EP1600516A2 - Bleifreie Automatenkupferlegierung - Google Patents

Bleifreie Automatenkupferlegierung Download PDF

Info

Publication number
EP1600516A2
EP1600516A2 EP05017190A EP05017190A EP1600516A2 EP 1600516 A2 EP1600516 A2 EP 1600516A2 EP 05017190 A EP05017190 A EP 05017190A EP 05017190 A EP05017190 A EP 05017190A EP 1600516 A2 EP1600516 A2 EP 1600516A2
Authority
EP
European Patent Office
Prior art keywords
remainder
weight
percent
alloy
machinability
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
EP05017190A
Other languages
English (en)
French (fr)
Other versions
EP1600516A3 (de
EP1600516B1 (de
Inventor
Keiichiro Oishi
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.)
Sambo Copper Alloy Co Ltd
Original Assignee
Sambo Copper Alloy Co Ltd
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 Sambo Copper Alloy Co Ltd filed Critical Sambo Copper Alloy Co Ltd
Publication of EP1600516A2 publication Critical patent/EP1600516A2/de
Publication of EP1600516A3 publication Critical patent/EP1600516A3/de
Application granted granted Critical
Publication of EP1600516B1 publication Critical patent/EP1600516B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • 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 lead-free, 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 enhanced in machinability by the addition of 1.0 to 6.0 percent, by weight, of lead and provide an industrially satisfactory machinability. Because of their excellent machinability, those 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 contained therein is an environment pollutant harmful to humans. That is, the lead-containing alloys pose a threat to human health and environmental hygiene because lead is contained in metallic vapor that is generated in the steps of processing those alloys at high temperatures such as melting and casting and there is also concern 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.
  • the first to twelfth invention alloys contain machinability improving elements such as silicon and have an excellent machinability because of the addition of such elements.
  • the alloys with a high copper content which have great amounts of other phases, mainly kappa phase, than alpha, beta, gamma and delta phases can further improve in machinability in a heat treatment.
  • the kappa phase turns to a gamma phase.
  • the gamma phase finely disperses and precipitates to further enhance the machinability.
  • the alloys with a high content of copper are high in ductility of the matrix and low in absolute quantity of gamma phase, and therefore are excellent in cold workability.
  • the aforesaid heat treatment is very useful.
  • those which are 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.
  • the low copper content alloy those with a low content of copper (hereinafter called the low copper content alloy") 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.
  • Fig. 1 shows perspective views of cuttings formed in cutting a round bar of copper alloy by lathe.
  • first invention alloys Nos. 1001 to 1008 second invention alloys Nos. 2001 to 2011, third invention alloys Nos. 3001 to 3012, fourth invention alloys Nos. 4001 to 4049, fifth invention alloys Nos. 5001 to 5020, sixth invention alloys Nos. 6001 to 6105, seventh invention alloys Nos. 7001 to 7030, eighth invention alloys Nos. 8001 to 8147, ninth invention alloys Nos. 9001 to 9005, tenth invention alloys Nos.
  • No. 13003 is an alloy test piece obtained by heat-treating an extruded test piece with the same composition as first invention alloy No. 1007 under the same conditions as for No. 13001 - for 30 minutes at 580°C.
  • No. 13004 is an alloy test piece obtained by heat-treating an extruded test piece with the same composition as No. 13007 under the same conditions as for 13002 - for two hours at 450°C.
