[go: up one dir, main page]

EP2960350B1 - Alliage de fonte au cuivre - Google Patents

Alliage de fonte au cuivre Download PDF

Info

Publication number
EP2960350B1
EP2960350B1 EP14002217.9A EP14002217A EP2960350B1 EP 2960350 B1 EP2960350 B1 EP 2960350B1 EP 14002217 A EP14002217 A EP 14002217A EP 2960350 B1 EP2960350 B1 EP 2960350B1
Authority
EP
European Patent Office
Prior art keywords
mass
alloy
phase
copper
massenprozent
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.)
Not-in-force
Application number
EP14002217.9A
Other languages
German (de)
English (en)
Other versions
EP2960350A1 (fr
Inventor
Andreas Hansen
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.)
Gebr Kemper GmbH and Co KG
Original Assignee
Gebr Kemper GmbH and Co KG
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 Gebr Kemper GmbH and Co KG filed Critical Gebr Kemper GmbH and Co KG
Priority to EP14002217.9A priority Critical patent/EP2960350B1/fr
Publication of EP2960350A1 publication Critical patent/EP2960350A1/fr
Application granted granted Critical
Publication of EP2960350B1 publication Critical patent/EP2960350B1/fr
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

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
    • C22C9/02—Alloys based on copper with tin as the next major constituent
    • 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 present invention relates to a copper casting alloy, in particular for use in components for drinking water systems.
  • Copper casting alloys in particular copper-tin-zinc casting alloys (multi-substance bronzes, in particular red brass) are today indispensable materials for water-bearing systems. Because these have bacteriostatic properties and also offer excellent corrosion resistance. Such copper casting alloys also show positive properties in shaping and can be cast well. Due to their high strength and toughness, the material is also highly valued in chipless, plastomechanical forming. However, this plastic deformability proves to be particularly disadvantageous in the case of machining by machining. In this case, copper casting alloys tend to form long chips, which inhibits the workflow during fully automated turning or drilling and leads to severe wear on the tool cutting edges.
  • the modified CuSn5Zn5Pb2-C alloy (marking according to DIN EN 1982, 2008: CC499K) is usually used, which is a CuSn5Zn5Pb5-C alloy adapted to the requirements of the requirements.
  • the CuSn5Zn5Pb2-C alloy contains 84 to 88 mass% Cu, 4.0 to 6.0 mass% Zn, 4.0 to 6.0 mass% Sn, up to 3.0 mass% Pb, up to 0.3 mass% Fe, up to 0.6 mass% Ni, up to 0.01 mass% Al, up to 0.04 mass% P, up to 0.04 mass% S, up to 0.01 mass% Si, up to 0.10 mass% Sb, up to 0.02 mass% Cd, up to 0.03 mass% As and up to 0.02 mass% Bi.
  • the lead additive serves as a chip breaker. Because lead is practically insoluble in solid copper and fills in the casting due to the low melting point of the previously formed, solidification-related porosity. Thus, at the end of solidification, lead is present in the form of evenly distributed drops in the microstructure. These drops act as chip breakers and thus support economical, fully automatic mechanical processing.
  • a copper casting alloy in which no lead is present and the chipbreaking property in the alloy is essentially achieved by Si.
  • This alloy has the following composition: 70 to 80% by weight of Cu, 1.8 to 3.5% by weight of Si, 0.02 to 0.25% by mass of P, 0.3 to 3.5% by weight of Sn and the balance Zn and unavoidable impurities.
  • the chipbreaker is a CuZnSi solid solution. While this alloy provides good machinability, the alloy is susceptible to wear during machining compared to the lead-containing copper alloys. In addition, relatively high Zn contents of often more than 10 percent by mass have a negative effect on the corrosion resistance of the alloy.
  • Another copper alloy is from the WO2011 / 121799 A1 known.
  • This alloy contains 19 to 22 mass% Zn, 1.0 to 2.0 mass% Si, 0.5 to 1.5 mass% Bi, and balance Cu and unavoidable impurities.
  • the chipbreaker is a CuZnSi mixed crystal and bi-particles.
  • bismuth wets the grain boundaries and thereby lowers the mechanical strength.
  • bismuth is expensive to buy.
  • the out of the WO2011 / 121799 A1 known alloy hard and leads to a wear-enhancing machinability.
  • Another copper casting alloy is from the WO 97/00977 A1 known.
  • the alloy contains 2 to 12 percent by weight of Zn and Bi and Se in the ratio of 1.8 to 5.
  • Bismuth selenide is used here as chip breaker. The problem here is that bismuth selenide are first produced in an additional process step and the brass alloy melt must be added. Bismuth is also relatively expensive and selenium has a sharp limit in the Drinking Water Ordinance.
  • a copper casting alloy having the features of claim 1 is given. Further advantageous developments are defined in claims 2 and 3.
  • a brass (Cu-Zn), bronze (Cu-Sn) or multi-metal bronze (Cu-Sn-Zn) alloy is added as a chip breaker instead of lead (Pb), strontium (Sr).
  • Strontium is regarded as harmless to health, is not subject to any limit and is therefore able to design drinking water installations in the future in accordance with the law.
  • the relatively non-noble strontium forms at least one Sr-containing phase (hereinafter the first Sr-containing phase) which is insoluble in a brass or bronze phase or multicomponent main phase (hereinafter copper alloy matrix phase).
  • the first Sr-containing phase is in the form of uniformly distributed aggregates in the structure before.
