EP1508626B1 - Alliage de décolletage à base de cuivre. - Google Patents

Alliage de décolletage à base de cuivre. Download PDF

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Publication number
EP1508626B1
EP1508626B1 EP04077561A EP04077561A EP1508626B1 EP 1508626 B1 EP1508626 B1 EP 1508626B1 EP 04077561 A EP04077561 A EP 04077561A EP 04077561 A EP04077561 A EP 04077561A EP 1508626 B1 EP1508626 B1 EP 1508626B1
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Prior art keywords
percent
weight
machinability
alloy
cutting
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Expired - Lifetime
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EP04077561A
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German (de)
English (en)
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EP1508626A1 (fr
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Keiichiro Sambo Copper Alloy Co. Ltd. Oishi
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Sambo Copper Alloy Co Ltd
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Sambo Copper Alloy Co Ltd
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    • 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
    • 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 present invention relates to free-cutting copper alloys.
  • bronze alloys such as the one under JIS designation H5111 BC6 and brass alloys such as the ones under JIS designations H3250-C3604 and C3771.
  • Those alloys are so enhanced in machinability with the addition of 1.0 to 6.0 percent, by weight, of lead as to give industrially satisfactory results as easy-to-work copper alloy.
  • lead-contained copper alloys have been an important basic material for a variety of articles such as city water faucets, water supply/drainage metal fittings and valves.
  • lead does not form a solid solution in the matrix but disperses in granular form, thereby improving the machinability of those alloys.
  • lead has to be added in as much as 2.0 or more percent by weight. If the addition of lead is less than 1.0 percent by weight, chippings will be spiral in form as (D) in Fig. 1. Spiral chippings cause various troubles such as, for example, tangling with the tool. If, on the other hand, the content of lead is 1.0 or more percent by weight and not larger than 2.0 percent by weight, the cut surface will be rough, though that will produce some results such as reduction of the cutting resistance. It is usual, therefore, that lead is added in not smaller than 2.0 percent by weight.
  • Some expanded copper alloys in which a high degree of cutting property is required are mixed with some 3.0 or more percent, by weight, of lead. Further, some bronze castings have a lead content of as much as some 5.0 percent, by weight.
  • lead-mixed alloys have been greatly limited in recent years, because lead contained therein is harmful to humans as an environment pollutant. That is, the lead-contained alloys pose a threat to human health and environmental hygiene because lead finds its way in metallic vapor that generates in the steps of processing those alloys at high temperatures such as melting and casting and there is also danger that lead contained in the water system metal fittings, valves and others made of those alloys will dissolve out into drinking water.
  • the cutting works, forgings, castings and others include city water faucets, water supply/drainage metal fittings, valves, stems, hot water supply pipe fittings, shaft and heat exchanger parts.
  • a free-cutting copper alloy also with an excellent easy-to-cut feature which is composed of 70 to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by weight, of silicon; 0.02 to 0.4 percent, by weight, of lead; at least one selected from among 0.3 to 3.5 percent, by weight, of tin, 1.0 to 3.5 percent, by weight, of aluminum, and 0.02 to 0.25 percent, by weight, of phosphorus; and the remaining percent, by weight, of zinc; and optionally one element selected from among 0.02 to 0.4 percent, by weight, of bismuth 0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to 0.4 percent, by weight, of selenium and wherein the metal structure comprises at least one phase selected from the ⁇ (gamma) phase and the ⁇ (Kappa) phase.
  • Silicon raises the easy-to-cut property by producing a gamma phase (in some cases, a kappa phase) in the structure of metal. That way, both are the same in that they are effective in improving the machinability, though they are quite different in contribution to the properties of the alloy.
  • silicon is added to the first invention alloy so as to bring about a high level of machinalbility meeting the industrial requirements, while making it possible to reduce greatly the lead content. That is, the alloy of the present invention is improved in machinability through formation of a gamma phase with the addition of silicon.
  • silicon is usually added in the form of a Cu-Si alloy, which boosts the production cost.
  • silicon is not desirable to add silicon in a quantity exceeding the saturation point or plateau of machinability improvement - 4.0 percent by weight.
  • the addition of silicon improves not only the machinability but also the flow of the molten metal in casting, strength, wear resistance, resistance to stress corrosion cracking, high-temperature oxidation resistance. Also, the ductility and dezincing corrosion resistance will be improved to some extent.
  • the addition of lead is set at 0.02 to 0.4 percent by weight on this ground.
  • a sufficient level of machinability is obtained by adding silicon that has the aforesaid effect even if the addition of lead is reduced.
  • lead has to be added in the amount not smaller than 0.02 percent by weight if the alloy is to be superior to the conventional free-cutting copper alloy in machinability, while the addition of lead exceeding 0.4 percent would have adverse effects, resulting in a rough surface condition, poor hot workability such as poor forging behaviour and low cold ductility. Meanwhile, it is expected that such a small content of not higher than 0.4 percent by weight will be able to clear the lead-related regulations however strictly they are to be stipulated in the advanced nations including Japan in the future.
  • the addition range of lead is set at 0.02 to 0.4 percent by weight in the alloy of the present invention.
  • Tin works the same way as silicon. That is, if tin is added, a gamma phase will be formed and the machinability of the Cu-Zn alloy will be improved. For example, the addition of tin in the amount of 1.8 to 4.0 percent by weight would bring about a high machinability in the Cu-Zn alloy containing 58 to 70 percent, by weight, of copper, even if silicon is not present. Therefore, the addition of tin to the Cu-Si-Zn alloy could facilitate the formation of a gamma phase and further improve the machinability of the Cu-Si-Zn alloy.