  • No. 13005 is an alloy test piece obtained by heat-treating an extruded test piece with the same composition as first invention alloy No. 1008 under the same conditions as for No. 13001 - for 30 minutes at 580°C.
  • No. 13006 is an alloy test piece obtained by heat-treating an extruded test piece with the same composition as No. 1008 and heat-treated under the same conditions as for 13002 - for two hours at 450°C.
  • 14005 corresponds to the alloy "JIS C 6191.” This aluminum bronze is the most excellent of the expanded copper alloys under the JIS designations with regard to strength and wear resistance.
  • No. 14006 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 Table 38 to Table 66.
  • the chips 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.
  • chips in the form of a fine needle as (A) in Fig. 1 or in the form of an arc as (B) will not present such problems as mentioned above and are not bulky as the chips in (C) and (D) and easy to process. But fine chips as (A) still could creep into the sliding surfaces 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 Table 38 to Table 66.
  • 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 s Rmax ⁇ 15 microns are judged as industrially acceptable, while those with Rmax ⁇ 15 microns are taken as poor in machinability.
  • the following invention alloys are all equal to the conventional lead- contained alloys Nos. 14001 to 14003 in machinability: first invention alloys Nos. 1001 to 1008, second invention alloys Nos. 2001 to 2011, third invention alloys Nos. 3001 to 3012, fourth invention alloys Nos. 4001 to 4049, fifth invention alloys Nos. 5001 to 5020, sixth invention alloys Nos. 6001 to 6105, seventh invention alloys Nos. 7001 to 7030, eighth invention alloys Nos. 8001 to 8147, ninth invention alloys Nos. 9001 to 9005, tenth invention alloys Nos. 10001 to 10008, eleventh invention alloys Nos.
  • thirteenth invention alloys Nos. 13001 to 13006 are improved over first invention alloy No. 1005, No. 1007 and No. 1008 with the same composition as the thirteenth invention alloys in machinability. It is thus confirmed that a proper heat treatment could further enhance the machinability.
  • the first to thirteenth invention alloys 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 700°C, and then compressed 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
  • the results are given in Table 38 to Table 66.
  • the evaluation of deformability was made by visually checking for cracks on the side of the test piece. In Table 38 to Table 66, the test pieces with no cracks found are marked "o", those with small cracks are indicated in " ⁇ " 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, %.
  • the first to thirteenth invention alloys are equal to or superior to the conventional alloys Nos. 14001 to 14004 and No. 14006 in hot workability and mechanical properties and are suitable for industrial use.
  • the seventh and eighth invention alloys in particular have the same level of mechanical properties as the conventional alloy No. 14005, the aluminum bronze which is the most excellent in strength of the expanded copper alloys under the JIS designations, and thus have understandably a prominent high strength feature.
  • first to six and ninth to thirteenth invention alloys were put to dezincification 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 first to fourth invention alloys and the ninth to thirteenth invention alloys are excellent in corrosion resistance and favourably comparable with the conventional alloys Nos. 14001 to 14003 containing great amounts of lead. And it was confirmed that especially the fifth and sixth invention alloys which seek improvement in both machinability and corrosion resistance are very high in corrosion resistance and superior in corrosion resistance to the conventional alloy No. 14006, a naval brass which is the most resistant to corrosion of all the expanded alloys under the JIS designations.
