolgen einen anderen Zweck einer für spezielle Einsatzzwecke optimierten Eigenschaftskombination. Eine Eigenschaftskombination aus einer Erhöhung der Festigkeit, der Temperaturbeständigkeit des Gefüges und der komplexen Verschleißbeständigkeit bei gleichzeitig ausreichenden Zähigkeitseigenschaften im Hinblick auf motorische Anwendungen.Such deviating applications pursue a different purpose of a combination of properties optimized for special purposes. A combination of properties from an increase in strength, the temperature resistance of the structure and the complex wear resistance with sufficient toughness properties with regard to motor applications.

Demgegenüber geht die Erfindung von der Überlegung aus, eine Elektroklemme mit einer Kupfer-Zink-Legierung mit eingelagerten Eisen-Nickel-Mangan-haltigen Mischsiliziden bereitzustellen, die insbesondere mit Hilfe des kontinuierlichen oder halbkontinuierlichen Stranggussverfahrens hergestellt werden kann. Durch die Mischsilizidbildung und Gefügeausbildung weist die Kupfer-Zink-Legierung eine für diese Werkstoffgruppe sehr hohe elektrische Leitfähigkeit auf.In contrast, the invention is based on the consideration of providing an electrical clamp with a copper-zinc alloy with embedded iron-nickel-manganese-containing mixed silicides, which can be produced in particular with the aid of the continuous or semi-continuous continuous casting process. Due to the mixed silicide formation and microstructure formation, the copper-zinc alloy has a very high electrical conductivity for this group of materials.

Auch weist die Legierung hohe Härte- und Festigkeitswerte auf, trotzdem wird ein notwendiges Maß an Duktilität, ausgedrückt durch den Bruchdehnungswert bei einem Zugversuch, gewährleistet. Mit dieser Eigenschaftskombination erweist sich der Erfindungsgegenstand als besonders geeignet für Elektroklemmen, wahlweise auch mit Verschraubungen.The alloy also has high hardness and strength values, nevertheless a necessary degree of ductility, expressed by the elongation at break during a tensile test, is guaranteed. With this combination of properties, the subject of the invention proves to be particularly suitable for electrical terminals, optionally also with screw connections.

Beim vorausgehenden Herstellungsschritt des Gießens der Legierung findet zunächst eine frühe Ausscheidung von eisen- und nickelreichen Mischsiliziden statt. Diese Ausscheidungen können bei weiterem Wachstum zu Eisen-Nickel-Mangan-haltigen Mischsiliziden mit beträchtlicher Größe mit oft stängeliger Form heranwachsen. Des Weiteren bleibt auch ein beträchtlicher Anteil eher klein mit globularer Gestalt, der in der Matrix fein verteilt vorliegt. Die fein verteilten Silizide werden als Grund dafür gesehen, dass eine Stabilisierung der β-Phase stattfindet. Insbesondere weist die Legierung beim Kaltumformen eine hohe Duktilität auf. Bei Elektroklemmen ist dies beim Crimpen, bei dem üblicherweise der Werkstoff einer starken plastischen Verformung ausgesetzt wird, besonders wichtig. So ist ein Bördeln, Quetschen oder Falten des Werkstoffs unter nahezu beliebigem Umformgrad möglich, ohne dass sich eine Rissbildung im Werkstoff einstellt.In the preceding manufacturing step of casting the alloy, iron and nickel-rich mixed silicides are first separated out. With further growth, these precipitates can grow into mixed silicides containing iron-nickel-manganese of considerable size, often in the form of stalks. Furthermore, a considerable proportion remains rather small with a globular shape, which is finely distributed in the matrix. The finely divided silicides are seen as the reason that the β phase is stabilizing. In particular, the alloy has a high ductility during cold forming. In the case of electrical clamps, this is particularly important in crimping, in which the material is usually subjected to severe plastic deformation. This enables the material to be flanged, squeezed or folded with almost any degree of deformation, without the formation of cracks in the material.

Besonders eignet sich der Werkstoff auch für zerspanend hergestellte Elektroklemmen. Die gute Zerspanbarkeit wird bereits durch eine β-Phase von 5 Vol.-% erzielt. Zu höheren Gehalten hin verbessert sich bis zu 45 Vol.-% an β-Phase auch die Spanausbildung beim Zerspanungsvorgang, indem sich wünschenswerterweise Kurzspäne ausbilden. Mit einem Anteil an β-Phase unter 5 Vol.-% ist die Zerspanbarkeit in der Verwendung als Automatenwerkstoff für hohe Zerspanungsraten nicht mehr zufriedenstellend. Bei einem β-Phasengehalt von über 45 Vol.-% zeigt sich, dass sich die Zähigkeit des Werkstoffs und die Temperaturbeständigkeit des Gefüges verschlechtert. Der Endzustand der Legierung aus dem jeweiligen Fertigungsverfahren führt zu einer β-Phase, die inselartig in einem Gefüge aus einer α-Matrix eingelagert ist. Derartige Inseln aus β-Phase sind besonders günstig für die Zerspanbarkeit und die Korrosionsbeständigkeit der Legierung.The material is also particularly suitable for machined electrical terminals. The good machinability is already achieved with a beta phase of 5% by volume. Up to 45 vol.% Of the β-phase, the chip formation during the machining process also improves at higher contents, by desirably forming short chips. With a β-phase content of less than 5% by volume, machinability is no longer satisfactory when used as an automatic material for high machining rates. With a β-phase content of over 45% by volume, it can be seen that the toughness of the material and the temperature resistance of the structure deteriorate. The final state of the alloy from the respective manufacturing process leads to a β phase, which is embedded in an island structure in an α matrix. Such β-phase islands are particularly favorable for the machinability and the corrosion resistance of the alloy.

