EP2742161B1 - Alliage de cuivre zinc - Google Patents

Alliage de cuivre zinc Download PDF

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Publication number
EP2742161B1
EP2742161B1 EP12735197.1A EP12735197A EP2742161B1 EP 2742161 B1 EP2742161 B1 EP 2742161B1 EP 12735197 A EP12735197 A EP 12735197A EP 2742161 B1 EP2742161 B1 EP 2742161B1
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mpa
copper
layer
alloy
rolling
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EP2742161A2 (fr
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Hans-Achim Kuhn
Andrea KÄUFLER
Stefan Gross
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Wieland Werke AG
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Wieland Werke AG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc as the next major constituent

Definitions

  • the invention relates to a copper alloy according to the preamble of claim 1.
  • Electronic components including terminal contacts, form the basis of information technology.
  • One of the most important considerations with any terminal contact is optimization of the embodiment at the lowest cost.
  • Desired properties of an alloy are, for example, a high electrical and thermal conductivity and a 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.
  • EP 1 290 234 B1 is known a copper alloy, which is already a cheaper alternative to conventional copper alloys with high electrical conductivity, high tensile strength and high Umformfestmaschine identifies.
  • the alloy consists of 13 to 15% zinc, 0.7 to 0.9% tin, 0.7 to 0.9% iron and a balance of copper. Due to the zinc, with a currently relatively low metal value on the market, costs can be saved in the base material.
  • 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 as Band processed copper alloy can be easily bendable and used as a spring material.
  • the invention relates to a copper alloy according to claim 1.
  • 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.
  • the tin concentration should be kept as low as possible, but at a level below 0.3%, no significant impact on the alloy properties is expected.
  • Iron is responsible for the formation of precipitate particles and thus for an improvement of 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 followed by selective cooling.
  • the hardening mechanisms effective in the alloy 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 in the production process in the molten phase.
  • Another key feature of tapes is the bendability, which improves especially at higher zinc contents. The investigation results show that both for low as well as for high zinc contents, approximately equal residual stresses occur in the alloy. It is essential that with the alloy according to the invention 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
  • the alloy according to the invention In the case of the alloy according to the invention, special emphasis is placed on its microstructure, which due to the processing steps identifies a special combination of main texturizing layers.
  • the texture is produced during the thermomechanical treatment due to different rolling processes.
  • Walzumformungen can include on the one hand cold rolling and intermediate annealing and on the other hand hot rolling processes in conjunction with other cold rolling and intermediate annealing.
  • the formation of the alloy according to the invention with the stated main textural layers must be technically coordinated in this case exactly to the formation of finely divided iron-containing particles in conjunction with the respective rolling degrees. Only then can the optimum of the expected property combinations be achieved.
  • 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.
  • 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.
  • the second limit type is the so-called alloy rolling texture, which 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.
  • An important prerequisite of the uniformly tin-pliable surface is that the small particles undergo no significant stretching in the rolling direction during mechanical forming by means of hot rolling or cold rolling in the matrix. In contrast to the higher iron fractions outside the solution according to the invention, there is no occurrence of a line-like spreading of larger iron particles disturbing the tin-plating.
  • the content of tin may be 0.7% to 1.5%.
  • the iron content is 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% to 31.5%.
  • the desired single-phase alpha-phase alloy can be produced.
  • Such alloys are easier to form and still suitable for a fine
  • the zinc content may advantageously be between 28.5% to 31.5%.
  • the ratio of the proportions of the main textural layers of brass layer and copper layer can be 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 in the strip material are formed with 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 distributed iron-containing particles with a diameter smaller than 1 ⁇ m are present at a density of at least 0.5 particles per ⁇ m 2 in the alloy matrix.
  • the combination of particle size and their distribution in the alloy ultimately shape the mechanical properties.
