EP1608789B1 - Copper-based alloy - Google Patents

Copper-based alloy Download PDF

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Publication number
EP1608789B1
EP1608789B1 EP04706595A EP04706595A EP1608789B1 EP 1608789 B1 EP1608789 B1 EP 1608789B1 EP 04706595 A EP04706595 A EP 04706595A EP 04706595 A EP04706595 A EP 04706595A EP 1608789 B1 EP1608789 B1 EP 1608789B1
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weight
parts
alloy
phased
alpha
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German (de)
French (fr)
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EP1608789A2 (en
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Hung-Quoc Tran
Stéphane GILLIERON
Emmanuel Vincent
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Swissmetal - UMS Usines Metallurgiques Suisses SA
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Swissmetal - UMS Usines Metallurgiques Suisses SA
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    • 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

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  • the present invention relates to a copper-based alloy and its applications and more specifically to a nickel silver for use in the manufacture of ballpoint pen components.
  • the incompatibility between the alloy and the ink can then reduce the functional efficiency and the writing comfort of the instrument.
  • the resistance to gel inks can be improved by increasing the copper content of the alloy, as for example in the breasts ⁇ and in nickel silver ⁇ .
  • This solution has the disadvantage of reducing the susceptibility to hot deformation of the alloy.
  • the poor hot deformability of the alloys of the prior art involves higher production costs.
  • An object of the present invention is to provide an alloy and ball pen components free from the limitations of the prior art.
  • FIG. 1 represents a metallographic section of an alloy according to the invention in a single phase ⁇ structure.
  • Figure 1a shows a micrograph corresponding to Figure 1.
  • FIG. 2 represents a metallographic section of a nickel silver of the prior art in a two-phase ⁇ / ⁇ structure.
  • Figure 2a shows a micrograph corresponding to Figure 2.
  • Figure 3 shows a metallographic section of a two-phase nickel silver of the prior art corroded following exposure to an ink.
  • Figure 3a shows a micrograph corresponding to Figure 3.
  • FIG. 4 represents a diagram of the phase ⁇ phase of an alloy according to the invention according to the temperature of the heat treatment.
  • the alloy according to the invention is a white, gray or silver nickel silver, the composition of which is: Table 1 % weight min max Cu 43.00 48.00 Zn 33.00 38.00 Or 10.00 15.00 mn 3.50 6.50 Pb 0.00 4.00
  • This alloy has the characteristic of having two types of microstructures controllable by heat treatment.
  • the first, the single-phase structure ⁇ consists essentially of a single crystalline phase of uniform structure.
  • FIG. 1 represents a photomicrograph of a metallographic section of the alloy according to the invention having the ⁇ structure. It can be noted that the alloy consists essentially of a uniform solid solution of its components 10, apart from the black lead particles 82.
  • the alloy according to the invention may also have the two-phase ⁇ / ⁇ structure.
  • This structure represented in FIG. 2, comprises grains of a second phase 20, the ⁇ phase, whose copper content is lower than that of the ⁇ phase and which are distinguishable in FIG. 2 by their darker color.
  • the various structures of the alloy according to the invention are suitable for specific forming and machining processes.
  • the two-phase ⁇ / ⁇ structure is favorable for hot deformation, whereas the ⁇ -phase structure is favorable for cold deformation.
  • lead in the alloy facilitates machining operations, for example bar turning.
  • the alloy according to the invention can therefore be present in the two single-phase ⁇ and two-phase ⁇ / ⁇ structures. It is however possible to control the structure by heat treatment between 570 ° C and 780 ° C for 1-3 hours, followed by rapid cooling to room temperature. As a result of this treatment, the structure of the alloy is essentially ⁇ .
  • the invention also includes alloys to which, to the elements of nature and in the proportions defined by Table 1 above, are added small amounts of other elements, metallic or not, such as Magnesium, Aluminum, Iron, Phosphorus, or any other element or chemical species.
  • the composition of the alloy is determined, except unavoidable impurities, by Table 2 above.
  • FIG. 4 represents the phase ⁇ level as a function of the heat treatment temperature.
  • the choice of the temperature of the heat treatment makes it possible to modify the proportion of the ⁇ phase, and consequently to obtain materials of different characteristics.
  • the heat treatment in the TT temperature page at temperatures between 630 ° C. and 720 ° C. gives rise to a single phase ⁇ structure.
  • the temperature range E is favorable for extrusion.
  • the diagram of FIG. 4 is specific to the alloy composition specified in Table 2. According to another aspect of the invention it would also be possible to adopt different proportions of Cu, Zn, Ni, Mn and Pb and of to obtain an alloy whose proportion of the ⁇ and ⁇ phases is modifiable by heat treatment. In particular, it will be possible to vary independently the proportion of each of the components of the alloy in the range of values indicated in Table 1, or beyond. The temperatures required to modify the structure of the alloy thus obtained will then be different.
  • the alloy according to the invention has an increased resistance to corrosion due to gel inks when it is in the single-phase structure ⁇ .
  • the ⁇ phase is indeed the only one that is dissolved by gel inks.
  • FIG. 3 represents a metallographic section of an ⁇ / ⁇ nickel silver corroded by chemical reaction with the ink. It can be observed that only the ⁇ phase is attacked and that its dissolution leaves cavities 25.
  • the present invention is not limited to this specific use, but also includes any other use of the alloy according to the invention.
  • the alloy having the above composition is first cast in billets or ingots or in another form adapted to heat distortion.
  • the alloy according to the invention offers excellent deformability at high temperature. All the usual methods of hot deformation are possible. Typically, the billets are hot-extruded at a temperature of between 720 ° C. and 870 ° C., at which temperature its structure is biphasic ⁇ / ⁇ . The son thus obtained are then heat-treated between 630 ° C and 720 ° C, as explained above, to obtain the single-phase structure ⁇ .
  • the extruded material is then drawn to obtain bars or wires of suitable diameter to form ink guide tubes, ink reservoirs, or tips for instruments. writing.
  • the material thus obtained can be easily cold-worked by striking, machining, crimping, turning or by any other method.