  • the copper casting alloy preferably contains a Sr-free copper alloy matrix phase and at least the first Sr-containing phase dispersed in the Sr-free copper alloy matrix phase.
  • the first Sr-containing phase preferably has a Cu-Sr and / or Cu-Sn-Sr mixed phase, in particular having one of the empirical formulas Cu 5 Sr, Cu 9 Sn 4 Sr, Cu 4 Sn 2 Sr.
  • the copper casting alloy contains a further Sr-containing phase (hereinafter second Sr-containing phase), which is dispersively distributed in the Sr-free copper alloy matrix phase and which has a deviating, in particular higher melting temperature than the first Sr-containing phase.
  • second Sr-containing phase further Sr-containing phase
  • the second Sr-containing phase is, as far as the alloy melt contains P, preferably a Cu-P-Sr mixed phase, in particular with the empirical formula Cu 9 P 4 Sr.
  • the invention proposes a method for producing a copper casting alloy according to claim 4.
  • a method for producing a copper casting alloy according to claim 4 By means of such a method, in particular the copper casting alloy according to the invention is produced.
  • the invention furthermore relates to a shaped body, in particular for a drinking water system or a fitting or a component made from this shaped body.
  • At least parts or regions of the fitting or of the component should contain the copper casting alloy according to the invention.
  • fittings in the drinking water and sanitary engineering mainly functional elements are referred to, in particular valves or faucets.
  • components within the meaning of the invention for example, a pipe connector, a piece of pipe or a functional assembly of a water pipe are considered.
  • the present invention particularly drinking water systems in view, but this does not exclude that the claimed copper casting alloys also due to their excellent properties in components for other water-bearing systems, not provided for drinking water supply are use can find.
  • the alloy according to the invention can also find application in other fields.
  • An alloy melt which forms a copper casting alloy after cooling is preferably produced by fusing a Sn-Sr alloy, a Cu-Zn alloy, and crude copper (Cu).
  • the so-called SnSr10 alloy is used as Sn-Sr alloy, which is available on the market prefabricated.
  • This usually contains between 89 and 91 percent by weight, in particular 90 percent by weight Sn, between 9 and 10 percent by mass, in particular 9.5 percent by mass Sr and between 0.2 and 0.3, in particular 0.28 percent by mass Al.
  • AI has an unfavorable effect on the properties of the casting alloy, it is present in the SnSr10 alloy for production reasons.
  • strontium is bound as a stable intermetallic phase and therefore has no endangerment due to reactivity and, unlike elemental strontium, is not subject to any hazardous substances ordinance.
  • a so-called CuZn32 master alloy is used as Cu-Zn alloy.
  • copper is usually melted together with zinc above 1100 ° C, in particular at about 1210 ° C. This forms a homogeneous alloy melt, which is subsequently cooled to solidification.
  • the alloy usually contains between 60 and 70 percent by mass copper, in particular about 68 percent by mass, and the remainder zinc, in particular 32 percent by mass (hence the name CuZn32 master alloy). Since elemental zinc has a high vapor pressure and a boiling point of 907 ° C, this would when in pure form at added higher temperatures of the alloy melt would leave the melt in the form of zinc vapor, unless special precautions were taken.
  • the CuZn32 master alloy may in particular contain the following elements: lead, tin, phosphorus, silicon or aluminum and / or the elements described below for the copper casting alloy Amounts.
  • the Sn-Sr alloy, the Cu-Zn alloy and crude copper (Cu) are preferably added together in solid form, in particular at 1200 ° C., preferably above or at 1100 ° C.
  • further additives may be added to the alloy melt as an alloying ingredient or for other purposes such as deoxidation, or may be melted together with the base materials.
  • phosphorus is advantageously added for deoxidation, for example in the form of "10% by mass of phosphorus copper” (so-called CuP10).
  • the alloy melt is advantageously covered with coke so far as it operates under atmospheric oxygen conditions, so that it forms a reducing CO atmosphere.
  • the alloy melt After the alloy melt has been produced, it is cooled in such a way that at least one 2-phase structure of the first Sr-containing mixed phase and a base phase, namely a copper alloy matrix phase, forms.
  • This cooling is usually done after casting at about 1200 ° C in a mold.
  • a casting mold can be any known casting mold, casting into a sand casting mold is particularly preferred here. With increasing pouring temperature and increasing contents of particularly oxygen-affinitive elements in the liquid metal, such as strontium in this case, the propensity to form reaction also increases.
  • the copper casting alloy is present as a homogeneous melt. From a temperature of 1050 to 1000 ° C., in particular at 1020 ° C., first ⁇ -mixed crystals of a main phase which forms (copper alloy matrix phase) typically precipitate.
  • This main phase is especially a brass or bronze, or multi-metal bronze phase, optionally with other alloying elements. Accordingly, the proportion of strontium increases in the residual alloy melt.