  • test sample was cut out from each extruded test piece.
  • the sample was bent with its centre placed on an arc-shaped tester with a radius of 40 mm in such a way that one end and the other end subtend an angle of 45 degrees.
  • the test sample 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 sample was held some 80 mm above the surface of aqueous ammonia in the desiccator.
  • test sample After the test sample was left standing in the ammonia environment for two hours, 8 hours and 24 hours, the test sample was taken out from the desiccator, washed in sulfuric acid solution 10% and examined for cracks under a magnifier of 10 magnifications.
  • the results are given in Table 38 to Table 50 and Table 61 to Table 66.
  • the alloys which have developed clear cracks when held in the ammonia environment for two hours are marked "xx.”
  • the test samples which had no cracks at passage of two hours but were found to have clear cracks at 8 hours are indicated by "x.”
  • the test samples which had no cracks at 8 hours, but were found to have clear cracks at 24 hours were indicated by " ⁇ ".
  • the test samples which were found to have no cracks at all at 24 hours are given a symbol "o.”
  • test piece in the shape of a round bar with the surface cut to a outside diameter of 14 mm and the length cut to 30 mm was prepared from each of the following extruded test pieces: No. 9001 to No. 9005, No. 10001 to No. 10008, No. 11001 to No. 11007, No. 12001 to No. 12021 and No. 14001 to No. 14006.
  • Each test piece was then weighed to measure the weight before oxidation. After that, the test piece was placed in a porcelain crucible and held in an electric furnace maintained at 500°C. At passage of 100 hours, the test piece was taken out of the electric furnace and weighed to measure the weight after oxidation. From the measurements before and after oxidation was calculated the increase in weight by oxidation.
  • the weight of each test piece increased after oxidation.
  • the increase was brought about by high-temperature oxidation. Subjected to a high temperature, oxygen combines with copper, zinc and silicon to form Cu 2 O, ZnO, SiO 2 . That is, oxygen increase contributes to the weight gain. It can be said, therefore, that the alloys which are the smaller in weight increase by oxidation are the more excellent in high-temperature oxidation resistance.
  • Table 61 to Table 64 and Table 66 The results obtained are shown in Table 61 to Table 64 and Table 66.
  • the ninth to twelfth invention alloys are equal to the conventional alloy No. 14005, an aluminum bronze ranking high in resistance to high-temperature oxidation among the expanded copper alloys under the JIS designations and are far smaller than any other conventional copper alloy.
  • the ninth to twelfth invention alloys are very excellent in machinability and resistance to high-temperature oxidation as well.
  • alloys Nos. 7001a to 7030a, Nos. 8001a to 8147a and Nos. 14001a to 14006a are identical in composition with the aforesaid copper alloys Nos. 7001 to 7030, Nos. 8001 to 8147 and Nos. 14001 to No. 14006 respectively.
  • test piece thus obtained was cut on the circumferential surface, holed and cut down into a ringshaped test piece 32 mm in outside diameter and 10 mm in thickness (that is, the length in the axial direction).
  • the test piece was then fitted around a free-rotating shaft, and a roll 48 mm in outside diameter placed in parallel with the axis of the shaft was urged against the test piece under a load of 50 kg.
  • the roll was made of stainless steel under the JIS designation SUS 304.
