WO2018033360A1 - Produit en alliage de laiton complexe et utilisation - Google Patents

Produit en alliage de laiton complexe et utilisation Download PDF

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Publication number
WO2018033360A1
WO2018033360A1 PCT/EP2017/069001 EP2017069001W WO2018033360A1 WO 2018033360 A1 WO2018033360 A1 WO 2018033360A1 EP 2017069001 W EP2017069001 W EP 2017069001W WO 2018033360 A1 WO2018033360 A1 WO 2018033360A1
Authority
WO
WIPO (PCT)
Prior art keywords
weight
brass alloy
phase
special brass
alloy product
Prior art date
Application number
PCT/EP2017/069001
Other languages
German (de)
English (en)
Inventor
Hermann Gummert
Thomas Plett
Björn Reetz
Original Assignee
Otto Fuchs - Kommanditgesellschaft
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
Priority claimed from DE202016104552.5U external-priority patent/DE202016104552U1/de
Priority claimed from DE202016105310.2U external-priority patent/DE202016105310U1/de
Application filed by Otto Fuchs - Kommanditgesellschaft filed Critical Otto Fuchs - Kommanditgesellschaft
Priority to EP17751673.9A priority Critical patent/EP3368701A1/fr
Publication of WO2018033360A1 publication Critical patent/WO2018033360A1/fr

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L3/00—Lift-valve, i.e. cut-off apparatus with closure members having at least a component of their opening and closing motion perpendicular to the closing faces; Parts or accessories thereof
    • F01L3/08—Valves guides; Sealing of valve stem, e.g. sealing by lubricant
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2301/00—Using particular materials
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2303/00—Manufacturing of components used in valve arrangements
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2820/00—Details on specific features characterising valve gear arrangements
    • F01L2820/01—Absolute values
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2204/00—Metallic materials; Alloys
    • F16C2204/10—Alloys based on copper
    • F16C2204/14—Alloys based on copper with zinc as the next major constituent
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
    • F16C33/121—Use of special materials

