EP1045041A1 - Leadless free-cutting copper alloy - Google Patents

Leadless free-cutting copper alloy Download PDF

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EP1045041A1
EP1045041A1 EP98953071A EP98953071A EP1045041A1 EP 1045041 A1 EP1045041 A1 EP 1045041A1 EP 98953071 A EP98953071 A EP 98953071A EP 98953071 A EP98953071 A EP 98953071A EP 1045041 A1 EP1045041 A1 EP 1045041A1
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remainder
weight
percent
alloy
machinability
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German (de)
French (fr)
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EP1045041A4 (en
EP1045041B1 (en
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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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Priority to EP05075421.7A priority Critical patent/EP1559802B1/en
Priority to EP05017191A priority patent/EP1600517B1/en
Priority to EP05017189A priority patent/EP1600515B8/en
Priority to EP05017190A priority patent/EP1600516B1/en
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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 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.
  • 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 ⁇ 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).
  • 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, Si0 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 ring-shaped 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.
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 7001 o ⁇ ⁇ 138 ⁇ 670 18 7002 o ⁇ ⁇ 136 ⁇ 712 20 7003 o ⁇ ⁇ 132 ⁇ 783 23 7004 o ⁇ ⁇ 138 ⁇ 736 21 7005 o ⁇ ⁇ 136 ⁇ 785 23 7006 o ⁇ ⁇ 139 ⁇ 700 24 7007 ⁇ ⁇ 138 ⁇ 707 23 7008 o ⁇ ⁇ 131 ⁇ 805 22 7009 o ⁇ ⁇ 136 ⁇ 768 19 7010 o ⁇ ⁇ 135 ⁇ 778 23 7011 ⁇ ⁇ 137 ⁇ 677 23 7012 o ⁇ ⁇ 134 ⁇ 800 21 7013 o ⁇ ⁇ 133 ⁇ 819 22 7014 ⁇ ⁇ 138 ⁇ 641 21 7015 o ⁇
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 7021 o ⁇ ⁇ 130 ⁇ 754 24 7022 o ⁇ ⁇ 134 ⁇ 780 23 7023 o ⁇ ⁇ 133 ⁇ 765 22 7024 o ⁇ ⁇ 135 ⁇ 772 23 7025 ⁇ ⁇ 138 ⁇ 687 24 7026 o ⁇ ⁇ 135 ⁇ 718 24 7027 o ⁇ ⁇ 136 ⁇ 742 18 7028 ⁇ ⁇ 138 ⁇ 785 20 7029 o ⁇ ⁇ 134 ⁇ 703 23 7030 o ⁇ ⁇ 135 ⁇ 820 18 No.
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 8001 o ⁇ ⁇ 132 ⁇ 655 15 8002 o ⁇ ⁇ 129 ⁇ 708 17 8003 o ⁇ ⁇ 127 ⁇ 768 20 8004 o ⁇ ⁇ 128 ⁇ 785 18 8005 o ⁇ ⁇ 131 ⁇ 714 16 8006 o ⁇ ⁇ 134 ⁇ 680 16 8007 o ⁇ ⁇ 132 ⁇ 764 17 8008 o ⁇ ⁇ 130 ⁇ 673 16 8009 o ⁇ ⁇ 132 ⁇ 759 18 8010 o ⁇ ⁇ 132 ⁇ 751 15 8011 o ⁇ ⁇ 134 ⁇ 767 17 8012 o ⁇ ⁇ 128 ⁇ 796 18 8013 o ⁇ ⁇ 129 ⁇ 784 18 8014 o ⁇ ⁇ 129 ⁇ 802
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 8021 o ⁇ ⁇ 134 ⁇ 765 16 8022 o ⁇ ⁇ 132 ⁇ 770 16 8023 o ⁇ ⁇ 131 ⁇ 746 18 8024 o ⁇ ⁇ 132 ⁇ 816 19 8025 o ⁇ ⁇ 129 ⁇ 759 18 8026 o ⁇ ⁇ 130 ⁇ 726 17 8027 o ⁇ ⁇ 133 ⁇ 703 17 8028 o ⁇ ⁇ 132 ⁇ 737 18 8029 o ⁇ ⁇ 129 ⁇ 719 20 8030 o ⁇ ⁇ 133 ⁇ 645 23 8031 o ⁇ ⁇ 129 ⁇ 764 22 8032 o ⁇ ⁇ 131 ⁇ 790 19 8033 o ⁇ ⁇ 133 ⁇ 674 20 8034 o ⁇ ⁇ 131 ⁇ 748
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 8041 o ⁇ ⁇ 128 ⁇ 735 23 8042 o ⁇ ⁇ 127 ⁇ 822 18 8043 o ⁇ ⁇ 131 ⁇ 780 18 8044 o ⁇ ⁇ 126 ⁇ 726 21 8045 o ⁇ ⁇ 128 ⁇ 766 22 8046 o ⁇ ⁇ 127 ⁇ 712 23 8047 o ⁇ ⁇ 128 ⁇ 674 21 8048 o ⁇ ⁇ 129 ⁇ 753 24 8049 o ⁇ ⁇ 127 ⁇ 768 22 8050 o ⁇ ⁇ 132 ⁇ 691 17 8051 o ⁇ ⁇ 131 ⁇ 717 17 8052 o ⁇ ⁇ 128 ⁇ 739 21 8053 o ⁇ ⁇ 128 ⁇ 730 22 8054 o ⁇ ⁇ 127 ⁇ 7
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 8061 o ⁇ ⁇ 129 ⁇ 705 21 8062 o ⁇ ⁇ 131 ⁇ 690 22 8063 o ⁇ ⁇ 133 ⁇ 811 18 8064 o ⁇ ⁇ 131 ⁇ 746 17 8065 o ⁇ ⁇ 133 ⁇ 652 19 8066 o ⁇ ⁇ 130 ⁇ 758 19 8067 o ⁇ ⁇ 129 ⁇ 734 19 8068 o ⁇ ⁇ 131 ⁇ 710 17 8069 o ⁇ ⁇ 131 ⁇ 767 20 8070 o ⁇ ⁇ 131 ⁇ 753 18 8071 o ⁇ ⁇ 129 ⁇ 792 19 8072 o ⁇ ⁇ 131 ⁇ 736 21 8073 o ⁇ ⁇ 130 ⁇ 767 22 8074 o ⁇ ⁇ 132 ⁇ 679 19
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 8081 o ⁇ ⁇ 132 ⁇ 706 23 8082 o ⁇ ⁇ 130 ⁇ 768 23 8083 o ⁇ ⁇ 128 ⁇ 774 25 8084 o ⁇ ⁇ 129 ⁇ 765 22 8085 o ⁇ ⁇ 130 ⁇ 729 23 8086 o ⁇ ⁇ 133 ⁇ 687 24 8087 o ⁇ ⁇ 131 ⁇ 798 20 8088 o ⁇ ⁇ 132 ⁇ 699 23 8089 o ⁇ ⁇ 130 ⁇ 740 21 8090 o ⁇ ⁇ 132 ⁇ 782 18 8091 o ⁇ ⁇ 129 ⁇ 763 22 8092 o ⁇ ⁇ 130 ⁇ 680 22 8093 o ⁇ ⁇ 131 ⁇ 655 23 8094 o ⁇ ⁇ 128 ⁇ 714 21 8095
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 8101 o ⁇ ⁇ 131 ⁇ 685 18 8102 o ⁇ ⁇ 132 ⁇ 690 21 8103 o ⁇ ⁇ 133 ⁇ 744 17 8104 o ⁇ ⁇ 130 ⁇ 726 17 8105 o ⁇ ⁇ 133 ⁇ 751 19 8106 o ⁇ ⁇ 130 ⁇ 752 21 8107 o ⁇ 131 ⁇ 760 21 8108 o ⁇ ⁇ 132 ⁇ 748 22 8109 o ⁇ ⁇ 130 ⁇ 807 18 8110 o ⁇ ⁇ 133 ⁇ 739 16 8111 o ⁇ ⁇ 132 ⁇ 717 17 8112 o ⁇ ⁇ 134 ⁇ 763 20 8113 o ⁇ ⁇ 129 ⁇ 745 22 8114 o ⁇ ⁇ 132 ⁇ 722 20 8
  • machinability hot workability mechanical properties form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm 2 ) elongation (%) 8121 o ⁇ ⁇ 130 ⁇ 788 20 8122 o ⁇ ⁇ 131 ⁇ 755 22 8123 o ⁇ ⁇ 127 ⁇ 711 21 8124 o ⁇ ⁇ 130 ⁇ 763 20 8125 o ⁇ ⁇ 131 ⁇ 687 18 8126 o ⁇ ⁇ 134 ⁇ 706 17 8127 o ⁇ ⁇ 128 ⁇ 730 22 8128 o ⁇ ⁇ 130 ⁇ 702 23 8129 o ⁇ ⁇ 132 ⁇ 727 21 8130 o ⁇ ⁇ 130 ⁇ 701 24 8131 o ⁇ ⁇ 129 ⁇ 745 22 8132 o ⁇ ⁇ 132 ⁇ 749 21 8133 o ⁇ ⁇ 130 ⁇ 826 18 8134 o ⁇ ⁇ 128 ⁇ 770 20 81
  • 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.

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Abstract

Lead-free copper alloys with industrially satisfactory machinability comprising 69 to 79 percent, by weight, of copper, 2.0 to 4.0 percent, by weight, of silicon, and the remaining percent, by weight, of zinc.

Description

BACKGROUND OF THE INVENTION 1. Field of The Invention
The present invention relates to lead-free, free-cutting copper alloys.
2. Prior Art
Among the copper alloys with a good machinability are 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.
However, the application of those lead-mixed alloys has been greatly limited in recent years, because 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.
On that ground, the United States and other advanced countries have been moving to tighten the standards for lead-contained copper alloys to drastically limit the permissible level of lead in copper alloys in recent years. In Japan, too, the use of lead-contained alloys has been increasingly restricted, and there has been a growing call for development of free-cutting copper alloys with a low lead content.