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  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Pens And Brushes (AREA)
  • Inks, Pencil-Leads, Or Crayons (AREA)
  • Conductive Materials (AREA)
  • Chemically Coating (AREA)

Abstract

A corrosion resistant alloy has the following composition, by wt: (a) 43 to 48% of copper; (b) 33 to 38% of zinc; (c) 10 to 15% of nickel; (d) 3.5 to 6.5% of manganese; (e) 0 to 4% of lead. Independent claims are also included for the following: (a) a writing instrument made of this alloy; and (b) a method for the fabrication of this alloy.

Description

La présente invention porte sur un alliage à base de cuivre et sur ses applications et plus précisément sur un maillechort destiné à être utilisé pour la manufacture de composants de stylo à bille.The present invention relates to a copper-based alloy and its applications and more specifically to a nickel silver for use in the manufacture of ballpoint pen components.

Il est connu d'utiliser des alliages à base de cuivre de différentes compositions pour former des guides d'encre tubulaires, des réservoirs d'encre et des pointes d'instruments d'écriture. Certains alliages connus présentent toutefois l'inconvénient d'être incompatibles avec les encres à faible viscosité utilisées dans les stylos à bille de nouvelle génération.It is known to use copper-based alloys of different compositions to form tubular ink guides, ink reservoirs, and writing instrument tips. Some known alloys, however, have the disadvantage of being incompatible with the low-viscosity inks used in the new-generation ballpoint pens.

L'incompatibilité entre l'alliage et l'encre peut alors réduire l'efficacité fonctionnelle et le confort d'écriture de l'instrument. Les fuites d'encre qui peuvent en suivre provoquent une dégradation de la qualité de l'écriture et, dans les cas plus graves, des taches et des salissures.The incompatibility between the alloy and the ink can then reduce the functional efficiency and the writing comfort of the instrument. The ink leaks that may follow lead to a degradation of the quality of writing and, in more serious cases, to stains and soiling.