  • alloy composition (wt%) Cu Si Sn Al P Zn 3001 71.8 2.4 3.1 remainder 3002 78.2 2.3 3.3 remainder 3003 75.0 1.9 1.5 1.4 remainder 3004 74.9 3.2 0.09 remainder 3005 71.6 2.4 2.3 0.03 remainder 3006 76.5 2.7 2.4 0.21 remainder 3007 76.5 3.1 0.6 1.1 0.04 remainder 3008 77.5 3.5 0.4 remainder 3009 75.4 3.0 1.7 remainder 3010 76.5 3.3 0.21 remainder 3011 73.8 2.7 0.04 remainder 3012 75.0 2.9 1.6 0.10 remainder No alloy composition (wt%) .
  • alloy composition (wt%) Cu Si Sn Al Bi Te Se P Zn 4041 77.2 2.7 2.1 0.33 0.05 0.05 remainder 4042 78.0 2.6 2.5 0.03 0.02 0.10 0.14 remainder 4043 72.5 2.4 1.9 1.1 0.12 0.03 remainder 4044 76.0 2.6 0.5 2.0 0.20 0.07 remainder 4045 77.5 2.6 0.7 3.1 0.21 0.12 remainder 4046 75.0 2.6 0.8 2.2 0.04 0.05 0.06 remainder 4047 71.0 1.9 3.1 1.0 0.15 0.02 0.04 remainder 4048 73.3 2.1 2.6 1.2 0.04 0.03 0.05 remainder 4049 74.8 2.5 0.6 1.1 0.03 0.03 0.04 0.07 remainder No alloy composition (wt%) .
  • machinability corrosion resistance hot workability mechanical properties stress resistance corrosion cracking resistance form of chippings condition of cut surface cutting force (N) maximum depth of corrosion ( ⁇ m) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 6101 ⁇ ⁇ 115 ⁇ 5 ⁇ 530 38 ⁇ 6102 o ⁇ ⁇ 118 ⁇ 5 ⁇ 512 36 ⁇ 6103 o ⁇ ⁇ 119 ⁇ 5 ⁇ 501 35 ⁇ 6104 o ⁇ ⁇ 117 ⁇ 5 ⁇ 535 32 ⁇ 6105 o ⁇ ⁇ 117 ⁇ 5 ⁇ 517 37 ⁇ No. machinability hot workability mechanical properties .
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 8141 o ⁇ ⁇ 131 ⁇ 687 22 8142 o ⁇ ⁇ 130 ⁇ 635 20 8143 o ⁇ ⁇ 129 ⁇ 710 23 8144 o ⁇ ⁇ 130 ⁇ 662 24 8145 o ⁇ ⁇ 128 ⁇ 728 23 8146 o ⁇ ⁇ 129 ⁇ 753 21 8147 o ⁇ ⁇ 130 ⁇ 709 24 No. machinability corrosion resistance hot workability mechanical properties stress resistance corrosion cracking resistance .
  • wear resistance weight loss by wear 7001a 1.3 7002a 0.8 7003a 0.9 7004a 1.4 7005a 1.3 7006a 1.7 7007a 1.8 7008a 1.2 7009a 0.8 7010a 2.4 7011a 1.9 7012a 1.2 7013a 1.1 7014a 2.7 7015a 1.4 7016a 1.3 7017a 1.6 7018a 1.4 7019a 1.9 7020a 1.5 No. wear resistance weight loss by wear (mg/100000rot.) 7021a 1.3 7022a 0.9 7023a 1.2 7024a 1.0 7025a 2.3 7026a 1.7 7027a 1.8 7028a 1.1 7029a 1.5 7030a 1.4 No.
  • wear resistance weight loss by wear 8001a 1.4 8002a 1.1 8003a 0.9 8004a 1.2 8005a 1.8 8006a 1.3 8007a 1.5 8008a 1.0 8009a 1.2 8010a 0.7 8011a 1.0 8012a 1.3 8013a 1.4 8014a 1.3 8015a 1.5 8016a 0.9 8017a 1.4 8018a 0.9 8019a 1.0 8020a 1.5 No.
  • wear resistance weight loss by wear 8021a 1.0 8022a 1.4 8023a 1.4 8024a 0.8 8025a 1.2 8026a 1.4 8027a 1.9 8028a 0.9 8029a 1.4 8130a 2.2 8131a 2.1 8132a 1.0 8133a 2.4 8134a 1.4 8135a 1.2 8136a 1.5 8137a 1.3 8138a 0.8 8139a 1.4 8140a 1.5 No.
  • wear resistance weight loss by wear 8041a 1.5 8042a 1.3 8043a 1.6 8044a 1.2 8045a 1.0 8046a 2.0 8097a 1.6 8048a 1.7 8049a 1.3 8050a 1.5 8051a 1.0 8052a 1.5 8053a 1.3 8054a 1.2 8055a 0.7 8056a 0.9 8057a 1.6 8058a 2.4 8059a 1.6 8060a 1.9 No.
  • wear resistance weight loss by wear 8061a 1.6 8062a 1.9 8063a 1.2 8064a 1.7 8065a 2.0 8066a 1.4 8067a 1.5 8068a 1.2 8069a 0.9 8070a 1.0 8071a 1.7 8072a 1.9 8073a 1.6 8074a 1.6 8075a 1.8 8076a 0.8 8077a 1.3 8078a 1.2 8079a 1.4 8080a 1.3 No.
  • wear resistance weight loss by wear 8081a 1.6 8082a 1.3 8083a 1.0 8084a 1.2 8085a 1.5 8086a 1.6 8087a 1.1 8088a 2.0 8089a 1.4 8090a 1.2 8091a 1.5 8092a 1.6 8093a 2.1 8094a 1.5 8095a 1.9 8096a 1.5 8097a 1.5 8098a 1.4 8099a 1.1 8100a 0.9 No. wear resistance .
  • weight loss by wear 8101 1.4 8102 1.3 8103 0.8 8104 0.8 8105 0.7 8106 0.9 8107 1.2 8108 1.1 8109 1.0 8110 0.7 8111 0.8 8112 1.2 8113 0.9 8114 1.2 8115 1.1 8116 1.4 8117 1.1 8118 0.9 8119 1.1 8120 0.9 No.
  • wear resistance weight loss by wear 8121a 1.0 8122a 1.0 8123a 1.2 8124a 0.8 8125a 1.1 8126a 0.9 8127a 1.3 8128a 1.4 8129a 1.3 8130a 1.5 8131a 1.2 8132a 1.3 8133a 0.8 8134a 1.0 8135a 0.8 8136a 1.3 8137a 1.1 8138a 0.9 8139a 1.2 8140a 1.0 No. wear resistance weight loss by wear (mg/100000rot.) 8141a 1.4 8142a 1.8 8143a 1.6 8144a 1.9 8145a 1.1 8146a 1.2 8147a 1.4 No. wear resistance weight loss by wear (mg/100000rot.) 14001a 500 14002a 620 14003a 520 14004a 450 14005a 25 14006a 600