Eine besonders hohe Oberflächengüte der spanend bearbeiteten Oberflächen wird mit einem β-Phasen-Anteil jedoch insbesondere von 10 bis 25 Vol.-% erzielt. In dem angegebenen Volumenintervall von 5 bis 45 Vol.-% an β-Phase stellt sich auch ein vergleichsweise geringer Werkzeugverschleiß ein, so das die Werkzeuge entsprechend lange Standzeiten haben und damit die Werkzeugkosten verringert werden. Anteile an Eisen-Nickel-Mangan-haltigen Mischsiliziden über 20 Vol.-% würden eine so große Härtesteigerung bedingen, dass der Werkstoff in seiner Ausgewogenheit in der Kombination günstiger Eigenschaften leidet.However, a particularly high surface quality of the machined surfaces is achieved with a β-phase fraction, in particular from 10 to 25% by volume. In the specified volume interval of 5 to 45 vol.% Of the β phase, there is also comparatively little tool wear, so that the tools have a correspondingly long service life and thus the tool costs are reduced. The proportions of mixed silicides containing iron-nickel-manganese above 20% by volume would result in such a high increase in hardness that the balance of the material suffers from the combination of favorable properties.

Besonders hervorzuheben ist auch die Relaxationsbeständigkeit des Werkstoffs, wodurch die Federkraft einer Elektroklemme erhalten bleibt.Of particular note is the material's resistance to relaxation, which retains the spring force of an electrical clamp.

Damit beruht der besondere Vorteil der erfindungsgemäßen Legierung auf einer für die Einsatzzwecke optimierten Eigenschaftskombination in Form einer Erhöhung der Festigkeit, der Temperaturbeständigkeit des Gefüges und der elektrischen Leitfähigkeit bei gleichzeitig ausreichenden Zähigkeitseigenschaften.The particular advantage of the alloy according to the invention is thus based on a combination of properties optimized for the intended use in the form of an increase in the strength, the temperature resistance of the structure and the electrical conductivity with sufficient toughness properties at the same time.

Zusätzlich berücksichtigt die beanspruchte Werkstofflösung aufgrund des gegenüber gebräuchlichen Legierungen substituierten Bleigehaltes die Notwendigkeit einer umweltfreundlichen bleifreien Legierungsalternative. Außerdem ist dieser Werkstoff für besondere Anwendungen prädestiniert, bei denen es trotz hoher Anforderungen an die Härte und die Festigkeit auf ein notwendiges Maß an Plastifizierbarkeit ankommt.In addition, the material solution claimed takes into account the need for an environmentally friendly lead-free alloy alternative due to the lead content substituted for conventional alloys. In addition, this material is predestined for special applications where, despite high demands on hardness and strength, a necessary degree of plasticizability is required.

In vorteilhafter Ausgestaltung der Erfindung kann die Kupfer-Zink-Legierung

  • 30,0 bis 36,0 % Zn,
  • 0,6 bis 1,1 % Si,
  • 1,5 bis 2,2 % Mn,
  • 0,2 bis 0,7 % Ni,
  • 0,5 bis 1,0 % Al,
  • 0,3 bis 0,5 % Fe enthalten.
In an advantageous embodiment of the invention, the copper-zinc alloy
  • 30.0 to 36.0% Zn,
  • 0.6 to 1.1% Si,
  • 1.5 to 2.2% Mn,
  • 0.2 to 0.7% Ni,
  • 0.5 to 1.0% Al,
  • Contain 0.3 to 0.5% Fe.

Durch die enger gefassten Grenzen wird eine besonders vorteilhafte Legierungszusammensetzung ausgewählt. Hierdurch werden die Zähigkeitseigenschaften und die elektrische Leitfähigkeit, gegebenenfalls mit einer abschließenden Entspannungsglühung noch weiter verbessert. Bevorzugt wird die abschließende Entspannungsglühung bei 300 °C bis 400 °C über 3 bis 4 Stunden hinweg durchgeführt.Due to the narrower limits, a particularly advantageous alloy composition is selected. As a result, the toughness properties and the electrical conductivity are further improved, if necessary with a final stress relief annealing. The final relaxation annealing is preferably carried out at 300 ° C. to 400 ° C. for 3 to 4 hours.

In weiterer vorteilhafter Ausgestaltung der Erfindung kann die Kupfer-Zink-Legierung 33,5 bis 36,0 % Zn enthalten. Bei diesen höheren Zinkgehalten lassen sich immer noch die für Elektroklemme erforderlichen Zähigkeitseigenschaften und eine gute elektrische Leitfähigkeit realisieren. Durch einen möglichst hohen Zinkgehalt wird der Anteil der weiteren Elemente, insbesondere der Kupferanteil, entsprechend reduziert. Mit der Folge, dass die Legierung durch einen höheren Anteil an billigerem Zink einen entsprechend geringeren Metallpreis zur Folge hat.In a further advantageous embodiment of the invention, the copper-zinc alloy can contain 33.5 to 36.0% Zn. With these higher zinc contents, the toughness properties and good electrical conductivity required for electrical clamps can still be achieved. The proportion of further elements, in particular the copper proportion, is correspondingly reduced by the highest possible zinc content. With the consequence that the alloy results in a correspondingly lower metal price due to a higher proportion of cheaper zinc.

