EP2742161A2 - Alliage de cuivre zinc - Google Patents

Alliage de cuivre zinc

Info

Publication number
EP2742161A2
EP2742161A2 EP12735197.1A EP12735197A EP2742161A2 EP 2742161 A2 EP2742161 A2 EP 2742161A2 EP 12735197 A EP12735197 A EP 12735197A EP 2742161 A2 EP2742161 A2 EP 2742161A2
Authority
EP
European Patent Office
Prior art keywords
copper
layer
mpa
alloy
rolling
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.)
Granted
Application number
EP12735197.1A
Other languages
German (de)
English (en)
Other versions
EP2742161B1 (fr
Inventor
Hans-Achim Kuhn
Andrea KÄUFLER
Stefan Gross
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.)
Wieland Werke AG
Original Assignee
Wieland Werke AG
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 Wieland Werke AG filed Critical Wieland Werke AG
Publication of EP2742161A2 publication Critical patent/EP2742161A2/fr
Application granted granted Critical
Publication of EP2742161B1 publication Critical patent/EP2742161B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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

Definitions

  • the invention relates to a copper alloy according to the preamble of
  • Terminal contact is an optimization of the embodiment at the lowest cost.
  • Desired properties of an alloy include, for example, high electrical and thermal conductivity and high stress relaxation resistance and tensile strength.
  • copper alloys are typically used because of their generally excellent corrosion resistance, high electrical and thermal conductivity, and good bearing and wear qualities. Copper alloys are also suitable because of their good cold working or hot working properties and their good deformation behavior.
  • US Pat. No. 6,132,528 discloses copper-tin-iron-zinc alloys which have a higher zinc content of up to 35.0%.
  • the iron content is between 1, 6 and 4.0%.
  • the addition of iron has the function to achieve a grain refinement after casting.
  • the invention has for its object to further develop a copper alloy to further develop this with respect to the stress relaxation resistance and other material properties.
  • the alloy with low metal value is based on the technological properties of the bronzes CuSn4 (C51100) and CuSn6 (C51900).
  • the manufacturing process should be as simple as possible. In terms of tensile strength, values of 600 MPa and electrical conductivity should be at least 20% IACS.
  • the processed as a strip of copper alloy should be well bendable and can be used as a spring material.
  • the invention is represented by the features of claim 1.
  • the other dependent claims relate to advantageous embodiments and further developments of the invention.
  • the invention includes a copper alloy which has been subjected to a thermomechanical treatment consisting of (in% by weight):
  • Ni optionally 0.05 to 0.5%
  • finely divided iron-containing particles are contained in the alloy matrix.
  • the copper alloy according to the invention is primarily ribbon, wire or tubular material, with the main constituents copper, zinc, tin and iron.
  • the zinc content between 15.5 and 36.0% is selected in the alloy in particular according to the criterion that an easily deformable, single-phase alloy is obtained.
  • the single-phase basic structure consists of alpha phase. Also, the basic structure must be suitable to absorb the finest possible precipitates of other elements. It has been shown that the zinc content should not exceed 36.0%, as otherwise sets a less favorable phase properties in the alloy. In a preferred embodiment the zinc content of a maximum of 32.0% is not exceeded. In particular, in excess of the specified value zinc content occurs in this context unwanted brittle beta phase.
  • a higher tin content in the alloy according to the invention has an effect on the strength and on the relaxation resistance.
  • the tin content should not exceed 3.0%, as the conductivity and bendability are negatively affected.
  • Tin concentration is kept as low as possible, but at a level below 0.3%, no significant impact on alloy properties is expected.
  • Iron is responsible for the formation of precipitate particles and thus for an improvement in the relaxation properties in comparison to conventional brasses.