SUMMARY OF THE INVENTION
It is an object of the present invention to provide a lead-free copper alloy which does not contain the machinability-improving element lead yet is quite excellent in machinability and can be used as safe substitute for the conventional free cutting copper alloy with a large content of lead presenting environmental hygienic problems and which permits recycling of chips without problems, thus a timely answer to the mounting call for restriction of lead-contained products.
It is an another object of the present invention to provide a lead-free copper alloy which has a high corrosion resistance as well as an excellent machinability and is suitable as basic material for cutting works, forgings, castings and others, thus having a very high practical value. 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.
It is yet another object of the present invention to provide a lead-free copper alloy with a high strength and wear resistance as well as machinability which is suitable as basic material for the manufacture of cutting works, forgings, castings and other uses requiring a high strength and wear resistance such as, for example, bearings, bolts, nuts, bushes, gears, sewing machine parts and hydraulic system parts, hence has a very high practical value.
It is a further object of the present invention to provide a lead-free copper alloy with an excellent high-temperature oxidation resistance as well as machinability which is suitable as basic material for the manufacture of cutting works, forgings, castings and other uses where a high thermal oxidation resistance is essential, e.g. nozzles for kerosene oil and gas heaters, burner heads and gas nozzles for hot-water dispensers, hence has a very high practical value.
The objects of the present inventions are achieved by provision of the following copper alloys:
  • 1. A lead-free, free-cutting copper alloy with excellent machinability which is composed of 69 to 79 percent, by weight, of copper, 2.0 to 4.0 percent, by weight, of silicon, and the remaining percent, by weight, of zinc. For purpose of simplicity, this copper alloy will be hereinafter called the "first invention alloy." Lead forms no solid solution in the matrix but disperses in a granular form to improve the machinability. 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 common in that they are effective in improving the machinability, though they are quite different in contribution to the properties of the alloy. On the basis of that recognition, silicon is added to the first invention alloy in place of lead so as to bring about a high level of machinability meeting the industrial requirements. That is, the first invention alloy is improved in machinability through formation of a gamma phase with the addition of silicon.The addition of less than 2.0 percent, by weight, of silicon cannot form a gamma phase sufficient to secure an industrially satisfactory machinability. With the increase in the addition of silicon, the machinability improves. But with the addition of more than 4.0 percent, by weight, of silicon, the machinability will not go up in proportion. The problem is, however, that silicon has a high melting point and a low specific gravity and is also liable to oxidize. If silicon alone is fed in the form of a simple substance into a furnace in the alloy melting step, then silicon will float on the molten metal and is oxidized into oxides of silicon or silicon oxide, hampering production of a silicon-contained copper alloy. In making an ingot of silicon-containing copper alloy, therefore, silicon is usually added in the form of a Cu-Si alloy, which boosts the production cost. In the light of the cost of making the alloy, too, it is not desirable to add silicon in a quantity exceeding the saturation point where machinability improvement levels off - 4.0 percent by weight. An experiment showed that when silicon is added in an amount of 2.0 to 4.0 percent, by weight, it is desirable to hold the content of copper at 69 to 79 percent, by weight, in consideration of its relation to the content of zinc in order to maintain the intrinsic properties of the Cu-Zn alloy. For this reason, the first invention alloy is composed of 69 to 79 percent by weight, of copper and 2.0 to 4.0 percent, by weight, of silicon. 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 dezincification resistance will be improved to some extent.
  • 2. A lead-free, free-cutting copper alloy also with an excellent machinability feature which is composed of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; at least 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 the remaining percent, by weight, of zinc. This second copper alloy will be hereinafter called the "second invention alloy." That is, the second invention alloy is composed of the first invention alloy and at least 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.Bismuth, tellurium and selenium as well as lead do not form a solid solution in the matrix but disperse in granular form to enhance the machinability and that through a mechanism different from that of silicon. Hence, the addition of those elements along with silicon could further improve the machinability beyond the level obtained by the addition of silicon alone. From this finding, the second invention alloy is provided in which at least one element selected from bismuth, tellurium and selenium is mixed to improve further the machinability obtained by the first invention alloy. The addition of bismuth, tellurium or selenium in addition to silicon produces a high machinability such that complicated forms could be freely cut at a high speed. But no improvement in machinability can be realized from the addition of bismuth, tellurium or selenium in an amount less than 0.02 percent, by weight. Meanwhile, those elements are expensive as compared with copper. Even if the addition exceeds 0.4 percent by weight, the proportional improvement in machinability is so small that the addition beyond that does not pay economically. What is more, if the addition is more than 0.4 percent by weight, the alloy will deteriorate in hot workability such as forgeability and cold workability such as ductility. While it might be feared that heavy metals like bismuth would cause problems similar to those of lead, an addition in a very small amount of less than 0.4 percent by weight is negligible and would present no particular problems. From those considerations, the second invention alloy is prepared with the addition of bismuth, tellurium or selenium kept to 0.02 to 0.4 percent by weight. The addition of those elements, which work on 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. On this ground, the contents of copper and silicon in the second invention alloy are set at the same level as those in the first invention alloy.
  • 3. A lead-free, free-cutting copper alloy also with an excellent machinability which is composed of 70 to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by weight, of silicon; at least one element 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. This third copper alloy will be hereinafter called the "third invention alloy". Tin works the same way as silicon. That is, if tin is added to a Cu-Zn alloy, a gamma phase will be formed and the machinability of the Cu-Zn alloy will be improved. For example, the addition of tin in an 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 added. 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 an 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 less than 1.0 percent by weight, on the other hand, no gamma phase will be formed. If the addition is 0.3 percent or more 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 not smaller than 0.3 percent by weight improves the machinability.Aluminum is, too, effective in promoting the formation of the gamma phase. The addition of aluminum together with tin or in place of tin could further improve the machinability of the Cu-Si-Zn. 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 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 affect the ductility as is the case with aluminum.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. In addition to dispersing the gamma phase, 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 an 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.In consideration of those observations, the third invention alloy is improved in machinability by adding to the Cu-Si-Zn alloy at least one element 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.Meanwhile, 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. In the third invention alloy mixed with silicon along with tin, aluminum or phosphorus, therefore, machinability is improved by not only silicon, but by tin, aluminium or phosphorus and thus the required addition of silicon is smaller than that in the second invention alloy in which the machinability is enhanced by adding bismuth, tellurium or selenium. That is, those 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, the addition of tin, aluminum or phosphorus 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 third invention alloy. Also, in consideration of the added amount of silicon and also the addition of tin, aluminum or phosphorus, the content range of copper in this third invention alloy is slightly raised from the level in the second invention alloy and is set at 70 to 80 percent by weight as preferred content of copper.
  • 4. A lead-free, 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; at least one element 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; at least 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 the remaining percent, by weight, of zinc. This fourth copper alloy will be hereinafter called the "fourth invention alloy". The fourth invention alloy thus contains at least 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 in addition to the components in the third invention alloy. The grounds for adding those additional elements and setting the amounts to be added are the same as given for the second invention alloy.
  • 5. A lead-free, free-cutting copper alloy with an excellent machinability and with a high corrosion resistance which is composed of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; at least one element selected from among 0.3 to 3.5 percent, by weight, of tin, 0.02 to 0.25 percent, by weight, of phosphorus, 0.02 to 0.15 percent, by weight, of antimony, and 0.02 to 0.15 percent, by weight, of arsenic, and the remaining percent, by weight, of zinc. This fifth copper alloy will be hereinafter called the "fifth invention alloy". The fifth invention alloy thus contains at least one element selected from among 0.3 to 3.5 percent, by weight, of tin, 0.02 to 0.25 percent, by weight, of phosphorus, 0.02 to 0.15 percent, by weight, of antimony, and 0.02 to 0.15 percent, by weight, of arsenic in addition to the first invention alloy.Tin is effective in improving not only the machinability but also corrosion resistance properties (dezincification resistance and erosion corrosion resistance) and forgeability. In other words, 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. The fifth invention alloy is thus improved in corrosion resistance by such property of tin and in machinability mainly by adding silicon. Therefore, the contents of silicon and copper in this alloy are set at the same as those in the first invention alloy. To raise the corrosion resistance and forgeability, on the other hand, tin would have to be added in an 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 added amount of tin. It is no good economy.As described above, 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 resistance and erosion corrosion resistance), forgeability, stress corrosion cracking resistance and mechanical strength. The fifth invention alloy is thus improved in corrosion resistance and others by such properties of phosphorus and in machinability mainly by adding silicon. The addition of phosphorus in a very small quantity, that is, 0.02 or more percent by weight could produce results. But the addition in an amount of more than 0.25 percent by weight would not produce proportional results. Instead, that would reduce the hot forgeability and extrudability.Just as phosphorus, antimony and arsenic in a very small quantity - 0.02 or more percent by weight - are effective in improving the dezincification resistance and other properties. But the addition exceeding 0.15 percent by weight would not produce results in proportion to the quantity mixed. Instead, it would lower the hot forgeability and extrudability as phosphorus applied in excessive amounts.Those observations indicate that the fifth invention alloy is improved in machinability and also corrosion resistance and other properties by adding at least one element selected from among tin, phosphorus, antimony and arsenic in quantities within the aforesaid limits in addition to the same quantities of copper and silicon as in the first invention copper alloy. In the fifth invention alloy, the additions of copper and silicon are set at 69 to 79 percent by weight and 2.0 to 4.0 percent by weight respectively - the same level as in the first invention alloy in which any other machinability improver than silicon is not added - because tin and phosphorus work mainly as corrosion resistance improver like antimony and arsenic.
  • 6. A lead-free free-cutting copper alloy also with an excellent machinability and with a high corrosion resistance which is composed of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; at least one element selected from among 0.3 to 3.5 percent, by weight, of tin, 0.02 to 0.25 percent, by weight, of phosphorus, 0.02 to 0.15 percent, by weight, of antimony, and 0.02 to 0.15 percent, by weight, of arsenic; at least 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 the remaining percent, by weight, of zinc. This sixth copper alloy will be hereinafter called the "sixth invention alloy". The sixth invention alloy thus contains at least 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 in addition to the components in the fifth invention alloy. The machinability is improved by adding silicon and at least one element selected from among bismuth, tellurium and selenium as in the second invention alloy and the corrosion resistance and other properties are raised by using at least one selected from among tin, phosphorus, antimony and arsenic as in the fifth invention alloy. Therefore, the additions of copper, silicon, bismuth, tellurium and selenium are set at the same levels as those in the second invention alloy, while the contents of tin, phosphorus, antimony and arsenic are adjusted to those in the fifth invention alloy.
