EP3225707B1 - Composant pour des canalisations d'eau ou de gaz acheminant des milieux comprenant un alliage de cuivre - Google Patents

Composant pour des canalisations d'eau ou de gaz acheminant des milieux comprenant un alliage de cuivre Download PDF

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EP3225707B1
EP3225707B1 EP17151949.9A EP17151949A EP3225707B1 EP 3225707 B1 EP3225707 B1 EP 3225707B1 EP 17151949 A EP17151949 A EP 17151949A EP 3225707 B1 EP3225707 B1 EP 3225707B1
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Prior art keywords
weight
alloy
lead
component
component according
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EP17151949.9A
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German (de)
English (en)
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EP3225707A1 (fr
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Martin Haake
Andreas Hansen
Frank Leistritz
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Geberit International AG
Gebr Kemper GmbH and Co KG
Rehau Automotive SE and Co KG
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Geberit International AG
Rehau AG and Co
Gebr Kemper GmbH and Co KG
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Priority to PL17151949T priority Critical patent/PL3225707T3/pl
Priority to RU2018137812A priority patent/RU2712161C1/ru
Priority to PCT/EP2017/000374 priority patent/WO2017167441A2/fr
Publication of EP3225707A1 publication Critical patent/EP3225707A1/fr
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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
    • C22C9/02—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
    • E—FIXED CONSTRUCTIONS
    • E03—WATER SUPPLY; SEWERAGE
    • E03B—INSTALLATIONS OR METHODS FOR OBTAINING, COLLECTING, OR DISTRIBUTING WATER
    • E03B7/00—Water main or service pipe systems