  • the gamma phase is formed with the addition of tin in the amount of 1.0 or more percent by weight and the formation reaches the saturation point at 3.5 percent, by weight, of tin. If tin exceeds 3.5 percent by weight, the ductility will drop instead. With the addition of tin in the amount less than 1.0 percent by weight, on the other hand, an insufficient gamma phase will be formed. If the addition is 0.3 or more percent by weight, then tin will be effective in uniformly dispersing the gamma phase formed by silicon. Through that effect of dispersing the gamma phase, too, the machinability is improved. In other words, the addition of tin in the amount not smaller than 0.3 percent by weight improves the machinability.
  • Aluminum is, too, effective in facilitating the formation of the gamma phase.
  • the addition of aluminum together with or in place of tin could further improve the machinability of the Cu-Si-Zn alloy.
  • Aluminum is also effective in improving the strength, wear resistance and high-temperature oxidation resistance as well as the machinability and also in keeping down the specific gravity. If the machinability is to be improved at all, aluminum will have to be added in the amount of at least 1.0 percent by weight. But the addition of more than 3.5 percent by weight could not produce the proportional results. Instead, that could lower the ductility as is the case with tin.
  • phosphorus As to phosphorus, it has no property of forming the gamma phase as tin and aluminum. But phosphorus works to uniformly disperse and distribute the gamma phase formed as a result of the addition of silicon alone or with tin or aluminum or both of them. That way, the machinability improvement through the formation of gamma phase is further enhanced.
  • phosphorus helps refine the crystal grains in the alpha phase in the matrix, improving hot workability and also strength and resistance to stress corrosion cracking. Furthermore, phosphorus substantially increases the flow of molten metal in casting. To produce such results, phosphorus will have to be added in the amount not smaller than 0.02 percent by weight. But if the addition exceeds 0.25 percent by weight, no proportional effect can be obtained. Instead, there would be a fall in hot forging property and extrudability.
  • the alloy of the present invention is improved in machinability by adding to a Cu-Si-Pb-Zn alloy at least one selected from among 0.3 to 3.5 percent, by weight, of tin, 1.0 to 3.5 percent, by weight, of aluminium, and 0.02 to 0.25 percent, by weight, of phosphorus.
  • tin, aluminum and phosphorus are to improve the machinability by forming a gamma phase or dispersing that phase, and work closely with silicon in promoting the improvement in machinability through the gamma phase.
  • the elements bismuth, tellurium and selenium contribute to improving the machinability, not acting on the gamma phase but dispersing in the form of grains in the matrix. Even if the addition of silicon is less than 2.0 percent by weight, silicon along with tin, aluminum or phosphorus will be able to enhance the machinability to an industrially satisfactory level as long as the percentage of silicon is 1.8 or more percent by weight. But even if the addition of silicon is not larger than 4.0 percent by weight, adding of tin, aluminum or phosphorus together will silicon will saturate the effect of silicon in improving the machinability, when the silicon content exceeds 3.5 percent by weight. On this ground, the addition of silicon is set at 1.8 to 3.5 percent by weight in the alloy of the present invention. Also, in consideration of the addition amount of silicon and also the addition of tin, aluminum or phosphorus, the content range of copper in the alloy of the present invention is properly set out at 70 to 80 percent by weight.
  • Bismuth, tellurium and selenium as well as lead do not form a solid solution with the matrix but disperse in granular form to enhance the machinability. That makes up for the reduction of the lead content.
  • the addition of any one of those elements along with silicon and lead could further improve the machinability beyond the level hoped from the addition of silicon and lead. From this finding, the alloy of the present invention is worked out in which one element selected from among bismuth, tellurium and selenium is mixed.
  • the addition of bismuth, tellurium or selenium as well as silicon and lead could make the copper alloy so machinable that complicated forms could be freely cut out at a high speed.
  • the alloy of the present invention is prepared with the addition of bismuth, tellurium or selenium kept to 0.02 to 0.4 percent by weight.
  • the addition of bismuth, tellurium or selenium which improves the machinability of the copper alloy though a mechanism different from that of silicon as mentioned above, would not affect the proper contents of copper and silicon.
  • Tin is effective in improving not only the machinability but also corrosion resistance properties (dezincification corrosion resistance) and forgeability.
  • tin improves the corrosion resistance in the alpha phase matrix and, by dispersing the gamma phase, the corrosion resistance, forgeability and stress corrosion cracking resistance.
  • tin would have to be added in the amount of at least 0.3 percent by weight. But even if the addition of tin exceeds 3.5 percent by weight, the corrosion resistance and forgeability will not improve in proportion to the amount added of tin. It is no good economy.
  • phosphorus disperses the gamma phase uniformly and at the same time refines the crystal grains in the alpha phase in the matrix, thereby improving the machinability and also the corrosion resistance properties (dezincification corrosion), forgeability, stress corrosion cracking resistance and mechanical strength.
  • a free-cutting copper alloy also with further improved easy-to-cut feature obtained by subjecting any alloy of the present invention to a heat treatment for 30 minutes to 5 hours at 400 to 600°C.
  • the alloy of the present invention contains machinability improving elements such as silicon and have an excellent machinability because of the addition of such elements.
  • machinability improving elements such as silicon
  • the effect of those machinability improving elements could be further enhanced by heat treatment.
  • the alloy of the present invention which is high in copper content with gamma phase in small quantities and kappa phase in large quantities undergo a change in phase from the kappa phase to the gamma phase in a heat treatment.
  • the gamma phase is finely dispersed and precipitated, and the machinability is improved.
  • the materials are often force-air-cooled or water cooled depending on the forging conditions, productivity after hot working (hot extrusion, hot forging etc.), working environment and other factors.