Landscapes

  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Powder Metallurgy (AREA)
  • Conductive Materials (AREA)
  • Adornments (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
EP05017190A 1998-10-12 1998-11-16 Bleifreie Automatenkupferlegierung Expired - Lifetime EP1600516B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP28859098 1998-10-12
JP28859098A JP3734372B2 (ja) 1998-10-12 1998-10-12 無鉛快削性銅合金
EP98953071A EP1045041B1 (de) 1998-10-12 1998-11-16 Bleifreie automatenkupferlegierung

Related Parent Applications (1)

Application Number Title Priority Date Filing Date
EP98953071A Division EP1045041B1 (de) 1998-10-12 1998-11-16 Bleifreie automatenkupferlegierung

Publications (3)

Publication Number Publication Date
EP1600516A2 true EP1600516A2 (de) 2005-11-30
EP1600516A3 EP1600516A3 (de) 2005-12-14
EP1600516B1 EP1600516B1 (de) 2007-07-18

Family

ID=17732235

Family Applications (5)

Application Number Title Priority Date Filing Date
EP05017189A Expired - Lifetime EP1600515B8 (de) 1998-10-12 1998-11-16 Bleifreie Automatenkupferlegierung
EP05017190A Expired - Lifetime EP1600516B1 (de) 1998-10-12 1998-11-16 Bleifreie Automatenkupferlegierung
EP05017191A Expired - Lifetime EP1600517B1 (de) 1998-10-12 1998-11-16 Bleifreie Automatenkupferlegierung
EP98953071A Expired - Lifetime EP1045041B1 (de) 1998-10-12 1998-11-16 Bleifreie automatenkupferlegierung
EP05075421.7A Expired - Lifetime EP1559802B1 (de) 1998-10-12 1998-11-16 Bleifrei Automatenkupferlegierung

Family Applications Before (1)

Application Number Title Priority Date Filing Date
EP05017189A Expired - Lifetime EP1600515B8 (de) 1998-10-12 1998-11-16 Bleifreie Automatenkupferlegierung

Family Applications After (3)

Application Number Title Priority Date Filing Date
EP05017191A Expired - Lifetime EP1600517B1 (de) 1998-10-12 1998-11-16 Bleifreie Automatenkupferlegierung
EP98953071A Expired - Lifetime EP1045041B1 (de) 1998-10-12 1998-11-16 Bleifreie automatenkupferlegierung
EP05075421.7A Expired - Lifetime EP1559802B1 (de) 1998-10-12 1998-11-16 Bleifrei Automatenkupferlegierung

Country Status (8)

Country Link
EP (5) EP1600515B8 (de)
JP (1) JP3734372B2 (de)
KR (1) KR100352213B1 (de)
AU (1) AU744335B2 (de)
CA (1) CA2314144C (de)
DE (4) DE69832097T2 (de)
TW (1) TW421674B (de)
WO (1) WO2000022182A1 (de)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2960350A1 (de) 2014-06-27 2015-12-30 Gebr. Kemper GmbH + Co. KG Metallwerke Kupfergusslegierung
EP3985136A1 (de) 2020-10-16 2022-04-20 Diehl Metall Stiftung & Co. KG Bleifreie kupferlegierung sowie verwendung der bleifreien kupferlegierung

Families Citing this family (52)