  • the described fine distribution with a diameter smaller than 1 ⁇ m is over 99% pronounced and primarily determining the advantageous properties.
  • the average particle diameter of the finely divided iron-containing particles is even less than 50 to 100 nm. If such small particles of mechanical deformation by means of hot rolling or cold rolling undergo no significant stretching in the rolling direction, which then results in the good tin plating of the surface.
  • the mean grain size of the alloy matrix can be less than 10 ⁇ m. More preferably, however, the mean grain size is at most 5 microns.
  • 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 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 / 3 h.
  • a yield strength of 109 MPa was achieved with a particle size of 30-35 microns and a conductivity of 26.5% IACS.
  • the yield strength is 311 MPa with a grain size of 2-3 microns and a conductivity of 27.3% IACS.
  • yield strengths of 622 MPa were achieved with an A10 elongation of 4.6%, a conductivity of 24.8% IACS and minBR / t perpendicular / parallel of 1.5 / 7.5.
  • the stress relaxation resistance is 90.2% after 100 ° C / 1000 h and 79.8% of the initial stress after 120 ° C / 1000 h.
  • 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 320 ° C / 3 h, but at 520 ° C / 3 h.
  • the yield strength is 106 MPa with a grain size of 45 microns 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.
  • yield strengths of 402 MPa at an A10 elongation of 29.5% and a conductivity of 27.3% 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 2.8 / 2.8.
  • the stress relaxation resistance is 98.7% after 100 ° C / 1000 h and 93.5% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 517 MPa were achieved with an A10 elongation of 8.3%, a conductivity of 26.4% IACS and minBR / t perpendicular / parallel of 4.5 / 6.0.
  • the stress relaxation resistance is 96.8% after 100 ° C / 1000 h and 91.9% of the initial stress after 120 ° C / 1000h.
  • Comparative Example 1 shows, after the second annealing, a yield strength of the fine-grained microstructure which is 200 MPa higher than that of the coarse-grained microstructure.
  • the subsequent cold deformation reduces this difference to as many as 160 MPa at 24% deformed and 110 MPa for the 40% deformed sample.
  • a comparable yield strength of about 520 MPa can be achieved both from coarse grain production (503 MPa) with 40% throughput and from fine grain production (541 MPa) with 24% throughput.
  • the A10 strains in fine grain production are more favorable at 19.3% compared to 10.2% for coarse grain production.
  • 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% Fe0.59%, see Table 1.
  • the samples were hot rolled at 1200 mm at 700-800 ° C and then milled to 10 mm.
  • the microstructure shows smaller, ⁇ 1 ⁇ m particles after hot rolling.
  • the ⁇ 1 ⁇ m particles were identified as Fe-containing by EDX.
  • the alloy was annealed at 500 ° C / 3 h.
  • a yield strength of 304 MPa was achieved with a grain size of 5-15 microns and a conductivity of 24.2% IACS.
  • the yield strength is 339 MPa with a grain size of 3-4 microns and a conductivity of 24.3% IACS.
  • yield strengths of 623 MPa at an A10 elongation of 10.5% and a conductivity of 22.9% 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 / 3.6.
  • the stress relaxation resistance is 90.7% after 100 ° C / 1000 h and 79.2% of the initial stress after 120 ° C / 1000 h.
  • 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 of 713 MPa were achieved with an A10 elongation of 2.8%, a conductivity of 23.0% IACS, and a minimum / average RMS / temp of 5/10.
  • the Fe-containing fine-grained variant after the final annealing at 300 ° C / 5 min by 82 MPa (24% rolling) or 64 MPa (40% rolling) higher yield strength.
  • 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 Cu74.77% -Zn23.45% -Sn1.04% Fe0.56% -P0.19%, see Table 1.
  • the samples were at 700-800 ° C hot-rolled to 12 mm and then milled to 10 mm.
  • the microstructure shows smaller, ⁇ 1 ⁇ m particles. In addition, some coarser,> 1 micron particles are present in the matrix.
  • the particles were identified by FeX as FeP-containing. After cold rolling at 1.8 mm, the alloy was annealed at 500 ° C / 3 h.
  • a yield strength of 293 MPa was achieved with a particle size of 10 microns and a conductivity of 26.6% IACS.
  • the yield strength is 393 MPa with a grain size of 3-4 microns and a conductivity of 26.7% IACS.
  • yield strengths of 633 MPa at an A10 elongation of 11.6% and a conductivity of 24.2% 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 2 / 4.8.
  • the stress relaxation resistance is 91.2% after 100 ° C / 1000 h and 81.3% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 710 MPa were achieved with an A10 elongation of 3.1%, a conductivity of 23.7% IACS and minBR / t perpendicular / parallel of 3.5 / 11.
  • the stress relaxation resistance is 90.1% after 100 ° C / 1000 h and 79.6% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 641 MPa at an A10 elongation of 9.5% and a conductivity of 23.6% 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 2/6.