Definitions

  • the invention relates to a special brass alloy product and to a use of such a special brass alloy product.
  • Special brass alloys are particularly suitable for producing forged alloy products.
  • special brass alloy products usually have sufficiently high strength values, so that such alloys are suitable for producing parts which are subjected to higher loads.
  • Described is a special brass alloy of the type in question, for example in WO 2006/058744 A1.
  • the alloy described in this document is used to make a valve guide.
  • the alloy disclosed in this document is also used to make synchronizer rings.
  • This prior art alloy has a composition of 59 to 73% by weight of Cu, 2.7 to 8.3% by weight of Mn, 1.5 to 6% by weight of Al, 0.2 to 4% by weight of Si , 0.2-3% by weight of Fe, max. 2% by weight Pb, max. 2% by weight of Ni, max.
  • the structure described in this prior art has a a- and ß-mixed crystal matrix, in which the ⁇ -phase is finely dispersed in proportions of up to 80%.
  • the ⁇ -precipitates are embedded in a needle-shaped and band-shaped manner in a mixed-Cr matrix.
  • the base material of ⁇ -phase gives the special brass alloy products produced from this alloy the desired strength values. Irregularly dispersedly distributed Mn-Fe silicides contribute to the wear resistance of a product made from this alloy.
  • the alloy described in this document can be subdivided into two alloy groups, namely a Pb-containing 0.5-1.5 wt.% Pb and an alloy with a lower lead content of max. 0.5% by weight of Pb.
  • the first alloy group is based on a Cu content of 70-73 wt.% Or 69.5-71.5 wt.%.
  • the lower lead version has a Cu content of 60 - 61, 5 wt .-% and a low lower Mn and AI content.
  • This object is achieved according to the invention by a special brass alloy product with 62-68 wt.% Cu, 0.2-2.2 wt.% Fe, 5.5-9.0 wt.% Mn, 3.5-7, 5% by weight Al, 0.6-2.5% by weight Si, max. 0.7% by weight of Sn, max. 0.7% by weight of Ni, max. 0.1 wt .-% Pb, balance Zn plus unavoidable impurities, wherein the special brass alloy product has a proportion of ⁇ -phase between 15% and 40%
  • a particular advantage of this special brass alloy product is the special composition of the alloy with its very precisely matched proportions of the alloying elements involved. This combined with a structure in the brass alloy product which has a proportion of ⁇ -phase of 15-40, in particular of more than 15% to less than 40%, wherein the ⁇ -phase not only finely dispersed, but forms larger grains gives the Special brass alloy product, surprisingly, properties that improve wear resistance.
  • the proportion of ⁇ -phase relatively softer ⁇ -phase gives the special brass alloy within certain limits a geometric adaptability to contact surfaces, the special brass alloy product should be provided for such an application. This is the case, for example, with distributor plates of hydraulic units.
  • the proportion of softer a-phase on the special brass alloy product also ensures that dirt particles can be embedded in the surface of the special brass alloy product. This is useful, for example, for special single-alloy products which are subject to slip or friction, for example synchronizer rings, bushings or valve guides. requirements.
  • dirt particles in particular of abrasive particles in the surface of such special brass alloy products, such dirt particles contained in the oil environment in such an application do not contribute to abrasion and thus to wear. The appearance of such particles is unavoidable. These are often small steel particles, mainly from components involved in the assembly.
  • the special brass alloy product has a proportion of ⁇ -phase between 15% and less than 40%.
  • the special brass alloy product has a proportion of ⁇ -phase between 15% and less than 40%.
  • the proportion of the ⁇ -phase present after the hot forming step (s), such as extrusion and / or forging is limited to between 300 ° C and 450 ° C in a narrower temperature window
  • the heat treatment is carried out in a temperature window between 400 ° C and 450 ° C for 8-10 hours. If this heat treatment at higher temperatures, and carried out at temperatures of more than 480 ° C, a further significant increase in the proportion of a-phase is no longer observed. Rather, their share decreases again.
  • this heat treatment for forming the ⁇ -phase in the desired proportions is preferably carried out at temperatures between 400 ° C and 450 ° C for a heat treatment time of 8 to 10 hours.
  • the result is of interest in that the proportion of ⁇ phase after a first hot working step, typically an extrusion step, performed at about 650 ° C or higher, is less than 10% to produce a pre-forged product.
  • the special brass alloy product no longer has a .alpha.-phase detectable by light microscopy.
  • the ⁇ -phase fraction then contributes less than 1% to the structure of the structure.
  • the proportion of ⁇ -phases can be increased to such a significant order of magnitude, up to the range of approximately 40%. In some cases, one will not want an ⁇ -phase content of about 40%, as this is too high for one or the other application.
  • the formation of the ⁇ -phase in the claimed proportion interval can be adjusted by the duration of the downstream heat treatment. If the heat treatment at a certain heat treatment temperature is made shorter, the resulting proportion of the a phase will be correspondingly lower. It is not overlooked that a certain, albeit small ⁇ -phase fraction can form in the course of hot forming, for example an extrusion process. However, the proportion of trainees can not, at least not be controlled to a sufficient extent, especially since the proportion forming is significantly below the a-phase fraction claimed by the invention.
  • the microstructure transformation alone leads to a change in volume and thus to a change in the topography of the surface subject to wear, for example the friction surface in the case of a synchronizer ring. This will affect the desired microadjustment. Since this does not occur in the case of the alloy according to the invention or a product made therefrom, the functionality of the special brass alloy product is considerably improved in comparison with previously known ones.