  • the entire copper alloy matrix phase is solidified. In this solidified copper alloy matrix phase, at least one first Sr-containing phase uniformly distributed in the microstructure is present. This first Sr-containing phase is immiscible with the copper alloy matrix phase, the latter being essentially Sr-free.
  • the first Sr-containing alloy phase forms an at least partially coherent network-like vein structure, wherein at high cooling rates, in particular of up to 5 ° C / s, a fine dispersive structure is formed, in which individual agglomerates of the first Sr-containing phase do not substantially touch.
  • a copper-containing and / or tin-containing Sr phase having a different composition is formed during the cooling process.
  • This first Sr-containing phase usually has a lower melting point than that of the copper alloy matrix phase and therefore falls only after the advanced solidification of the copper alloy matrix phase.
  • this Sr-containing phase is formed from the residual melt as the last solidifying phase and is thus able to fill previously formed by solidification of the copper alloy matrix phase resulting voids in the casting and thus has a vein-like shape in Gussleg istmaschinestige.
  • the first Sr-containing phase has the empirical formula Cu 4 Sn 2 Sr. lower Sr contents of less than 0.2 mass percent and the presence of phosphorus, the first Sr-containing phase has the empirical formula Cu 9 Sn 4 Sr.
  • the first Sr-containing phase has in particular the empirical formula Cu 5 Sr, Cu 9 Sn 4 Sr , Cu 4 Sn 2 Sr.
  • the first Sr-containing phase has the same empirical formula throughout the entire structure. However, it is also possible that a mixture of the aforementioned phases is present.
  • the first Sr-containing phase is always common that this is essentially formed only after the beginning of the solidification of the copper alloy matrix phase from the residual melt and thus has a vein-shaped structure in the structure.
  • the empirical formula of the alloy or the alloy phases this was determined by means of EDX or ICP.
  • the first Sr-containing phase is a Cu 5 Sr compound, it is preferably formed in a temperature range of 850 ° C to 854 ° C.
  • the first Sr-containing phase is the Cu 4 Sn 2 Sr mixed phase, it is preferably formed in a temperature range from 810 ° C. to 790 ° C., very particularly preferably in a temperature range from 810 ° to 797 ° C.
  • the first Sr-containing phase is the Cu 9 Sn 4 Sr mixed phase, it is formed in particular in a temperature range from 720 ° C. to 700 ° C., preferably at approximately 710 ° C.
  • phase During the cooling of the alloy melt, other phases may also form which are immiscible with the copper alloy matrix phase. These are then also distributed in the casting alloy. If, for example, further Sr-affine elements are present in the melt, preferably one or more further Sr-containing phases form (second Sr-containing mixed phase). If, for example, phosphorus is added to the melt as a deoxidizer, or is present in particular in amounts of more than 0.02% by mass in the melt, a phase with the following composition is formed, for example: Cu 9 P 4 Sr.
  • This second Sr-containing phase is often not soluble in the alloy melt even at low temperatures and thus forms a dispersion with the second Sr-containing phase (liquid and / or partially or completely precipitated), the is dispersed in the at least partially molten copper alloy matrix phase.
  • This second Sr-containing phase solidifies in particular above the temperature at which the first Sr-containing mixed phase solidifies, but below the temperature of the start of solidification of the copper alloy matrix phase.
  • the second Sr-containing phase is the Cu 9 P 4 Sr phase
  • the second phase has an oval or droplet-like structure, in contrast to the vein-shaped structure of the first Sr-containing phase.
  • At least most of the aggregates of the first Sr-containing phase and the second Sr-containing phase do not contact each other within the microstructure.
  • first Sr-containing alloy phase or second Sr-containing phase is used, this is to be understood as an individualization of the individual phases and not as an order in which individual phases crystallize out of the melt and are formed.
  • the copper casting alloy contains at least two phases (first Sr-containing phase and copper alloy matrix phase), particularly three phases (first Sr-containing alloy phase, second Sr-containing phase, and copper alloy matrix phase). But there may also be other phases.
  • the copper casting alloy contains at least 80 to 95% by mass, preferably 83 to 87% by mass, or alternatively preferably about 89 to 90% by mass Cu and at least one of the elements Sn or Zn.
  • the proportion of the aforementioned elements (Sn / Zn) together is 5 to 20% by mass, preferably 9 to 10% by mass. Particularly preferably, both elements are present in the alloy.
  • preferably 4 to 6% by mass of Sn, in particular 4 to 5% by mass of Sn and 4 to 6% by mass of Zn, in particular 5 to 6% by mass of Zn are provided.
  • the Zn content is higher than that of the Sn to choose, in particular about 1 percentage point higher.
  • the alloy contains strontium in an amount of greater than 0.01 mass percent to 1.0 mass percent.
  • the strontium content is preferably between 0.01 and 0.7 percent by mass, very particularly preferably between 0.1 and 0.5 percent by mass, in particular about 0.4 percent by mass or alternatively about 0.14 percent by mass.
  • the values in the rounding range of the unrecorded decimal places belong to the specified range.
  • Arsenic can adversely affect the mechanical properties of Cu-Sn cast alloys due to embrittlement.