  • Alloys with a low content of copper in particular are rather low in the content of the gamma phase and contain beta phase.
  • the beta phase changes into gamma phase, and the gamma phase is finely dispersed and precipitated, whereby the machinability is improved.
  • cylindrical ingots with compositions given in Table 1 each 100 mm in outside diameter and 150 mm in length, were hot extruded into a round bar 15 mm in outside diameter at 750 C to produce test pieces of the alloy of the present invention Nos. 4001 to 4021.
  • This aluminum bronze is the most excellent of the expanded copper alloys under the JIS designations with regard to strength and wear resistance.
  • No. 13006 corresponds to the naval brass alloy "JIS C 4622" and is the most excellent of the expanded copper alloys under the JIS designations with regard to corrosion resistance.
  • the chips from the cutting work were examined and classified into four forms (A) to (D) as shown in Fig. 1.
  • the results are enumerated in Tables 3 and 4.
  • the chippings in the form of a spiral with three or more windings as (D) in Fig. 1 are difficult to process, that is, recover or recycle, and could cause trouble in cutting work as, for example, getting tangled with the tool and damaging the cut metal surface.
  • chippings in the form of a fine needle as (A) in Fig. 1 or in the form of arc shaped pieces as (B) will not present such problems as mentioned above and are not bulky as the chippings in (C) and (D) and easy to process.
  • fine chippings as (A) still could creep in on the slide table of a machine tool such as a lathe and cause mechanical trouble, or could be dangerous because they could stick into the worker's finger, eye or other body parts.
  • the surface condition of the cut metal surface was checked after cutting work.
  • the results are shown in Tables 3 and 4.
  • the commonly used basis for indication of the surface roughness is the maximum roughness (Rmax). While requirements are different depending on the application field of brass articles, the alloys with Rmax ⁇ 10 microns are generally considered excellent in machinability. The alloys with 10 microns ⁇ Rmax ⁇ 15 microns are judged as industrially acceptable while those with Rmax ⁇ 15 microns are taken as poor in machinability.
  • the alloys of the present invention are all equal to the conventional lead-contained alloys Nos. 13001 to 13003 in machinability
  • alloys of the present invention are favorably compared not only with the conventional alloys Nos. 13004 to 13006 with a lead content of not higher than 0.1 percent by weight but also Nos. 13001 to 13003 which contain large quantities of lead.
  • the alloys of the present invention were examined in comparison with the conventional alloys in hot workability and mechanical properties.
  • hot compression and tensile tests were conducted the following way.
  • test pieces two test pieces, first and second test pieces, in the same shape 15 mm in outside diameter and 25 mm in length were cut out of each extruded test piece obtained as described above.
  • the first test piece was held for 30 minutes at 7000C, and then compressed at the compression rate of 70 percent in the direction of axis to reduce the length from 25 mm to 7.5 mm.
  • the surface condition after the compression 700°C deformability was visually evaluated.
  • the results were given in Tables 3 and 4.
  • the evaluation of deformability was made by visually checking for cracks on the side of the test piece. In Tables 3 and 4, the test pieces with no cracks found are marked "o"; those with small cracks are indicated by " ⁇ " and those with large cracks are represented by a symbol "x".
  • the second test pieces were put to a tensile test by the commonly practised test method to determine the tensile strength, N/mm 2 and elongation, %.
  • alloy of the present invention as put to dezincification corrosion and stress corrosion cracking tests in accordance with the test methods specified under "ISO 6509” and “JIS H 3250” respectively to examine the corrosion resistance and resistance to stress corrosion cracking in comparison with the conventional alloys.
  • the test piece taken from each extruded test piece was imbedded laid in a phenolic resin material in such a way that the exposed test piece surface is perpendicular to the extrusion direction of the extruded test piece.
  • the surface of the test piece was polished with emery paper No. 1200, and then ultrasonic-washed in pure water and dried.
  • the test piece thus prepared was dipped in a 12.7 g/l aqueous solution of cupric chloride dihydrate (CuCl 2 .2N 2 O) 1.0% and left standing for 24 hours at 75°C.
  • the test piece was taken out of the aqueous solution and the maximum depth of dezincing corrosion was determined.
  • the measurements of the maximum dezincification corrosion depth are given in Tables 3, and 4.
  • the alloy of the present invention is excellent in corrosion resistance in comparison with the conventional alloys Nos. 13001 to 13003 which contain great amount of lead.
  • test piece In the stress corrosion cracking tests in accordance with the test method described in "JIS H 3250", a 150-mm-long test piece was cut out from each extruded material. The test piece was bent with the center placed on an arc-shaped tester with a radius of 40 mm in such a way that one end forms an angle of 45 degrees with respect the other end. The test piece thus subjected to a tensile residual stress was degreased and dried, and then placed in an ammonia environment in the desiccator with a 12.5% aqueous ammonia (ammonia diluted in the equivalent of pure water). To be exact, the test piece was held some 80 mm above the surface of aqueous ammonia in the desiccator.
  • test piece After the test piece was left standing in the ammonia environment for 2 hours, 8 hours and 24 hours, the test piece was taken out from the desiccator, washed in sulfuric acid solution 10% and examined for cracks under a magnifier of 10 magnifications.
  • Tables 3 and 4 In those tables, the alloys which developed clear cracks when held in the ammonia environment for two hours are marked "xx.” The test pieces which had no cracks at two hours but were found clearly cracked in 8 hours are indicated in "x.” The test pieces which had no cracks in 8 hours, but were found clearly to have cracks in 28 hours are identified by the symbol " ⁇ ". The test pieces which were found to have no cracks at all in 24 hours are given a symbol "o".
  • the alloy of the present invention is both equal to the conventional alloy No. 13005, an aluminum bronze containing no zinc, in stress corrosion cracking resistance.
  • the alloy of the present invention was superior in stress corrosion cracking resistance to the conventional naval brass alloy No. 13006, the best in corrosion resistance of all the expanded copper alloys under the JIS designations. Table 1 No.