  • the stress relaxation resistance is 93.5% after 100 ° C / 1000 h and 81.0% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 723 MPa were achieved with an A10 elongation of 1.4%, a conductivity of 23.8% IACS and minBR / t perpendicular / parallel of 4.5 / 10.5.
  • the stress relaxation resistance is 92.9% after 100 ° C / 1000 h and 78.4% of the initial stress after 120 ° C / 1000 h.
  • 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.
  • the A10 strains in the FeP-containing variant are higher at 11.6% compared to 4.6% for CuZn23.5Sn1.0.
  • the stress relaxation resistance of both variants is similar.
  • 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 10-25 ⁇ m and a conductivity of 26.7% IACS.
  • yield strengths of 534 MPa at 23% A10 elongation and 24.5% IACS conductivity 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 95.8% after 100 ° C / 1000 h and 90.9% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 634 MPa were achieved with an A10 elongation of 7.8%, a conductivity of 24.1% IACS and minBR / t perpendicular / parallel of 3.5 / 8.5.
  • the stress relaxation resistance is 93.9% after 100 ° C / 1000 h and 85.2% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 544 MPa at an A10 elongation of 17.8% and a conductivity of 24.7% 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 / 4.0.
  • the stress relaxation resistance is 95.1% after 100 ° C / 1000 h and 90.1% of the initial stress after 120 ° C / 1000 h.
  • yield strengths of 642 MPa were achieved with an A10 elongation of 4.3%, a conductivity of 24.0% IACS, and minBR / t perpendicular / parallel of 4.5 / 8.5.
  • the stress relaxation resistance is 95.0% after 100 ° C / 1000 h and 86.4% of the initial stress after 120 ° C / 1000 h.
  • 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 (degree of deformation 24%) and 75 MPa (degree of deformation 40%).
  • the alloy components were melted in graphite crucible and Subsequently, laboratory blocks were poured into steel molds by the Tammann method.
  • the composition of the laboratory block is Cu68.26% -Zn30.16% -Sn1.03% Fe0.55%, 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 ⁇ m particles after hot rolling.
  • the ⁇ 1 ⁇ m particles were identified as Fe-containing by EDX.
  • the alloy was annealed at 500 ° C / 3 h. In this case, a yield strength of 339 MPa was achieved with a grain size of 5 microns and a conductivity of 23.1% 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 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 120 ° C / 1000 h.
  • yield strengths of 505 MPa at an A10 elongation of 18.5% and a conductivity of 22.6% IACS were achieved at 12% previous cold work.
  • 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 100 ° C / 1000 h and 77.6% of the initial stress after 120 ° C / 1000 h.
  • the minimum bending radius in relation to the strip thickness (minBR / t vertical / parallel) in the V-die is 1.6 / 6.4.
  • the stress relaxation resistance is 77.9% after 100 ° C / 1000h and 61.0% of the initial stress after 120 ° C / 1000h.
  • 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% 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 ⁇ m 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 ⁇ m exist.
  • the average particle density is 0.9 particles per ⁇ m 2 .
  • the main textural types were determined by X-ray diffractometry on 18%, 24% and 40% cold-formed and 300 ° C / 5 min annealed sheet for all samples from Table 3.
  • the intensity distributions of the skeleton lines in the Euler space and the orientation distribution functions were used for this purpose evaluated.
  • the percentage of copper layer, S / R layer, brass layer, Goss layer, 22RD cube layer, and cube layer as respective main texture layers are shown in Table 4.
  • the ratio of the volume of the brass layer to the copper layer is in all cases less than 1.
  • the ratio of the volume of the brass layer to the copper layer in the case of the comparative alloy CuZn30 is 1.38 at a rolling rate of 47%. during final forming.
  • the layers originating from the rolling texture or recrystallization texture are named in the same Euler space.
  • the strips were fire-tinned with a layer thickness of 2-3 microns.
  • 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 a graphite crucible and then laboratory blocks were cast in steel molds by the Tammann method.
  • the composition of the laboratory block is Cu 73.82% Zn 23.19% -Sn 1.04% Fe 1.95%, see Table 1.
  • the samples were hot rolled at 1200 mm at 700-800 ° C. Similar to CuZn23.5Sn1.0 Fe 0.6, the microstructure shows smaller, less than 1 ⁇ m particles.
  • CuZn23.5 Sn1,0 Fe2,0 coarse, about 5 microns sized particles are present. Both the 1 ⁇ m and the 5 ⁇ m particles were identified as Fe-containing by EDX.
  • 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 microns and a conductivity of 24.2% IACS. After the subsequent cold rolling at 0.33 mm and annealing at 520 ° C / 3h, the yield strength is 386 MPa with a grain size of 2 microns and a conductivity of 24.0% IACS.
  • 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.
  • a lift-immersion solder test according to DIN EN 60068-2-20 was carried out on the samples tempered at 300 ° C./5 min. 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.

