EP0346645A1 - Use of an age-hardenable copper-based alloy - Google Patents

Use of an age-hardenable copper-based alloy Download PDF

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Publication number
EP0346645A1
EP0346645A1 EP89109136A EP89109136A EP0346645A1 EP 0346645 A1 EP0346645 A1 EP 0346645A1 EP 89109136 A EP89109136 A EP 89109136A EP 89109136 A EP89109136 A EP 89109136A EP 0346645 A1 EP0346645 A1 EP 0346645A1
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casting
zirconium
copper alloy
copper
blocks
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EP89109136A
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German (de)
French (fr)
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EP0346645B1 (en
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Horst Dipl.-Ing. Gravemann
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KM Kabelmetal AG
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KM Kabelmetal AG
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0637—Accessories therefor
    • B22D11/0648—Casting surfaces
    • B22D11/066—Side dams

Definitions

  • the invention relates to the use of a hardenable copper alloy for the production of blocks for the side dams of double belt casting systems, in which the melt solidifies in the gap of two strips guided in parallel.
  • the side dams consist of metal blocks which are lined up on an endless belt, for example made of steel, and which move in the longitudinal direction synchronously with the casting belts.
  • the metallic dam blocks laterally delimit the mold cavity formed by the casting belts.
  • a hardenable copper alloy is described as a material for the blocks of side dams in US Pat. No. 3,955,615.
  • This alloy consisting of 1.5 to 2.5% nickel, 0.4 to 0.9% silicon, 0.1 to 0.5% chromium and 0.1 to 0.3% iron, the rest of copper, is usually used in double belt casting plants used for the continuous continuous casting of copper.
  • the side dam blocks made from this copper alloy tend to experience fatigue cracks in the area of the T-slot after a relatively short period of operation.
  • the alloy also has a relatively low electrical conductivity with about 35% IACS and thus also a too low thermal conductivity.
  • copper-based alloys containing beryllium are also unsuitable for the production of side dam blocks, since damage to health when machining or re-grinding the blocks cannot be ruled out with certainty.
  • the object of the present invention is to provide a material for the production of casting molds which is insensitive to cracking under a thermal shock treatment and which also has high heat resistance.
  • the solution to this problem according to the invention consists in the use of a hardenable copper alloy of 1.6 to 2.4% nickel, 0.5 to 0.8% silicon, 0.01 to 0.20% zirconium, the rest of copper including production-related impurities and more Processing additives as a material for the production of casting molds which are subject to permanent changing temperature stress, in particular blocks for the side dams of double belt casting plants.
  • a hardenable copper alloy of 1.6 to 2.4% nickel, 0.5 to 0.8% silicon, 0.01 to 0.20% zirconium, the rest of copper including production-related impurities and more Processing additives as a material for the production of casting molds which are subject to permanent changing temperature stress, in particular blocks for the side dams of double belt casting plants.
  • an addition of up to 0.4% chromium and - if necessary to reduce the grain growth during solution annealing - an iron addition of up to 0.2% is particularly advantageous.
  • the specific effect of the zirconium on the insensitivity of the copper material to crack formation is not adversely affected
  • Deoxidants such as boron, lithium, magnesium or phosphorus, up to a maximum of 0.03%, as well as usual manufacturing-related impurities also have no negative influence on the tendency of the alloy to be used according to the invention to crack.
  • zirconium in the merely hardened state and not cold-formed before hardening, practically eliminates the sensitivity to thermal shock of the known copper-nickel-silicon alloy. Additional studies also found that the heat resistance of the alloy to be used according to the invention at 500 ° C. significantly exceeds that of the materials previously used for the production of blocks of side dams.
  • alloys A, B, C Three alloys to be used according to the invention (alloys A, B, C) and three comparative alloys (alloys D, E, F) show how critical the composition of the respective example alloys is in order to achieve the desired combination of properties.
  • the composition of the example alloys is given in Table 1 in% by weight.
  • Table 1 Leg. Composition in% by weight Ni Si Cr Fe Zr Cu A 2.12 0.70 0.03 rest B 2.06 0.63 0.24 0.09 rest C. 1.94 0.58 0.29 0.12 0.15 rest D 1.82 0.63 rest E 1.95 0.69 0.28 rest F 1.87 0.72 0.38 0.12 rest
  • Alloys A and D were melted in a vacuum furnace, the remaining alloys were melted in air in a medium-frequency furnace, each cast into circular blocks with a diameter of 173 mm and extruded into rods of the format 55 ⁇ 55 mm. After solution annealing at 790 to 810 ° C, the rods were cured for four hours at 480 ° C. The tensile strength R m at room temperature, the Brinell hardness HB (2.5 / 62.5), the electrical conductivity and the Heat resistance (R m at 500 ° C) determined.
  • the thermal shock behavior was finally checked on blocks measuring 50 x 50 x 40 mm.
  • the blocks were first kept at 500 ° C. for two hours and then quenched in water at 25 ° C. It was generally possible to determine with the naked eye whether the blocks showed cracks or were free of cracks after the thermal shock test.
  • the T-slot of the blocks was checked with a microscope at 10x magnification. The extent of the cracks found, all of which emanated from the T-groove of the blocks, was mainly in the range from 1 to 7 mm, in individual cases the cracks even reached a length of over 20 mm.
  • the comparison shows that the alloys A, B and C to be used according to the invention have comparable strength properties at room temperature, both in terms of their electrical properties and, in particular, in terms of their heat resistance and thermal shock behavior, overall more favorable values than the comparative alloys D, E and F.
  • the copper alloy to be used according to the invention is therefore outstandingly suitable for all casting molds which are subject to a permanently changing temperature load during the casting process.
  • these are above all casting wheels and casting belts, as well as die casting molds and pressure pistons for die casting machines.