  • the precipitation formation can be controlled and optimized during the manufacturing process. In particular, precipitates form in this alloy during a hot rolling step
  • Hardening mechanisms are primarily supported by the element iron.
  • the iron-containing particles present in the alloy matrix are formed in the sub-micron range.
  • the other elements optionally contained in the alloy can bring about a further improvement in the properties of the alloy with regard to the process control or else have an effect on the production process in the molten phase.
  • the relaxation resistance is significantly improved compared to the conventional brass rings and is only slightly below the values customary for bronze. With respect to the relaxation resistance, therefore, the present brass alloy is in the range of commercial tin bronzes. In the alloy according to the invention special emphasis is placed on their
  • Microstructure which identifies a special combination of main textures due to the processing steps.
  • the texture is produced during the thermomechanical treatment due to different rolling processes.
  • Walzumform Institute can on the one hand cold rolling and intermediate annealing and on the other hand hot rolling processes in conjunction with other
  • the desired material characteristics are for example for the construction of spring elements of particular interest, because thereby the stiffness of the spring and its load capacity are determined. There is a narrow
  • Cubic face-centered metals usually form two different types of textures after high rolling deformation, depending on their stacking fault energy.
  • copper rolling texture which is composed of the ideal layers, the so-called brass layer and the S-layer and the copper layer.
  • alloy rolling texture is formed of low staple fault energy metallic materials, which include most copper alloys, and which consists essentially of the brass layer.
  • the particular advantage is that the resistance to stress relaxation of the alloy of the present invention is significantly better than that of tin-free and iron-free copper-zinc alloys and that the alloy simultaneously has a lower metal value than copper-tin-phosphorus alloys.
  • the Cu-Zn-Sn-Fe materials according to the invention also exhibit a more favorable softening behavior than the tin bronze used in comparable products.
  • the loss of strength at any rate decreases with the onset of recrystallization.
  • the iron-containing particles present in the alloy matrix are consistently sufficiently small in the sub-micron range that good tin-plating and processability to a plug connector is ensured.
  • the desired intermetallic phases can be formed with the copper of the alloy matrix during hot-dip galvanizing. Even with galvanic tinning with a subsequent reflow treatment, the advantageous intermetallic phases form uniformly over the entire surface.
  • the prerequisite for the uniformly tin-pliable surface is that the small particles do not undergo significant stretching in the rolling direction during mechanical forming by means of hot rolling or cold rolling in the matrix.
  • the content of tin 0.7% to 1, 5% and of iron from 0.5% to 0.7%.
  • a lower tin content within the stated limits is therefore particularly advantageous, because in this way the conductivity and the bendability of the alloy are further improved.
  • the specified iron content is selected so that particularly fine iron-containing particles form in the alloy matrix. However, these particles still have the size to significantly improve the mechanical properties.
  • the zinc content may be between 21.5% and 31.5%.
  • the desired single-phase alpha-phase alloy can be produced.
  • Such alloys are easier to form and still suitable for a fine Excretion distribution of iron-containing particles.
  • the zinc content may be between 28.5% to 31.5%.
  • Ratio of the proportions of the main textures of brass layer and copper layer are less than 1. Compared to the known brass alloys of similar composition, but without iron precipitates, this quotient shows the peculiarities of this alloy. While in comparable studies pure CuZn30 alloys have a quotient of more than 1.2, the desired mechanical properties develop in the strip material given a low ratio of the brass layer to the copper layer. The amount of stiffness and resilience of spring materials is determined.