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Claims (3)

  1. Alliage de décolletage à base de cuivre comprenant 70 à 80 pour cent, en poids, de cuivre; 1,8 à 3,5 pour cent, en poids, de silicium; 0,02 à 0,4 pour cent, en poids, de plomb; au moins un élément sélectionné parmi entre 0,3 et 3,5 pour cent, en poids, d'étain, 1,0 et 3,5 pour cent, en poids, d'aluminium, et 0,02 et 0,25 pour cent, en poids, de phosphore, le pourcentage en poids restant étant constitué de zinc;
    et optionnellement un élément sélectionné parmi entre 0,02 et 0,4 pour cent, en poids, de bismuth, 0,02 et 0,4 pour cent, en poids, de tellure, et 0,02 et 0,4 pour cent, en poids, de sélénium, et dans lequel la structure métallique comprend au moins une phase sélectionnée parmi la phase γ (gamma) et la phase κ (kappa).
  2. Alliage de décolletage à base de cuivre selon la revendication 1, dans lequel, lorsqu'il est coupé sur la surface circonférentielle par un tour pourvu d'un outil droit à nez pointu à un angle de coupe de -8 (moins 8) et une vitesse de coupe de 50 mètres par minute, une profondeur de coupe de 1,5 mm, une vitesse d'avance de 0,11 mm par tour, il donne des copeaux présentant une ou plusieurs forme(s) sélectionnée(s) dans le groupe comprenant une forme arquée et une forme d'aiguille fine.
  3. Alliage de décolletage à base de cuivre selon la revendication 1 ou 2 soumis à un traitement thermique pendant une durée de 30 minutes à 5 heures à une température de 400°C à 600°C.
EP04077561A 1998-10-09 1998-11-16 Alliage de décolletage à base de cuivre. Expired - Lifetime EP1508626B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP28792198 1998-10-09
JP28792198A JP3917304B2 (ja) 1998-10-09 1998-10-09 快削性銅合金
EP98953070A EP1038981B1 (fr) 1998-10-09 1998-11-16 Alliage de decolletage a base de cuivre