Abstract

For the manufacture of casting moulds, which are subjected to a permanently changing temperature stress during casting, for example blocks of side dams of double strip steel casting installations or casting wheels, thermally highly conductive materials are required, which are insensitive to thermal shock treatment and additionally exhibit high thermal stability. According to the invention, a copper-based alloy is proposed for this application which, in addition to 1.6 to 2.4% of nickel, 0.5 to 0.8% of silicon and, if appropriate, up to 0.4% of chromium and/or up to 0.2% of iron, also contains 0.01 to 0.20% of zirconium. As a result of the additional content of zirconium, the thermal shock sensitivity of hitherto used alloys is eliminated.

Description

Die Erfindung betrifft die Verwendung einer aushärtbaren Kupfer­legierung zur Herstellung von Blöcken für die Seitendämme von Doppelbandgießanlagen, bei denen die Schmelze im Spalt von zwei parallel geführten Bändern erstarrt. Die Seitendämme bestehen bei der beispielsweise aus der US-PS 3 865 176 bekannten Doppel­bandgießanlage aus Metallblöcken, die auf einem endlosen Band, zum Beispiel aus Stahl, aufgereiht sind und die sich synchron mit den Gießbändern in Längsrichtung bewegen. Die metallischen Seitendamm-Blöcke (dam blocks) grenzen dabei den durch die Gieß­bänder gebildeten Gießformhohlraum seitlich ein.The invention relates to the use of a hardenable copper alloy for the production of blocks for the side dams of double belt casting systems, in which the melt solidifies in the gap of two strips guided in parallel. In the double belt caster known for example from US Pat. No. 3,865,176, the side dams consist of metal blocks which are lined up on an endless belt, for example made of steel, and which move in the longitudinal direction synchronously with the casting belts. The metallic dam blocks laterally delimit the mold cavity formed by the casting belts.