Definitions

  • the present invention relates to a component for media-carrying gas or water pipes, in particular a fitting or armature for drinking water pipes, the component at least partially consisting of a lead-free copper alloy.
  • the corrosion resistance should be mentioned.
  • Non-ferrous metal alloys with a high copper content such as bronze, brass or gunmetal, also contain a certain amount of lead because lead improves the machinability of such alloys.
  • nickel is also present in such alloys to increase the strength and corrosion resistance of the alloys. Due to the toxicity of these metals, however, such materials must have a low tendency for metal ions to migrate into the medium, ie a low release of ions from the alloy components to the medium.
  • the materials used to protect consumers must comply with very narrow limits, which are regulated by the drinking water regulations.
  • This is from the EP 1 798 298 A1 a largely lead- and nickel-free copper alloy which, in addition to copper and unavoidable impurities, contains 2% by weight to 4.5% by weight silicon, 1% to 15% by weight zinc, 0.05% by weight up to 2% by weight manganese and optionally 0.05% by weight to 0.4% by weight aluminum and 0.05% by weight to 2% by weight tin.
  • the ones in the EP 1 798 298 A1 The alloy described shows an improved migration behavior for lead, nickel, copper and zinc ions compared to a conventional gunmetal. After casting, the alloy can be subjected to a heat treatment in order to achieve a high proportion of ⁇ mixed crystal and thus a particularly favorable migration behavior of the alloy.
  • the gunmetal alloy CuSn5Zn5Pb2 with contents of around 5% by weight tin and around 5% by weight zinc is currently widely used for use in drinking water installations.
  • This copper alloy has excellent corrosion resistance and can therefore be used in all water qualities within the drinking water supply.
  • Alloys of this type usually have a single-phase structure and therefore offer high plastic deformability. However, it is precisely this plastic deformability that causes problems during machining.
  • Single-phase copper materials tend to form long chips. This type of chip inhibits the workflow during fully automated turning or drilling and leads to heavy wear on the tool cutting edges. In order to still be able to process the products economically, lead is added to the alloys as a chip-breaking additive. Lead enables economical, fully automated mechanical processing.
  • Lead is practically insoluble in copper and has a low melting point. As a result, it is the last element to solidify in copper-tin alloys.
  • This constitutional behavior means that, at the end of solidification, lead is present in the structure in the form of evenly distributed, small, drop-shaped particles between the dendrite arms. These fine, drop-shaped particles act as chip breakers without affecting the original properties of the material. This can be seen particularly clearly from the corrosion resistance, since the lead particles are present as incoherent phases and thus cannot interact with the surrounding matrix.
  • the uniform distribution of small, drop-shaped lead particles also ensures that consistently similar mechanical parameters can be expected over a uniform cross-section.
  • nickel In copper alloys, nickel is able to both increase corrosion resistance and improve the distribution of sulfide phases in the structure. However, high nickel contents lead to a high release of metal ions into drinking water and are therefore classified as hygienically questionable.
  • the specified alloy range in the patent US 8,470,101 B2 cannot guarantee over the entire scope described therein that sufficiently high corrosion, strength, processing or hygiene properties are present. But these properties in particular are essential for thin-walled components that carry drinking water.
  • the present invention is based on the object of specifying a lead-free copper alloy for the production of components for media-carrying gas or water pipes which, compared to a conventional gunmetal alloy, e.g. CuSn5Zn5Pb2, a corrosion-resistant matrix, has good strength properties combined with good processing properties, high pressure tightness and improved migration behavior.
  • the lead-free copper alloy should have good casting behavior, for example in sand or continuous casting.
  • a lead-free copper alloy which as alloy components in wt .-% in addition to copper (Cu) and unavoidable impurities still 3.5 wt .-% ⁇ tin (Sn) ⁇ 4.8 wt .-% , 1.5% by weight ⁇ zinc (Zn) ⁇ 3.5% by weight, 0.25% by weight ⁇ sulfur (S) ⁇ 0.65% by weight, 0.04% by weight Phosphorus (P) 0.1 wt%, optionally not more than 0.09 wt% lead; optionally no more than 0.4 wt% nickel; optionally no more than 0.1 wt% antimony; as well as optionally not more than 0.3% by weight iron, zirconium and / or boron alone or in combination of two or more of the elements mentioned, in contact with water of different water qualities one compared to standard brass (CuZn40Pb2) and dezincification-resistant brass (CuZn36Pb2As) Improved
  • the lead-free copper alloy Due to this improved formation of the top layer, the lead-free copper alloy shows no dezincification or similar selective corrosion attacks. Therefore, the lead-free copper alloy has improved corrosion resistance over the entire framework specified by the Drinking Water Ordinance (hereinafter referred to as "TWVO"). Accordingly, the present invention preferably represents a component for media-carrying gas or water lines, in particular a fitting or a fitting for drinking water pipes, the component at least partially consisting of the lead-free copper alloy according to the invention, the component having a wall thickness in the range from 0.5 mm to 6.0 mm at least in sections.
  • the tin content influences the strength, corrosion resistance and phase distribution and, in the claimed range of 3.5% by weight to ⁇ 4.8% by weight, achieves an optimally balanced, economic ratio of the properties described above.
  • a tin content of more than 4.8% by weight the strength and corrosion resistance in the matrix increase further, but under normal cooling conditions in sand casting, the distribution of the sulfides becomes coarser and the size increases.
  • tin contents below 3.5% by weight there is insufficient corrosion inhibition.
  • the weak solid solution strengthening the properties necessary for practice are not achieved.
  • a high tensile strength can be achieved at contents of more than 4.8% wt.% Tin, whereas the elongation values of the material are reduced. Contents of far more than 4.8 wt .-% tin lead to the formation of a structure which has an embrittling and unfavorable effect on the processing.
  • the sulfur content of 0.25% by weight to 0.65% by weight also determines the volume fraction of the sulfides. From 0.25% by weight sulfur, an amount of sulfide particles is generated which ensures that the alloy is sufficiently machinable. A sulfur content above 0.65% by weight sulfur can lead to the formation of undesirable, coarse sulfide particles. In addition, due to the high proportion of sulfide particles, the load-transferring cross-section, ie the cross-section of the component that absorbs external stresses, can be reduced so much that the mechanical parameters, such as elongation at break and the like, deteriorate.