* 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
US7056396B2 (en) 1998-10-09 2006-06-06 Sambo Copper Alloy Co., Ltd. Copper/zinc alloys having low levels of lead and good machinability
JP3459623B2 (ja) * 2000-08-08 2003-10-20 京和ブロンズ株式会社 無鉛青銅合金
JP4496662B2 (ja) 2001-04-20 2010-07-07 株式会社豊田自動織機 斜板式圧縮機における斜板
US20040234412A1 (en) * 2002-09-09 2004-11-25 Keiichiro Oishi High-strength copper alloy
JP4522736B2 (ja) * 2004-03-30 2010-08-11 株式会社キッツ 金型鋳造用銅基合金とこの合金を用いた鋳塊・製品
US20070169854A1 (en) 2004-08-10 2007-07-26 Sanbo Shindo Kogyo Kabushiki Kaisha Copper-based alloy casting in which grains are refined
BRPI0516067B1 (pt) * 2004-10-11 2014-10-14 Diehl Metall Stiftung & Co Kg Liga de cobre/zinco/silício, e seu processo de produção
KR100631041B1 (ko) 2005-03-04 2006-10-04 주식회사 풍산 절삭성 및 가공성이 우수한 쾌삭황동합금
ES2294604T3 (es) 2005-07-28 2008-04-01 Gebr. Kemper Gmbh + Co. Kg Metallwerke Procedimiento de fabricacion de piezas fundidas en cobre, con tendencia a la migracion reducida.
WO2007013428A1 (ja) * 2005-07-28 2007-02-01 San-Etsu Metals Co., Ltd. 銅合金押出材およびその製造方法
ATE557108T1 (de) 2005-09-22 2012-05-15 Mitsubishi Shindo Kk Kupferautomatenlegierung mit sehr wenig blei
JP4951517B2 (ja) 2005-09-30 2012-06-13 三菱伸銅株式会社 溶融固化処理物並びに溶融固化処理用銅合金材及びその製造方法
EP1798298B2 (de) 2005-12-14 2016-05-04 Gebr. Kemper GmbH + Co. KG Metallwerke Verwendung einer migrationsarmen Kupferlegierung sowie Bauteile aus dieser Legierung
EP1801250B1 (de) 2005-12-22 2017-11-08 Viega Technology GmbH & Co. KG Migrationsarme Bauteile aus Kupferlegierung für Medien oder Trinkwasser führender Gewerke
JP2008095918A (ja) * 2006-10-16 2008-04-24 Yamaha Marine Co Ltd サーモエレメント及びこのサーモエレメントを用いたサーモスタット装置
EP2014964B1 (de) 2007-06-05 2011-11-23 R. Nussbaum AG Armatur
JP2009007657A (ja) * 2007-06-29 2009-01-15 Joetsu Bronz1 Corp 無鉛快削性銅合金並びに連続鋳造用無鉛快削性銅合金
JP5320638B2 (ja) * 2008-01-08 2013-10-23 株式会社Ｓｈカッパープロダクツ 圧延銅箔およびその製造方法
CN101235448B (zh) * 2008-02-22 2010-10-13 中南大学 一种无铅易切削硅石墨黄铜
CN101440444B (zh) * 2008-12-02 2010-05-12 路达(厦门)工业有限公司 无铅易切削高锌硅黄铜合金及其制造方法
DE102009015186A1 (de) * 2009-03-31 2010-10-14 Viega Gmbh & Co. Kg Fitting zum Anschluss eines Rohres
JP5326114B2 (ja) 2009-04-24 2013-10-30 サンエツ金属株式会社 高強度銅合金
EP2290114A1 (de) 2009-08-04 2011-03-02 Gebr. Kemper GmbH + Co. KG Metallwerke Wasserführendes Bauteil
TWI398532B (zh) 2010-01-22 2013-06-11 Modern Islands Co Ltd Lead-free brass alloy
CN101787461B (zh) * 2010-03-02 2014-11-19 路达(厦门)工业有限公司 一种环保型锰黄铜合金及其制造方法
JP2011214095A (ja) * 2010-03-31 2011-10-27 Joetsu Bronz1 Corp 鋳造用無鉛快削黄銅合金
JP2011214094A (ja) * 2010-03-31 2011-10-27 Joetsu Bronz1 Corp 無鉛快削黄銅合金
EP2614167B1 (de) 2010-09-10 2017-04-12 Raufoss Water & Gas AS Messinglegierung mit silizium und arsen sowie herstellungsverfahren dafür
CN102321827B (zh) * 2011-09-25 2013-01-09 宁波市鄞州锡青铜带制品有限公司 一种高导电率低锡青铜带的制备方法
KR101340487B1 (ko) * 2011-09-30 2013-12-12 주식회사 풍산 쾌삭성 무연 구리합금 및 이의 제조방법
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
DE102012013817A1 (de) 2012-07-12 2014-01-16 Wieland-Werke Ag Formteile aus korrosionsbeständigen Kupferlegierungen
US8991787B2 (en) 2012-10-02 2015-03-31 Nibco Inc. Lead-free high temperature/pressure piping components and methods of use
ES2704430T3 (es) 2012-10-31 2019-03-18 Kitz Corp Aleación de latón que presenta capacidad de reciclaje y resistencia a la corrosión
JP5778736B2 (ja) 2013-10-04 2015-09-16 ファナック株式会社 モータ冷却用の冷却管継手、および冷却管継手を備えるモータ冷却装置
JP6868761B2 (ja) * 2015-12-17 2021-05-12 パナソニックＩｐマネジメント株式会社 流体用開閉弁及びそれを用いた空気調和機
TWI598452B (zh) * 2016-01-21 2017-09-11 慶堂工業股份有限公司 具優異熔鑄性之無鉛快削黃銅合金及其製造方法和用途
JP6391204B2 (ja) 2016-08-15 2018-09-19 三菱伸銅株式会社 快削性銅合金加工材、及び、快削性銅合金加工材の製造方法
JP2018156771A (ja) * 2017-03-16 2018-10-04 住友電装株式会社 雌端子
US11155909B2 (en) 2017-08-15 2021-10-26 Mitsubishi Materials Corporation High-strength free-cutting copper alloy and method for producing high-strength free-cutting copper alloy
KR101969010B1 (ko) 2018-12-19 2019-04-15 주식회사 풍산 납과 비스무트가 첨가되지 않은 쾌삭성 무연 구리합금
CN109930025A (zh) * 2019-03-22 2019-06-25 广东出入境检验检疫局检验检疫技术中心 一种无铅环保易切削黄铜材料
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
WO2020261666A1 (ja) 2019-06-25 2020-12-30 三菱マテリアル株式会社 快削性銅合金、及び、快削性銅合金の製造方法
CN113348260B (zh) 2019-06-25 2022-09-16 三菱综合材料株式会社 易切削铜合金及易切削铜合金的制造方法
KR102623143B1 (ko) 2019-06-25 2024-01-09 미쓰비시 마테리알 가부시키가이샤 쾌삭성 구리 합금 주물, 및 쾌삭성 구리 합금 주물의 제조 방법
KR102914924B1 (ko) 2019-12-11 2026-01-19 미쓰비시 마테리알 가부시키가이샤 쾌삭성 구리 합금, 및 쾌삭성 구리 합금의 제조 방법
KR20240145044A (ko) 2019-12-11 2024-10-04 미쓰비시 마테리알 가부시키가이샤 쾌삭성 구리 합금, 및 쾌삭성 구리 합금의 제조 방법
GB2614752B (en) 2022-01-18 2024-07-31 Conex Ipr Ltd Components for drinking water pipes, and method for manufacturing same
WO2024090037A1 (ja) 2022-10-28 2024-05-02 日本碍子株式会社 鉛フリー快削ベリリウム銅合金
KR102799468B1 (ko) * 2022-12-08 2025-04-25 주식회사 대창 절삭성이 우수한 저실리콘계 무연 황동 합금