La résistance aux encres en gel peut être améliorée en augmentant la teneur en cuivre de l'alliage, comme par exemple dans les laitons α et dans les maillechorts α. Cette solution présente toutefois l'inconvénient de réduire la susceptibilité à la déformation à chaud de l'alliage. La mauvaise déformabilité à chaud des alliages de l'art antérieur implique des coûts de production plus importants.The resistance to gel inks can be improved by increasing the copper content of the alloy, as for example in the breasts α and in nickel silver α. This solution, however, has the disadvantage of reducing the susceptibility to hot deformation of the alloy. The poor hot deformability of the alloys of the prior art involves higher production costs.

D.M. WARD, Monograph and Report series, 10M, LONDON, 1970, Pages 155 à 159 , décrit un alliage de structure monophasée soumis à une étape de déformation à chaud. DM WARD, Monograph and Report Series, 10M, LONDON, 1970, Pages 155-159 , discloses a single-phase structural alloy subjected to a heat-deformation step.

Une autre limitation du laiton est que leur coloration jaune n'est pas appréciée par tous les consommateurs.Another limitation of brass is that their yellow color is not appreciated by all consumers.

Un but de la présente invention est de proposer un alliage et des composants de stylo à bille exempts des limitations de l'art antérieur.An object of the present invention is to provide an alloy and ball pen components free from the limitations of the prior art.

Selon l'invention décrite dans les revendications, ces buts sont atteints par les alliages, les dispositifs et les méthodes faisant l'objet des revendication dans les catégories correspondantes, et par exemple par un alliage comprenant :

  • entre 44.1 et 45.6 parties en poids de Cu;
  • entre 35.6 et 37.1 parties en poids de Zn ;
  • entre 11.8 et 12.7 parties en poids de Ni ;
  • entre 4.6 et 5.4 parties en poids de Mn.
According to the invention described in the claims, these objects are achieved by the alloys, devices and methods claimed in the corresponding classes, and for example by an alloy comprising:
  • between 44.1 and 45.6 parts by weight of Cu;
  • between 35.6 and 37.1 parts by weight of Zn;
  • between 11.8 and 12.7 parts by weight of Ni;
  • between 4.6 and 5.4 parts by weight of Mn.

La présente invention sera mieux comprise à la lecture des revendications ci-jointes et de la description donnée à titre d'exemple et illustrée par les figures annexées.The present invention will be better understood on reading the appended claims and the description given by way of example and illustrated by the appended figures.

La figure 1 représente une coupe métallographique d'un alliage selon l'invention dans une structure monophasée α.FIG. 1 represents a metallographic section of an alloy according to the invention in a single phase α structure.

La figure 1a représente une micrographie correspondant à la figure 1.Figure 1a shows a micrograph corresponding to Figure 1.

La figure 2 représente une coupe métallographique d'un maillechort de l'art antérieur dans une structure biphasée α/β.FIG. 2 represents a metallographic section of a nickel silver of the prior art in a two-phase α / β structure.

La figure 2a représente une micrographie correspondant à la figure 2.Figure 2a shows a micrograph corresponding to Figure 2.

La figure 3 représente une coupe métallographique d'un maillechort biphasé de l'art antérieur corrodé suite à l'exposition à une encre.Figure 3 shows a metallographic section of a two-phase nickel silver of the prior art corroded following exposure to an ink.

La figure 3a représente une micrographie correspondant à la figure 3.Figure 3a shows a micrograph corresponding to Figure 3.

La figure 4 représente un diagramme du taux de phase β d'un alliage selon l'invention selon la température du traitement thermique.FIG. 4 represents a diagram of the phase β phase of an alloy according to the invention according to the temperature of the heat treatment.

Selon un aspect de l'invention, l'alliage selon l'invention est un maillechort de couleur blanc, gris ou argentée, dont la composition est : Tableau 1 % poids min max Cu 43.00 48.00 Zn 33.00 38.00 Ni 10.00 15.00 Mn 3.50 6.50 Pb 0.00 4.00 According to one aspect of the invention, the alloy according to the invention is a white, gray or silver nickel silver, the composition of which is: Table 1 % weight min max Cu 43.00 48.00 Zn 33.00 38.00 Or 10.00 15.00 mn 3.50 6.50 Pb 0.00 4.00