  • the metal sulfides are present in the lead-free copper alloy as an incoherent, finely divided, disperse phase in the form of finely divided particles with such a sulfur content. This offers the advantage that any corrosion that may occur occurs only to a small extent locally on these particles and not along coherent, larger, individual phases of the alloy structure, as is the case, for example, with standard brass. Due to the small size of the particles, there is no significant corrosion attack.
  • the proportion of phosphorus (P) in the lead-free copper alloy is 0.04% by weight to 0.1% by weight. Below 0.04% by weight of phosphorus, there is insufficient deoxidation of the melt, which has a negative effect on the phase formation of the alloy. In contrast, the lead-free copper alloy with a phosphorus content of more than 0.1% by weight tends to have adverse effects on the mechanical properties, such as reduced elongation at break. From these points of view, the proportion by weight of phosphorus in the lead-free copper alloy is preferably in the range from 0.04% by weight to 0.08% by weight, particularly preferably in the range from 0.04% by weight to 0.06% by weight. -%.
  • the term "lead-free copper alloy” means a copper alloy that includes lead as an unavoidable impurity in an amount of not more than 0.09% by weight, more preferably not more than 0.05% by weight.
  • the lead content in the alloy is a maximum of 0.09% by weight and particularly preferably a maximum of less than or equal to 0.05% by weight.
  • the alloy shows no signs of increased lead release in the first few weeks. Instead, you can From the eighth week of the test, no more significant lead migration into the drinking water can be determined or is within the range of the measurement accuracy of the method.
  • the low lead content in the alloy used according to the invention thus leads to a significant reduction in metal ion migration in drinking water, the low lead content having no negative effects on chip breaking and thus on the machinability of the alloy used according to the invention.
  • the nickel content in the alloy used according to the invention is a maximum of 0.4% by weight, preferably the nickel content is a maximum of 0.3% by weight.
  • the addition of nickel increases the corrosion resistance of the alloy without contradicting the hygienic safety. Similar to lead, the values of nickel migration in a test according to DIN EN 15664-1 are far below the legally required limit value.
  • an antimony content of a maximum of 0.1% by weight is not critical with regard to the properties of drinking water migration.
  • the alloy can also have an iron content of a maximum of 0.3% by weight.
  • the lead-free copper alloy can also contain proportions of the elements iron (Fe), zirconium (Zr) and / or boron (B) alone or in a combination of at least two of the elements mentioned as grain refiners. It is preferred that iron in a weight fraction of up to 0.3 wt .-%, zirconium in a weight fraction of up to 0.01 wt .-% and / or boron in a weight fraction of up to 0.01 wt. -% are contained in the lead-free copper alloy.
  • the grain refiners avoid hot cracking and influence the mechanical properties, e.g. Tensile strength, material hardness and the like are positive.
  • the copper content of the lead-free copper alloy is preferably at least 90% by weight, preferably more than 91% by weight.
  • the sulfides of the lead-free copper alloy are homogeneously distributed in the structure.
  • the number of sulphide particles should be high and their mean size should be small in order to ensure uniform mechanical parameters, good corrosion resistance, improved machinability and high pressure tightness over the entire structure.
  • Copper sulfide is preferred as the material of the sulfide particles, since the occurrence of copper sulfide makes it possible to substitute the volume of lead with a significantly lower content of sulfur.
  • the component according to the invention has, at least in sections, a wall thickness in the range from 0.5 mm to 6.0 mm, since the thin wall thickness leads to cooling rates suitable for the formation of the copper sulfides. It is also preferred if the entire component according to the invention has a wall thickness within the stated ranges of 0.5 mm to 4.0 mm, since a wall thickness in this range leads to a particularly increased formation of the desired sulfide particles. A wall thickness below 0.5 mm could not have sufficient mechanical strength of the component according to the invention due to the small cross section. From this point of view, it is preferred that the component according to the invention has, at least in sections, a wall thickness in the range from 1.0 mm to 4.0 mm.
  • the cross-section of the component according to the invention has a wall thickness of less than 6 mm at least 1.6 percent by area of sulfide particles and / or an area index ASP% less than 1000.
  • Such values lead to sulfur sulphides being present as an incoherent, finely divided, disperse phase. This avoids deep trough-shaped and / or hole-shaped attacks, in particular corrosion attacks, on the components according to the invention.
  • area index ASP% is the mathematical description for the measure of the shape and position of a bell curve, which is obtained from a plot of the mean values of the area classes (abscissa) in combination with the percentage distribution of the sulfide particles in these area classes (ordinate ) results (cf. Fig. 1 ).
  • the value of the area index ASP% is obtained by measuring the area of the respective particles, for example from an enlarged photograph of a micrograph, the percentage allocation of the particles recognizable in the recording into classes, the multiplication of the percentage values of the allocation by the mean value of the class and the formation of a large mean value from the resulting mean values of the classes, the large mean value being assumed to be the "area index ASP%".
  • the alloy used according to the invention has the excellent property of forming a top layer very quickly on the inner surface wetted with drinking water.
  • the cover layer has a thickness of preferably at least 2 ⁇ m, particularly preferably of at least 3 ⁇ m.
  • This top layer increases the corrosion resistance and ensures the longevity of the components made of this material, since further corrosion is prevented. Migration from the material to the drinking water can only take place if corrosion processes take place in the material.
  • the top layer functions as a protective layer and limits the further metal release to the drinking water to a minimum.
  • the copper content in the alloy described is higher than in conventional gunmetal alloys, such as. B. CuSnZn5Pb2, there is only a reduced copper metal release.
  • the components according to the invention for media-carrying gas or water pipes can be produced using conventional casting processes, such as sand, permanent mold or continuous casting processes.
  • the cast part produced by such a casting process can be machined well.
  • the term "component for media-carrying gas or drinking water lines" is to be understood as meaning in particular those components that come into contact with a house installation pipe system, in particular with drinking water, fittings and fittings of such house installation pipe systems being preferred according to the invention.