  • the ratio of the proportions of the main textural layers of brass layer and copper layer can be between 0.4 to 0.90. In the specified range, particularly favorable mechanical properties of the alloy are formed.
  • finely divided iron-containing particles with a diameter smaller than 1 ⁇ be present at a density of at least 0.5 particles per ⁇ 2 in the alloy matrix.
  • the combination of particle size and their distribution in the alloy ultimately shape the mechanical properties.
  • Diameter smaller than 1 ⁇ is more than 99% pronounced and primarily determining the advantageous properties.
  • the middle one is more than 99% pronounced and primarily determining the advantageous properties.
  • Particle diameter of the finely divided iron-containing particles even smaller than 50 to 100 nm. If such small particles subjected to mechanical deformation by means of hot rolling or cold rolling, so they undergo no significant stretching in the rolling direction, from which then the good tin plating of
  • the mean grain size of the alloy matrix can be less than 10 ⁇ . More preferably, however, the mean grain size is at most 5 ⁇ .
  • Comparative Example 1 (CuZn23.5Sn1.0): fine-grained
  • the alloy components were melted in graphite crucible and
  • the composition of a laboratory block is Cu 75.47% -Zn 23.47% -Sn 1.06% (see Table 1). After milling at 22 mm thickness, the samples were hot rolled to 12 mm at 700-800 ° C and then milled to 10 mm.
  • the alloy was annealed at 500 ° C. for 3 hours. In this case, a yield strength of 109 MPa was achieved with a grain size of 30- 35 pm and a conductivity of 26.5% IACS. After the subsequent cold rolling at 0.33 mm and annealing at 320 ° C / 3 h, the yield strength is
  • yield strengths of 541 MPa at an A10 elongation of 19.3% and a conductivity of 25.1% IACS were obtained at 24% previous cold work.
  • the minimum bending radius minBR in relation to the strip thickness t (minBR / t vertical / parallel) in the V die is 0.4 / 1, 2.
  • the stress relaxation resistance is 92.3% after 100 ° C / 1000 h and 82.1% of the initial stress after 120X / 1000 h.
  • yield strengths were achieved by
  • the stress relaxation resistance is 90.2% after 100 ° C./1000 h and, after 120 ° C./1000 h, 79.8% of the initial stress.
  • Bending radius based on the strip thickness (minBR / t vertical / parallel) in the V-die is 0.4 / 2.8.
  • the composition corresponds to that of Comparative Example 1, the production is the same as in Comparative Example 1 to 0.30 mm cold rolling. However, unlike Comparative Example 1, the second annealing does not occur 320X / 3 h, but at 520X / 3 h.
  • the yield strength is 106 MPa at a particle size of 45 ⁇ and a conductivity of 27.9% IACS.
  • yield strengths of 378 MPa at an A10 elongation of 33.7% and a conductivity of 26.9% IACS were achieved at 24% previous cold work.
  • the minimum bending radius in relation to the strip thickness (minBR / t vertical / parallel) in the V-die is 2.4 / 1.6.
  • the stress relaxation resistance is 94.7% after 100 ° C / 1000 h and 93.0% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 503 MPa were achieved with an A10 elongation of 10.2%, a conductivity of 26.5% IACS and minBR / t perpendicular / parallel of 3.5 / 4.0.
  • the stress relaxation resistance is 96.1% after 100 ° C / 1000 h and 91.2% of the initial stress after 120 ° C / 1000 h.
  • Fine grain production (541 MPa) can be achieved with 24% speed. At the same time, however, the A10 strains in fine grain production are more favorable at 19.3% compared to 10.2% for coarse grain production. Similarly cheap are the
  • the alloy components were melted in a graphite crucible and then laboratory blocks were cast in steel molds by the Tammann method.
  • the composition of the laboratory block is Cu74.95% - Zn23.40% - Sn1, 06% FeO, 59%, see Table 1.
  • the samples were hot rolled to 12 mm at 700-800 ° C and then milled to 10 mm.
  • the microstructure shows smaller, ⁇ 1 pm particles after hot rolling.
  • the ⁇ 1 pm particles were identified as Fe-containing by EDX.
  • the alloy was annealed at 500 ° C. for 3 hours. Here was a
  • yield strengths of 686 MPa were obtained with an A10 elongation of 6.5%, a conductivity of 22.8% IACS, and a minimum / average of 4/10 RPM / t.
  • yield strengths of 632 MPa at an A10 elongation of 9.4% and a conductivity of 23.2% IACS were achieved at 24% previous cold work.