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB352639A (en) * 1930-02-13 1931-07-16 Hirsch Kupfer & Messingwerke Improvements in and relating to copper-silicon-zinc alloys
CH148824A (de) * 1930-03-31 1931-08-15 Hirsch Kupfer & Messingwerke Verfahren zur Herstellung von Kokillengruss- und Spritzgussteilen.
US1954003A (en) * 1930-03-31 1934-04-10 Vaders Eugen Copper alloy for chill and die casting
GB354966A (en) * 1930-05-24 1931-08-20 Hirsch Kupfer & Messingwerke The method of manufacturing bells
US2237774A (en) * 1940-07-23 1941-04-08 Chase Brass & Copper Co Treating silicon copper-base alloys
FR1031211A (fr) * 1951-01-19 1953-06-22 Alliage utilisable dans l'art dentaire
DE1558470A1 (de) * 1967-02-02 1970-03-19 Dies Dr Ing Kurt Fliesspressteil
US3736131A (en) * 1970-12-23 1973-05-29 Armco Steel Corp Ferritic-austenitic stainless steel
US3900349A (en) * 1974-01-18 1975-08-19 Anaconda Co Silicon brass resistant to parting corrosion
GB1443090A (en) * 1974-03-25 1976-07-21 Anaconda Co Silicon brass resistant to partin corrosion-
JPS5696040A (en) * 1979-12-28 1981-08-03 Seiko Epson Corp Exterior decorative part material for casting
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
JPH0368731A (ja) * 1989-08-08 1991-03-25 Nippon Mining Co Ltd ラジエータープレート用銅合金および銅合金材の製造法
JPH09143598A (ja) * 1995-11-22 1997-06-03 Chuetsu Gokin Chuko Kk 加熱装置用黄銅合金材料
JP3956322B2 (ja) * 1996-05-30 2007-08-08 中越合金鋳工株式会社 ワンウェイクラッチ用エンドベアリング及びその他の摺動部品
FR2765243B1 (fr) * 1997-06-30 1999-07-30 Usinor Acier inoxydable austenoferritique a tres bas nickel et presentant un fort allongement en traction