  • 7. A lead-free free-cutting copper alloy also with an excellent machinability and with an excellent high strength feature and high corrosion resistance which is composed of 62 to 78 percent, by weight, of copper; 2.5 to 4.5 percent, by weight, of silicon; at least one element selected from among 0.3 to 3.0 percent, by weight, of tin, 0.2 to 2.5 percent, by weight, of aluminum, and 0.02 to 0.25 percent, by weight, of phosphorus; and at least one element selected from among 0.7 to 3.5 percent, by weight, of manganese and 0.7 to 3.5 percent, by weight, of nickel; and the remaining percent, by weight, of zinc. The seventh copper alloy will be hereinafter called the "seventh invention alloy". Manganese and nickel combine with silicon to form intermetallic compounds represented by MnxSiy or NixSiy which are evenly precipitated in the matrix, thereby raising the wear resistance and strength. Therefore, the addition of manganese and/or nickel would improve the high strength feature and wear resistance. Such effects will be exhibited if manganese and nickel are added in an amount not smaller than 0.7 percent by weight respectively. But the saturation state is reached at 3.5 percent by weight, and even if the addition is increased beyond that, no proportional results will be obtained. The addition of silicon is set at 2.5 to 4.5 percent by weight to match the addition of manganese or nickel, taking into consideration the consumption to form intermetallic compounds with those elements.It is also noted that tin, aluminum and phosphorus help to reinforce the alpha phase in the matrix, thereby improving strength, wear resistance, and also machinability. Tin and phosphorus disperse the alpha and gamma phases, by which the strength, wear resistance and also machinability are improved. Tin in an amount of 0.3 or more percent by weight is effective in improving the strength and machinability. But if the addition exceeds 3.0 percent by weight, the ductility will fall. For this reason, the addition of tin is set at 0.3 to 3.0 percent by weight to raise the high strength feature and wear resistance in the seventh invention alloy and also to enhance the machinability. Aluminum also contributes to improving the wear resistance and exhibits its effect of reinforcing the matrix when added in 0.2 or more percent by weight. But if the addition exceeds 2.5 percent by weight, there will be a fall in ductility. Therefore, the addition of aluminum is set at 0.2 to 2.5 in consideration of improvement of machinability. Also, the addition of phosphorus disperses the gamma phase and at the same time refines the crystal grains in the alpha phase in the matrix, thereby improving the hot workability and also the strength and wear resistance. Furthermore, it is very effective in improving the flow of molten metal in casting. Such results will be produced when phosphorus is added in the range of 0.02 to 0.25 percent by weight. The content of copper is set at 62 to 78 percent by weight in the light of the addition of silicon and bonding of silicon with manganese and nickel.
  • 8. A lead-free, free-cutting copper alloy also with an excellent machinability and with an excellent high strength feature and a high wear resistance which comprises 62 to 78 percent, by weight, of copper; 2.5 to 4.5 percent, by weight, of silicon; at least one element selected from among 0.3 to 3.0 percent, by weight, of tin, 1.0 to 2.5 percent, by weight, of aluminum, and 0.02 to 0.25 percent, by weight, of phosphorus; and at least one element selected from among 0.7 to 3.5 percent, by weight, of manganese and 0.7 to 3.5 percent, by weight, of nickel; at least one 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 the remaining percent, by weight, of zinc. The eighth copper alloy will be hereinafter called the "eighth invention alloy". The eighth copper alloy contains at least 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 in addition to the components in the seventh invention alloy. While as high a high-strength feature and wear resistance as in the seventh invention alloy is secured, the eighth invention alloy is further improved in machinability by adding at least one element selected among bismuth and other elements which are effective in raising the machinability through a mechanism different from that exhibited by silicon. The reasons for adding machinability improvers such as bismuth and others and deciding on the quantities to be added are the same as given for the second, fourth and sixth invention alloys. The grounds for adding the other elements copper, zinc, tin, manganese and nickel and setting the contents are the same as given for the seventh alloy.
  • 9. A lead-free, free-cutting copper alloy also with excellent machinability coupled with a good high-temperature oxidation resistance which is composed of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; and the remaining percent, by weight, of zinc. The ninth copper alloy will be hereinafter called the "ninth invention alloy". Aluminum is an element which improves the strength, machinability, wear resistance and also high-temperature oxidation resistance. Silicon, too, has a property of enhancing the machinability, strength, wear resistance, resistance to stress corrosion cracking and also high-temperature oxidation resistance, as mentioned above . Aluminum works to raise the high-temperature oxidation resistance when aluminium is added in an amount not less than 0.1 percent by weight together with silicon. But even if the addition of aluminum increases beyond 1.5 percent by weight, no proportional results can be expected. For this reason, the addition of aluminum is set at 0.1 to 1.5 percent by weight. Phosphorus is added to enhance the flow of molten metal in casting. Phosphorus also works for improvement of the aforesaid machinability, dezincification resistance and also high-temperature oxidation resistance in addition to the flow of molten metal. Those effects are exhibited when phosphorus is added in an amount not less than 0.02 percent by weight. But even if phosphorus is used in more than 0.25 percent by weight, it will not result in a proportional increase in effect. For this consideration, the addition of phosphorus settles down on 0.02 to 0.25 percent by weight.While silicon is added to improve the machinability as mentioned above, it is also capable of increasing the flow of molten metal like phosphorus. The effect of silicon in raising the flow of molten metal is exhibited when it is added in an amount not less than 2.0 percent by weight. The range of the addition of silicon for improving the flow of molten metal overlaps that for improvement of the machinability. These taken into consideration, the addition of silicon is set to 2.0 to 4.0 percent by weight.
  • 10. A lead-free, free-cutting copper alloy also with excellent machinability and a good high-temperature oxidation resistance which is composed of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at least one element selected from among 0.02 to 0.4 percent, by weight, of chromium and 0.02 to 0.4 percent, by weight, of titanium; and the remaining percent, by weight, of zinc. The tenth copper alloy will be hereinafter called the "tenth invention alloy". Chromium and titanium are added for improving the high-temperature oxidation resistance. Good results can be expected especially when they are added together with aluminum to produce a synergistic effect. Those effects are exhibited when the addition is 0.02 percent or more by weight, whether they are used alone or in combination. The saturation point is 0.4 percent by weight. In consideration of such observations, the tenth invention alloy contains at least one element selected from among 0.02 to 0.4 percent by weight of chromium and 0.02 to 0.4 percent by weight of titanium in addition to the components of the ninth invention alloy and is an improvement over the ninth invention alloy with regard to the high-temperature oxidation resistance.
  • 11. A lead-free, free-cutting copper alloy also with excellent machinability and a good high-temperature oxidation resistance which is composed of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at least 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 the remaining percent, by weight, of zinc. The eleventh copper alloy will be hereinafter called the "eleventh invention alloy". The eleventh invention alloy contains at least 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 an 0.02 to 0.4 percent, by weight, of selenium in addition to the components of the ninth invention alloy. While as high a high-temperature oxidation resistance as in the ninth invention alloy is secured, the eleventh invention alloy is further improved in machinability by adding at least one element selected from among bismuth and other elements which are effective in raising the machinability through a mechanism other than that exhibited by silicon.
  • 12. A lead-free, free-cutting copper alloy also with excellent machinability and a good high-temperature oxidation resistance which is composed of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at least one element selected from among 0.02 to 0.4 percent, by weight, of chromium, and 0.02 to 0.4 percent by weight of titanium; at least 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 the remaining percent, by weight, of zinc. The twelfth copper alloy will be hereinafter called the "twelfth invention alloy". The twelfth invention alloy contains at least 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 in addition to the components of the tenth invention alloy. While as high a high-temperature oxidation resistance as in the tenth invention alloy is secured, the twelfth invention alloy is further improved in machinability by adding at least one element selected from among bismuth and other elements which are effective in raising the machinability through a mechanism other than that exhibited by silicon.
  • 13. A lead-free, free-cutting copper alloy also with further improved machinability obtained by subjecting any one of the preceding invention alloys to a heat treatment for 30 minutes to 5 hours at 400°C to 600° C. The thirteenth copper alloy will be hereinafter called the "thirteenth invention alloy".
    • 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. Of those invention alloys, 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. In the 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. But in case cold working such as caulking and cutting are required, the aforesaid heat treatment is very useful. In other words, among the first to twelfth invention alloys, those which are high in copper content with gamma phase in small quantities and kappa phase in large quantities (hereinafter referred to as the "high copper content alloy") undergo a change in phase from the kappa phase to the gamma phase in a heat treatment. As a result, the gamma phase is finely dispersed and precipitated, and the machinability is improved. In the manufacturing process of castings, expanded metals and hot forgings in practice, 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. In such cases, among the first to twelfth invention alloys, 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. In a heat treatment, the beta phase changes into gamma phase, and the gamma phase is finely dispersed and precipitated, whereby the machinability is improved. Experiments showed that heat treatment is especially effective with high copper content alloys where mixing ratio of copper and silicon to other added elements (except for zinc) A is given as 67 ≤ Cu - 3Si + aA or low copper content alloys with such a composition with 64 ≥ Cu - 3Si + aA. It is noted that a is a coefficient. The coefficient is different depending on the added element A. For example, with tin a is - 0.5; aluminum, -2; phosphorus, -3; antimony, 0; arsenic, 0; manganese, +2.5; and nickel, +2.5.
    But a heat treatment temperature at less than 400°C is not economical and practical, because the aforesaid phase change will proceed slowly and much time will be needed. At temperatures over 600 C, on the other hand, the kappa phase will grow or the beta phase will appear, bringing about no improvement in machinability. From the practical viewpoint, therefore, it is desired to perform the heat treatment for 30 minutes to 5 hours at 400 to 600 C.
    BRIEF DESCRIPTION OF THE DRAWING
  • Fig. 1 shows perspective views of cuttings formed in cutting a round bar of copper alloy by lathe.
    • DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Example 1
    As the first series of examples of the present invention, cylindrical ingots with compositions given in Tables 1 to 35, 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 the following test pieces: 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. 11001 to 11007, and twelfth invention alloys Nos. 12001 to 12021. Also, cylindrical ingots with the compositions given in Table 36, 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 the following test pieces: thirteenth invention alloys Nos. 13001 to 13006. That is, No. 13001 is an alloy test piece obtained by heat-treating an extruded test piece with the same composition as first invention alloy No. 1005 for 30 minutes at 580°C. No. 13002 is an alloy test piece obtained by heat-treating an extruded test piece with the same composition as No. 13001 for two hours at 450°C. 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.
    As comparative examples, cylindrical ingots with the compositions as shown in Table 37, 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 obtain the following round extruded test pieces: Nos. 14001 to 14006 (hereinafter referred to as the "conventional alloys"). No. 14001 corresponds to the alloy "JIS C 3604," No. 14002 to the alloy "CDA C 36000," No. 14003 to the alloy "JIS C 3771" and No. 14004 to the alloy "CDA C 69800." No. 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.
    To study the machinability of the first to thirteenth invention alloys in comparison with the conventional alloys, cutting tests were carried out. In the tests, evaluations were made on the basis of cutting force, condition of chips cut surface condition.
    The tests were conducted this way: The extruded test pieces obtained, as mentioned above, were cut on the circumferential surface by a lathe mounted with a point noise straight tool at a rake angle of - 8 degrees and at a cutting rate of 50 meters/minute, a cutting depth of 1.5 mm, a feed of 0.11 mm/rev. Signals from a three-component dynamometer mounted on the tool were converted into electric voltage signals and recorded on a recorder. From the signals were then calculated the cutting resistance. It is noted that while, to be perfectly exact, an amount of the cutting resistance should be judged by three component forces - cutting force, feed force and thrust force, the judgement was made on the basis of the cutting force (N) of the three component forces in the present example. The results are shown in Table 38 to Table 66.
    Furthermore, 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. In this regard, 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 an arc with a half winding to a spiral with two about windings as shown in (C), Fig. 1 do not cause such serous trouble as the chips in the form of a spiral with three or more windings yet are not easy to remove and could get tangled with the tool or damage the cut metal surface. In contrast, 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. Those taken into account, it is appropriate to consider that the chips in (B) are the best, and the second best are the chips in (A). Those in (C) and (D) are not good. In Table 38 to Table 66, the chips judged to be shown in (B), (A), (C) and (D) are indicated by the symbols "o ○", "o", "▵" and "x" respectively.
    In addition, the surface condition of the cut metal surface was checked after cutting work. The results are shown in Table 38 to Table 66. In this regard, 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. In Table 38 to Table 65, the alloys with Rmax < 10 microns are marked "o", those with 10 microns ≤ Rmax < 15 microns are indicated as "▵" and those with Rmax ≥ 15 microns are represented by a symbol "x".
    As is evident from the results of the cutting tests shown in Table 38 to Table 66, 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. 11001 to 11007, twelfth invention alloys Nos. 12001 to 12021. Especially with regard to formation of the chips, those invention alloys are favourably compared not only with the conventional alloys Nos. 14004 to 14006 with a lead content of not higher than 0.1 percent by weight but also Nos. 14001 to 14003 which contain large quantities of lead.
    Also to be noted is that as is clear from Tables Nos. 38 to 65, 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.
    In another series of tests, the first to thirteenth invention alloys were examined in comparison with the conventional alloys in hot workability and mechanical properties. For the purpose, hot compression and tensile tests were conducted the following way.
    First, 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. In the hot compression tests, 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) was visually evaluated. 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/mm2 and elongation, %.
    As the test results of the hot compression and tensile tests in Table 38 to Table 66 indicate, it was confirmed that 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.
    Furthermore, the 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.
    In the dezincification test by the "ISO 6509" method, a sample taken from each extruded test piece was imbedded in a phenolic resin material in such a way that part of the side surface of the sample is exposed, the exposed surface perpendicular to the extrusion direction of the extruded test piece. The surface of the example was polished with emery paper No. 1200, and then ultrasonic-washed in pure water and dried. The sample thus prepared was dipped in a 12.7 g/l aqueous solution of cupric chloride dihydrate (CuCl2.2H2O) 1.0% and left standing for 24 hours at 75°C. The sample was taken out of the aqueous solution and the maximum depth of dezincification was determined. The measurements of the maximum dezincification depth are given in Table 38 to Table 50 and Table 61 to Table 66.
    As is clear from the results of dezincification tests shown in Table 38 to Table 50 and Table 61 to Table 66, 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.
    In the stress corrosion cracking tests in accordance with the test method described in "JIS H 3250," a 150-mm-long 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. 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. In those tables, 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."
    As is indicated by the results of the stress corrosion cracking test given in Table 38 to Table 50 and Table 61 to Table 66, it was confirmed that not only the fifth and sixth invention alloys which seek improvement in both machinability and corrosion resistance but also the first to fourth invention alloys and the ninth and thirteenth alloys in which nothing particular was done to improve corrosion resistance were both equal to the conventional alloy No. 14005, an aluminum bronze containing no zinc, in stress corrosion cracking resistance and were superior in stress corrosion cracking resistance to the conventional naval brass alloy No. 14006, the one which has a highest corrosion resistance of all the expanded copper alloys under the JIS designations.
    In addition, oxidation tests were carried out to study the high-temperature oxidation resistance of the ninth to twelfth invention alloys in comparison with the conventional alloys.
    A 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. It is understood that the increase by oxidation is an amount, mg, of increase in weight by oxidation per 10cm2 of the surface area of the test piece and is calculated by the equation: increase in weight by oxidation, mg/10cm2 = (weight, mg, after oxidation - weight, mg, before oxidation) x (10cm2 / surface area, cm2, of test piece). 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 Cu2O, ZnO, Si02. 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. The results obtained are shown in Table 61 to Table 64 and Table 66.
    As is evident from the test results 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. Thus, it was confirmed that the ninth to twelfth invention alloys are very excellent in machinability and resistance to high-temperature oxidation as well.
    Example 2
    As the second series of examples of the present invention, cylindrical ingots with compositions given in Tables 14 to 31, each 100 mm in outside diameter and 200 mm in length, were hot extruded into a round bar 35 mm in outside diameter at 700 C to produce the following test pieces: seventh invention alloys Nos. 7001a to 7030a and eighth invention alloys Nos. 8001a to 8147a. In parallel, cylindrical ingots with compositions given in Table 37, each 100 mm in outside diameter and 200 mm in length, were hot extruded into a round bar 35 mm in outside diameter at 700 C to produce the following alloy test pieces: Nos. 14001a to 14006a as second comparative examples (hereinafter referred to as the "conventional alloys"). It is noted that the 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.
    Those seventh invention alloys Nos. 7001a to 7030a and eighth invention alloys Nos. 8001a to 8147a were put to wear resistance tests in comparison with the conventional alloys Nos. 14001a to 14006a.
    The tests were carried out in this procedure. Each extruded test piece thus obtained was cut on the circumferential surface, holed and cut down into a ring-shaped 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. Then, the SUS 304 roll and the test piece put in rotational sliding contact with the roll were rotated at the same rate of revolutions/minute - 209 r.p.m., with multipurpose gear oil being dropped onto the circumferential surface of the test piece. When the number of revolutions reached 100,000, the SUS 304 roll and the test piece were stopped, and the weight difference between the start and the end of rotation, that is, the loss of weight by wear, mg, was determined. It can be said that the alloys which are smaller in the loss of weight by wear are higher in wear resistance. The results are given in Tables 67 to 77.
    As is clear from the wear resistance test results shown in Tables 67 to 77, the tests showed that those seventh invention alloys Nos. 7001a to 7030a and eighth invention alloys Nos. 8001a to 8147a were excellent in wear resistance as compared with not only the conventional alloys Nos. 14001a to 14004a and 14006a but also No. 14005a, which is an aluminium bronze having a highest wear resistance of the expanded copper alloys under the JIS designations. From comprehensive considerations of the test results including the tensile test results, it may safely be said that the seventh and eighth invention alloys are excellent in machinability and also possess a higher strength feature and wear resistance than the aluminum bronze which is the highest in wear resistance of all the expanded copper alloys under the JIS designations.