  • the minimum bending radius in relation to the strip thickness (minBR / t vertical / parallel) in the V-die is 3.2 / 4.8.
  • the stress relaxation resistance is 90.8% after 100 ° C / 1000 h and 80.1% of the initial stress after 120 ° C / 1000 h.
  • yield strengths were achieved by
  • the Fe-containing fine-grained variant after the final annealing at 300 ° C / 5 min by 82 MPa (24% roll) or 64 MPa (40% rolling) higher yield strength.
  • 620 MPa can be achieved with different production.
  • CuZn23.5Sn1, 0Fe0.6 achieves a yield strength of 623 MPa after 24% rolling and final annealing at 300 ° C / 5 min and CuZn23.5Sn1, 0 a yield strength of 622 MPa after 40% rolling and final annealing at 300 ° C / 5 minute
  • the A10 strains in the Fe-containing variant are higher at 10.5% compared to 4.6% for CuZn23.5Sn1.0.
  • the stress relaxation resistance of both variants is similar.
  • Average particle density is 1, 2 / ⁇ 2 .
  • the alloy components were melted in graphite crucible and
  • the composition of the laboratory block is Cu74.77% -Zn23.45% -Sn1, 04% FeO, 56% -P0.19%, see Table 1. After milling at 22 mm thickness, the samples were at 700-800 ° C at 12 mm
  • the microstructure shows smaller, ⁇ 1 pm particles. In addition, some coarser,> 1 pm particles are present in the matrix.
  • the particles were identified by FeX as FeP-containing.
  • the alloy was annealed at 500 ° C. for 3 hours.
  • a yield strength of 293 MPa was achieved with a particle size of 10 pm and a conductivity of 26.6% IACS.
  • the yield strength is 393 MPa with a grain size of 3-4 pm and a conductivity of
  • yield strengths of 710 MPa were achieved with an A10 elongation of 3.11%, a conductivity of 23.7% IACS, and a minimum / min of 3.5 / 1 1.
  • the stress relaxation resistance is 100 ° C / 1000 h 90.1% and after 120 ° C / 1000 h 79.6% of the initial stress.
  • Bending radius in relation to the strip thickness (minBR / t vertical / parallel) in the V-die is 2/6.
  • the stress relaxation resistance is 93.5% after 100 ° C / 1000 h and 81.0% of the initial stress after 120 ° C / 1000 h. at
  • the FeP-containing fine-grained variant after the final annealing at 300 ° C / 5 min by 92 MPa (24% roll) or 88 MPa (40% rolling) higher yield strength.
  • Example 5 (CuZn23.5Sn1.0 Fe0.6P0.2): - coarse-grained
  • Example 4 The composition corresponds to that of Example 4, the production is the same as in Example 4 to cold rolling at 0.33 mm. However, unlike Example 4, the second annealing does not take place at 370 ° C./3 h but at 520 ° C./3 h. This results in a yield strength of 212 MPa with a grain size of 10-25pm and a conductivity of 26.7% IACS. After rolling at final caliper and tempering at 300 ° C / 5 minutes, yield strengths of 534 MPa at an A10 elongation of 23.1% and a conductivity of 24.5% IACS were achieved at 24% previous cold work. The minimum bending radius in relation to the strip thickness (minBR / t vertical / parallel) in the V-die is 2.4 / 3.2. The stress relaxation resistance is after
  • Example 4 shows after the second annealing 180 MPa higher yield strength of the fine-grained structure compared to the coarse-grained structure.
  • the subsequent cold working reduces this difference to 60 MPa for the 24% deformed and 40 MPa for the 40% deformed sample.
  • the difference in the yield strength between coarse grain and fine grain is 100 MPa
  • the alloy components were melted in graphite crucible and Subsequently, using the Tammann method, laboratory blocks were placed in
  • the composition of the laboratory block is Cu68.26% -Zn30.16% -Sn1, 03% FeO, 55%, see Table 1.
  • the samples were hot rolled at 1200 mm at 700-800 ° C and then milled to 10 mm.
  • the microstructure shows after hot rolling smaller, ⁇ 1 ⁇ particles.
  • the ⁇ 1 ⁇ particles were identified by means of EDX as Fe-containing.
  • the alloy was annealed at 500 ° C. for 3 hours. In this case, a yield strength of 339 MPa was achieved with a grain size of 5 pm and a conductivity of 23.1% IACS.
  • strip casting is also considered in this context.
  • a part was annealed at 520 ° C / 3 h. In this case, a yield strength of 340 MPa at a grain size of 3- 4 pm and a conductivity of 23% IACS was obtained.
  • the minimum bending radius in relation to the strip thickness (minBR / t vertical / parallel) in the V-die is 0/0.