  • An example of such a fitting is in particular that from EP 2 250 421 A1 to name known connector.
  • Fig. 2 shows a Turner diagram for the test waters used in the artificial aging test.
  • the carbonate hardness (as a measure of the water hardness) is plotted against the chloride ion content of the test water.
  • the line labeled "Turner classic” represents the corrosion characteristic for dezincification developed by Turner (" The Influence of Water Composition on the Decincification of Duplex Brass Fittings "; 1965 ). According to the current interpretation of the corrosion experts, no dezincification takes place in the area below this line, but above this line there is a very high risk of damage to the component in question due to dezincification.
  • the points shown give an overview of the different test waters that were used in the artificial aging test described.
  • test specimens For the production of test specimens, half cylinders with a wall thickness of 5 mm were cast from alloys 1 and 2. The test specimens were then turned on the outside to a roughness Rz of max. 25 ⁇ m and machined on the inside by means of drilling with a through-hole with a roughness Rz of max. 40 ⁇ m. This special surface treatment should enable the test specimens to be compared with actually manufactured components.
  • test specimen was cleaned with acetone.
  • test specimens were then placed in a test container in a freely hanging manner.
  • the test containers were then placed in a heating cabinet at 90 ° C. for five months, the test medium being changed at seven-day intervals.
  • Table 2 ⁇ u> Table 2: ⁇ /u> Water number PH value Carbonate hardness in ° dH Chloride in mg / l Sulphate in mg / l 1 8th 0.5 10 - 2 8th 0.5 100 - 3 8th 0.5 250 - 4th 8th 0.5 1000 - 5 8th 1.5 15th - 6th 8th 1.5 60 - 7th 8th 1.5 140 - 8th 8th 3.0 30th - 9 8th 3.0 100 - 10 8th 5.5 80 - 11 8th 5.5 120 - 12 8th 5.5 250 - 13th 7th 9.0 100 - 14th 7th 9.0 160 - 15th 7th 14.0 140 - 16 7th 18.0 40 - 17th 7th 18.0 100 - 18th 7th 18.0 250 - 19th 8th 0.5 250 250 20th 8th 5.5 250 250 21st 7th 18.0 250 250 250
  • test containers are removed from the heating cabinet, cooled to room temperature, the test specimens are removed from the respective test containers, dried, cut open and the cut surface is examined with a light microscope after appropriate processing.
  • Alloys 1 and 2 showed, over the entire area of the drinking water ordinance tested in the artificial aging, an outstanding formation of a protective, firmly adhering, closed top layer which is necessary for copper alloys, which in the artificial aging test has a thickness of at least 2 ⁇ m and thus an improved top layer in relation to a conventional, lead-containing copper alloy based on a CuSnZn alloy (eg CuSn5Zn5Pb). Furthermore, this layer is almost free from disturbances or defects and thus unfolds its complete protection by avoiding a deeper, local corrosion attack (see Fig. 4 and Fig. 6 ).
  • Fig. 4 shows the behavior of the top layer formation of a lead-free copper alloy (alloy 1 and alloy 2) after a five-month artificial aging test for the respective test waters. It turns out that only a protective top layer is formed. No selective corrosion attack whatsoever is visible.
  • the thickness of the firmly adhering protective cover layer formed is at least 4 ⁇ m.
  • Fig. 5 is a photograph of the microstructure of standard brass (CuZn40Pb2) as the result of an exemplary corrosion attack after the five-month artificial aging test, based on Turner, with a chloride content of 250 mg / l and a carbonate hardness of 5.5 ° dH. An uneven, partially disturbed structure of the top layer and the selective corrosion attack in the form of dezincification can be clearly seen.
  • Fig. 6 a photographic recording of the microstructure of a result of the five-month artificial aging test, based on Turner, with a chloride content of 250 mg / l and a carbonate hardness of 5.5 ° dH, of a component according to the invention made of alloy 2 (alloy 1 shows a behavior analogous to this ) was carried out.
  • alloy 2 shows a behavior analogous to this .
  • the microstructure shown shows no selective corrosion attack in the component after an identical heat exposure test, but a uniform, homogeneous structure of a protective, firmly adhering cover layer with a thickness of 4 ⁇ m to 23 ⁇ m.
  • the artificial aging test carried out here shows that the alloy is free of selective corrosion attacks (e.g. dezincification and stress corrosion cracking) and almost all other signs of corrosion based on Turner's approach.
  • Fig. 7 represents a thermal analysis in a temperature-time diagram, by means of which thermal effects (e.g. release of latent heat) can be detected in metals, which can arise during transitions from solid to liquid or during phase transformations in the solid state.
  • the cooling temperature of the alloy and the first time derivative of the measurement signal are plotted against the time, which is described as the cooling rate.
  • a change in the peak in the cooling rate curve corresponds to a thermal effect in the material.
  • a sulfide formation should be aimed for shortly before the end of solidification at a low temperature, since this way the sulfides are distributed more homogeneously in the structure, similar to lead.
  • Table 3 ⁇ /u> alloy Cu Sn Zn S.
  • the cooling rate in Fig. 7 corresponds to the typical solidification process of a copper-tin alloy up to 5% by weight tin in sand casting.
  • a further comparison of the two curves shows that in alloy 3 at approx. 400 s there is an early thermal effect during the ongoing solidification process, which is due to the formation of sulfide.
  • alloy 4 according to the invention the sulfide formation takes place with a delay, shortly before the end of solidification.
  • the fact that both samples were cooled under identical conditions underpins the further course of the cooling rate of the samples, which is identical after the phase formation. The varying point in time of the phase formation is therefore due to the different zinc content in the alloys.
  • the early sulfide formation influences the sulfide form and the distribution in the structure.
  • the early sulfide formation in alloy 3 thus leads to a heterogeneous, partial phase distribution, which has a negative impact on the mechanical parameters such as elongation.
  • Fig. 8 (Alloy 3) and Fig. 9 (Alloy 4 used according to the invention) are the differences in the structure of components that are made from melts according to alloy 3 and 4 Fig. 7 can be seen with the different zinc contents.
  • the material composition is adjusted in a way that avoids premature sulfide formation and promotes homogeneous distribution.
  • FIG. 10 and 11 shows microstructural images of components according to the invention from an identical melt that was cooled under varying conditions. In the case of rapid cooling, the microstructure shows in Fig. 11 a structure that leads to higher mechanical characteristics such as tensile strength, elongation at break and the like.
  • the particles were examined and characterized by means of image analysis on ground structures of the test specimens.
  • the volume of sulphides and the area can be determined by means of this image analysis.
  • the alloys used according to the invention can be characterized with an area index ASP% of less than 1000.