Cet alliage a la caractéristique d'avoir deux types de microstructures contrôlables par traitement thermique. La première, la structure monophasée α, est composé essentiellement d'une seule phase cristalline de structure uniforme. La figure 1 représente une microphotographie d'une coupe métallographique de l'alliage selon l'invention présentant la structure α. On peur constater que l'alliage se compose essentiellement d'une solution solide uniforme de ses composantes 10, mis à part les particules noires de plomb 82.This alloy has the characteristic of having two types of microstructures controllable by heat treatment. The first, the single-phase structure α, consists essentially of a single crystalline phase of uniform structure. FIG. 1 represents a photomicrograph of a metallographic section of the alloy according to the invention having the α structure. It can be noted that the alloy consists essentially of a uniform solid solution of its components 10, apart from the black lead particles 82.

L'alliage selon l'invention peut aussi présenter la structure biphasée α/β. Cette structure, représentée sur la figure 2, comporte des grains d'une deuxième phase 20, la phase β, dont la teneur en cuivre est inférieure à celle de la phase α et qui sont distinguables sur la figure 2 par leur couleur plus foncée.The alloy according to the invention may also have the two-phase α / β structure. This structure, represented in FIG. 2, comprises grains of a second phase 20, the β phase, whose copper content is lower than that of the α phase and which are distinguishable in FIG. 2 by their darker color.

Les différentes structures de l'alliage selon l'invention sont adaptées à des procédés de formage et d'usinage spécifiques. En particulier la structure biphasée α/β est favorable à la déformation à chaud, alors que la structure monophasée α est favorable à la déformation à froid.The various structures of the alloy according to the invention are suitable for specific forming and machining processes. In particular, the two-phase α / β structure is favorable for hot deformation, whereas the α-phase structure is favorable for cold deformation.

L'adjonction de plomb dans l'alliage facilite les opérations d'usinage, par exemple de décolletage. Il serait toutefois aussi possible d'éliminer le plomb, ou de réduire sa teneur, lorsque cette caractéristique n'est pas requise.The addition of lead in the alloy facilitates machining operations, for example bar turning. However, it would also be possible to remove the lead, or reduce its content, when this characteristic is not required.

L'alliage selon l'invention peut donc se présenter dans les deux structures monophasée α et biphasée α/β. Il est toutefois possible de contrôler la structure par un traitement thermique entre 570 °C et 780 °C pendant 1-3 heures, suivi d'un refroidissement rapide jusqu'à température ambiante. A la suite de ce traitement la structure de l'alliage est essentiellement α.The alloy according to the invention can therefore be present in the two single-phase α and two-phase α / β structures. It is however possible to control the structure by heat treatment between 570 ° C and 780 ° C for 1-3 hours, followed by rapid cooling to room temperature. As a result of this treatment, the structure of the alloy is essentially α.

L'invention comprend aussi des alliages auxquels, aux éléments de la nature et dans les proportions définies par le tableau 1 ci-dessus, s'ajoutent des faibles quantités d'autres éléments, métalliques ou non, tels que Magnésium, Aluminium, Fer, Phosphore, ou tout autre élément ou espèce chimique.The invention also includes alloys to which, to the elements of nature and in the proportions defined by Table 1 above, are added small amounts of other elements, metallic or not, such as Magnesium, Aluminum, Iron, Phosphorus, or any other element or chemical species.

Dans un deuxième exemple d'alliage selon l'invention, la composition de l'alliage est déterminée, sauf les impuretés inévitables, par le tableau 2 ci-dessus. Tableau 2 % poids min max Cu 44.10 45.60 Zn 35.60 37.10 Ni 11.80 12.70 Mn 4.60 5.40 Pb 1.35 1.85 In a second example of an alloy according to the invention, the composition of the alloy is determined, except unavoidable impurities, by Table 2 above. Table 2 % weight min max Cu 44.10 45.60 Zn 35.60 37.10 Or 11.80 12.70 mn 4.60 5.40 Pb 1.35 1.85