  • the stress relaxation resistance is 88% after 100 ° C / 1000 h and 76.7% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 550 MPa were achieved with an A10 elongation of 21.3%, a conductivity of 21.9% IACS and minBR / t perpendicular / parallel of 0.9 / 0.4.
  • the stress relaxation resistance is 88.3% after 100 ° C / 1000 h and 75.6% of the initial stress after 120X / 1000 h.
  • yield strengths of 505 MPa were achieved at 12% previous cold work, with an A10 elongation of 18.5% and a conductivity of 22.6% IACS.
  • the minimum bending radius in relation to the strip thickness (minBR / t vertical / parallel) in the V-die is 0/0.
  • the stress relaxation resistance is 87.3% after 100 ° C / 1000 h and 76.2% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 564 MPa were achieved with an A10 elongation of 19.9%, a conductivity of 22.2% IACS and minBR / t perpendicular / parallel of 0.9 / 0.6.
  • the stress relaxation resistance is 88.4% after 100X / 1000 h and 77.6% of the initial stress after 120X / 1000 h.
  • yield strengths of 704 MPa were achieved with an A10 elongation of 2.9%, a conductivity of 21.5% IACS and minBR / t perpendicular / parallel of 2 / 6.4.
  • the stress relaxation resistance is 77.5% after 100 ° C / 1000 h and 61.8% after 120X / 1000 h
  • yield strengths of 765 MPa were achieved with an A10 elongation of 1.5%, a conductivity of 21.6% IACS, and a minimum / average of 4.0 / 9.2 minBR / t.
  • the stress relaxation resistance is 76.8% after 100 ° C / 1000 h and 59.9% of the initial stress after 120 ° C / 1000 h.
  • the microstructure of a flat section from the final state was represented by an AsB detector on a scanning electron microscope. At an image magnification of 5000: 1 and 10000: 1, the number of particles per 1 pm 2 image detail was counted.
  • the diameter of at least 90% of the iron particles is less than 200 nm. With less than 10%, iron particles with a diameter of 200 nm to 1 pm exist.
  • the average particle density is 0.9 particles per ⁇ m 2 .
  • Comparative alloy CuZn30 a value of 1.38 at a rolling degree of 47% at the final forming.
  • S / R position the respectively originating from the rolling texture or recrystallization texture are in the Euler space
  • the strips were hot-tinned with a layer thickness of 2-3 pm.
  • the tinning result is poor, pores and streaks occur.
  • the line inhomogeneities on the tinned surface go back to the elongated Fe lines, where no Cu is present to form an intermetallic phase.
  • the alloy components were melted in graphite crucible and
  • the composition of the laboratory block is Cu 73.82% Zn 23.19% -Sn 1, 04% Fe 1.95%, see Table 1. After milling at 22 mm thickness, the samples were hot rolled at 1200 mm at 700-800 ° C. The microstructure shows similar to CuZn23,5Sn1, 0Fe0,6 smaller, under 1 ⁇ particles.
  • the alloy was annealed at 500 ° C / 3h. In this case, a yield strength of 362 MPa was achieved with a grain size of 2- 3 ⁇ and a conductivity of 24.2% IACS. After the subsequent
  • the yield strength is 386 MPa at a particle size of 2 ⁇ and a conductivity of 24.0% IACS.
  • yield strengths of 642 MPa at an A10 elongation of 8.4% and a conductivity of 23.1% IACS were achieved at 24% previous cold work.
  • the minimum bending radius in relation to the strip thickness (minBR / t vertical / parallel) in the V-die is 2/5.
  • yield strengths of 712 MPa were achieved with an A10 elongation of 5.0%, a conductivity of 22.4% IACS, and minBR / t perpendicular / parallel of 2.5 / 9.
  • DIN EN 60068-2-20 performed on the samples tempered at 300 ° C / 5min. The samples were pickled and brushed. The solder bath was made of Sn60Pb40 at 235 ° C. The test was carried out at a dipping speed of 25 mm / sec and a residence time of 5 sec using as the flux pure rosin at 260 g / l. During the subsequent visual inspection, the samples were rated as poor due to strong dewetting.
  • the reason for the poor tininess of the samples are the elongated Fe-containing lines. At this Cu is not present for the formation of an intermetallic phase and there are undesirable inhomogeneities on the tinned ribbons.
  • Table 2 Properties after final cold rolling to final thickness and annealing 250 ° C / 3h
  • Table 3 Properties after final cold rolling to final thickness and annealing 300 ° C / 5min