    No. alloy composition (wt%)
    Cu Si Zn
    1001 70.2 2.1 remainder
    1002 74.1 2.9 remainder
    1003 74.8 3.1 remainder
    1004 77.6 3.7 remainder
    1005 78.5 3.2 remainder
    1006 73.3 2.4 remainder
    1007 77.0 2.9 remainder
    1008 69.9 2.3 remainder
    No. alloy composition (wt%)
    Cu Si Bi Te Se Zn
    2001 74.5 2.9 0.05 remainder
    2002 74.8 2.8 0.25 remainder
    2003 75.0 2.9 0.13 remainder
    2004 69.9 2.1 0.32 0.03 remainder
    2005 72.4 2.3 0.11 0.31 remainder
    2006 78.2 3.4 0.14 0.03 remainder
    2007 76.2 2.9 0.03 0.05 0.12 remainder
    2008 78.2 3.7 0.33 remainder
    2009 73.0 2.4 0.16 remainder
    2010 74.7 2.8 0.04 0.30 remainder
    2011 76.3 3.0 0.18 0.12 remainder
    No. 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%)
    Cu Si Sn Al Bi Te Se Zn
    4001 70.8 1.9 3.4 0.36 remainder
    4002 76.3 3.4 1.3 0.03 remainder
    4003 73.2 2.5 1.9 0.15 remainder
    4004 72.3 2.4 0.6 0.29 0.23 remainder
    4005 74.2 2.7 2.0 0.03 0.26 remainder
    4006 75.4 2.9 0.4 0.31 0.03 remainder
    4007 71.5 2.1 2.6 0.11 0.05 0.23 remainder
    4008 79.1 1.9 3.3 0.28 remainder
    4009 76.3 2.7 1.2 0.13 remainder
    4010 77.2 2.5 2.0 0.07 remainder
    4011 79.2 3.1 1.1 0.04 0.06 remainder
    4012 76.3 2.3 1.3 0.13 0.04 remainder
    4013 77.4 2.6 2.6 0.22 0.03 remainder
    4014 77.9 2.2 2.3 0.09 0.05 0.11 remainder
    4015 73.5 2.0 2.9 1.2 0.23 remainder
    4016 76.3 2.5 0.7 3.2 0.04 remainder
    4017 75.5 2.3 1.2 2.0 0.12 remainder
    4018 77.1 2.1 0.9 3.4 0.03 0.03 remainder
    4019 72.9 3.2 3.3 1.7 0.11 0.04 remainder
    4020 74.2 2.8 2.7 1.1 0.33 0.03 remainder
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Zn
    4021 74.2 2.3 1.5 2.3 0.07 0.05 0.09 remainder
    4022 70.9 2.1 0.11 0.11 remainder
    4023 74.8 3.1 0.07 0.06 remainder
    4024 76.3 3.2 0.05 0.02 remainder
    4025 78.1 3.1 0.26 0.02 0.15 remainder
    4026 71.1 2.2 0.13 0.02 0.05 remainder
    4027 74.1 2.7 0.03 0.06 0.03 0.03 remainder
    4028 70.6 1.9 3.2 0.31 0.04 remainder
    4029 73.6 2.4 2.3 0.03 0.04 remainder
    4030 73.4 2.6 1.7 0.31 0.22 remainder
    4031 74.8 2.9 0.5 0.03 0.02 0.05 remainder
    4032 73.0 2.6 0.7 0.09 0.02 0.08 remainder
    4033 74.5 2.8 0.03 0.12 0.05 remainder
    4034 77.2 3.3 1.3 0.03 0.12 0.04 remainder
    4035 74.9 3.1 0.4 0.02 0.05 0.05 0.08 remainder
    4036 79.2 3.3 2.5 0.05 0.12 remainder
    4037 74.2 2.6 1.2 0.12 0.05 remainder
    4038 77.0 2.8 1.3 0.05 0.20 remainder
    4039 76.0 2.4 3.2 0.10 0.04 0.05 remainder
    4040 74.8 2.4 1.1 0.07 0.04 0.03 remainder
    No. 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%)
    Cu Si Sn P Sb As Zn
    5001 69.9 2.1 3.3 remainder
    5002 74.1 2.7 0.21 remainder
    5003 75.8 2.4 0.14 remainder
    5004 77.3 3.4 0.05 remainder
    5005 73.4 2.4 2.1 0.04 remainder
    5006 75.3 2.7 0.4 0.04 remainder
    5007 70.9 2.2 2.4 0.07 remainder
    5008 71.2 2.6 1.1 0.03 0.03 remainder
    5009 77.3 2.9 0.7 0.19 0.03 remainder
    5010 78.2 3.1 0.4 0.09 0.15 remainder
    5011 72.5 2.1 2.8 0.02 0.10 0.03 remainder
    5012 79.0 3.3 0.24 0.02 remainder
    5013 75.6 2.9 0.07 0.14 remainder
    5014 74.8 3.0 0.11 0.02 remainder
    5015 74.3 2.8 0.06 0.02 0.03 remainder
    5016 72.9 2.5 0.03 remainder
    5017 77.0 3.4 0.14 remainder
    5018 76.8 3.2 0.7 0.12 remainder
    5019 74.5 2.8 1.8 remainder
    5020 74.9 3.0 0.20 0.05 remainder
    No. alloy composition (wt%)
    Cu Si Sn Bi Te P Sb As Zn
    6001 69.6 2.1 3.2 0.15 remainder
    6002 77.3 3.7 0.5 0.02 0.23 remainder
    6003 75.2 2.4 1.1 0.33 0.12 remainder
    6004 70.9 2.3 3.1 0.11 0.03 remainder
    6005 78.1 2.7 0.6 0.14 0.02 0.07 remainder
    6006 74.5 2.6 1.5 0.21 0.10 0.04 remainder
    6007 74.7 3.2 2.1 0.05 0.02 0.12 remainder
    6008 73.8 2.5 0.7 0.31 0.03 0.02 0.10 remainder
    6009 74.5 2.9 0.05 0.19 remainder
    6010 78.1 3.1 0.11 0.15 remainder
    6011 74.6 3.3 0.02 0.22 remainder
    6012 69.9 2.3 0.35 0.08 0.02 remainder
    6013 73.2 2.6 0.21 0.03 0.07 remainder
    6014 76.3 2.9 0.07 0.09 0.02 remainder
    6015 74.4 2.8 0.19 0.13 0.03 0.02 remainder
    6016 70.5 2.3 2.9 0.10 0.02 remainder
    6017 74.7 2.4 0.9 0.31 0.04 0.05 remainder
    6018 78.1 3.8 0.6 0.02 0.33 0.07 remainder
    6019 69.4 2.0 3.4 0.11 0.03 0.03 remainder
    6020 77.8 2.8 0.5 0.06 0.11 0.21 0.02 remainder
    No. alloy composition (wt%)
    Cu Si Sn Bi Te Se P Sb As Zn
    6021 74.2 2.6 0.6 0.20 0.03 0.02 0.14 remainder
    6022 75.8 3.3 1.8 0.03 0.06 0.11 0.02 remainder
    6023 74.4 2.6 1.5 0.09 0.12 0.03 0.02 0.06 remainder
    6024 77.3 3.1 0.02 0.25 0.08 remainder
    6025 70.5 2.4 0.12 0.04 0.06 0.03 remainder
    6026 74.3 2.9 0.24 0.02 0.13 0.11 remainder
    6027 69.8 2.3 0.34 0.03 0.21 0.02 0.02 remainder
    6028 74.5 2.9 0.03 0.11 0.13 remainder
    6029 78.4 3.2 0.02 0.08 0.04 0.05 remainder
    6030 73.8 3.0 0.08 0.31 0.23 remainder
    6031 72.8 2.5 1.6 0.11 0.36 remainder
    6032 78.1 3.7 0.5 0.03 0.02 0.05 remainder
    6033 77.2 2.8 0.6 0.09 0.04 0.07 remainder
    6034 76.9 3.8 0.4 0.03 0.06 0.07 remainder
    6035 74.1 2.3 3.3 0.06 0.03 0.02 0.05 remainder
    6036 69.8 2.0 2.5 0.31 0.12 0.03 0.06 remainder
    6037 74.9 3.0 1.1 0.07 0.21 0.12 0.02 remainder
    6038 72.6 2.8 0.6 0.20 0.05 0.21 0.07 0.03 remainder
    6039 69.7 2.3 0.23 0.06 0.10 remainder
    6040 75.4 3.0 0.02 0.09 0.11 0.03 remainder
    No. alloy composition (wt%)
    Cu Si Sn Bi Te Se P Sb As Zn
    6041 73.2 2.5 0.11 0.36 0.05 0.02 remainder
    6042 78.2 3.7 0.03 0.04 0.03 0.04 0.10 remainder
    6043 77.8 2.8 0.09 0.02 0.04 remainder
    6044 73.4 2.6 0.16 0.06 0.03 0.02 remainder
    6045 71.2 2.4 0.35 0.14 0.08 remainder
    6046 70.3 2.5 1.9 0.09 0.05 0.03 remainder
    6047 74.5 3.6 2.2 0.02 0.20 0.04 0.04 remainder
    6048 73.8 2.9 1.2 0.03 0.10 0.05 0.12 remainder
    6049 69.8 2.1 3.1 0.32 0.03 0.05 0.13 remainder
    6050 74.2 2.2 0.6 0.19 0.11 0.02 0.02 0.03 remainder
    6051 74.8 3.2 0.5 0.03 0.07 0.03 0.05 0.02 remainder
    6052 78.0 2.8 0.6 0.06 0.04 0.11 0.11 0.03 remainder
    6053 76.3 2.4 0.8 0.05 0.03 0.22 0.03 0.04 0.03 remainder
    6054 74.2 2.6 0.21 0.02 0.04 0.05 remainder
    6055 78.2 2.9 0.16 0.08 0.03 0.21 0.03 remainder
    6056 72.3 2.5 0.08 0.36 0.02 0.10 0.04 remainder
    6057 69.8 2.4 0.36 0.04 0.04 0.06 0.07 0.02 remainder
    6058 74.6 3.1 0.05 0.09 0.04 0.14 remainder
    6059 73.8 2.5 0.08 0.05 0.03 0.02 0.04 remainder
    6060 74.9 2.7 0.03 0.16 0.02 0.03 remainder
    No. alloy composition (wt%)
    Cu Si Sn Te Se P Sb As Zn
    6061 69.7 2.6 3.1 0.26 remainder
    6062 74.2 3.2 0.6 0.03 0.04 remainder
    6063 74.9 2.6 0.7 0.14 0.14 remainder
    6064 73.8 3.0 0.4 0.07 0.13 remainder
    6065 78.1 3.3 0.8 0.02 0.12 0.02 remainder
    6066 72.8 2.4 1.2 0.32 0.03 0.05 remainder
    6067 73.6 2.7 2.1 0.03 0.07 0.02 remainder
    6068 72.3 2.6 0.5 0.16 0.02 0.04 0.03 remainder
    6069 70.6 2.3 0.33 0.09 remainder
    6070 76.5 3.2 0.14 0.21 0.03 remainder
    6071 74.5 3.1 0.05 0.03 0.03 remainder
    6072 72.8 2.7 0.08 0.13 remainder
    6073 78.0 3.8 0.04 0.02 0.12 remainder
    6074 73.8 2.9 0.20 0.10 remainder
    6075 74.5 2.9 0.07 0.04 0.10 0.02 remainder
    6076 73.6 3.2 2.1 0.04 0.07 remainder
    6077 74.1 2.5 0.8 0.21 0.18 0.05 remainder
    6078 77.8 2.9 0.6 0.11 0.05 0.07 remainder
    6079 71.5 2.1 1.1 0.06 0.03 0.06 remainder
    6080 72.6 2.3 0.5 0.15 0.23 0.11 0.02 remainder