  • Bi Up to 0.05 mass percent Bi, preferably up to 0.02 mass percent. Although Bi improves castability, higher contents than 0.05 mass percent lead to a marked decrease in mechanical properties.
  • O may be incorporated in the alloy during the manufacturing process in oxidic form as an unavoidable impurity.
  • Alloys were produced under the atmosphere of the protective gas agon and a maximum oxygen content of 8 x 10 -4 mol.
  • a copper alloy melt was produced in an induction furnace.
  • the SnSr10 master alloy had the following composition: 90.22% by mass of Sn, 9.50% by mass of Sr and 0.28% by mass of Al.
  • Strontium is bound in this as a stable intermetallic phase. So there is no risk due to reactivity and unlike elemental strontium, the alloy is not subject to any hazardous substances regulation.
  • This alloy melt was cooled in each case in three different ways. On the one hand, the alloy melt was cooled directly in the Al 2 O 3 crucible used for melting (hereinafter crucible), on the other hand in a mold (hereinafter mold) and thirdly in a cylindrical cavity formed by a sand mold (hereinafter Cylinder) poured off and cooled there.
  • crucible Al 2 O 3 crucible used for melting
  • mold a mold
  • Cylinder sand mold
  • FIG. 1a Microscopic micrographs of the mold and the cylinder of the alloys obtained after cooling are shown.
  • the bar (bottom right) in each figure indicates a length of 100 ⁇ m.
  • FIG. 1a In the pictures in FIG. 1a it can be seen that a two-phase structure is formed.
  • a main phase which is like the EDX spectrum in FIG. 1b is formed by a Sr-free Cu-Sn-Zn phase
  • the copper alloy matrix phase is distributed in this copper alloy matrix phase, such as the EDX spectrum in FIG. 1b shows Sr-containing phase (first Sr-containing phase).
  • the Sr-containing phase has a vein-shaped formation, with increasing cooling rate (cylinder, mold), the fineness of the phases increases.
  • FIG. 1b For example, an EDX spectrum is shown in the positions 1 (first Sr-containing phase) and 2 (copper alloy matrix phase) of the alloy shown in this figure from the cylinder.
  • the phase in position 2 has the following chemical composition: 89.84 mass% Cu, 3.30 mass% Sn, 6.86 mass% Zn, 0.00 mass% Sr.
  • the main phase contains only copper, tin and zinc (in addition to the aforementioned impurities) but is Sr-free.
  • the phase 1 phase which is distributed in the main phase, contains strontium.
  • the phase in position 1 is, as the EDX analysis shows, a Cu4Sn2Sr phase having the following composition: 43.88 to 44.2% by mass of Cu, 39.90 to 40.90% by mass of Sn, 15.13 up to 15.3 mass percent Sr.
  • this first Sr-containing phase takes place in the temperature range between 810 and 797 ° C (see Figure 1c , Graph dT / dt).
  • the Sr-rich residual melt forms the Cu 4 Sn 2 Sr phase, which then solidifies in the temperature range of 810 to 797 ° C, which also causes the vein-shaped habit. This phase is not soluble in the Cu-Zn-Sn copper matrix phase.
  • An alloy melt was melted together from HCP copper, Zn, SnSr10 and CuP10.
  • the alloy melt was covered with coke, so that a CO-atmosphere was formed.
  • the resulting copper alloy melt was poured into a sand mold and plates with different plate thickness, namely u.a. manufactured with a plate thickness of 6 mm and 9 mm.
  • the cast copper alloy had the following composition determined by ICP-OES analysis: 89.54 mass% Cu, 4.6 mass% Sn, 5.68 mass% Zn, 0.04 mass% P, 0.142 mass% Sr and less than 0.01 mass% Pb.
  • FIG. 2a A microscopic image of a microstructure cut after cooling and solidification of the alloy in the sand mold is for the plate with 9 millimeters in FIG. 2a shown.
  • main phase which like the EDX spectrum in FIG. 2b 2 (see position 3) is formed by a Sr-free Cu-Sn-Zn phase
  • the copper alloy matrix phase two further phases are distributed in this copper alloy matrix phase, one such as the EDX spectrum in FIG. 2b (Position 1) shows Sr-containing phase (first Sr-containing phase), as well as another, such as the EDX spectrum in FIG. 2b (Position 2) shows strontium-containing phase (second strontium-containing phase). Both Sr-containing phases are finely distributed in the copper alloy matrix phase.
  • the first Sr-containing phase in position 1 has the following chemical composition (without considering the proportion of O as an undesired impurity): 50.42 to 50.49 mass% Cu, 41.86 to 41.70 mass% Sn, 7 , 72 to 7.81 mass percent Sr.
  • the second Sr-containing phase in position 2 has the following chemical composition (excluding the proportion of O as undesirable impurity): 73.00 to 73.46 mass% Cu, 15.04 to 15.81 mass% P, 11 , 18 to 11.50 mass percent Sr.
  • the copper alloy matrix phase (position 3) (excluding the proportion of O as undesirable impurity), has the following chemical composition: 88.1 to 89.2 mass% Cu, 3.5 to 3.54 mass% Sn, 7.2 to 7.3 mass% Zn, 0.0 mass% Sr and 0.0 mass% P.
  • the Cu 9 P 4 Sr phase in position 2 has an oval or teardrop-like structure, the phase in position 1 having a vein-shaped structure similar to the Cu 4 Sn 2 Sr phase in test series 1 (cf. FIG. 2a combined with FIG. 2b ).
  • the Cu 9 P 4 Sr phase (second Sr-containing phase) solidifies in a temperature range of 762 ° C and 729 ° C.
  • the Cu 9 Sn 4 Sr phase (first Sr-containing phase) forms with a vein-shaped structure.
  • the reason for the different habit of the structures is explained in the general description.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Domestic Plumbing Installations (AREA)