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Conductive Materials (AREA)
  • Contacts (AREA)

Abstract

L'invention concerne un alliage de cuivre ayant été soumis à un traitement thermomécanique, composé de (en % en poids): 15,5 à 36,0 % Zn, 0,3 à 3,0 % Sn, 0,1 à 1,5 % Fe, sélectivement 0,001 à 0,4 % P, sélectivement 0,01 à 0,1 % AI, sélectivement 0,01 à 0,3 % Ag, Mg, Zr, In, Co, Cr, Ti, Mn, sélectivement 0,05 à 0,5 % Ni, reste de cuivre et impuretés inévitables. La microstructure de l'alliage est caractérisée en ce que les fractions des couches de texture principales sont constituées d'au moins 10 % en vol. de texture cuivre, au moins 10 % en vol. de texture S/R, au moins 5 % en vol. de texture laiton, au moins 2 % en vol. de texture Goss, au moins 2 % en vol. de texture cubique 22RD, au moins 0,5 % en vol. de texture cubique, des particules ferriques finement dispersées étant contenues dans la matrice de l'alliage.
EP12735197.1A 2011-08-13 2012-06-15 Alliage de cuivre zinc Active EP2742161B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102011110588 2011-08-13
PCT/EP2012/002523 WO2013023717A2 (fr) 2011-08-13 2012-06-15 Alliage de cuivre

Publications (2)

Publication Number Publication Date
EP2742161A2 true EP2742161A2 (fr) 2014-06-18
EP2742161B1 EP2742161B1 (fr) 2016-12-07

Family

ID=46513683

Family Applications (1)

Application Number Title Priority Date Filing Date
EP12735197.1A Active EP2742161B1 (fr) 2011-08-13 2012-06-15 Alliage de cuivre zinc

Country Status (9)

Country Link
US (1) US9493858B2 (fr)
EP (1) EP2742161B1 (fr)
JP (1) JP2014527578A (fr)
KR (1) KR20140050003A (fr)
CN (1) CN103732769B (fr)
BR (1) BR112014003377A2 (fr)
MX (1) MX2014000570A (fr)
TW (1) TWI591192B (fr)
WO (1) WO2013023717A2 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2759612A4 (fr) * 2011-09-20 2015-06-24 Mitsubishi Shindo Kk Feuille d'alliage de cuivre et procédé de production de feuille d'alliage de cuivre

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102012002450A1 (de) * 2011-08-13 2013-02-14 Wieland-Werke Ag Verwendung einer Kupferlegierung
CN105579600B (zh) * 2013-09-26 2019-08-30 三菱伸铜株式会社 铜合金及铜合金板
CN104342578B (zh) * 2014-10-21 2016-08-24 大丰市南亚阀门有限公司 一种用于阀门铸造的青铜合金材料及其处理工艺
CN106756222A (zh) * 2016-12-20 2017-05-31 薛亚红 一种铜锌合金材料
CN109112351B (zh) * 2018-08-27 2020-12-11 山东光韵智能科技有限公司 一种高弹性模量的黄铜合金材料及其制备方法
MX2019000947A (es) * 2019-01-22 2020-07-23 Nac De Cobre S A De C V Aleacion cobre-zinc libre de plomo y resistente al ambiente marino.
DE102021103686A1 (de) 2021-02-17 2022-08-18 Diehl Metall Stiftung & Co. Kg Messinglegierung
CN113073229B (zh) 2021-03-25 2021-12-07 上海五星铜业股份有限公司 一种锡黄铜合金及其制备方法