Die Leistungsfähigkeit von Doppelbandgießanlagen hängt entschei­dend von der einwandfreien Funktion der aus Blöcken gebildeten Seitendammkette ab. So ist es erforderlich, daß die Blöcke eine mög­lichst hohe thermische Leitfähigkeit aufweisen, damit die Schmelz­beziehungsweise Erstarrungswärme möglichst rasch abgeführt wer­den kann. Um einen frühzeitigen Verschleiß der Seitenkanten der Blöcke durch mechanische Beanspruchung zu vermeiden, die zur Spaltbildung zwischen den Blöcken und dann zum Eindringen der Schmelze in diesen Spalt führt, muß der Werkstoff neben einer hohen Härte und Zugfestigkeit auch eine geringe Korngröße auf­weisen. Von ganz entscheidender Bedeutung ist schließlich ein optimales Ermüdungsverhalten, welches sicherstellt, daß nach dem Verlassen der Gießstrecke die beim Rückkühlen der Blöcke auftretenden thermischen Spannungen nicht zum Reißen der Blöcke in den Ecken der für die Aufnahme des Stahlbandes eingearbei­teten T-Nut führt. Treten nämlich derartige durch Thermoschock hervorgerufene Risse auf, fällt schon nach kurzer Zeit der be­ treffende Block aus der Kette heraus, wobei das schmelzflüssige Metall aus dem Gießformhohlraum unkontrolliert auslaufen und An­lagenteile beschädigen kann. Für das Auswechseln des schadhaften Blocks muß die Anlage angehalten und der Gießvorgang unterbrochen werden.The performance of double belt casting systems depends crucially on the perfect function of the side dam chain formed from blocks. So it is necessary that the blocks have the highest possible thermal conductivity so that the melt or solidification heat can be dissipated as quickly as possible. In order to avoid premature wear of the side edges of the blocks due to mechanical stress, which leads to the formation of a gap between the blocks and then to the penetration of the melt into this gap, the material must have not only high hardness and tensile strength but also a small grain size. Ultimately, optimal fatigue behavior is of crucial importance, which ensures that after leaving the casting line, the thermal stresses that occur when the blocks are cooled back do not lead to the blocks tearing in the corners of the T-slot incorporated to hold the steel strip. If such cracks caused by thermal shock occur, the be falls after a short time block from the chain, whereby the molten metal can leak out of the mold cavity in an uncontrolled manner and damage system parts. To replace the defective block, the system must be stopped and the casting process interrupted.

Zur Überprüfung der Rißneigung hat sich eine Testmethode bewährt, bei der die Blöcke einer zweistündigen Wärmebehandlung bei 500 °C unterzogen und anschließend in Wasser von 25 °C abgeschreckt wer­den. Auch bei mehrfacher Wiederholung dieser Thermoschockprüfung, dürfen bei einem geeigneten Material keine Risse im Bereich der T-Nut auftreten.To test the tendency to crack, a test method has proven itself in which the blocks are subjected to a two-hour heat treatment at 500 ° C. and then quenched in water at 25 ° C. Even if this thermal shock test is repeated several times, no cracks may occur in the area of the T-slot with a suitable material.

Als Werkstoff für die Blöcke von Seitendämmen ist in der US-Patent­schrift 3 955 615 eine aushärtbare Kupferlegierung beschrieben. Diese aus 1 ,5 bis 2,5 % Nickel, 0,4 bis 0,9 % Silizium, 0,1 bis 0,5 % Chrom und 0,1 bis 0,3 % Eisen, Rest Kupfer bestehende Le­gierung wird üblicherweise in Doppelbandgießanlagen zum konti­nuierlichen Stranggießen von Kupfer eingesetzt. Allerdings neigen die aus dieser Kupferlegierung hergestellten Seitendammblöcke schon nach relativ kurzer Betriebszeit der Gießanlage zu Ermü­dungsrissen im Bereich der T-Nut. Neben dem unbefriedigenden Ver­halten bei der Thermoschockprüfung weist die Legierung ferner mit etwa 35 % IACS eine relativ geringe elektrische Leitfähig­keit und damit auch eine zu geringe Wärmeleitfähigkeit auf.A hardenable copper alloy is described as a material for the blocks of side dams in US Pat. No. 3,955,615. This alloy, consisting of 1.5 to 2.5% nickel, 0.4 to 0.9% silicon, 0.1 to 0.5% chromium and 0.1 to 0.3% iron, the rest of copper, is usually used in double belt casting plants used for the continuous continuous casting of copper. However, the side dam blocks made from this copper alloy tend to experience fatigue cracks in the area of the T-slot after a relatively short period of operation. In addition to the unsatisfactory behavior in the thermal shock test, the alloy also has a relatively low electrical conductivity with about 35% IACS and thus also a too low thermal conductivity.