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EP98953070A Division EP1038981B1 (fr) 1998-10-09 1998-11-16 Alliage de decolletage a base de cuivre

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EP1508626A1 EP1508626A1 (fr) 2005-02-23
EP1508626B1 true EP1508626B1 (fr) 2006-09-13

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EP04077561A Expired - Lifetime EP1508626B1 (fr) 1998-10-09 1998-11-16 Alliage de décolletage à base de cuivre.
EP98953070A Expired - Lifetime EP1038981B1 (fr) 1998-10-09 1998-11-16 Alliage de decolletage a base de cuivre
EP04077560A Expired - Lifetime EP1502964B1 (fr) 1998-10-09 1998-11-16 Alliage de décolletage à base de cuivre.

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EP98953070A Expired - Lifetime EP1038981B1 (fr) 1998-10-09 1998-11-16 Alliage de decolletage a base de cuivre
EP04077560A Expired - Lifetime EP1502964B1 (fr) 1998-10-09 1998-11-16 Alliage de décolletage à base de cuivre.

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EP (3) EP1508626B1 (fr)
JP (1) JP3917304B2 (fr)
KR (1) KR100375426B1 (fr)
AU (1) AU738301B2 (fr)
CA (1) CA2303512C (fr)
DE (3) DE69833582T2 (fr)
TW (1) TW577931B (fr)
WO (1) WO2000022181A1 (fr)