La figure 4 représente le taux de phase β en fonction de la température de traitement thermique. Le choix de la température du traitement thermique permet de modifier la proportion de la phase β, et par conséquent, d'obtenir des matériaux de caractéristiques différentes. En particulier le traitement thermique dans la page de températures TT à des températures comprises entre 630 °C et 720 °C donne lieu à une structure monophasée α. La plage de températures E est favorable à l'extrusion.FIG. 4 represents the phase β level as a function of the heat treatment temperature. The choice of the temperature of the heat treatment makes it possible to modify the proportion of the β phase, and consequently to obtain materials of different characteristics. In particular, the heat treatment in the TT temperature page at temperatures between 630 ° C. and 720 ° C. gives rise to a single phase α structure. The temperature range E is favorable for extrusion.

Le diagramme de la figure 4 est spécifique à la composition d'alliage spécifiée dans le tableau 2. Selon un autre aspect de l'invention il serait aussi possible d'adopter des différentes proportions de Cu, Zn, Ni, Mn et Pb et d'obtenir un alliage dont la proportion des phases α et β est modifiable par traitement thermique. En particulier on pourra varier indépendamment la proportion de chacune des composantes de l'alliage dans la plage de valeurs indiquée dans le tableau 1, ou au delà. Les températures requises pour modifier la structure de l'alliage ainsi obtenu seront alors différentes.The diagram of FIG. 4 is specific to the alloy composition specified in Table 2. According to another aspect of the invention it would also be possible to adopt different proportions of Cu, Zn, Ni, Mn and Pb and of to obtain an alloy whose proportion of the α and β phases is modifiable by heat treatment. In particular, it will be possible to vary independently the proportion of each of the components of the alloy in the range of values indicated in Table 1, or beyond. The temperatures required to modify the structure of the alloy thus obtained will then be different.

L'alliage selon l'invention présente une résistance accrue à la corrosion due aux encres en gel lorsque il est dans la structure monophasée α. La phase β est en effet la seule qui est dissoute par les encres en gel. La figure 3 représente une coupe métallographique d'un maillechort α/β corrodé par réaction chimique avec l'encre. On peut observer que seule la phase β est attaquée et que sa dissolution laisse des cavités 25.The alloy according to the invention has an increased resistance to corrosion due to gel inks when it is in the single-phase structure α. The β phase is indeed the only one that is dissolved by gel inks. FIG. 3 represents a metallographic section of an α / β nickel silver corroded by chemical reaction with the ink. It can be observed that only the β phase is attacked and that its dissolution leaves cavities 25.

Bien que l'alliage de l'invention décrite ci-dessus se prête particulièrement à la réalisation des pointes d'instruments d'écriture, et notamment de stylo à bille, la présente invention ne se limite pas à cet usage spécifique, mais comprend aussi tout autre usage de l'alliage selon l'invention.Although the alloy of the invention described above is particularly suitable for producing writing instrument tips, and in particular ballpoint pens, the present invention is not limited to this specific use, but also includes any other use of the alloy according to the invention.

Selon un autre aspect de l'invention, l'alliage ayant la composition ci-dessus est d'abord coulé en billettes ou en lingots ou en une autre forme adaptée à la déformation à chaud.According to another aspect of the invention, the alloy having the above composition is first cast in billets or ingots or in another form adapted to heat distortion.

Contrairement aux maillechorts α, l'alliage selon l'invention offre une excellente déformabilité à haute température. Tous les procédés usuels de déformation à chaud sont possibles. Typiquement les billettes sont extrudées à chaud à une température comprise entre 720 °C et 870 °C, température à laquelle sa structure est biphasée α/β. Les fils ainsi obtenus sont ensuite traités thermiquement entre 630°C et 720 °C, comme expliqué ci-dessus, pour obtenir la structure monophasée α.Unlike nickel silver α, the alloy according to the invention offers excellent deformability at high temperature. All the usual methods of hot deformation are possible. Typically, the billets are hot-extruded at a temperature of between 720 ° C. and 870 ° C., at which temperature its structure is biphasic α / β. The son thus obtained are then heat-treated between 630 ° C and 720 ° C, as explained above, to obtain the single-phase structure α.