Ungeeignet für die Herstellung von Seitendammblöcken sind schließ­lich auch Kupferbasislegierungen, die Beryllium enthalten, da Ge­sundheitsschädigungen bei der Bearbeitung oder beim Nachschleifen der Blöcke nicht mit Sicherheit auszuschließen sind.Finally, copper-based alloys containing beryllium are also unsuitable for the production of side dam blocks, since damage to health when machining or re-grinding the blocks cannot be ruled out with certainty.

Aufgabe der vorliegenden Erfindung ist es, einen Werkstoff für die Herstellung von Gießformen zur Verfügung zu stellen, der gegenüber einer Thermoschockbehandlung rißunempfindlich und der zudem eine hohe Warmfestigkeit aufweist.The object of the present invention is to provide a material for the production of casting molds which is insensitive to cracking under a thermal shock treatment and which also has high heat resistance.

Die erfindungsgemäße Lösung dieser Aufgabe besteht in der Ver­wendung einer aushärtbaren Kupferlegierung aus 1 ,6 bis 2,4 % Nickel, 0,5 bis 0,8 % Silizium, 0,01 bis 0,20 % Zirkonium, Rest Kupfer einschließlich herstellungsbedingter Verunreinigungen und üblicher Verarbeitungszusätze als Werkstoff zur Herstel­lung von beim Gießen einer permanent wechselnden Temperatur­beanspruchung unterliegenden Gießformen, insbesondere von Blök­ken für die Seitendämme von Doppelbandgießanlagen. Zur Erhö­hung der Leitfähigkeit ist ein Zusatz von bis zu 0,4 % Chrom sowie - gegebenenfalls zur Reduzierung des Kornwachstums beim Lösungsglühen - ein Eisenzusatz von bis zu 0,2 % besonders vor­teilhaft. Die spezifische Wirkung des Zirkoniums auf die Unem­pfindlichkeit des Kupferwerkstoffs gegenüber Rißbildung wird durch derartige Zusätze innerhalb der angegebenen Gehaltsbe­reiche nicht negativ beeinflußt.The solution to this problem according to the invention consists in the use of a hardenable copper alloy of 1.6 to 2.4% nickel, 0.5 to 0.8% silicon, 0.01 to 0.20% zirconium, the rest of copper including production-related impurities and more Processing additives as a material for the production of casting molds which are subject to permanent changing temperature stress, in particular blocks for the side dams of double belt casting plants. To increase the conductivity, an addition of up to 0.4% chromium and - if necessary to reduce the grain growth during solution annealing - an iron addition of up to 0.2% is particularly advantageous. The specific effect of the zirconium on the insensitivity of the copper material to crack formation is not adversely affected by such additives within the specified content ranges.

Desoxidationsmittel, wie zum Beispiel Bor, Lithium, Magnesium oder Phosphor, bis zu maximal 0,03 % sowie übliche herstel­lungsbedingte Verunreinigungen haben ebenfalls keinen negati­ven Einfluß auf die Rißneigung der erfindungsgemäß zu verwen­denden Legierung.Deoxidants, such as boron, lithium, magnesium or phosphorus, up to a maximum of 0.03%, as well as usual manufacturing-related impurities also have no negative influence on the tendency of the alloy to be used according to the invention to crack.