  • the temperature stability of the structure thus also has a positive effect on the tempering resistance of the alloy product with regard to its hardness, which then does not change even if the temperature is influenced.
  • the elongation at break of the alloy products produced from the special brass alloy is low and is typically between 2 and 5%.
  • the fraction of ⁇ -phase in the structure according to the invention which is significantly higher than non-heat-treated alloy products, increases the local ductility of the alloy product, which in turn reduces its impact sensitivity.
  • Fig. 2 a cross section (top) and a longitudinal section (bottom) by a performed at a first temperature
  • FIG. 3 shows a cross section (top) and a longitudinal section (bottom) by a heat treatment of the special brass alloy product carried out at a second temperature
  • FIG. 4 shows a cross section (top) and a longitudinal section (bottom) by a heat treatment of the special brass alloy product carried out at a third temperature
  • FIG. 5 shows a cross section (top) and a longitudinal section (bottom) through a heat treatment of the special brass alloy product carried out at a temperature above the claimed temperature window
  • FIG. 6 shows a micrograph of the sample of FIG. 4 for illustrating the rod-shaped distribution of the ⁇ -phase with the indication of the extent of individual primary grains in the high-temperature ⁇ -phase phase
  • FIG. 7 is a colored micrograph showing the hard phase distribution in a sample according to the invention.
  • FIG. 8 is a graph showing the frequency distribution of the areas of the intermetallic phases on the basis of the sample of FIG.
  • FIG. 10 shows the distribution of the spacing of the intermetallic phases from one another in the micrograph of FIG. 7
  • FIG. 11 shows a scanning electron micrograph with the sample points of an EDX analysis at a first location of the sample of the above figures, a scanning electron micrograph with the sample points of an EDX analysis at another location of the sample of the preceding figures, a scanning electron micrograph Image taken at 5000x magnification, a perspective view of a washer made of a forged semi-finished product for hydraulic application, and a diagram for making the wheel of FIG. 6.
  • This special brass alloy product has the following composition (all data in% by weight):
  • the extruded pre-forged product has a 9% a-phase content.
  • the proportion of intermetallic phases is over the length of the extruded pre-forged product about 10%.
  • the Brinell hardness (HBW 2.5 / 62.5) of the extruded pre-forged product was measured to be 218.
  • the extrusion process was carried out at about 650 ° C. Rings cut from the tube as pre-forged product were then heated to about 560 ° C and forged to synchronizer rings.
  • the proportion of ⁇ -phase was reduced by this heat treatment to less than 1%. Subsequently, the proportion of ⁇ -phase was adjusted because the synchronizing ring should have an ⁇ -phase content of about 25%.
  • This adjustment of the ⁇ -phase content was adjusted by means of a subsequent heat treatment at 420 ° C for 10 hours and subsequent air cooling and thus significantly increased compared to the present before this heat treatment a-phase component. Due to the special ⁇ -phase content of this special brass alloy product produced by way of example as a synchronizer ring, it has, above all, an embedding capability of foreign particles intended for minimizing wear.
  • the sequence of figures of Figures 1 to 5 shows the formation of the ⁇ -phase in the structure of the samples examined.
  • the sample of FIG. 1 was not subjected to any heat treatment following its shaping (forming).
  • the sample of Figure 2 was subjected to a heat treatment of 380 ° C for 10 hours.
  • the sample of Figure 3 was subjected to a heat treatment of 450 ° C for 3 hours, that of the sample of Figure 4 to a heat treatment of 450 ° C for 10 hours and the sample of Figure 5 to a heat treatment at 550 ° C for 10 hours.
  • the formation of the ⁇ -phase is clearly visible in the samples which have been subjected to a heat treatment of 380 ° C and 450 ° C for the indicated periods of time. In the sample subjected to a heat treatment of 550 ° C no ⁇ -phase is visible. Thus, these observations are consistent with the above observations on the different hardnesses of these samples.
  • the rod-shaped ⁇ phase is homogeneous within the ground plane. arranged in a distributed manner, which in turn has a positive effect on the above-described embeddability on contact surfaces (see FIG.
  • phase proportions in the microstructure are as follows: a- mixed crystal fraction: 31%, intermetallic phase: 1 1% and the remainder of the ⁇ -mixed crystal fraction.
  • Microhardness tests were performed on the individual phases according to HV 0.05. In each case, five sites of the sample have been sampled for ⁇ , ⁇ and ⁇ -mixed mixtures. The microhardness of the samples in the different phases is very similar to each other. The range of measurements at the ⁇ -phase sample sites is between 228-269 HV 0.05. That of the beta phase between 225-253 HV 0.05. In this spectrum are also the determined hardnesses for the mixed phase mixture. The fairly uniform hardness in the microstructure has a positive effect on the desired properties of the alloy product produced from the alloy. The silicides in the structure have a hardness of on average 1088 HV 0.05.
  • FIG. 7 shows the distribution of the hard phases in the microstructure.
  • the silicides are shown in different shades of gray compared to the ⁇ -ß structure shown in color.
  • the hard phases (silicides), as can be clearly seen in FIG. 7, are arranged in a line-like manner, wherein the distance between the nearest neighbors in a row is significantly smaller than the distance between the line neighbors.
  • the diagram of Figure 8 shows the frequency distribution of the surfaces of the intermetallic phases in a logarithmic classification with a maximum at about 1 1 ⁇ second
  • the area distribution curve shown in Figure 8 shows a narrow area distribution pattern.
  • the hard phases have a fairly uniform grain size. In fact, there are two maxima, but they are close together. These are almost seamlessly merged in the frequency distribution. This expresses itself also in a frequency distribution of the average grain diameter of the intermetallic phases, which can be seen from the diagram of Figure 9, a very narrow grain size spectrum between 10 and 16 ⁇ having a maximum at about 13 ⁇ .