Vorteilhafterweise kann die elektrische Leitfähigkeit der Legierung zumindest 5,8 MS/m betragen. Besonders bevorzugte Leitfähigkeiten sind zumindest 10 MS/m bis über 13 MS/m. Diese Werte werden durch vergleichbare Werkstoffe, wie beispielsweise die bleihaltigen Messinge, nicht erzielt. Sogar Werte über 13 MS/m können durch geeignete Weiterbehandlungsschritte eingestellt werden.The electrical conductivity of the alloy can advantageously be at least 5.8 MS / m. Particularly preferred conductivities are at least 10 MS / m to over 13 MS / m. These values are not achieved by comparable materials, such as the brass containing lead. Even values above 13 MS / m can be set by suitable further processing steps.

Vorteilhafterweise kann das aus einer α-Matrix bestehende Gefüge, in der Einlagerungen an β-Phase von 5 bis zu 45 Vol.-% sowie an Eisen-Nickel-Mangan-haltigen Mischsiliziden bis zu 20 Vol.-% enthalten sind nach einer Weiterbearbeitung, die zumindest eine Warmumformung und/oder Kaltumformung und wahlweise weitere Glühschritte beinhaltet, ausgebildet sein. Mit den β-Einlagerungen und Hartphasen unterschiedlicher Größenverteilung in einer α-Matrix gewährleistet diese Legierung eine vorteilhafte Temperaturbeständigkeit des Gefüges mit hinreichenden Zähigkeitseigenschaften zur Herstellung der Elektroklemme.Advantageously, the structure consisting of an α matrix, which contains deposits of 5 to 45% by volume in the β phase and mixed silicides containing iron-nickel-manganese up to 20% by volume after further processing, which includes at least one hot forming and / or cold forming and optionally further annealing steps. With the β-deposits and hard phases of different size distribution in an α-matrix, this alloy ensures an advantageous temperature resistance of the structure with sufficient toughness properties for the manufacture of the electrical clamp.

Zur Weiterbearbeitung kann die Legierung vorteilhafterweise bei ihrer Weiterbearbeitung folgende Schritte durchlaufen haben:

  • Strangpressen oder Warmwalzen in einem Temperaturbereich von 600 bis 800 °C,
  • zumindest eine Kaltumformung, bevorzugt durch Ziehen oder Kaltwalzen.
For further processing, the alloy can advantageously have gone through the following steps during its further processing:
  • Extrusion or hot rolling in a temperature range from 600 to 800 ° C,
  • at least one cold forming, preferably by drawing or cold rolling.

Auch kann in bevorzugter Ausgestaltung der Erfindung die Legierung bei ihrer Weiterbearbeitung folgende Schritte durchlaufen haben:

  • Strangpressen oder Warmwalzen in einem Temperaturbereich von 600 bis 800 °C,
  • eine Kombination aus zumindest einer Kaltumformung, bevorzugt durch Ziehen oder Kaltwalzen und zumindest einer Glühung in einem Temperaturbereich von 250 bis 700 °C, bevorzugt mit einer Glühdauer von 20 Minuten bis 5 Stunden.
In a preferred embodiment of the invention, the alloy may have undergone the following steps in its further processing:
  • Extrusion or hot rolling in a temperature range from 600 to 800 ° C,
  • a combination of at least one cold forming, preferably by drawing or cold rolling and at least one annealing in a temperature range from 250 to 700 ° C, preferably with an annealing time of 20 minutes to 5 hours.

Mittels einer Kombination von Kaltumformung durch Ziehen und einer oder mehrerer Glühungen der Ausgangsmaterialen in Form von Runddrähten, Profildrähten, Rundstangen, Profilstangen, Hohlstangen und Rohren im Temperaturbereich von 250 bis 700 °C ist es möglich, eine feine Verteilung des heterogenen Gefüges einzustellen. Auf diese Weise wird der Forderung nach der Verbesserung der elektrischen Leitfähigkeit entsprochen.By means of a combination of cold forming by drawing and one or more annealing of the starting materials in the form of round wires, Profile wires, round bars, profile bars, hollow bars and tubes in the temperature range from 250 to 700 ° C, it is possible to set a fine distribution of the heterogeneous structure. In this way, the demand for improving the electrical conductivity is met.

Von besonderem Interesse ist auch der Zusammenhang zwischen der Höhe und Verteilung des Anteils der β-Phase und der Temperaturbeständigkeit des Gefüges. Da jedoch diese kubisch-raumzentrierte Kristallart eine unverzichtbare festigkeitssteigernde Funktion in den Kupfer-Zink-Legierungen übernimmt, sollte die Minimierung des β-Gehaltes nicht ausschließlich im Vordergrund stehen. Mittels der Fertigungsfolge Strangpressen oder Warmwalzen / Ziehen oder Kaltwalzen / Zwischenglühungen kann das Gefüge der Kupfer-Zink-Legierung in seiner Phasenverteilung derart modifiziert werden, dass es neben einer hohen Festigkeit zusätzlich eine hinreichende Temperaturbeständigkeit, Duktilität und gute elektrische Leitfähigkeit aufweist.Of particular interest is the relationship between the level and distribution of the proportion of the β phase and the temperature resistance of the structure. However, since this cubic, body-centered type of crystal has an indispensable strength-increasing function in the copper-zinc alloys, the minimization of the β content should not be the only focus. By means of the production sequence extrusion or hot rolling / drawing or cold rolling / intermediate annealing, the structure of the copper-zinc alloy can be modified in such a way that, in addition to high strength, it also has sufficient temperature resistance, ductility and good electrical conductivity.