Aus der DE-OS 26 34 614 ist zwar schon eine aushärtbare Kupfer-­Nickel-Silizium-Zirkonium-Legierung bekannt, deren Zusammen­setzung aus 1 bis 5 % Nickel, 0,3 bis 1 ,5 % Silizium, 0,05 bis 0,35 % Zirkonium, Rest Kupfer besteht. Diese bekannte Le­gierung soll jedoch zur Herstellung von Gegenständen verwen­det werden, die im aushärtbaren Zustand bei Raumtemperatur eine erhöhte Zähigkeit aufweisen müssen. Aus der Beschreibung geht hervor, daß die Wirkung des Zirkoniums insbesondere dann günstig ist, wenn der Werkstoff zwischen dem Lösungsglühen und dem Aushärten einer Kaltverformung von 10 bis 40 % unterzogen wird.From DE-OS 26 34 614 a hardenable copper-nickel-silicon-zirconium alloy is already known, the composition of which consists of 1 to 5% nickel, 0.3 to 1.5% silicon, 0.05 to 0.35 % Zirconium, rest copper. However, this known alloy is to be used for the production of objects which, in the hardenable state, must have increased toughness at room temperature. The description shows that the effect of zirconium is particularly favorable if the material is subjected to a cold deformation of 10 to 40% between solution annealing and hardening.

Als um so überraschender ist es bei der vorliegenden Erfindung anzusehen, daß Zirkonium im lediglich ausgehärteten, und vor dem Aushärten nicht kaltverformten Zustand die Thermoschock­empfindlichkeit der bekannten Kupfer-Nickel-Silizium-Legierung praktisch beseitigt. Durch ergänzende Untersuchungen wurde außerdem festgestellt, daß die Warmfestigkeit der erfindungs­gemäß zu verwendenden Legierung bei 500 °C diejenige der bis­her für die Herstellung von Blöcken von Seitendämmen einge­setzten Werkstoffe deutlich übertrifft.It is all the more surprising in the case of the present invention that zirconium, in the merely hardened state and not cold-formed before hardening, practically eliminates the sensitivity to thermal shock of the known copper-nickel-silicon alloy. Additional studies also found that the heat resistance of the alloy to be used according to the invention at 500 ° C. significantly exceeds that of the materials previously used for the production of blocks of side dams.

Es hat sich ferner herausgestellt, daß weitere Verbesserungen der mechanischen Eigenschaften erreicht werden können, wenn ein Teil des Zirkoniumgehalts durch bis zu 0,15 % mindestens eines Elements aus der Gruppe Cer, Hafnium, Niob, Titan und Vanadium ersetzt ist.It has also been found that further improvements in the mechanical properties can be achieved if part of the zirconium content is replaced by up to 0.15% of at least one element from the group consisting of cerium, hafnium, niobium, titanium and vanadium.

Anhand von einigen Ausführungsbeispielen wird die Erfindung im folgenden noch näher erläutert. An drei erfindungsgemäß zu verwendenden Legierungen (Legierungen A, B, C) und drei Vergleichslegierungen (Legierungen D, E, F) wird gezeigt, wie kritisch die Zusammensetzung der jeweiligen Beispiellegierun­gen ist, um die gewünschte Eigenschaftskombination zu errei­chen. Die Zusammensetzung der Beispiellegierungen ist in Tabelle 1 jeweils in Gew.% angegeben. Tabelle 1 Leg. Zusammensetzung in Gew.% Ni Si Cr Fe Zr Cu A 2,12 0,70 0,03 Rest B 2,06 0,63 0,24 0,09 Rest C 1,94 0,58 0,29 0,12 0,15 Rest D 1,82 0,63 Rest E 1,95 0,69 0,28 Rest F 1,87 0,72 0,38 0,12 Rest The invention is explained in more detail below with the aid of a few exemplary embodiments. Three alloys to be used according to the invention (alloys A, B, C) and three comparative alloys (alloys D, E, F) show how critical the composition of the respective example alloys is in order to achieve the desired combination of properties. The composition of the example alloys is given in Table 1 in% by weight. Table 1 Leg. Composition in% by weight Ni Si Cr Fe Zr Cu A 2.12 0.70 0.03 rest B 2.06 0.63 0.24 0.09 rest C. 1.94 0.58 0.29 0.12 0.15 rest D 1.82 0.63 rest E 1.95 0.69 0.28 rest F 1.87 0.72 0.38 0.12 rest