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2960350A1 (de) 2014-06-27 2015-12-30 Gebr. Kemper GmbH + Co. KG Metallwerke Kupfergusslegierung
EP3985136A1 (de) 2020-10-16 2022-04-20 Diehl Metall Stiftung & Co. KG Bleifreie kupferlegierung sowie verwendung der bleifreien kupferlegierung
DE102020127317A1 (de) 2020-10-16 2022-04-21 Diehl Metall Stiftung & Co. Kg Bleifreie Kupferlegierung sowie Verwendung der bleifreien Kupferlegierung

Also Published As

Publication number Publication date
DE69838115T2 (de) 2008-04-10
EP1600515B1 (de) 2008-07-30
EP1600516A3 (de) 2005-12-14
WO2000022182A1 (en) 2000-04-20
CA2314144C (en) 2006-08-22
EP1600515A2 (de) 2005-11-30
EP1600517B1 (de) 2009-02-18
AU744335B2 (en) 2002-02-21
DE69838115D1 (de) 2007-08-30
TW421674B (en) 2001-02-11
EP1600517A2 (de) 2005-11-30
EP1600515B8 (de) 2008-10-15
JP2000119775A (ja) 2000-04-25
EP1600516B1 (de) 2007-07-18
EP1045041B1 (de) 2005-10-26
EP1045041A1 (de) 2000-10-18
EP1600515A3 (de) 2005-12-14
DE69832097D1 (de) 2005-12-01
DE69832097T2 (de) 2006-07-06
EP1559802A1 (de) 2005-08-03
DE69839830D1 (de) 2008-09-11
DE69840585D1 (de) 2009-04-02
EP1559802B1 (de) 2014-01-15
JP3734372B2 (ja) 2006-01-11
EP1600517A3 (de) 2005-12-14
KR20010033073A (ko) 2001-04-25
AU1054199A (en) 2000-05-01
KR100352213B1 (ko) 2002-09-12
EP1045041A4 (de) 2003-05-07
CA2314144A1 (en) 2000-04-20

Similar Documents

Publication Publication Date Title
EP1045041B1 (de) Bleifreie automatenkupferlegierung
US6413330B1 (en) Lead-free free-cutting copper alloys
EP1038981B1 (de) Automatenlegierung auf kupferbasis
US20130276938A1 (en) Copper/zinc alloys having low levels of lead and good machinability
CA2619357C (en) Free-cutting copper alloy containing very low lead
US7056396B2 (en) Copper/zinc alloys having low levels of lead and good machinability
JP3903297B2 (ja) 耐脱亜鉛性銅基合金
JPWO2006016442A1 (ja) 結晶粒が微細化された銅基合金鋳物
JP4620963B2 (ja) 黄銅およびその製造方法ならびにこれを用いた部品
CN111655878A (zh) 不含有铅和铋的易切割无铅铜合金
KR20070023646A (ko) 결정립이 미세화된 구리기합금주물

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

PUAL Search report despatched

Free format text: ORIGINAL CODE: 0009013

17P Request for examination filed

Effective date: 20050808

AC Divisional application: reference to earlier application

Ref document number: 1045041

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: A2

Designated state(s): BE DE FI FR GB IT SE

AK Designated contracting states

Kind code of ref document: A3

Designated state(s): BE DE FI FR GB IT SE

AKX Designation fees paid

Designated state(s): BE DE FI FR GB IT SE

17Q First examination report despatched

Effective date: 20060726

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AC Divisional application: reference to earlier application

Ref document number: 1045041

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): BE DE FI FR GB IT SE

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 69838115

Country of ref document: DE

Date of ref document: 20070830

Kind code of ref document: P

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

ET Fr: translation filed
PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FI

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: 20070718

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

Effective date: 20070718

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: 20080421

REG Reference to a national code

Ref country code: GB

Ref legal event code: 732E

REG Reference to a national code

Ref country code: FR

Ref legal event code: TP

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 18

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 19

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 20

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

Ref country code: FR

Payment date: 20171127

Year of fee payment: 20

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

Ref country code: SE

Payment date: 20171130

Year of fee payment: 20

Ref country code: IT

Payment date: 20171127

Year of fee payment: 20

Ref country code: GB

Payment date: 20171130

Year of fee payment: 20

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

Ref country code: DE

Payment date: 20180124

Year of fee payment: 20

REG Reference to a national code

Ref country code: DE

Ref legal event code: R071

Ref document number: 69838115

Country of ref document: DE

REG Reference to a national code

Ref country code: GB

Ref legal event code: PE20

Expiry date: 20181115

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

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

Ref country code: GB

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20181115