Family Cites Families (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3816109A (en) 1972-07-03 1974-06-11 Olin Corp Copper base alloy
US4047978A (en) 1975-04-17 1977-09-13 Olin Corporation Processing copper base alloys
US4259124A (en) 1978-06-28 1981-03-31 Olin Corporation Modified brass alloys with improved stress relaxation resistance
JPS6326320A (ja) 1986-07-18 1988-02-03 Nippon Mining Co Ltd 高力導電銅合金
JPH01165734A (ja) 1987-09-21 1989-06-29 Nippon Mining Co Ltd 圧電振動子ケース用材料
US20010001400A1 (en) * 1997-04-18 2001-05-24 Dennis R. Brauer Et Al Grain refined tin brass
US5853505A (en) 1997-04-18 1998-12-29 Olin Corporation Iron modified tin brass
US6132528A (en) 1997-04-18 2000-10-17 Olin Corporation Iron modified tin brass
US5893953A (en) * 1997-09-16 1999-04-13 Waterbury Rolling Mills, Inc. Copper alloy and process for obtaining same
JP4294196B2 (ja) * 2000-04-14 2009-07-08 Ｄｏｗａメタルテック株式会社 コネクタ用銅合金およびその製造法
US6949150B2 (en) 2000-04-14 2005-09-27 Dowa Mining Co., Ltd. Connector copper alloys and a process for producing the same
US6264764B1 (en) 2000-05-09 2001-07-24 Outokumpu Oyj Copper alloy and process for making same
CN1177946C (zh) * 2001-09-07 2004-12-01 同和矿业株式会社 连接器用铜合金及其制造方法
JP2005060773A (ja) * 2003-08-12 2005-03-10 Mitsui Mining & Smelting Co Ltd 特殊黄銅及びその特殊黄銅の高力化方法
JP4584692B2 (ja) 2004-11-30 2010-11-24 株式会社神戸製鋼所 曲げ加工性に優れた高強度銅合金板およびその製造方法
EP2045344B1 (fr) * 2006-07-21 2012-05-23 Kabushiki Kaisha Kobe Seiko Sho Procede de fabrication de tôles en alliage de cuivre pour pièces électriques et électroniques
JP5191725B2 (ja) * 2007-08-13 2013-05-08 Ｄｏｗａメタルテック株式会社 Ｃｕ−Ｚｎ−Ｓｎ系銅合金板材およびその製造法並びにコネクタ
WO2011019042A1 (fr) 2009-08-10 2011-02-17 古河電気工業株式会社 Matériau d’alliage de cuivre pour composants électriques/électroniques
DE102012002450A1 (de) * 2011-08-13 2013-02-14 Wieland-Werke Ag Verwendung einer Kupferlegierung

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2759612A4 (fr) * 2011-09-20 2015-06-24 Mitsubishi Shindo Kk Feuille d'alliage de cuivre et procédé de production de feuille d'alliage de cuivre

Also Published As

Publication number Publication date
CN103732769A (zh) 2014-04-16
TW201307585A (zh) 2013-02-16
WO2013023717A2 (fr) 2013-02-21
KR20140050003A (ko) 2014-04-28
EP2742161B1 (fr) 2016-12-07
CN103732769B (zh) 2016-08-17
TWI591192B (zh) 2017-07-11
US20140377127A9 (en) 2014-12-25
MX2014000570A (es) 2014-04-30
BR112014003377A2 (pt) 2017-03-01
US9493858B2 (en) 2016-11-15
US20140161661A1 (en) 2014-06-12
WO2013023717A3 (fr) 2013-06-20
JP2014527578A (ja) 2014-10-16