Die Legierungen A und D wurden im Vakuumofen, die übrigen Le­gierungen wurden an Luft in einem Mittelfrequenzofen erschmol­zen, jeweils zu Rundblöcken mit einem Durchmesser von 173 mm abgegossen und zu Stangen des Formats 55 x 55 mm stranggepreßt. Nach einem Lösungsglühen bei 790 bis 810 °C wurden die Stangen vier Stunden lang bei 480 °C ausgehärtet An den Beispielle­gierungen wurden jeweils die Zugfestigkeit Rm bei Raumtem­peratur, die Brinellhärte HB (2,5/62,5), die elektrische Leit­fähigkeit sowie die Warmfestigkeit (Rm bei 500 °C) ermittelt.Alloys A and D were melted in a vacuum furnace, the remaining alloys were melted in air in a medium-frequency furnace, each cast into circular blocks with a diameter of 173 mm and extruded into rods of the format 55 × 55 mm. After solution annealing at 790 to 810 ° C, the rods were cured for four hours at 480 ° C. The tensile strength R m at room temperature, the Brinell hardness HB (2.5 / 62.5), the electrical conductivity and the Heat resistance (R m at 500 ° C) determined.

An Blöcken der Abmessung 50 x 50 x 40 mm wurde schließlich das Thermoschockverhalten überprüft. Hierzu wurden die Blöcke zunächst zwei Stunden bei 500 °C gehalten und dann in Wasser von 25 °C abgeschreckt. Ob die Blöcke nach dem Thermoschock­test Risse aufwiesen oder rißfrei waren, konnte in der Regel mit bloßem Auge festgestellt werden. Ergänzend wurde die T-Nut der Blöcke mit einem Mikroskop bei 10-facher Vergröße­rung überprüft. Die Ausdehnung der festgestellten Risse, die sämtlich von der T-Nut der Blöcke ausgingen, lag hauptsäch­lich im Bereich von 1 bis 7 mm, in Einzelfällen erreichten die Risse sogar eine Länge von über 20 mm.The thermal shock behavior was finally checked on blocks measuring 50 x 50 x 40 mm. For this purpose, the blocks were first kept at 500 ° C. for two hours and then quenched in water at 25 ° C. It was generally possible to determine with the naked eye whether the blocks showed cracks or were free of cracks after the thermal shock test. In addition, the T-slot of the blocks was checked with a microscope at 10x magnification. The extent of the cracks found, all of which emanated from the T-groove of the blocks, was mainly in the range from 1 to 7 mm, in individual cases the cracks even reached a length of over 20 mm.

Sämtliche Untersuchungsergebnisse sind in Tabelle 2 zusammen­gefaßt. Tabelle 2 Leg. Rm N/mm² HB Leitf. %IACS Rm(500 °C) N/mm² Verhalten nach Thermoschocktest A 660 186 41,4 286 rißfrei B 656 191 42,2 372 rißfrei C 635 185 43,4 335 rißfrei D 635 179 34,5 219 rissig E 653 181 39,7 247 rissig F 642 184 37,2 233 rissig All test results are summarized in Table 2. Table 2 Leg. R m N / mm² HB % IACS R m (500 ° C) N / mm² Behavior after thermal shock test A 660 186 41.4 286 crack-free B 656 191 42.2 372 crack-free C. 635 185 43.4 335 crack-free D 635 179 34.5 219 cracked E 653 181 39.7 247 cracked F 642 184 37.2 233 cracked

Der Gegenüberstellung ist zu entnehmen, daß die erfindungsgemäß zu verwendenden Legierungen A, B und C bei vergleichbaren Festig­keitseigenschaften bei Raumtemperatur sowohl in ihren elektrischen Eigenschaften als auch insbesondere im Warmfestigkeits- und im Thermoschockverhalten insgesamt günstigere Werte aufweisen als die Vergleichslegierungen D, E und F.The comparison shows that the alloys A, B and C to be used according to the invention have comparable strength properties at room temperature, both in terms of their electrical properties and, in particular, in terms of their heat resistance and thermal shock behavior, overall more favorable values than the comparative alloys D, E and F.