Claims (9)

  1. Composant pour des conduits de gaz ou d'eau d'acheminement de milieux, en particulier pour un raccord ou une robinetterie pour des conduits d'eau potable, dans lequel le composant est constitué au moins en partie d'un alliage de cuivre sans plomb, qui présente les composants d'alliage suivant en % en poids :
    3,5 % en poids ≤ Sn ≤ 4,8 % en poids ;
    1,5 % en poids ≤ Zn ≤ 3,5 % en poids ;
    0,25 % en poids ≤ S ≤ 0,65 % en poids ;
    0,04 % en poids ≤ P ≤ 0,1 % en poids ;
    en option pas plus de 0,09 % en poids de plomb ;
    en option pas plus de 0,4 % en poids de nickel ;
    en option pas plus de 0,1 % en poids d'antimoine ;
    en option pas plus de 0,3 % en poids de fer, de zirconium et/ou de bore seuls ou en combinaison avec deux ou plus des éléments évoqués ;
    des impuretés inévitables ainsi
    du cuivre pour le reste,
    dans lequel le composant présente au moins par endroits une épaisseur de paroi dans la plage de 0,5 mm à 6,0 mm.
  2. Composant selon la revendication 1, caractérisé en ce que la fraction en soufre dans l'alliage est de 0,3 % en poids ≤ S ≤ 0,60 % en poids, en particulier de 0,35 % en poids ≤ S ≤ 0,55 % en poids.
  3. Composant selon la revendication 1 ou la revendication 2, caractérisé en ce que la fraction en zinc dans l'alliage est de 2,0 % en poids ≤ Zn ≤ 3,0 % en poids.
  4. Composant selon l'une quelconque des revendications précédentes, caractérisé en ce que la fraction en phosphore dans l'alliage est de 0,04 % en poids ≤ P ≤ 0,08 % en poids, en particulier 0,04 % en poids ≤ P ≤ 0,06 % en poids.
  5. Composant selon l'une quelconque des revendications précédentes, caractérisé en ce que la teneur en plomb n'est pas supérieure à 0,05 % en poids.
  6. Composant selon l'une quelconque des revendications précédentes, caractérisé en ce que le cuivre est contenu dans l'alliage de cuivre sans plomb en une quantité supérieure à 90 % en poids.
  7. Composant selon l'une quelconque des revendications précédentes, caractérisé en ce que le composant présente au moins par endroits une épaisseur de paroi dans la plage de 1,0 mm à 4,0 mm.
  8. Composant selon l'une quelconque des revendications 1 à 7, caractérisé en ce qu'il présente une couche de recouvrement de protection homogène d'au moins 2 µm.
  9. Composant selon l'une quelconque des revendications précédentes, caractérisé en ce que le matériau ne présente selon la norme DIN EN 15664-2 après 16 semaines aucune migration de plomb ou de nickel élevée et satisfait aux spécifications de la norme DIN EN 15664-2.
EP17151949.9A 2016-03-29 2017-01-18 Composant pour des canalisations d'eau ou de gaz acheminant des milieux comprenant un alliage de cuivre Active EP3225707B1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
PL17151949T PL3225707T3 (pl) 2016-03-29 2017-01-18 Element konstrukcyjny do prowadzących media przewodów gazowych lub wodociągowych, zawierający stop miedzi
RU2018137812A RU2712161C1 (ru) 2016-03-29 2017-03-28 Конструктивный элемент для средопроводящих газо- или водопроводов
PCT/EP2017/000374 WO2017167441A2 (fr) 2016-03-29 2017-03-28 Pièce pour conduites de gaz ou d'eau