In bevorzugter Ausgestaltung kann sich bei der Weiterbearbeitung nach dem Umformen zumindest eine Entspannungsglühung in einem Temperaturbereich von 250 bis 450 °C und bevorzugt einer Glühdauer von 2 bis 5 Stunden anschließen.In a preferred embodiment, at least one relaxation annealing in a temperature range from 250 to 450 ° C. and preferably an annealing time of 2 to 5 hours can follow in the further processing after the shaping.

Im Fertigungsverlauf besteht die Notwendigkeit, anhand einer oder mehrerer Entspannungsglühungen die Höhe der Eigenspannungen zu reduzieren. Die Absenkung der Eigenspannungen ist auch bedeutsam für die Gewährleistung einer ausreichenden Temperaturbeständigkeit des Gefüges und für die Sicherstellung einer genügenden Geradheit der Runddrähte, Profildrähte, Rundstangen, Profilstangen, Hohlstangen und Rohre als Vorläuferprodukte der Elektroklemme.In the course of production there is a need to reduce the amount of residual stress using one or more stress relief anneals. The lowering of the residual stresses is also important for ensuring that the structure is sufficiently temperature-resistant and for ensuring that the round wires, profile wires, round bars, profile bars, hollow bars and tubes are precursors of the electrical clamp.

Weitere Ausführungsbeispiele der Erfindung werden anhand einer Tabellen näher erläutert. Hierbei handelt es sich nach den Untersuchungen um eine am besten angesehene Ausführungsform. Weitere hiervon abweichende Ausführungsformen eigenen sich im Rahmen der Erfindung jedoch gleichermaßen dazu, die erfinderischen Vorteile zu erzielen.Further exemplary embodiments of the invention are explained in more detail using a table. According to the investigations, this is an am best viewed embodiment. Other embodiments deviating from this are equally suitable within the scope of the invention to achieve the inventive advantages.

Es wurden Gussbolzen der erfindungsgemäßen Kupfer-Zink-Legierung durch Strangguss bzw. Kokillenguss hergestellt. Die chemische Zusammensetzung des Stranggusses der Legierung 1 und des Kokillengusses der Legierungen 2 und 3 geht aus Tab. 1 hervor. Tabelle 1: Chemische Zusammensetzung der Gussbolzen bzw. Gussblöcke (in Gew.-%) ohne Angabe möglicher Verunreinigungen Cu [%] Zn [%] Si [%] Mn [%] Ni [%] Sn [%] Al [%] Fe [%] Leg. 1 64,0 31,1 1,0 2,0 0,6 < 0,01 0,9 0,4 Leg. 2 64,0 30,8 1,1 2,1 0,6 - 0,9 0,5 Leg. 3 61,6 34,8 0,7 1,7 0,3 - 0,5 0,4 Cast bolts of the copper-zinc alloy according to the invention were produced by continuous casting or permanent mold casting. The chemical composition of the continuous casting of alloy 1 and the die casting of alloys 2 and 3 is shown in Table 1. Table 1: Chemical composition of the casting bolts or casting blocks (in% by weight) without indication of possible impurities Cu [%] Zn [%] Si [%] Mn [%] Ni [%] Sn [%] Al [%] Fe [%] Leg. 1 64.0 31.1 1.0 2.0 0.6 <0.01 0.9 0.4 Leg. 2 64.0 30.8 1.1 2.1 0.6 - 0.9 0.5 Leg. 3 61.6 34.8 0.7 1.7 0.3 - 0.5 0.4

Fertigungsfolge 1:Production sequence 1:

  • Strangpressen der Gussbolzen aus Leg.1 zu Rohren bei der Temperatur von 670-770 °CExtrusion of the cast bolts from Leg.1 to tubes at a temperature of 670-770 ° C
  • Kombination von Kaltumformung/Zwischenglühungen (630-700 °C / 50min-3h)/Richten/Entspannungsglühungen (300-400 °C / 3h)Combination of cold forming / intermediate annealing (630-700 ° C / 50min-3h) / straightening / relaxation annealing (300-400 ° C / 3h)

Nach durchlaufener Fertigung befinden sich die Gefügekennwerte, die elektrische Leitfähigkeit und die mechanischen Eigenschaften der Rohre mit der Abmessung (30,1x24,7) mm auf dem Niveau, das in Zahlenwerten in Tab. 2 dargestellt ist. Tabelle 2: Gefügekennwerte, elektrische Leitfähigkeit und mechanische Eigenschaften an zwei Positionen der Rohre im Endzustand (Leg. 1) β-Gehalt [%] Korngröße [µm] Elektrische Leitfähigkeit [MS/m] Rm [MPa] Rp0,2 [MPa] Bruchdehnung A5 [%] Härte HB 5 15-20 11,4 640 560 14,5 201 15-20 20-25 11,2 647 572 13,2 199 After production has been completed, the structural parameters, the electrical conductivity and the mechanical properties of the tubes with the dimensions (30.1x24.7) mm are at the level shown in numerical values in Table 2. Table 2: Structure parameters, electrical conductivity and mechanical properties at two positions of the pipes in the final state (Leg. 1) β content [%] Grain size [µm] Electrical conductivity [MS / m] Rm [MPa] R p0.2 [MPa] Elongation at break A5 [%] Hardness HB 5 15-20 11.4 640 560 14.5 201 15-20 20-25 11.2 647 572 13.2 199