Die erfindungsgemäß zu verwendende Kupferlegierung eignet sich daher hervorragend für sämtliche Gießformen, die beim Gießvor­gang einer permanent wechselnden Temperaturbeanspruchung unter­liegen. Dies sind neben den Blöcken für die Seitendämme von Doppelbandgießanlagen vor allem Gießräder und Gießbänder, ferner Druckgießformen und Druckkolben für Druckgießmaschinen.The copper alloy to be used according to the invention is therefore outstandingly suitable for all casting molds which are subject to a permanently changing temperature load during the casting process. In addition to the blocks for the side dams of double belt casting systems, these are above all casting wheels and casting belts, as well as die casting molds and pressure pistons for die casting machines.

Claims (6)

1. Verwendung einer aushärtbaren Kupferlegierung aus 1,6 bis 2,4 % Nickel, 0,5 bis 0,8 % Silizium, 0,01 bis 0,20 % Zir­konium, Rest Kupfer einschließlich herstellungsbedingter Verunreinigungen und üblicher Verarbeitungszusätze als Werk­stoff zur Herstellung von Gießformen, die beim Gießen einer permanent wechselnden Temperaturbeanspruchung unterliegen, insbesondere von Blöcken für die Seitendämme von Doppelband­gießanlagen.1. Use of a hardenable copper alloy of 1.6 to 2.4% nickel, 0.5 to 0.8% silicon, 0.01 to 0.20% zirconium, the rest of copper including production-related impurities and usual processing additives as a material for the production of Casting molds that are subject to constantly changing temperature stresses during casting, in particular blocks for the side dams of double belt casting systems. 2. Verwendung einer Kupferlegierung gemäß Anspruch 1, die außer­dem noch bis zu 0,4 % Chrom und/oder bis zu 0,2 % Eisen ent­hält, für den in Anspruch 1 genannten Zweck.2. Use of a copper alloy according to claim 1, which also contains up to 0.4% chromium and / or up to 0.2% iron, for the purpose mentioned in claim 1. 3. Verwendung einer Kupferlegierung gemäß einem der Ansprüche 1 oder 2, gekennzeichnet durch einen Zirkoni­umgehalt von 0,03 bis 0,15 % für den in Anspruch 1 genannten Zweck.3. Use of a copper alloy according to one of claims 1 or 2, characterized by a zirconium content of 0.03 to 0.15% for the purpose mentioned in claim 1. 4. Verwendung einer Kupferlegierung gemäß einem der Ansprüche 2 oder 3, die 1,9 bis 2,25 % Nickel, 0,55 bis 0,65 % Sili­zium, 0,20 bis 0,30 % Chrom, 0,08 bis 0,15 % Zirkonium, Rest Kupfer einschließlich herstellungsbedingter Verunreinigungen und üblicher Verarbeitungszusätze enthält, für den in An­spruch 1 genannten Zweck.4. Use of a copper alloy according to one of claims 2 or 3, the 1.9 to 2.25% nickel, 0.55 to 0.65% silicon, 0.20 to 0.30% chromium, 0.08 to 0, Contains 15% zirconium, balance copper including manufacturing-related impurities and usual processing additives, for the purpose mentioned in claim 1. 5. Verwendung einer Kupferlegierung gemäß einem der Ansprüche 1 bis 4, bei der ein Teil des Zirkoniumgehalts durch bis zu 0,15 % mindestens eines Elements aus der Gruppe Cer, Hafnium, Niob, Titan und Vanadium ersetzt ist, für den in Anspruch 1 genannten Zweck.5. Use of a copper alloy according to one of claims 1 to 4, in which a part of the zirconium content is replaced by up to 0.15% of at least one element from the group cerium, hafnium, niobium, titanium and vanadium, for that mentioned in claim 1 Purpose. 6. Verwendung einer Kupferlegierung gemäß einem der Ansprüche 1 bis 5, die zunächst bei 700 bis 900 °C geglüht dann abge­schreckt und anschließend einer 0,5 bis 10-stündigen Aus­härtungsbehandlung bei 350 bis 520 °C unterworfen wird, für den in Anspruch 1 genannten Zweck.6. Use of a copper alloy according to any one of claims 1 to 5, which is first annealed at 700 to 900 ° C then quenched and then subjected to a 0.5 to 10-hour hardening treatment at 350 to 520 ° C for the one mentioned in claim 1 Purpose.
EP89109136A 1988-06-14 1989-05-20 Use of an age-hardenable copper-based alloy Expired - Lifetime EP0346645B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT89109136T ATE65437T1 (en) 1988-06-14 1989-05-20 USE OF A HARVESTABLE COPPER ALLOY.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE3820203A DE3820203A1 (en) 1988-06-14 1988-06-14 USE OF A CURABLE copper alloy
DE3820203 1988-06-14