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Claims (7)

  1. Alliage de cuivre, qui a été soumis à un traitement thermomécanique, constitué par (en % en poids) :
    15,5 à 36,0 % Zn,
    0,3 à 3,0 % Sn,
    0,5 à 0,7 % Fe,
    au choix, en outre 0,001 à 0,4 % P,
    au choix, en outre 0,01 à 0,1 % Al,
    au choix, en outre respectivement 0,01 à 0,3 % Ag, Mg,
    Zr, In, Co, Cr, Ti, Mn,
    au choix, en outre 0,05 à 0,5 % Ni,
    reste cuivre et impuretés inévitables, la microstructure de l'alliage présentant les parts suivantes des couches de texture principales :
    au moins 10 % en volume de la couche de cuivre,
    au moins 10 % en volume de la couche S/R,
    au moins 5 % en volume de la couche de laiton,
    au moins 2 % en volume de la couche de texture de Goss,
    au moins 2 % en volume de la couche cubique 22RD,
    au moins 0,5 % en volume de la couche cubique,
    les parts des couches de texture principales étant déterminées par diffractométrie aux rayons X, en réalisant le traitement de la répartition d'intensité des lignes de squelette dans l'espace d'Euler, et de la fonction de distribution des orientations,
    caractérisé
    - en ce que des particules à teneur en fer finement réparties sont contenues dans la matrice de l'alliage, et
    - en ce que les particules à teneur en fer finement réparties sont présentes dans la matrice de l'alliage avec un diamètre inférieur à 1 µm et une densité d'au moins 0,5 particules par µm2.
  2. Alliage de cuivre selon la revendication 1, caractérisé par une teneur de 0,7 à 1,5 % Sn.
  3. Alliage de cuivre selon la revendication 1 ou la revendication 2, caractérisé par une teneur de 21,5 à 31,5 % Zn.
  4. Alliage de cuivre selon l'une des revendications 1 à 3, caractérisé par une teneur de 28,5 à 31,5 % Zn.
  5. Alliage de cuivre selon l'une des revendications 1 à 4, caractérisé en ce que le rapport des parts des couches de texture principales de la couche de laiton et de la couche de cuivre est inférieur à 1.
  6. Alliage de cuivre selon la revendication 5, caractérisé en ce que le rapport des parts des couches de texture principales de la couche de laiton et de la couche de cuivre se situe entre 0,4 et 0,90.
  7. Alliage de cuivre selon l'une des revendications 1 à 6, caractérisé en ce que la grosseur de grains moyenne de la matrice de l'alliage est inférieure à 10 µm.
EP12735197.1A 2011-08-13 2012-06-15 Alliage de cuivre zinc Active EP2742161B1 (fr)

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DE102011110588 2011-08-13
PCT/EP2012/002523 WO2013023717A2 (fr) 2011-08-13 2012-06-15 Alliage de cuivre

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

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Families Citing this family (9)

* 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
JP5386655B2 (ja) * 2011-09-20 2014-01-15 三菱伸銅株式会社 銅合金板及び銅合金板の製造方法
EP3050982B1 (fr) * 2013-09-26 2019-03-20 Mitsubishi Shindoh Co., Ltd. Alliage de cuivre et feuille d'alliage de cuivre
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
US6132528A (en) * 1997-04-18 2000-10-17 Olin Corporation Iron modified tin brass
US5853505A (en) 1997-04-18 1998-12-29 Olin Corporation Iron modified tin brass
US20010001400A1 (en) * 1997-04-18 2001-05-24 Dennis R. Brauer Et Al Grain refined tin brass
US5893953A (en) * 1997-09-16 1999-04-13 Waterbury Rolling Mills, Inc. Copper alloy and process for obtaining same
US6949150B2 (en) * 2000-04-14 2005-09-27 Dowa Mining Co., Ltd. Connector copper alloys and a process for producing the 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
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
WO2008010378A1 (fr) * 2006-07-21 2008-01-24 Kabushiki Kaisha Kobe Seiko Sho Tôle d'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

Non-Patent Citations (1)

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

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TWI591192B (zh) 2017-07-11
CN103732769B (zh) 2016-08-17
US9493858B2 (en) 2016-11-15
TW201307585A (zh) 2013-02-16
CN103732769A (zh) 2014-04-16
KR20140050003A (ko) 2014-04-28
MX2014000570A (es) 2014-04-30
EP2742161A2 (fr) 2014-06-18
US20140161661A1 (en) 2014-06-12
WO2013023717A3 (fr) 2013-06-20
US20140377127A9 (en) 2014-12-25
JP2014527578A (ja) 2014-10-16
WO2013023717A2 (fr) 2013-02-21
BR112014003377A2 (pt) 2017-03-01

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