Fertigungsfolge 2:Production sequence 2:

  • Strangpressen der Gussbolzen aus Leg. 1 zu Rundstangen bei der Temperatur von 650-750 °CExtrusion of the cast bolts from Leg. 1 to round bars at the temperature of 650-750 ° C
  • Kombination von Kaltumformung/Glühungen (630-720 °C / 50min-4h) / Richten/Entspannungsglühungen (300-450 °C / 2-4h)Combination of cold forming / annealing (630-720 ° C / 50min-4h) / straightening / relaxation annealing (300-450 ° C / 2-4h)

Nach durchlaufener Fertigung befinden sich die Gefügekennwerte, die elektrische Leitfähigkeit und die mechanischen Eigenschaften der Rundstangen mit dem Durchmesser von 13,40 mm, 16,35 mm und 45,50 mm auf dem Niveau, das in Zahlenwerten in Tab. 3 dargestellt ist. Tabelle 3: Gefügekennwerte, elektrische Leitfähigkeit und mechanische Eigenschaften der Rundstangen im Endzustand (Leg. 1) Rundstange Ø [mm] β-Gehalt [%] Korngröße [µm] Elektrische Leitfähigkeit [MS/m] Rm [MPa] Rp0,2 [MPa] Bruchdehnung A5 [%] Härte HB 13,40 5 20-25 11,4 607 512 12,4 191 16,35 15-20 25 10,9 638 549 12,0 199 45,50 10-15 25 10,7 570 420 20,1 172 After production has been completed, the structural parameters, the electrical conductivity and the mechanical properties of the round bars with the diameters of 13.40 mm, 16.35 mm and 45.50 mm are at the level shown in figures in Table 3. Table 3: Structure parameters, electrical conductivity and mechanical properties of the round bars in the final state (Leg. 1) Round rod Ø [mm] β content [%] Grain size [µm] Electrical conductivity [MS / m] R m [MPa] R p0.2 [MPa] Elongation at break A5 [%] Hardness HB 13.40 5 20-25 11.4 607 512 12.4 191 16.35 15-20 25 10.9 638 549 12.0 199 45.50 10-15 25 10.7 570 420 20.1 172

Fertigungsfolge 3:Production sequence 3:

  • Warmwalzen der Gussblöcke aus Leg. 2 und 3 zu Walzplatten bei der Temperatur von 650-730 °C
  • Kaltwalzen der Platten mit einer Umformung von 15 bis 25 % gegebenenfalls mit Entspannungsglühungen (300-450 °C / 2-4h)
Zusätzlich zwischen den einzelnen Verfahrensschritten gegebenenfalls noch Fräsen der Oberflächen. Tabelle 4: Gefügekennwerte, elektrische Leitfähigkeit und mechanische Eigenschaften der Walzplatten im Endzustand (Walzplattendicke 3 mm, mit und ohne Entspannungsglühung ESG als letzten Prozessschritt) Legierung β-Gehalt [%] Korngröße [µm] Elektr. Leitfähigkeit [MS/m] Rm [MPa] Rp0,2 [MPa] Bruchdehnung A5 [%] Härte HB Leg. 2 (ohne ESG) 14 15-20 8,9 608 540 7,8 188 Leg. 2 (ESG 340°C/3h) 13 15-20 10,5 646 543 15,6 192 Leg. 2 (ESG 400°C/3h) 13 15-20 10,7 615 483 19,0 184 Leg. 3 (ohne ESG) 20 20-25 11,0 596 516 11,3 178 Leg. 3 (ESG 340°C/3h) 18 20-25 12,7 593 464 18,6 176 Leg. 3 (ESG 400°C/3h) 18 20-25 12,7 580 428 21,6 170
  • Hot rolling the cast blocks from Leg. 2 and 3 to rolled plates at the temperature of 650-730 ° C
  • Cold rolling of the plates with a deformation of 15 to 25%, if necessary with stress relief annealing (300-450 ° C / 2-4h)
In addition, between the individual process steps, if necessary, milling of the surfaces. Table 4: Structural parameters, electrical conductivity and mechanical properties of the rolled plates in the final state (rolled plate thickness 3 mm, with and without stress relief annealing ESG as the last process step) alloy β content [%] Grain size [µm] Electrical conductivity [MS / m] R m [MPa] R p0.2 [MPa] Elongation at break A5 [%] Hardness HB Leg. 2 (without ESG) 14 15-20 8.9 608 540 7.8 188 Leg. 2 (ESG 340 ° C / 3h) 13 15-20 10.5 646 543 15.6 192 Leg. 2 (ESG 400 ° C / 3h) 13 15-20 10.7 615 483 19.0 184 Leg. 3 (without ESG) 20 20-25 11.0 596 516 11.3 178 Leg. 3 (ESG 340 ° C / 3h) 18 20-25 12.7 593 464 18.6 176 Leg. 3 (ESG 400 ° C / 3h) 18 20-25 12.7 580 428 21.6 170

Fertigungsfolge 4:Production sequence 4:

  • Warmwalzen der Gussblöcke aus Leg. 2 und 3 zu Walzplatten bei der Temperatur von 650-730 °C
  • Kombination einer Glühung (650 °C / 3h) und Kaltwalzen der Platten mit einer Umformung von 15 bis 25 % gegebenenfalls mit Entspannungsglühungen (300-450 °C / 2-4h)
Zusätzlich zwischen den einzelnen Verfahrensschritten gegebenenfalls noch Fräsen der Oberflächen. Tabelle 5: Gefügekennwerte, elektrische Leitfähigkeit und mechanische Eigenschaften der Walzplatten im Endzustand (Walzplattendicke 3 mm, mit und ohne Entspannungsglühung ESG als letzten Prozessschritt) Legierung β-Gehalt [%] Korngröße [µm] Elektr. Leitfähigkeit [MS/m] Rm [MPa] Rp0,2 [MPa] Bruchdehnung A5 [%] Härte HB Leg. 2 (ohne ESG) 10 10-15 9,3 573 510 11,8 180 Leg. 2 (ESG 340°C/3h) 10 10-15 10,6 587 470 19,4 176 Leg. 2 (ESG 400°C/3h) 10 10-15 10,6 583 452 20,0 174 Leg. 3 (ohne ESG) 15 20-25 10,5 555 482 13,5 172 Leg. 3 (ESG 340°C/3h) 15 20-25 12,7 553 422 21,0 166 Leg. 3 (ESG 400°C/3h) 15 20-25 12,7 544 403 19,5 162
  • Hot rolling the cast blocks from Leg. 2 and 3 to rolled plates at the temperature of 650-730 ° C
  • Combination of annealing (650 ° C / 3h) and cold rolling of the plates with a deformation of 15 to 25%, optionally with stress relief annealing (300-450 ° C / 2-4h)
In addition, between the individual process steps, if necessary, milling of the surfaces. Table 5: Structure parameters, electrical conductivity and mechanical properties of the rolled plates in the final state (rolled plate thickness 3 mm, with and without stress relief annealing ESG as the last process step) alloy β content [%] Grain size [µm] Electrical conductivity [MS / m] R m [MPa] R p0.2 [MPa] Elongation at break A5 [%] Hardness HB Leg. 2 (without ESG) 10 10-15 9.3 573 510 11.8 180 Leg. 2 (ESG 340 ° C / 3h) 10 10-15 10.6 587 470 19.4 176 Leg. 2 (ESG 400 ° C / 3h) 10 10-15 10.6 583 452 20.0 174 Leg. 3 (without ESG) 15 20-25 10.5 555 482 13.5 172 Leg. 3 (ESG 340 ° C / 3h) 15 20-25 12.7 553 422 21.0 166 Leg. 3 (ESG 400 ° C / 3h) 15 20-25 12.7 544 403 19.5 162

Fertigungsfolge 5:Production sequence 5:

  • Warmwalzen der Gussblöcke aus Leg. 2 und 3 zu Walzplatten bei der Temperatur von 650-730 °C
  • Kombination von Kaltwalzen der Platten mit einer Umformung von 15 bis 65 %/Glühungen (630-720 °C / 50min-4h)
Zusätzlich zwischen den einzelnen Verfahrensschritten gegebenenfalls noch Fräsen der Oberflächen. Tabelle 6: Gefügekennwerte, elektrische Leitfähigkeit und mechanische Eigenschaften der Walzplatten im Endzustand (Walzplattendicke 2,3 mm, ohne Entspannungsglühung ESG) Legierung β-Gehalt [%] Korngröße [µm] Elektr. Leitfähigkeit [MS/m] Rm [MPa] Rp0,2 [MPa] Bruchdehnung A5 [%] Härte HB Leg. 2 10 10-15 9,1 558 484 17,6 171 Leg. 3 15 15-20 10,2 556 471 18,9 167
  • Hot rolling the cast blocks from Leg. 2 and 3 to rolled plates at the temperature of 650-730 ° C
  • Combination of cold rolling of the plates with a conversion of 15 to 65% / annealing (630-720 ° C / 50min-4h)
In addition, between the individual process steps, if necessary, milling of the surfaces. Table 6: Structure parameters, electrical conductivity and mechanical properties of the rolled plates in the final state (rolled plate thickness 2.3 mm, without stress relief annealing ESG) alloy β content [%] Grain size [µm] Electrical conductivity [MS / m] R m [MPa] R p0.2 [MPa] Elongation at break A5 [%] Hardness HB Leg. 2 10 10-15 9.1 558 484 17.6 171 Leg. 3 15 15-20 10.2 556 471 18.9 167

Insbesondere der Kennwert für die elektrische Leitfähigkeit kann für die nach der Fertigungsfolge 5 hergestellten Formate der Legierungen 2 und 3 durch eine zusätzlich durchgeführte Entspannungsglühung bei einer Temperatur von 250 bis 450°C weiter erhöht werden.In particular, the characteristic value for the electrical conductivity can be further increased for the formats of alloys 2 and 3 produced according to production sequence 5 by an additional stress relief annealing carried out at a temperature of 250 to 450 ° C.

Zu den Ausführungsbeispielen ist hervorzuheben, dass bei allen 5 Fertigungsfolgen der β-Gehalt zwischen 5-20 % liegt. Weitere Untersuchungen zeigen, dass bevorzugt die β-Gehalte zwischen 5-30 % liegen. Die im Endzustand der Fertigung inselartige Ausbildung der β-Phase, eingelagert in einem Gefüge aus einer α-Matrix, kann dabei in etwas unterschiedlicher Ausprägung in Erscheinung treten. Bei zunehmend geringeren Gehalten an β-Phase treten eher voneinander isolierte Inseln auf, die im Grenzfall gegenüber den Kristalliten der α-Matrix eine Art Zwickelfüllung bilden können.With regard to the exemplary embodiments, it should be emphasized that the β content is between 5-20% in all 5 production sequences. Further investigations show that the β contents are preferably between 5-30%. The island-like formation of the β phase in the final state of production, embedded in a structure of an α matrix, can appear in somewhat different forms. With increasingly lower contents of the β-phase, islands that are isolated from each other appear, which in the limit case can form a kind of gusset filling compared to the crystallites of the α-matrix.