Publications (2)

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EP0346645A1 true EP0346645A1 (en) 1989-12-20
EP0346645B1 EP0346645B1 (en) 1991-07-24

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US (1) US5069270A (en)
EP (1) EP0346645B1 (en)
JP (1) JP2904804B2 (en)
CN (1) CN1018937B (en)
AT (1) ATE65437T1 (en)
AU (1) AU615753B2 (en)
BR (1) BR8902818A (en)
CA (1) CA1333666C (en)
DE (2) DE3820203A1 (en)
ES (1) ES2025354B3 (en)
FI (1) FI88885C (en)
GR (1) GR3002363T3 (en)
MX (1) MX170249B (en)
PL (1) PL164673B1 (en)
RU (1) RU1831510C (en)
SA (1) SA89100003B1 (en)
TW (1) TW198068B (en)
ZA (1) ZA894493B (en)

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RU2492961C2 (en) * 2008-03-19 2013-09-20 Кме Джермани Аг Унд Ко. Кг Method of producing mould parts and mould parts thus made

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JPH07103431B2 (en) * 1988-11-09 1995-11-08 株式会社日立製作所 CELL MOLD MOLD FOR MOLDING AND METHOD FOR MANUFACTURING THE SAME
US20040101540A1 (en) * 1999-09-01 2004-05-27 John Cooker Oral delivery system and method for making same
CN1688732B (en) * 2002-09-13 2010-05-26 Gbc金属有限责任公司 Age-hardening copper-base alloy and processing process
JP4255330B2 (en) * 2003-07-31 2009-04-15 日鉱金属株式会社 Cu-Ni-Si alloy member with excellent fatigue characteristics
JP4930993B2 (en) * 2007-01-05 2012-05-16 住友軽金属工業株式会社 Copper alloy material, method for producing the same, and electrode member for welding equipment
CN102418003B (en) * 2011-11-24 2013-05-08 中铝洛阳铜业有限公司 Processing method of nickel-chromium-silicon-bronze alloy
DE102018122574B4 (en) * 2018-09-14 2020-11-26 Kme Special Products Gmbh Use of a copper alloy
CN114645154B (en) * 2020-12-21 2023-06-27 广东省钢铁研究所 Preparation method of high-hardness copper alloy

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Also Published As

Publication number Publication date
JP2904804B2 (en) 1999-06-14
CN1041184A (en) 1990-04-11
JPH01319642A (en) 1989-12-25
FI88885C (en) 1993-07-26
AU615753B2 (en) 1991-10-10
ES2025354B3 (en) 1992-03-16
ZA894493B (en) 1990-03-28
FI892340A (en) 1989-12-15
PL279973A1 (en) 1990-01-08
ATE65437T1 (en) 1991-08-15
BR8902818A (en) 1990-02-01
SA89100003B1 (en) 2000-01-22
TW198068B (en) 1993-01-11
MX170249B (en) 1993-08-12
CN1018937B (en) 1992-11-04
EP0346645B1 (en) 1991-07-24
FI892340A0 (en) 1989-05-16
DE3820203A1 (en) 1989-12-21
RU1831510C (en) 1993-07-30
CA1333666C (en) 1994-12-27
AU3630689A (en) 1989-12-21
FI88885B (en) 1993-04-15
US5069270A (en) 1991-12-03
DE58900190D1 (en) 1991-08-29
GR3002363T3 (en) 1992-12-30
PL164673B1 (en) 1994-09-30

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