Similar Documents

Publication Publication Date Title
EP2742161B1 (fr) Alliage de cuivre zinc
DE112005001197B4 (de) Verfahren zum Herstellen eines Werkstückes aus einer Kupferlegierung
DE112009000731B4 (de) Cu-Ni-Si-Co-Cr-Systemlegierung für elektronische Materialien
EP2341257B1 (fr) Couche de glissement
DE3520407C2 (de) Verfahren zur thermomechanischen Behandlung von kobalthaltigen Kupfer-Beryllium-Legierungen
EP3225707B1 (fr) Composant pour des canalisations d'eau ou de gaz acheminant des milieux comprenant un alliage de cuivre
EP2013371A2 (fr) Alliage de cuivre multi-matière et son utilisation
EP2209621B1 (fr) Procédé de production d'un élément de palier lisse présentant une couche de glissement contenant du bismuth, et élément de palier lisse
DE2720460C2 (de) Verfahren zur Herstellung von Kupfer-Nickel-Zinn-Legierungen mit optimaler Kombination von Festigkeit und Duktilität
EP3377663A1 (fr) Alliage de cuivre, nickel et zinc et son utilisation
DE102015212937A1 (de) Messinglegierung
EP3272888B1 (fr) Matière à base d'alliage de zinc/cuivre, procédé de fabrication d'une telle matière et élément coulissant constitué d'une telle matière
EP3960890A1 (fr) Alliage palladium-cuivre-argent-ruthénium
KR20010093083A (ko) 구리 합금
WO2012163774A1 (fr) Alliage d'aluminium très conducteur pour produits électroconducteurs
EP3252179B1 (fr) Alliage de cuivre comprenant aluminium et nickel, son utilisation et procédé de sa production
EP1273671B1 (fr) Alliage cuivre-zinc résistant à la dezincification et son procédé de fabrication
DE69814657T2 (de) Legierung auf kupferbasis, gekennzeichnet durch ausscheidungshärtung und durch härtung im festen zustand
EP0521319A1 (fr) Alliage cuivre-nickel-étain, procédé de traitement de cet alliage ainsi que son application
DE60120697T2 (de) Kupferlegierung mit zink, zinn und eisen zur elektrischen verbindung und verfahren zur herstellung der legierung
EP3366793B1 (fr) Élément coulissant en alliage de cuivre
EP2823077B1 (fr) Alliage de cuivre-nickel-zinc contenant du silicium
EP3075870B1 (fr) Alliage cuivre-zinc, matiere en bande en cet alliage, procede de fabrication d'un semi-produit a partir de cet alliage et element coulissant en cet alliage
DE202017103901U1 (de) Sondermessinglegierung sowie Sondermessinglegierungsprodukt
DE102005023307A1 (de) Gleitlagerverbundwerkstoff, Verwendung und Herstellungsverfahren

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

17P Request for examination filed

Effective date: 20131214

AK Designated contracting states

Kind code of ref document: A2

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

DAX Request for extension of the european patent (deleted)
17Q First examination report despatched

Effective date: 20150310

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20160721

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: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

Ref country code: AT

Ref legal event code: REF

Ref document number: 851781

Country of ref document: AT

Kind code of ref document: T

Effective date: 20161215

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: 502012008980

Country of ref document: DE

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: 20161207

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20161207

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

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: 20161207

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: 20170307

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: 20161207

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 6

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

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: 20161207

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: 20161207

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: 20161207

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: 20161207

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

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: 20170407

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: 20161207

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: 20161207

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: 20161207

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: 20161207

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: 20170407

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: 20161207

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: 20161207

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502012008980

Country of ref document: DE

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: 20170908

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: 20161207

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: 20161207

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: 20161207

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: 20170615

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: LI

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

Effective date: 20170630

Ref country code: LU

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

Effective date: 20170615

Ref country code: CH

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

Effective date: 20170630

Ref country code: IE

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

Effective date: 20170615

Ref country code: GB

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

Effective date: 20170615

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 7

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20170630

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 851781

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170615

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: 20170630

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: 20161207

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: 20170615

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

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: 20120615

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 NON-PAYMENT OF DUE FEES

Effective date: 20161207

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20161207

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: 20161207

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: 20161207

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20230510

Year of fee payment: 12

Ref country code: FR

Payment date: 20230411

Year of fee payment: 12

Ref country code: DE

Payment date: 20230630

Year of fee payment: 12

Ref country code: BG

Payment date: 20230420

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GR

Payment date: 20230511

Year of fee payment: 12

Ref country code: FI

Payment date: 20230615

Year of fee payment: 12