    No. alloy composition (wt%)
    Cu Si Sn Te Se P Sb As Zn
    6081 74.2 3.0 0.5 0.03 0.03 0.20 0.02 remainder
    6082 70.6 2.2 2.6 0.32 0.05 0.13 0.03 remainder
    6083 73.7 2.6 0.8 0.14 0.16 0.06 0.02 0.03 remainder
    6084 74.5 3.1 0.04 0.04 0.05 remainder
    6085 72.8 2.7 0.09 0.21 0.04 0.02 remainder
    6086 76.2 3.3 0.03 0.04 0.11 0.04 remainder
    6087 73.8 2.7 0.11 0.03 0.02 0.04 0.03 remainder
    6088 74.9 2.9 0.05 0.31 0.05 remainder
    6089 75.8 2.8 0.08 0.04 0.03 0.14 remainder
    6090 73.6 2.4 0.27 0.10 0.06 remainder
    6091 72.4 2.2 3.2 0.33 remainder
    6092 75.0 3.2 0.6 0.05 0.10 remainder
    6093 76.8 3.1 0.5 0.04 0.11 remainder
    6094 74.5 2.9 0.7 0.08 0.15 remainder
    6095 73.2 2.7 1.2 0.12 0.06 0.03 remainder
    6096 69.6 2.4 2.3 0.14 0.04 0.02 remainder
    6097 74.2 2.8 0.8 0.07 0.02 0.03 remainder
    6098 74.4 2.9 0.8 0.06 0.03 0.03 0.03 remainder
    6099 74.8 3.1 0.09 0.04 remainder
    6100 73.9 2.8 0.05 0.10 0.04 remainder
    No. alloy composition (wt%)
    Cu Si Se P Sb As Zn
    6101 76.1 3.0 0.04 0.05 0.02 remainder
    6102 74.5 2.8 0.03 0.04 0.02 0.03 remainder
    6103 74.3 2.6 0.31 0.04 remainder
    6104 75.0 3.3 0.06 0.02 0.05 remainder
    6105 73.9 2.9 0.10 0.11 remainder
    No. alloy composition (wt%)
    Cu Si Sn Al P Mn Ni Zn
    7001 62.9 2.7 2.6 2.2 remainder
    7001a
    7002 64.8 3.4 1.8 3.1 remainder
    7002a
    7003 68.2 4.1 0.6 1.9 1.5 remainder
    7003a
    7004 66.5 3.5 1.9 0.9 1.9 remainder
    7004a
    7005 71.3 3.7 0.4 1.8 2.3 remainder
    7005a
    7006 73.6 2.9 0.7 2.1 1.3 0.8 remainder
    7006a
    7007 70.1 3.2 0.5 1.4 0.11 1.8 remainder
    7007a
    7008 77.1 4.2 0.8 2.3 0.03 1.8 remainder
    7008a
    7009 67.3 3.7 2.6 0.2 0.08 0.9 1.8 remainder
    7009a
    7010 75.5 3.9 2.3 0.8 remainder
    7010a
    No. alloy composition (wt%)
    Cu Si Sn Al P Mn Ni Zn
    7011 69.8 3.4 0.3 1.3 remainder
    7011a
    7012 71.2 4.0 1.4 2.1 1.2 remainder
    7012a
    7013 73.3 3.9 2.0 0.03 3.2 remainder
    7013a
    7014 65.9 2.9 0.3 0.21 1.3 remainder
    7014a
    7015 68.8 3.9 1.1 0.05 0.9 2.0 remainder
    7015a
    7016 68.1 4.0 0.4 0.04 2.8 remainder
    7016a
    7017 63.8 2.6 2.7 0.19 0.9 remainder
    7017a
    7018 66.7 3.4 1.3 0.07 1.2 0.8 remainder
    7018a
    7019 67.2 3.6 0.21 1.9 remainder
    7019a
    7020 69.1 3.8 0.06 2.2 remainder
    7020a
    No. alloy composition (wt%)
    Cu Si Sn Al P Mn Ni Zn
    7021 72.1 4.3 0.07 2.0 0.8 remainder
    7021a
    7022 71.3 3.9 1.1 3.1 remainder
    7022a
    7023 70.5 3.5 1.6 2.3 remainder
    7023a
    7024 70.0 3.6 1.5 3.2 remainder
    7024a
    7025 69.3 2.7 2.1 0.9 remainder
    7025a
    7026 70.2 3.5 1.4 2.1 remainder
    7026a
    7027 65.0 2.8 2.6 2.3 0.8 remainder
    7027a
    7028 69.8 3.6 1.5 1.7 2.4 remainder
    7028a
    7029 71.0 3.6 0.4 0.3 2.2 remainder
    7029a
    7030 68.4 4.2 2.6 3.3 remainder
    7030a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se Mn Zn
    8001 62.6 2.6 2.6 0.31 1.9 remainder
    8001a
    8002 65.3 3.4 1.8 0.11 0.02 2.5 remainder
    8002a
    8003 66.4 4.2 0.5 0.05 0.03 3.4 remainder
    8003a
    8004 72.1 4.4 0.4 0.06 0.05 0.02 2.8 remainder
    8004a
    8005 67.4 3.3 2.3 0.31 0.9 remainder
    8005a
    8006 63.8 2.8 2.9 0.06 0.07 2.1 remainder
    8006a
    8007 71.5 3.9 1.5 0.20 1.4 remainder
    8007a
    8008 64.2 2.9 2.4 0.3 0.28 2.1 remainder
    8008a
    8009 68.8 3.4 1.0 1.5 0.07 0.20 1.7 remainder
    8009a
    8010 65.3 3.6 2.8 0.2 0.05 0.13 2.2 remainder
    8010a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Mn Zn
    8011 66.8 3.3 1.9 2.1 0.04 0.05 0.05 2.3 remainder
    8011a
    8012 75.1 4.1 0.4 2.4 0.03 1.8 remainder
    8012a
    8013 74.2 3.9 0.5 1.8 0.10 0.04 1.7 remainder
    8013a
    8014 77.1 4.2 0.4 2.1 0.32 2.0 remainder
    8014a
    8015 62.8 2.6 2.9 0.12 0.03 1.2 remainder
    8015a
    8016 64.4 2.9 2.7 0.23 0.09 0.13 1.8 remainder
    8016a
    8017 68.3 3.6 0.4 0.05 0.05 0.04 2.2 remainder
    8017a
    8018 73.2 4.3 0.5 0.06 0.02 0.11 0.02 3.1 remainder
    8018a
    8019 72.4 4.1 0.7 0.14 0.21 2.1 remainder
    8019a
    8020 69.5 3.7 0.7 0.06 0.04 0.05 1.9 remainder
    8020a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Mn Zn
    8021 64.2 3.4 2.5 0.31 0.03 1.9 remainder
    8021a
    8022 65.6 3.7 2.3 0.2 0.06 0.03 1.4 remainder
    8022a
    8023 67.1 3.6 0.4 0.5 0.04 0.05 0.05 2.0 remainder
    8023a
    8024 73.2 4.0 0.5 2.1 0.03 0.05 0.12 2.4 remainder
    8024a
    8025 68.8 3.5 0.4 1.8 0.12 0.03 0.03 0.04 1.8 remainder
    8025a
    8026 66.5 3.4 1.2 0.3 0.24 0.21 1.7 remainder
    8026a
    8027 64.8 3.0 1.3 1.2 0.16 0.10 0.06 1.5 remainder
    8027a
    8028 71.2 3.9 0.4 1.0 0.14 0.03 2.6 remainder
    8028a
    8029 68.1 3.6 0.2 0.05 2.0 remainder
    8029a
    8030 64.9 2.9 0.3 0.28 0.08 1.0 remainder
    8030a
    No. alloy composition (wt%)
    Cu Si Al Bi Te Se P Mn Zn
    8031 75.3 3.9 2.1 0.07 0.04 0.8 remainder
    8031a
    8032 77.2 4.3 2.3 0.03 0.25 0.04 2.8 remainder
    8032a
    8033 64.7 2.8 2.2 0.33 0.9 remainder
    8033a
    8034 69.3 3.5 1.6 0.03 0.03 1.8 remainder
    8034a
    8035 71.2 3.8 1.5 0.21 2.0 remainder
    8035a
    8036 70.6 3.7 0.3 0.04 0.13 1.7 remainder
    8036a
    8037 69.7 3.8 1.4 0.12 0.04 0.04 1.8 remainder
    8037a
    8038 70.7 4.2 1.5 0.03 0.16 0.03 3.3 remainder
    8038a
    8039 70.4 3.9 0.2 0.15 0.10 0.02 0.04 2.2 remainder
    8039a
    8040 68.8 3.7 0.4 0.05 0.12 1.9 remainder
    8040a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Mn Ni Zn
    8041 70.3 3.9 0.2 0.20 0.03 0.22 2.1 remainder
    8041a
    8042 74.6 4.3 2.1 0.12 0.03 2.4 remainder
    8042a
    8043 77.0 4.5 0.03 0.12 1.7 remainder
    8043a
    8044 70.6 3.9 0.10 0.06 0.04 2.6 remainder
    8044a
    8045 74.2 4.3 0.11 0.21 0.16 2.8 remainder
    8045a
    8046 69.9 3.8 0.06 0.11 0.03 0.08 1.2 remainder
    8046a
    8047 66.8 3.4 0.09 0.06 2.2 remainder
    8047a
    8048 71.3 4.2 0.04 0.05 0.05 1.4 remainder
    8048a
    8049 72.4 4.1 0.12 0.09 2.7 remainder
    8049a
    8050 62.9 2.8 2.8 0.12 1.5 remainder
    8050a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se Ni Zn
    8051 64.8 3.1 2.4 0.08 0.03 2.0 remainder
    8051a
    8052 68.9 3.9 0.3 0.03 0.06 1.8 remainder
    8052a
    8053 67.3 3.7 0.7 0.05 0.04 0.04 2.1 remainder
    8053a
    8054 66.5 3.8 0.9 0.31 2.2 remainder
    8054a
    8055 73.8 4.3 2.1 0.03 0.05 3.3 remainder
    8055a
    8056 74.2 4.4 1.3 0.03 2.7 remainder
    8056a
    8057 70.1 3.8 1.5 1.9 0.06 1.8 remainder
    8057a
    8058 67.9 2.9 0.8 2.3 0.16 0.06 0.9 remainder
    8058a
    8059 68.2 3.6 2.0 0.6 0.04 0.09 1.7 remainder
    8059a
    8060 66.6 3.5 1.8 0.2 0.10 0.05 0.05 1.2 remainder
    8060a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Ni Zn
    8061 67.6 3.6 0.4 0.6 0.30 1.8 remainder
    8061a
    8062 68.8 3.0 0.6 2.1 0.08 0.03 1.1 remainder
    8062a
    8063 71.2 4.1 2.4 0.8 0.31 2.2 remainder
    8063a
    8064 68.2 3.6 2.6 0.04 0.05 1.5 remainder
    8064a
    8065 63.9 2.9 2.3 0.32 0.02 0.08 0.8 remainder
    8065a
    8066 70.5 3.9 1.1 0.05 0.05 0.05 2.2 remainder
    8066a
    8067 67.7 3.7 1.2 0.09 0.03 0.02 0.04 2.0 remainder
    8067a
    8068 66.6 3.5 1.4 0.06 0.04 2.6 remainder
    8068a
    8069 72.3 4.1 0.6 0.05 0.04 0.10 3.0 remainder
    8069a
    8070 70.6 4.0 0.4 0.16 0.05 3.2 remainder
    8070a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Ni Zn