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE202016101661.4U DE202016101661U1 (de) 2016-03-29 2016-03-29 Bauteil für medienführende Gas- oder Wasserleitungen

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EP3225707A1 EP3225707A1 (fr) 2017-10-04
EP3225707B1 true EP3225707B1 (fr) 2020-12-30

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DE (1) DE202016101661U1 (fr)
DK (1) DK3225707T3 (fr)
PL (1) PL3225707T3 (fr)
RU (1) RU2712161C1 (fr)
WO (1) WO2017167441A2 (fr)

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AT520560B1 (de) * 2018-01-29 2019-05-15 Miba Gleitlager Austria Gmbh Mehrschichtgleitlagerelement
DE102018004702A1 (de) 2018-06-12 2019-12-12 Gebr. Kemper Gmbh + Co. Kg Metallwerke Formteile aus einer korrosionsbeständigen und zerspanbaren Kupferlegierung
DE102019106136A1 (de) * 2019-03-11 2020-09-17 M.G. Meccanica Srl Verfahren zur Herstellung von metallischen Bauteilen sowie dadurch hergestelltes metallisches Bauteil
DE102019106131A1 (de) * 2019-03-11 2020-09-17 M.G. Meccanica Srl Verfahren zur Herstellung von Bauteilen für medienführende Gas- oder Wasserleitungen sowie dadurch hergestelltes Bauteil
AT522440B1 (de) 2019-05-07 2020-11-15 Miba Gleitlager Austria Gmbh Mehrschichtgleitlagerelement
AU2021399776A1 (en) 2020-12-17 2023-07-20 REHAU Industries SE & Co. KG Connecting element system for producing a tube connection, tube connection comprising the former, and method for producing a tube connection of this type
DE202020107328U1 (de) 2020-12-17 2022-03-18 REHAU Industries SE & Co. KG Rohrverbindung und Verbindungselement zur Herstellung einer Rohrverbindung
DE102021106229A1 (de) 2020-12-17 2022-06-23 REHAU Industries SE & Co. KG Verbindungselementsystem zur Herstellung einer Rohrverbindung, dieses umfassende Rohrverbindung sowie Verfahren zur Herstellung einer solchen Rohrverbindung
DE102021110302A1 (de) * 2021-04-22 2022-10-27 Ks Gleitlager Gmbh Kupfer-Zinn-Stranggusslegierung

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EP3225707A1 (fr) 2017-10-04
RU2712161C1 (ru) 2020-01-24
DK3225707T3 (da) 2021-04-06
WO2017167441A2 (fr) 2017-10-05
DE202016101661U1 (de) 2017-06-30
PL3225707T3 (pl) 2021-07-19
WO2017167441A3 (fr) 2018-03-01

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