Families Citing this family (31)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8506730B2 (en) 1998-10-09 2013-08-13 Mitsubishi Shindoh Co., Ltd. Copper/zinc alloys having low levels of lead and good machinability
JP2002069551A (ja) * 2000-09-04 2002-03-08 Sumitomo Light Metal Ind Ltd 快削性銅合金
DE10132055C2 (de) * 2001-07-05 2003-12-11 Diehl Metall Stiftung & Co Kg Entzinkungsbeständige Kupfer-Zink-Legierung sowie Verfahren zu ihrer Herstellung
JP2004244672A (ja) 2003-02-13 2004-09-02 Dowa Mining Co Ltd 耐脱亜鉛性に優れた銅基合金
CZ20032094A3 (cs) * 2003-08-01 2005-04-13 Kovohutě Čelákovice A. S. Automatová mosaz
DE502005009545D1 (de) * 2004-10-11 2010-06-17 Diehl Metall Stiftung & Co Kg Kupfer-zink-silizium-legierung, deren verwendung und deren herstellung
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KR100864909B1 (ko) * 2007-01-30 2008-10-22 주식회사 풍산 쾌삭성 구리합금
KR100864910B1 (ko) * 2007-01-30 2008-10-22 주식회사 풍산 쾌삭성 구리합금
JP5326114B2 (ja) 2009-04-24 2013-10-30 サンエツ金属株式会社 高強度銅合金
JP5645570B2 (ja) * 2010-09-27 2014-12-24 株式会社Ｌｉｘｉｌ 鍛造用及び切削加工用銅基合金並びに水道用器具
US20140294665A1 (en) 2011-02-04 2014-10-02 Baoshida Swissmetal Ag Cu-Ni-Zn-Mn Alloy
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JP5763504B2 (ja) * 2011-11-11 2015-08-12 三菱伸銅株式会社 銅合金製の転造加工用素材及び転造加工品
JP2013194277A (ja) * 2012-03-19 2013-09-30 Lixil Corp 切削加工用銅基合金及びその合金を用いた水道用器具
AU2013340034B2 (en) 2012-10-31 2018-03-22 Kitz Corporation Brass alloy and processed part and wetted part
JP2015175008A (ja) * 2014-03-13 2015-10-05 株式会社Ｌｉｘｉｌ 鉛レス黄銅材料および水道用器具
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WO2019035224A1 (fr) * 2017-08-15 2019-02-21 三菱伸銅株式会社 Alliage de cuivre de décolletage, et procédé de fabrication de celui-ci
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JP7180488B2 (ja) * 2019-03-25 2022-11-30 三菱マテリアル株式会社 銅合金丸棒材
TWI731506B (zh) 2019-06-25 2021-06-21 日商三菱伸銅股份有限公司 快削性銅合金及快削性銅合金的製造方法
WO2020261666A1 (fr) 2019-06-25 2020-12-30 三菱マテリアル株式会社 Alliage de cuivre à décolletage et procédé de production d'alliage de cuivre à décolletage
KR102623143B1 (ko) 2019-06-25 2024-01-09 미쓰비시 마테리알 가부시키가이샤 쾌삭성 구리 합금 주물, 및 쾌삭성 구리 합금 주물의 제조 방법
KR20220059528A (ko) 2019-12-11 2022-05-10 미쓰비시 마테리알 가부시키가이샤 쾌삭성 구리 합금, 및 쾌삭성 구리 합금의 제조 방법
DE102020127317A1 (de) 2020-10-16 2022-04-21 Diehl Metall Stiftung & Co. Kg Bleifreie Kupferlegierung sowie Verwendung der bleifreien Kupferlegierung

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5696040A (en) * 1979-12-28 1981-08-03 Seiko Epson Corp Exterior decorative part material for casting
DE3427740A1 (de) * 1984-07-27 1986-02-06 Diehl GmbH & Co, 8500 Nürnberg Messinglegierung, herstellungsverfahren und verwendung
JPS61133357A (ja) * 1984-12-03 1986-06-20 Showa Alum Ind Kk 加工性および耐焼付性にすぐれた軸受用Ｃｕ合金
JPS62297429A (ja) * 1986-06-17 1987-12-24 Nippon Mining Co Ltd 耐食性に優れた銅合金
US5288458A (en) * 1991-03-01 1994-02-22 Olin Corporation Machinable copper alloys having reduced lead content
DE4339426C2 (de) * 1993-11-18 1999-07-01 Diehl Stiftung & Co Kupfer-Zink-Legierung
JP3459520B2 (ja) * 1996-09-05 2003-10-20 古河電気工業株式会社 リードフレーム用銅合金
WO1998010105A1 (fr) * 1996-09-05 1998-03-12 The Furukawa Electric Co., Ltd. Alliage de cuivre pour dispositifs electroniques

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AU738301B2 (en) 2001-09-13
EP1508626A1 (fr) 2005-02-23
DE69828818D1 (de) 2005-03-03
EP1038981B1 (fr) 2005-01-26
JP3917304B2 (ja) 2007-05-23
KR20010033101A (ko) 2001-04-25
EP1038981A1 (fr) 2000-09-27
DE69833582T2 (de) 2007-01-18
JP2000119774A (ja) 2000-04-25
WO2000022181A1 (fr) 2000-04-20
EP1502964B1 (fr) 2006-03-01
KR100375426B1 (ko) 2003-03-10
TW577931B (en) 2004-03-01
EP1038981A4 (fr) 2003-02-19
CA2303512C (fr) 2006-07-11
DE69835912D1 (de) 2006-10-26
EP1502964A1 (fr) 2005-02-02
DE69833582D1 (de) 2006-04-27
DE69835912T2 (de) 2007-03-08
AU1054099A (en) 2000-05-01
DE69828818T2 (de) 2006-01-05
CA2303512A1 (fr) 2000-04-20

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