    8071 75.6 3.9 0.5 2.2 0.21 0.21 1.4 remainder
    8071a
    8072 71.2 3.4 0.7 1.5 0.18 0.10 0.14 1.3 remainder
    8072a
    8073 68.5 3.7 0.7 1.2 0.03 0.08 0.03 1.9 remainder
    8073a
    8074 64.9 3.2 0.8 0.4 0.12 0.03 0.04 0.04 1.8 remainder
    8074a
    8075 65.3 3.3 2.8 0.2 0.06 0.05 1.5 remainder
    8075a
    8076 68.8 4.0 2.5 0.6 0.05 0.13 0.03 2.7 remainder
    8076a
    8077 67.3 3.4 1.6 0.5 0.06 0.12 2.4 remainder
    8077a
    8078 77.0 4.1 2.2 0.13 2.1 remainder
    8078a
    8079 71.2 3.8 1.4 0.05 0.20 2.0 remainder
    8079a
    8080 68.2 3.6 1.3 0.04 0.05 2.6 remainder
    8080a
    No. alloy composition (wt%)
    Cu Si Al Bi Te Se P Ni Zn
    8081 67.3 3.4 0.8 0.05 0.06 0.03 1.7 remainder
    8081a
    8082 70.4 3.9 1.2 0.05 2.2 remainder
    8082a
    8083 73.6 3.9 1.3 0.21 0.06 3.1 remainder
    8083a
    8084 68.8 3.8 1.2 0.18 2.6 remainder
    8084a
    8085 67.5 3.5 1.2 0.04 0.16 1.8 remainder
    8085a
    8086 64.9 2.9 1.6 0.08 0.04 0.05 1.5 remainder
    8086a
    8087 76.3 4.3 1.5 0.29 0.05 0.10 2.8 remainder
    8087a
    8088 65.8 2.8 2.3 0.16 0.06 0.03 0.05 1.3 remainder
    8088a
    8089 66.7 3.3 2.1 0.32 0.03 1.8 remainder
    8089a
    8090 69.2 4.0 1.2 0.11 0.02 0.10 2.5 remainder
    8090a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Mn Ni Zn
    8091 70.6 3.8 1.3 0.14 0.05 1.7 remainder
    8091a
    8092 67.2 3.4 0.05 0.04 2.0 remainder
    8092a
    8093 65.8 3.2 0.15 0.03 0.06 1.2 remainder
    8093a
    8094 67.7 3.7 0.06 0.10 0.08 2.1 remainder
    8094a
    8095 64.7 2.9 0.31 0.04 0.05 0.09 1.5 remainder
    8095a
    8096 66.5 3.6 0.18 0.21 2.3 remainder
    8096a
    8097 67.3 3.8 0.08 0.05 0.12 2.2 remainder
    8097a
    8098 65.9 3.6 0.21 0.20 2.5 remainder
    8098a
    8099 64.9 3.6 0.4 0.18 0.8 2.6 remainder
    8099a
    8100 67.3 3.8 1.8 0.03 0.06 1.9 1.0 remainder
    8100a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se Mn Ni Zn
    8101 62.9 2.9 2.4 0.20 0.16 1.3 0.9 remainder
    8101a
    8102 66.3 3.4 0.5 0.04 0.04 0.05 1.5 0.8 remainder
    8102a
    8103 65.8 3.8 2.6 0.03 1.4 1.2 remainder
    8103a
    8104 64.7 3.6 2.7 0.25 0.03 1.3 1.6 remainder
    8104a
    8105 70.4 3.9 1.8 0.07 1.0 2.0 remainder
    8105a
    8106 70.3 3.8 0.4 1.8 0.05 2.3 0.7 remainder
    8106a
    8107 72.1 3.7 0.4 2.1 0.03 0.05 1.3 1.2 remainder
    8107a
    8108 69.8 3.8 0.6 1.5 0.05 0.05 1.5 2.1 remainder
    8108a
    8109 75.4 4.2 0.6 1.8 0.05 0.04 0.04 2.3 1.1 remainder
    8109a
    8110 66.4 3.5 2.5 0.2 0.12 1.6 0.9 remainder
    8110a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Mn Ni Zn
    8111 64.9 3.3 2.5 0.3 0.08 0.05 1.2 1.3 remainder
    8111a
    8112 70.0 3.8 1.2 0.5 0.03 1.5 0.8 remainder
    8112a
    8113 72.0 3.9 1.1 0.25 0.20 2.4 0.9 remainder
    8113a
    8114 66.5 3.6 1.2 0.06 0.04 0.05 1.3 1.1 remainder
    8114a
    8115 67.0 3.5 1.3 0.12 0.04 0.08 0.9 1.2 remainder
    8115a
    8116 64.0 2.8 2.6 0.30 0.08 0.03 0.05 0.8 1.0 remainder
    8116a
    8117 67.3 3.7 2.3 0.03 0.03 1.2 1.3 remainder
    8117a
    8118 66.4 3.8 2.4 0.05 0.15 0.03 1.0 1.6 remainder
    8118a
    8119 70.2 3.9 0.5 0.30 0.07 1.7 0.9 remainder
    8119a
    8120 73.1 4.2 0.5 2.3 0.04 0.14 2.0 1.1 remainder
    8120a
    No. alloy composition (wt%)
    Cu Si Sn Al Bi Te Se P Mn Ni Zn
    8121 71.0 3.6 0.6 2.3 0.03 0.12 0.20 1.8 1.0 remainder
    8121a
    8122 70.0 3.5 0.5 1.8 0.06 0.03 0.10 1.2 1.3 remainder
    8122a
    8123 66.5 3.4 0.5 0.7 0.30 0.03 0.02 0.03 1.0 1.5 remainder
    8123a
    8124 68.8 3.9 1.2 0.2 0.06 0.05 1.0 1.2 remainder
    8124a
    8125 64.9 3.0 1.8 0.5 0.25 0.05 0.05 1.1 0.8 remainder
    8125a
    8126 63.7 2.9 2.7 1.0 0.31 0.03 1.2 0.8 remainder
    8126a
    8127 70.4 3.9 0.2 0.04 1.6 1.3 remainder
    8127a
    8128 66.5 3.6 0.3 0.02 0.04 1.2 1.1 remainder
    8128a
    8129 67.3 3.7 0.7 0.03 0.08 1.3 1.2 remainder
    8129a
    8130 66.0 3.4 0.7 0.22 0.06 0.04 1.3 1.0 remainder
    8130a
    No. alloy composition (wt%)
    Cu Si Al Bi Te Se P Mn Ni Zn
    8131 68.0 3.8 0.8 0.05 1.1 1.4 remainder
    8131a
    8132 70.0 3.4 2.1 0.03 0.22 0.9 1.1 remainder
    8132a
    8133 75.5 4.2 2.2 0.05 1.2 1.9 remainder
    8133a
    8134 68.5 3.8 1.8 0.10 0.04 1.4 1.6 remainder
    8134a
    8135 76.5 4.3 2.1 0.03 0.10 0.15 1.6 1.3 remainder
    8135a
    8136 66.5 3.6 1.2 0.05 0.16 0.05 1.2 1.3 remainder
    8136a
    8137 72.0 4.1 1.0 0.04 0.03 0.02 0.07 1.3 2.2 remainder
    8137a
    8138 70.2 4.0 1.0 0.04 0.03 2.1 1.4 remainder
    8138a
    8139 66.8 3.8 0.5 0.32 0.03 0.03 1.2 1.6 remainder
    8139a
    8140 67.3 3.9 0.4 0.05 0.03 1.8 1.0 remainder
    8140a
    No. alloy composition (wt%)
    Cu Si Bi Te Se P Mn Ni Zn
    8141 66.5 3.6 0.05 0.05 1.5 1.2 remainder
    8141a
    8142 63.9 2.9 0.30 0.03 0.04 1.2 0.9 remainder
    8142a
    8143 68.4 3.8 0.03 0.05 0.12 0.9 2.5 remainder
    8143a
    8144 65.8 3.4 0.10 0.05 0.02 0.03 1.0 1.4 remainder
    8144a
    8145 70.5 3.9 0.12 0.05 2.6 0.8 remainder
    8145a
    8146 72.0 4.2 0.04 0.05 0.18 1.0 2.4 remainder
    8146a
    8147 68.0 3.7 0.20 0.06 1.5 1.0 remainder
    8147a
    No. alloy composition (wt%)
    Cu Si Al P Zn
    9001 72.6 2.3 0.8 0.03 remainder
    9002 74.8 2.8 1.3 0.09 remainder
    9003 77.2 3.6 0.2 0.21 remainder
    9004 75.7 3.0 1.1 0.07 remainder
    9005 78.0 3.8 0.7 0.12 remainder
    No. alloy composition (wt%)
    Cu Si Al P Cr Ti Zn
    10001 74.3 2.9 0.6 0.05 0.03 remainder
    10002 74.8 3.0 0.2 0.12 0.32 remainder
    10003 74.9 2.8 0.9 0.08 0.33 remainder
    10004 77.8 3.6 1.2 0.22 0.08 remainder
    10005 71.9 2.3 1.4 0.07 0.02 0.24 remainder
    10006 76.0 2.8 1.2 0.03 0.15 remainder
    10007 75.5 3.0 0.3 0.06 0.20 remainder
    10008 71.5 2.2 0.7 0.12 0.14 0.05 remainder
    No. alloy composition (wt%)
    Cu Si Al P Bi Te Se Zn
    11001 74.8 2.8 1.4 0.10 0.03 remainder
    11002 76.1 3.0 0.6 0.06 0.21 remainder
    11003 78.3 3.5 1.3 0.19 0.18 remainder
    11004 71.7 2.4 0.8 0.04 0.21 0.03 remainder
    11005 73.9 2.8 0.3 0.09 0.33 0.03 remainder
    11006 74.8 2.8 0.7 0.11 0.16 0.02 remainder
    11007 78.3 3.8 1.1 0.05 0.22 0.05 0.04 remainder
    No. alloy composition (wt%)
    Cu Si Al Bi Te Se P Cr Ti Zn
    12001 73.8 2.6 0.5 0.21 0.05 0.11 remainder
    12002 76.5 3.2 0.9 0.03 0.11 0.03 remainder
    12003 78.1 3.4 1.3 0.09 0.20 0.05 remainder
    12004 70.8 2.1 0.6 0.22 0.06 0.08 0.32 remainder
    12005 77.8 3.8 0.2 0.02 0.03 0.03 0.26 remainder
    12006 74.6 2.9 0.7 0.15 0.02 0.10 0.06 remainder
    12007 73.9 2.8 0.3 0.04 0.05 0.16 0.03 0.18 remainder
    12008 75.7 2.9 1.2 0.03 0.12 0.05 remainder
    12009 72.9 2.6 0.5 0.33 0.04 0.12 remainder
    12010 76.5 3.2 0.3 0.32 0.03 0.35 remainder
    12011 71.9 2.5 0.8 0.19 0.03 0.03 0.03 remainder
    12012 74.7 2.9 0.6 0.07 0.05 0.21 0.06 remainder
    12013 74.8 2.8 1.3 0.04 0.21 0.06 0.26 remainder
    12014 78.2 3.8 1.1 0.22 0.05 0.03 0.04 0.24 remainder
    12015 74.6 2.7 1.0 0.15 0.03 0.02 0.10 remainder
    12016 75.5 2.9 0.7 0.22 0.05 0.34 0.02 remainder
    12017 76.2 3.4 0.3 0.05 0.12 0.08 0.31 remainder
    12018 77.0 3.3 1.1 0.03 0.14 0.03 0.05 0.03 remainder
    12019 73.7 2.8 0.3 0.32 0.03 0.10 0.03 0.19 remainder
    12020 74.8 2.8 1.2 0.02 0.14 0.05 0.14 0.05 remainder
    12021 74.0 2.9 0.4 0.07 0.05 0.05 0.08 0.11 0.26 remainder
    No. alloy composition (wt%) heat treatment
    Cu Si Zn temperature time
    13001 78.5 3.2 remainder 580°C 30min.