Claims (10)

  1. Electrical connection element containing a copper/zinc alloy, comprising (in % by weight):
    from 28.0 to 36.0% Zn,
    from 0.5 to 1.5% Si,
    from 1.5 to 2.5% Mn,
    from 0.2 to 1.0% Ni,
    from 0.5 to 1.5% Al,
    from 0.1 to 1.0% Fe,
    optionally also up to a maximum of 0.1% Pb,
    optionally also up to a maximum of 0.1% P,
    optionally also up to 0.08% S,
    the balance being Cu and inevitable impurities,
    characterised in that
    - iron/nickel/manganese-containing mixed silicides are incorporated in the matrix,
    - in that the structure comprises an α-matrix, in which deposits of β-phase of from 5 to 45% by volume and iron/nickel/manganese-containing mixed silicides at up to 20% by volume are contained,
    - in that in the structure the iron/nickel/manganese-containing mixed silicides are present in stalk-like form and iron/nickel-enriched mixed silicides are present in globular form.
  2. Electrical connection element according to claim 1, characterised by:
    from 30.0 to 36.0% Zn,
    from 0.6 to 1.1% Si,
    from 1.5 to 2.2% Mn,
    from 0.2 to 0.7% Ni,
    from 0.5 to 1.0% Al,
    from 0.3 to 0.5% Fe.
  3. Electrical connection element according to claim 2,
    characterised by:
    from 33.5 to 36.0% Zn.
  4. Electrical connection element according to any one of claims 1 to 3, characterised in that the electrical conductivity of the alloy is at least 5.8 MS/m.
  5. Electrical connection element according to claim 4, characterised in that the electrical conductivity of the alloy is at least 10 MS/m.
  6. Electrical connection element according to claim 5, characterised in that the electrical conductivity of the alloy is at least 13 MS/m.
  7. Electrical connection element comprising a copper/zinc alloy according to any one of claims 1 to 6, characterised in that the structure which comprises an α-matrix and in which deposits of β-phase of from 5 to 45% by volume and iron/nickel/manganese-containing mixed silicides at up to 20% by volume are contained, is formed after further processing which involves at least one hot-forming and/or cold-forming operation and optionally additional annealing steps.
  8. Electrical connection element comprising a copper/zinc alloy according to claim 7, characterised in that the alloy during the further processing thereof has undergone the following steps:
    - extrusion or hot-rolling in a temperature range from 600 to 800°C,
    - at least one cold-forming operation.
  9. Electrical connection element comprising a copper/zinc alloy according to claim 7, characterised in that the alloy during the further processing thereof has undergone the following steps:
    - extrusion or hot-rolling in a temperature range from 600 to 800°C,
    - a combination of at least one cold-forming and at least one annealing operation in a temperature range from 250 to 700°C.
  10. Electrical connection element comprising a copper/zinc alloy according to claim 8 or claim 9, characterised in that, during the further processing, the shaping operation is followed by at least one stress-relieving annealing operation in a temperature range from 250 to 450°C.
EP15756842.9A 2014-09-25 2015-08-29 Electrical clamps Active EP3198048B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL15756842T PL3198048T3 (en) 2014-09-25 2015-08-29 Electrical clamps

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102014014239.6A DE102014014239B4 (en) 2014-09-25 2014-09-25 Electrical connecting element
PCT/EP2015/001759 WO2016045770A1 (en) 2014-09-25 2015-08-29 Electrical connection element

Publications (2)

Publication Number Publication Date
EP3198048A1 EP3198048A1 (en) 2017-08-02
EP3198048B1 true EP3198048B1 (en) 2020-02-26

Family

ID=54014765

Family Applications (1)

Application Number Title Priority Date Filing Date
EP15756842.9A Active EP3198048B1 (en) 2014-09-25 2015-08-29 Electrical clamps

Country Status (9)

Country Link
US (1) US20170204501A1 (en)
EP (1) EP3198048B1 (en)
JP (1) JP6514318B2 (en)
KR (1) KR20170059436A (en)
CN (1) CN106715731A (en)
DE (1) DE102014014239B4 (en)
PL (1) PL3198048T3 (en)
TW (1) TWI651422B (en)
WO (1) WO2016045770A1 (en)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3404774B1 (en) * 2017-05-17 2021-10-06 Infineon Technologies AG Method for electrically connecting an electronic module and electronic assembly
DE202018104958U1 (en) 2018-08-30 2018-09-12 Harting Electric Gmbh & Co. Kg Connector with components of improved material
DE202020101700U1 (en) * 2020-03-30 2021-07-01 Otto Fuchs - Kommanditgesellschaft - Pb-free Cu-Zn alloy
CN113981268B (en) * 2021-10-29 2022-10-21 宁波金田铜业(集团)股份有限公司 Preparation method of brass wire
DE102022122830A1 (en) 2022-09-08 2024-03-14 Diehl Brass Solutions Stiftung & Co. Kg Lead-free brass alloy and bearing component made therefrom
DE102022122831A1 (en) 2022-09-08 2024-03-14 Diehl Brass Solutions Stiftung & Co. Kg Lead-free brass alloy and machine element made therefrom