Claims (9)

  1. Alliage de cuivre pour coulée, constitué par :
    80 à 95 pour cent en masse de Cu ;
    5 à 20 pour cent en masse de Sn et/ou Zn ;
    0,1 à 1,0 pour cent en masse de Sr ; éventuellement un ou plusieurs des éléments suivants en les proportions suivantes :
    jusqu'à 0,6 pour cent en masse de P, jusqu'à 2,0 pour cent en masse de Ni, jusqu'à 2,0 pour cent en masse de Fe, jusqu'à 0,03 pour cent en masse d'AI, jusqu'à 0,2 pour cent en masse de Mn, jusqu'à 0,1 pour cent en masse de S, jusqu'à 0,15 pour cent en masse de Sb, jusqu'à 0,01 pour cent en masse de Si, jusqu'à 0,02 pour cent en masse de Cd, jusqu'à 0,03 pour cent en masse d'As, jusqu'à 0,05 pour cent en masse de Bi, jusqu'à 0,25 pour cent en masse de Pb ; et éventuellement d'autres impuretés inévitables dues à la fabrication.
  2. Alliage de cuivre pour coulée selon la revendication 1, caractérisé par 4,0 à 6,0 pour cent en masse de Sn et 4,0 à 6,0 pour cent en masse de Zn.
  3. Alliage de cuivre pour coulée selon l'une quelconque des revendications précédentes, caractérisé en ce que l'alliage de cuivre pour coulée est exempt de Pb.
  4. Procédé de fabrication d'un alliage de cuivre pour coulée selon l'une quelconque des revendications 1 à 3, contenant les étapes suivantes :
    a) la fabrication d'une masse fondue d'alliage par fusion commune d'un alliage Sn-Sr, d'un alliage Cu-Zn et de Cu ; et
    b) le refroidissement de la masse fondue d'alliage fabriquée à l'étape de procédé a) avec formation d'une phase de matrice d'alliage de cuivre exempte de Sr et d'une première phase contenant Sr répartie dans celle-ci.
  5. Procédé selon la revendication 4, caractérisé en ce que la première phase contenant Sr est une phase mixte Cu4Sn2Sr, qui se forme dans une plage de température comprise entre 810 et 797 °C.
  6. Procédé selon l'une quelconque des revendications 4 ou 5, caractérisé en ce que le procédé est réalisé dans des conditions de gaz protecteur.
  7. Procédé selon l'une quelconque des revendications 4 à 6, caractérisé en ce que P est ajouté à l'étape de procédé a) et, en plus de la première phase contenant Sr, une deuxième phase contenant Sr répartie dans la phase de matrice d'alliage de cuivre exempte de Sr est formée, la deuxième phase d'alliage contenant Sr étant une phase mixte Cu-P-Sr.
  8. Corps moulé, notamment pour un système d'eau potable, contenant un alliage de cuivre pour coulée selon l'une quelconque des revendications 1 à 3.
  9. Armature ou composant en un corps moulé selon la revendication 8.
EP14002217.9A 2014-06-27 2014-06-27 Alliage de fonte au cuivre Not-in-force EP2960350B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP14002217.9A EP2960350B1 (fr) 2014-06-27 2014-06-27 Alliage de fonte au cuivre