La structure monophasée α se prêtant à la déformation à froid, le matériau extrudé est alors tréfilé pour obtenir des barres ou des fils de diamètre convenable pour former des tubes de guides d'encre, des réservoirs d'encre, ou des pointes pour des instruments d'écriture.Since the single-phase structure α is suitable for cold forming, the extruded material is then drawn to obtain bars or wires of suitable diameter to form ink guide tubes, ink reservoirs, or tips for instruments. writing.

Le matériau ainsi obtenu peut être aisément mis en oeuvre à froid par frappe, usinage, sertissage, tournage ou par tout autre procédé.The material thus obtained can be easily cold-worked by striking, machining, crimping, turning or by any other method.

Les caractéristiques mécaniques de l'alliage selon l'invention traité comme ci-dessus dépendent de son taux d'écrouissage, selon le tableau suivant : Tableau 3 Etat résistance mécanique [MPa] Allongement à la rupture [%] Après traitement thermique 450-600 25-50 Taux de réduction de 20% Après traitement thermique 600-800 10-30 Taux de réduction de 40% Après traitement thermique 800-1100 1-20 The mechanical characteristics of the alloy according to the invention treated as above depend on its degree of hardening, according to the following table: Table 3 State mechanical resistance [MPa] Elongation at break [%] After heat treatment 450-600 25-50 20% reduction rate after heat treatment 600-800 10-30 40% reduction rate after heat treatment 800-1100 1-20

La résistance mécanique et l'allongement à la rupture dans le tableau ci-dessus ont été déterminés selon la méthode standardisée EN10002-1The mechanical strength and elongation at break in the table above were determined according to the standardized method EN10002-1

Claims (10)

  1. Method using an alloy composed of:
    between 43 and 48 parts by weight of Cu;
    between 33 and 38 parts by weight of Zn;
    between 10 and 15 parts by weight of Ni;
    between 3.5 and 6.5 parts by weight of Mn;
    between 0 and 4 parts by weight of Pb;
    where the alloy can have a mono-phased alpha structure α and a bi-phased alpha-beta structure α/β,
    wherein the method comprises:
    one or several steps of heat-deformation of the alloy in the bi-phased alpha-beta structure α/β,
    one or several steps of hot treatment to obtain said mono-phased alpha structure α.
  2. Method according to claim 1, including:
    a step of casting the melted alloy;
    one or several steps of heat-deformation of the alloy in the bi-phased alpha-beta structure α/β;
    one or several steps of hot treatment to obtain said mono-phased alpha structure α
    one or several steps of cold-deformation of the alloy in the mono-phased alpha structure α.
  3. Method according to claim 1, wherein the temperature of said hot treatment is included between 570°C and 780°C.
  4. Method according to claim 1, wherein the temperature of said hot treatment is included between 630°C and 720°C.
  5. Method according to claim 4, wherein the temperature of said heat deformation is included between 720°C and 870°C.
  6. Use, in the making of writing tips or ink reservoirs of writing implements or ball-point pens, of an alloy composed of:
    between 43 and 48 parts by weight of Cu;
    between 33 and 38 parts by weight of Zn;
    between 10 and 15 parts by weight of Ni;
    between 3.5 and 6.5 parts by weight of Mn;
    between 0 and 4 parts by weight of Pb;
    characterized in that the alloy has a mono-phased alpha structure α that can be obtained by a hot treatment.
  7. Use according to claim 6, the alloy being composed of:
    between 44.1 and 45.6 parts by weight of Cu;
    between 35.6 and 37.1 parts by weight of Zn;
    between 11.8 and 12.7 parts by weight of Ni;
    between 4.6 and 5.4 parts by weight of Mn;
    between 1.35 and 1.85 parts by weight of Pb.
  8. Use according to claim 6, wherein the temperature of said hot treatment is comprised between 570°C and 780°C.
  9. Writing implement, including an alloy composed of:
    between 43 and 48 parts by weight of Cu;
    between 33 and 38 parts by weight of Zn;
    between 10 and 15 parts by weight of Ni;
    between 3.5 and 6.5 parts by weight of Mn;
    between 0 and 4 parts by weight of Pb;
    characterized in that the alloy has a mono-phased alpha structure α that can be obtained by a hot treatment.
  10. Writing implement according to the preceding claim, wherein the alloy is included in an ink reservoir and/or a writing tip.
EP04706595A 2003-03-21 2004-01-30 Copper-based alloy Expired - Lifetime EP1608789B1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
CH496032003 2003-03-21
CH00496/03A CH693948A5 (en) 2003-03-21 2003-03-21 Copper based alloy used for fabrication of ball-point pen components contains specified amounts of copper, zinc, nickel, manganese and lead
PCT/CH2004/000051 WO2004083471A2 (en) 2003-03-21 2004-01-30 Copper-based alloy