  • the intermetallic phases (the hard phases) have a sufficient distance from one another, since embedding does not take place in the area of the hard phases. This can only be done in the hard phase spaces.
  • the diagram of Figure 10 shows a frequency distribution diagram of the distances with a maximum at a distance of about 16 ⁇ , the distance is hardly less than 2 ⁇ .
  • the next distances of the hard phases are regularly entered into the diagram of FIG. 10, and thus these distances represent the distances of the hard phases within a row.
  • the distances between the hard phases between the individual lines are two to three times greater than between the hard phases within a line.
  • Item 2 silicide 20,6 50,3 27,2 1, 9
  • Point 5 matrix total 5.1 3.4 68.3 23.1
  • Item 8 Matrix total 5.2 5.2 69.3 22.0
  • Item 9 Matrix total 5.6 1, 9 5.8 64.7 22.0
  • Figure 13 shows a scanning electron micrograph of high resolution of the same sample showing very fine precipitation-like phases (bright). These are very fine ⁇ -phase portions that seem to be in an orientation relationship with the ⁇ -phase ergot. A certain preferential orientation of the excretions is recognizable. These very fine-grained precipitates have a positive effect on the mechanical strength and the temperature resistance, since these displacement movements are blocked at the phase boundaries.
  • a distributor plate 1 for a hydraulic application was produced (see Figure 14).
  • the disc 1 comprises a central aperture 2 and a plurality of satellites of the central aperture 2 surrounding, also designed as perforations oil passage openings 3.
  • the oil passage openings 3 have a, according to their distance from the central axis curved, proximal slot-like geometry. In the illustrated embodiment, the diameter of the disc is about 1 10 mm.
  • the disk 1 has been produced in several steps. This will be explained below with reference to the flowchart of FIG.
  • a forging blank 4 has been separated in a first step.
  • This forging blank 4 is an annular disk-shaped body, which in FIG a side view is shown. The ring opening is not recognizable due to the chosen perspective.
  • the fiber course in the structure of the forging blank 4 extends in the longitudinal extent of the pressed pipe and thus parallel to the longitudinal axis of the central opening of the forging blank 4.
  • This central opening of the forging blank is the precursor to the central opening 2 of the disc 1.
  • the fiber course in the structure of the forging blanket runs in the illustration in Figure 15 in the vertical direction from top to bottom.
  • a forged semi-finished product 5 is made in a subsequent, performed at about 550 ° C forging step.
  • Forging depressions 6 have been created, which form the oil passage openings 3 after the subsequent finishing of the semifinished product.
  • the formed to form the recesses 6 material forms a bottom 7.
  • the wells 6 in the perspective of the semifinished product in Figure 15 are closed on the underside. Due to the geometry of the forging punch used for this purpose, which carries corresponding projections for forming the depressions 6, the transition from the walls enclosing the depressions 6 into the upper flat side recognizable in FIG. 7 is executed with a radius.
  • FIG. 15 shows the semifinished product 5 in a perspective view and in a cross-sectional view.
  • the cross-section through the semifinished product 5 shown in FIG. 15 runs along the line A-B of the perspective view.
  • FIG. 15 An enlarged schematic partial cross-sectional view in Figure 15 in the transition from a recess 6 in the forging punch facing flat side of the forged semi-finished product 5 illustrates the relevant structure formation.
  • the surface near the edge region has a first edge zone 8, which is characterized by its particular fine grain of the adjacent thereto and with respect to the surface 9 more remote areas.
  • a second edge zone 10 that extends to a slightly greater depth, the grains are the course of the adjacent Surface 9 following, adjusted.
  • the edge zone 10 is set to a particular extent on the forge pressure side, thus on the side on which the forging punch acts with its to support the depressions 6 supporting extensions.
  • the semifinished product 5 is brought to its final geometry by machining.
  • the machining is done by turning. Turned off in the illustrated embodiment of the surface 9, of the surface 9 opposite flat side 12, the radial outer side and the central aperture wall forming removed so that then the semifinished product 5 has the final contour shown in Figure 14.
  • the contour of the finished wheel 1 is indicated by dashed lines. This also shows the spatial position of the disc to be created within the semifinished product 5.
  • the floors 7 including the adjoining radii are also removed in the transition to the walls 1 1 and the initially forged depressions 6 thereby opened to form the oil passage openings 3.
  • the depth of the recesses 6 starting from the surface 9 of the forging dies facing flat side of the semifinished product 5 is designed so that they extend to a depth that they are completely opened by removing their bottoms 7 including the adjacent radii for forming the oil passage openings 3 ,
  • the distributor plate 1 was subjected to a heat treatment at 420 ° C for 10 hours, followed by air cooling. Brinell hardness (HBW 2.5 / 62.5) was measured at this special brass alloy product at 218. This special brass alloy product was tested for strength values. These led to the following result:
  • silicides are incorporated following the forming structure.
  • the longitudinal extension of the rod-shaped silicides follows the surface of the special brass alloy product provided by the shaping. Therefore, these special brass alloy products have high wear resistance at the contact surface (s).
  • the pronounced ⁇ -phase in the special brass alloy products ensures the desired local ductility and the associated embedding capacity of foreign particles.
  • the uniform distribution of the silicides and the equally uniform distribution of the ⁇ -phase components in the structure in addition to a relatively high hardness, give these special brass alloy products properties so that they can be used for a very wide variety of applications.