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP14002217.9A EP2960350B1 (fr) 2014-06-27 2014-06-27 Alliage de fonte au cuivre

Publications (2)

Publication Number Publication Date
EP2960350A1 EP2960350A1 (fr) 2015-12-30
EP2960350B1 true EP2960350B1 (fr) 2017-11-29

Family

ID=51062615

Family Applications (1)

Application Number Title Priority Date Filing Date
EP14002217.9A Not-in-force EP2960350B1 (fr) 2014-06-27 2014-06-27 Alliage de fonte au cuivre

Country Status (1)

Country Link
EP (1) EP2960350B1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109628781A (zh) * 2019-01-23 2019-04-16 中南大学 高铁含量的Cu-Fe系合金材料及其制备方法

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102021110301A1 (de) * 2021-04-22 2022-10-27 Ks Gleitlager Gmbh Kupfer-Zinn-Stranggusslegierung
DE102023116139A1 (de) * 2023-06-20 2024-12-24 Sundwiger Messingwerk GmbH Bleifreie Messinglegierung

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5614038A (en) 1995-06-21 1997-03-25 Asarco Incorporated Method for making machinable lead-free copper alloys with additive
JP3734372B2 (ja) 1998-10-12 2006-01-11 三宝伸銅工業株式会社 無鉛快削性銅合金
CN102666888B (zh) * 2010-01-26 2014-06-18 三菱综合材料株式会社 高强度高导电性铜合金
JP2011214095A (ja) 2010-03-31 2011-10-27 Joetsu Bronz1 Corp 鋳造用無鉛快削黄銅合金

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109628781A (zh) * 2019-01-23 2019-04-16 中南大学 高铁含量的Cu-Fe系合金材料及其制备方法