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EP1608789A2 EP1608789A2 (en) 2005-12-28
EP1608789B1 true EP1608789B1 (en) 2007-10-03

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US (1) US9080226B2 (en)
EP (1) EP1608789B1 (en)
JP (1) JP2006520850A (en)
KR (1) KR20050108405A (en)
CN (1) CN100439537C (en)
AT (1) ATE374843T1 (en)
BR (1) BRPI0408610A (en)
CH (1) CH693948A5 (en)
DE (1) DE602004009297T2 (en)
DK (1) DK1608789T3 (en)
ES (1) ES2293213T3 (en)
HK (1) HK1088932A1 (en)
MX (1) MXPA05009635A (en)
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WO2012104426A2 (en) 2011-02-04 2012-08-09 Swissmetal Industries Ltd Cu-ni-zn-mn alloy
DE102012004725A1 (en) 2012-03-07 2013-09-12 Wieland-Werke Ag Silicon-containing copper-nickel-zinc alloy
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US9023272B2 (en) * 2010-07-05 2015-05-05 Ykk Corporation Copper-zinc alloy product and process for producing copper-zinc alloy product
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DE102009021336B4 (en) 2009-05-14 2024-01-11 Wieland-Werke Ag Copper-nickel-zinc alloy and its use
DE102009021336B9 (en) 2009-05-14 2024-04-04 Wieland-Werke Ag Copper-nickel-zinc alloy and its use
WO2012104426A2 (en) 2011-02-04 2012-08-09 Swissmetal Industries Ltd Cu-ni-zn-mn alloy
DE102012004725A1 (en) 2012-03-07 2013-09-12 Wieland-Werke Ag Silicon-containing copper-nickel-zinc alloy
WO2013131604A2 (en) 2012-03-07 2013-09-12 Wieland-Werke Ag Copper-nickel-zinc alloy containing silicon
US9617629B2 (en) 2012-03-07 2017-04-11 Wieland-Werke Ag Copper-nickel-zinc alloy containing silicon
US9738961B2 (en) 2012-03-07 2017-08-22 Wieland-Werke Ag Copper-nickel-zinc alloy containing silicon
DE102012004725B4 (en) 2012-03-07 2018-07-19 Wieland-Werke Ag Silicon-containing copper-nickel-zinc alloy
DE102013008822A1 (en) 2013-05-24 2014-11-27 Wieland-Werke Ag Mine for pens and use
WO2014187544A1 (en) 2013-05-24 2014-11-27 Wieland-Werke Ag Refill for a ball-point pen and use thereof
US9637808B2 (en) 2013-05-24 2017-05-02 Wieland-Werke Ag Refill for a ball-point pen and use thereof

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MXPA05009635A (en) 2006-03-08
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CH693948A5 (en) 2004-05-14
JP2006520850A (en) 2006-09-14
MY149452A (en) 2013-08-30
BRPI0408610A (en) 2006-03-07
CN1761768A (en) 2006-04-19
DE602004009297D1 (en) 2007-11-15
US20060065336A1 (en) 2006-03-30
ATE374843T1 (en) 2007-10-15
CN100439537C (en) 2008-12-03
EP1608789A2 (en) 2005-12-28
TWI314164B (en) 2009-09-01
KR20050108405A (en) 2005-11-16
DE602004009297T2 (en) 2008-07-10
US9080226B2 (en) 2015-07-14
ES2293213T3 (en) 2008-03-16
WO2004083471A2 (en) 2004-09-30
TW200502411A (en) 2005-01-16

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