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3082288A (en) * 1959-06-03 1963-03-19 British Fed Welder & Machine C Welding cables
DE29712696U1 (en) * 1996-07-18 1997-11-20 Trafiment S P A Connection part for welding cable with built-in connector for connection to the electrical supply cable
WO2005018055A1 (en) * 2003-07-29 2005-02-24 Gator Loc, Llc Cable terminal and cable assembly

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6471792B1 (en) * 1998-11-16 2002-10-29 Olin Corporation Stress relaxation resistant brass
JP4123459B2 (en) * 2000-06-12 2008-07-23 三菱マテリアル株式会社 Hot forged synchronizer ring made of copper alloy with excellent fatigue strength at the chamfer
CN1225564C (en) * 2003-03-14 2005-11-02 宁波博威集团有限公司 High-zinc-tin-manganese-chromium prass-alloy and its wire material making process
CH693948A5 (en) * 2003-03-21 2004-05-14 Swissmetal Boillat Sa Copper based alloy used for fabrication of ball-point pen components contains specified amounts of copper, zinc, nickel, manganese and lead
JP4660735B2 (en) * 2004-07-01 2011-03-30 Ｄｏｗａメタルテック株式会社 Method for producing copper-based alloy sheet
JP4834592B2 (en) * 2007-03-29 2011-12-14 株式会社東芝 3D image display device
DE102007063643B4 (en) * 2007-06-28 2012-07-26 Wieland-Werke Ag Copper-zinc alloy, method of manufacture and use
EP2009122B1 (en) * 2007-06-28 2014-10-08 Wieland-Werke AG Copper-zinc alloy, method for its manufacture and use
CN103589903B (en) * 2013-08-16 2016-04-20 武汉泛洲中越合金有限公司 A kind of high-strength wear-resistant copper alloy and manufacture method thereof

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3082288A (en) * 1959-06-03 1963-03-19 British Fed Welder & Machine C Welding cables
DE29712696U1 (en) * 1996-07-18 1997-11-20 Trafiment S P A Connection part for welding cable with built-in connector for connection to the electrical supply cable
WO2005018055A1 (en) * 2003-07-29 2005-02-24 Gator Loc, Llc Cable terminal and cable assembly

Also Published As

Publication number Publication date
TW201617460A (en) 2016-05-16
JP6514318B2 (en) 2019-05-15
US20170204501A1 (en) 2017-07-20
CN106715731A (en) 2017-05-24
PL3198048T3 (en) 2020-07-13
DE102014014239A1 (en) 2016-03-31
KR20170059436A (en) 2017-05-30
EP3198048A1 (en) 2017-08-02
WO2016045770A1 (en) 2016-03-31
JP2017532436A (en) 2017-11-02
DE102014014239B4 (en) 2024-04-11
TWI651422B (en) 2019-02-21

Similar Documents

Publication Publication Date Title
EP3198048B1 (en) Electrical clamps
DE112005001197B4 (en) Method for producing a workpiece made of a copper alloy
DE60101026T2 (en) Copper alloy containing silver
EP2806044B1 (en) Copper-zinc alloy, method for its manufacture and use
EP1850018B2 (en) Strip-shaped composite material
DE112009000731B4 (en) Cu-Ni-Si-Co-Cr system alloy for electronic materials
EP1997920A2 (en) Copper alloy for electric and electronic equipments
DE112005000312B4 (en) copper alloy
DE102013018216A1 (en) Copper alloy material for electrical and electronic components and method of making same (COPPER ALLOY MATERIAL FOR ELECTRONIC COMPONENTS AND METHOD FOR PREPARING THE SAME)
JP2013194268A (en) Copper alloy material excellent in die wear resistance during press, and method of manufacturing the same
EP3004413B1 (en) Refill for a ball-point pen and use thereof
EP3529389B1 (en) Copper-zinc alloy
EP3908682B1 (en) Pb-free cu-zn alloy
WO2014154191A1 (en) Copper alloy
DE69814657T2 (en) COPPER BASED ALLOY, CHARACTERIZED BY DECAY CURING AND CURING IN SOLID CONDITION
EP3366793B1 (en) Sliding element made of a copper alloy
DE102016223430A1 (en) Electric cable made of aluminum alloy and wiring harness
DE102022002927B4 (en) Wrought material made of a copper-zinc alloy, semi-finished product made of a wrought material and process for producing such a semi-finished product
EP3041966B1 (en) Copper alloy, which contains iron and phosphor
DE102022002928B4 (en) Wrought material made of a copper-zinc alloy, semi-finished product made of a wrought material and process for producing such a semi-finished product
EP2088215A1 (en) Copper alloy material for electrical/electronic part and process for producing the same
DE102013014500A1 (en) copper alloy

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20170228

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20180516

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20191004

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: CH

Ref legal event code: NV

Representative=s name: BOHEST AG, CH

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1237697

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200315

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502015011871

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200526

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20200226

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200626

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200527

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200526

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200719

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502015011871

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20201127

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200829

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20200831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200829

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200831

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 1237697

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200829

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200829

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200226

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: PL

Payment date: 20230615

Year of fee payment: 9

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: TR

Payment date: 20230828

Year of fee payment: 9

Ref country code: IT

Payment date: 20230711

Year of fee payment: 9

Ref country code: GB

Payment date: 20230706

Year of fee payment: 9

Ref country code: CH

Payment date: 20230902

Year of fee payment: 9

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20230703

Year of fee payment: 9

Ref country code: DE

Payment date: 20230831

Year of fee payment: 9