Also Published As

Publication number Publication date
EP2960350A1 (fr) 2015-12-30

Similar Documents

Publication Publication Date Title
DE69417553T2 (de) Sanitaereinrichtungen
EP2964797B1 (fr) Alliage cuivre-zinc pour une robinetterie sanitaire, et procédé de fabrication de ladite robinetterie
DE69416512T2 (de) Gelbes reduziertes blei-wismut-messing
AT522440A4 (de) Mehrschichtgleitlagerelement
DE102005002763A1 (de) Kupferlegierung mit hoher Festigkeit und hoher Leitfähigkeit
EP2960350B1 (fr) Alliage de fonte au cuivre
DE69207289T2 (de) Legierung auf Kupfer-Nickel-Basis
WO2016045770A1 (fr) Élément de connexion électrique
EP3581667B1 (fr) Pièces moulées d'un alliage de cuivre résistant à la corrosion et pouvant être usiné
EP0711843A2 (fr) Utilisation d'un alliage de cuivre-zinc pour installations d'eau potable
DE3729509C2 (de) Verbesserte Kupferlegierung, insbesondere für die Herstellung elektronischer Bauteile
DE19800433C2 (de) Stranggießverfahren zum Vergießen einer Aluminium-Gleitlagerlegierung
WO2012062248A2 (fr) Alliage de cuivre
DE2241243C2 (de) Verfahren zur Erhöhung der Beständigkeit von Messing gegen Entzinken
EP1647352B1 (fr) Matériau de brasure
EP4271847B1 (fr) Alliage de coulée continue à base de cuivre et d'étain
EP4271846B1 (fr) Alliage de coulée continue à base de cuivre et d?étain
DE3627282A1 (de) Legierung zur kornfeinung von kupferwerkstoffen
EP4271848B1 (fr) Alliage de coulée continue à base de cuivre et d'étain
AT412725B (de) Mittel zur beeinflussung der erstarrungsstruktur von magnesium und magnesiumlegierungen
EP3024956B1 (fr) Alliage de fonderie en cuivre à grains affinés comprenant du fer et du bore
EP4481076A1 (fr) Alliage de reargent
EP4569148A1 (fr) Matériau de coulée fait d'un alliage de cuivre-zinc, procédé de fabrication d'un produit coulé et pièce coulée
WO2022223673A1 (fr) Alliage de coulée continue cuivre-étain
WO1989007660A1 (fr) Alliage d'affinage structural de materiaux cuivreux

Legal Events

Date Code Title Description
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

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

17P Request for examination filed

Effective date: 20160629

RBV Designated contracting states (corrected)

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

R17P Request for examination filed (corrected)

Effective date: 20160629

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20170508

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTC Intention to grant announced (deleted)
INTG Intention to grant announced

Effective date: 20170915

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

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: CH

Ref legal event code: EP

Ref country code: CH

Ref legal event code: NV

Representative=s name: BOVARD AG PATENT- UND MARKENANWAELTE, CH

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 950464

Country of ref document: AT

Kind code of ref document: T

Effective date: 20171215

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: 502014006366

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20171129

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: 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: 20171129

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: 20171129

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: 20171129

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: 20180228

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: 20171129

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

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: 20171129

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: 20171129

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: 20171129

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: 20180228

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: 20180301

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: 20171129

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

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: 20171129

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: 20171129

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: 20171129

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: 20171129

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: 20171129

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502014006366

Country of ref document: DE

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

Ref country code: IT

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: 20171129

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: 20171129

Ref country code: PL

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: 20171129

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: 20171129

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: 20171129

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: 20180830

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: 20171129

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502014006366

Country of ref document: DE

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20180627

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20180630

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: 20171129

Ref country code: LU

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

Effective date: 20180627

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

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

Ref country code: GB

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

Effective date: 20180627

Ref country code: IE

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

Effective date: 20180627

Ref country code: LI

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

Effective date: 20180630

Ref country code: FR

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

Effective date: 20180630

Ref country code: CH

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

Effective date: 20180630

Ref country code: DE

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

Effective date: 20190101

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

Ref country code: BE

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

Effective date: 20180630

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

Ref country code: TR

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: 20171129

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

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: 20171129

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 NON-PAYMENT OF DUE FEES

Effective date: 20171129

Ref country code: HU

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

Effective date: 20140627

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

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: 20171129

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: 20180329

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 950464

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190627

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: 20190627