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

Abstract

L'invention concerne un produit en laiton complexe comprenant 62 – 68 % en poids de Cu, 0,2 – 2,2 % en poids de Fe, 5,5 – 9,0 % en poids Mn, 3,5 – 7,5 % en poids de Al, 0,6 – 2,5 % en poids de Si, max. 0,7 % en poids de Sn, max. 0,7 % en poids de Ni, max. 0,1 % en poids de Pb, le reste constitué de Zn, en plus des impuretés inévitables, présentant une fraction de phase α entre 15 % et 40 %. L'invention concerne un procédé de fabrication d'un tel produit en alliage de laiton complexe, une première étape consistant à fabriquer un demi-produit à partir d'une ébauche par au moins une étape de mise en forme à chaud ; puis à le soumettre à un traitement thermique entre 300°C et 450°C pendant 3 à 12 heures aux fins de formation de la fraction de la phase α.
PCT/EP2017/069001 2016-08-19 2017-07-27 Produit en alliage de laiton complexe et utilisation WO2018033360A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP17751673.9A EP3368701A1 (fr) 2016-08-19 2017-07-27 Produit en alliage de laiton complexe et utilisation

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
DE202016104552.5 2016-08-19
DE202016104552.5U DE202016104552U1 (de) 2016-08-19 2016-08-19 Sondermessinglegierungsprodukt sowie Verwendung desselben
DE202016105310.2 2016-09-23
DE202016105310.2U DE202016105310U1 (de) 2016-09-23 2016-09-23 Aus einem geschmiedeten Halbzeug hergestellte Scheibe für eine hydraulische Anwendung

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WO2018033360A1 true WO2018033360A1 (fr) 2018-02-22

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WO (1) WO2018033360A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113166849A (zh) * 2018-10-29 2021-07-23 奥托福克斯两合公司 特种黄铜合金和特种黄铜合金产品

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0621346A1 (fr) * 1993-04-23 1994-10-26 Wieland-Werke Ag Utilisation d'un alliage cuivre-zinc pour la fabrication d'objets utilitaires sans nickel
WO2006058744A1 (fr) 2004-12-02 2006-06-08 Diehl Metall Stiftung & Co. Kg Utilisation d'un alliage cuivre-zinc
US20120020600A1 (en) * 2009-01-06 2012-01-26 Oiles Corporation High-strength brass alloy for sliding members, and sliding members
US20130078137A1 (en) * 2005-04-04 2013-03-28 Norbert Gaag Use of a copper zinc alloy
WO2015173291A2 (fr) * 2014-05-16 2015-11-19 Otto Fuchs - Kommanditgesellschaft - Alliage de laiton à haute résistance et produit d'alliage
US20150373964A1 (en) * 2013-03-12 2015-12-31 Diehl Metall Stiftung & Co. Kg Horseshoe and copper-zinc alloy for a horseshoe

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0621346A1 (fr) * 1993-04-23 1994-10-26 Wieland-Werke Ag Utilisation d'un alliage cuivre-zinc pour la fabrication d'objets utilitaires sans nickel
WO2006058744A1 (fr) 2004-12-02 2006-06-08 Diehl Metall Stiftung & Co. Kg Utilisation d'un alliage cuivre-zinc
US20070227631A1 (en) * 2004-12-02 2007-10-04 Diehl Metall Stiftung & Co. Kg Copper-zinc alloy for a valve guide
US20130078137A1 (en) * 2005-04-04 2013-03-28 Norbert Gaag Use of a copper zinc alloy
US20120020600A1 (en) * 2009-01-06 2012-01-26 Oiles Corporation High-strength brass alloy for sliding members, and sliding members
US20150373964A1 (en) * 2013-03-12 2015-12-31 Diehl Metall Stiftung & Co. Kg Horseshoe and copper-zinc alloy for a horseshoe
WO2015173291A2 (fr) * 2014-05-16 2015-11-19 Otto Fuchs - Kommanditgesellschaft - Alliage de laiton à haute résistance et produit d'alliage

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113166849A (zh) * 2018-10-29 2021-07-23 奥托福克斯两合公司 特种黄铜合金和特种黄铜合金产品
US11572606B2 (en) 2018-10-29 2023-02-07 Otto Fuchs Kommanditgesellschaft High-tensile brass alloy and high-tensile brass alloy product

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