    13002 78.5 3.2 remainder 450°C 2hr.
    13003 77.0 2.9 remainder 580°C 30min.
    13004 77.0 2.9 remainder 450°C 2hr.
    13005 69.9 2.3 remainder 580°C 30min.
    13006 69.9 2.3 remainder 450°C 2hr.
    No. alloy composition (wt%)
    Cu Si Sn Al Mn Pb Fe Ni Zn
    14001 58.8 0.2 3.1 0.2 remainder
    14001a
    14002 61.4 0.2 3.0 0.2 remainder
    14002a
    14003 59.1 0.2 2.0 0.2 remainder
    14003a
    14004 69.2 1.2 0.1 remainder
    14004a
    14005 remainder 9.8 1.1 3.9 1.2
    14005a
    14006 61.8 1.0 0.1 remainder
    14006a
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    1001 ▵ ▵ 146 290 ○ 470 32 ▵
    1002 o ○ ○ 122 210 ○ 524 36 ○
    1003 o ○ ○ 119 190 ○ 543 34 ○
    1004 o ○ ○ 126 170 ▵ 590 37 ○
    1005 ▵ ○ 134 150 ▵ 532 42 ○
    1006 o ○ ▵ 129 230 ○ 490 34 ○
    1007 ▵ ○ 132 170 ▵ 512 41 ○
    1008 ▵ ▵ 137 270 ○ 501 31 ▵
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    2001 ○ ○ 116 190 ○ 523 34 ○
    2002 o ○ ○ 117 190 ○ 508 36 ○
    2003 o ○ ○ 118 180 ○ 525 36 ○
    2004 o ○ ○ 119 280 ▵ 463 28 ▵
    2005 o ○ ○ 119 240 ▵ 481 30 ○
    2006 o ○ ○ 119 170 ▵ 552 36 ○
    2007 o ○ ○ 116 180 ○ 520 41 ○
    2008 o ○ ○ 115 140 ▵ 570 34 ○
    2009 o ○ ○ 117 200 ▵ 485 31 ○
    2010 o ○ ○ 114 180 ○ 507 34 ○
    2011 o ○ ○ 115 170 ▵ 522 33 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    3001 o ○ ▵ 128 40 ○ 553 26 ○
    3002 o ○ ○ 126 130 ▵ 538 32 ○
    3003 o ○ ○ 126 50 ○ 526 28 ○
    3004 o ○ ○ 119 <5 ○ 533 36 ○
    3005 o ○ ○ 125 50 ○ 525 28 ○
    3006 o ○ ○ 120 <5 ○ 546 38 ○
    3007 o ○ ○ 121 <5 ○ 552 34 ○
    3008 o ○ ○ 122 80 ○ 570 36 ○
    3009 o ○ ○ 123 50 ○ 541 29 ○
    3010 o ○ ○ 118 <5 ○ 560 35 ○
    3011 o ○ ○ 119 20 ○ 502 34 ○
    3012 o ○ ○ 120 <5 ○ 534 31 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    4001 o ○ ○ 119 40 ▵ 512 24 ○
    4002 o ○ ○ 122 50 ○ 543 30 ○
    4003 o ○ ○ 123 50 ○ 533 30 ○
    4004 o ○ ○ 117 80 ▵ 520 31 ○
    4005 o ○ ○ 119 50 ○ 535 32 ○
    4006 o ○ ○ 116 60 ○ 532 31 ○
    4007 o ○ ○ 122 50 ○ 528 26 ○
    4008 o ○ ○ 124 100 ▵ 554 30 ○
    4009 o ○ ○ 119 130 ○ 542 34 ○
    4010 o ○ ○ 119 120 ○ 562 35 ○
    4011 o ○ ○ 122 100 ▵ 563 34 ○
    4012 o ○ ○ 119 130 ○ 524 40 ○
    4013 o ○ ○ 120 110 ○ 548 37 ○
    4014 o ○ ○ 120 120 ▵ 539 36 ○
    4015 o ○ ○ 121 40 ○ 528 28 ○
    4016 o ○ ○ 122 60 ○ 597 32 ○
    4017 o ○ ○ 120 50 ○ 520 33 ○
    4018 o ○ ○ 123 60 ○ 553 31 ○
    4019 o ○ ○ 118 40 ○ 606 24 ○
    4020 o ○ ○ 120 40 ○ 561 26 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    4021 o ○ ○ 120 50 ○ 540 29 ○
    4022 o ○ ○ 123 <5 ○ 487 32 ▵
    4023 o ○ ○ 117 <5 ○ 524 34 ○
    4024 o ○ ○ 117 40 ○ 541 37 ○
    4025 o ○ ○ 115 <5 ▵ 526 43 ○
    4026 o ○ ○ 122 30 ○ 498 30 ▵
    4027 o ○ ○ 118 30 ○ 516 35 ○
    4028 o ○ ○ 120 <5 ○ 529 27 ○
    4029 o ○ ○ 121 <5 ○ 544 28 ○
    4030 o ○ ○ 118 <5 ○ 536 30 ○
    4031 o ○ ○ 116 <5 ○ 524 31 ○
    4032 o ○ ○ 114 <5 ○ 515 32 ○
    4033 o ○ ○ 118 <5 ○ 519 37 ○
    4034 o ○ ○ 118 <5 ○ 582 31 ○
    4035 o ○ ○ 117 <5 ○ 538 32 ○
    4036 o ○ ○ 118 <5 ▵ 600 34 ○
    4037 o ○ ○ 117 20 ○ 523 34 ○
    4038 o ○ ○ 116 <5 ▵ 539 38 ○
    4039 o ○ ○ 118 20 ○ 544 34 ○
    4040 o ○ ○ 117 40 ○ 522 31 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    4041 o ○ ○ 120 20 ○ 565 31 ○
    4042 o ○ ○ 119 <5 ○ 567 34 ○
    4043 o ○ ○ 121 <5 ○ 530 29 ○
    4044 o ○ ○ 120 <5 ○ 548 31 ○
    4045 o ○ ○ 121 <5 ○ 572 32 ○
    4046 o ○ ○ 119 <5 ○ 579 29 ○
    4047 o ○ ○ 123 <5 ○ 542 26 ○
    4048 o ○ ○ 123 <5 ○ 540 28 ○
    4049 o ○ ○ 120 <5 ○ 539 33 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    5001 o ○ ▵ 127 30 ○ 501 25 ○
    5002 o ○ ○ 119 <5 ○ 524 37 ○
    5003 o ○ ▵ 135 10 ○ 488 41 ○
    5004 o ○ ○ 126 20 ▵ 552 38 ○
    5005 o ○ ○ 123 <5 ○ 518 29 ○
    5006 o ○ ○ 122 <5 ○ 520 34 ○
    5007 o ○ ▵ 125 <5 ○ 507 23 ○
    5008 o ○ ○ 122 <5 ○ 515 30 ○
    5009 o ○ ○ 124 <5 ○ 544 35 ○
    5010 o ○ ○ 123 <5 ▵ 536 36 ○
    5011 o ○ ▵ 126 <5 ○ 511 27 ○
    5012 o ○ ○ 124 <5 ○ 596 36 ○
    5013 o ○ ○ 119 <5 ○ 519 39 ○
    5014 o ○ ○ 122 <5 ○ 523 37 ○
    5015 o ○ ○ 123 <5 ○ 510 40 ○
    5016 o ○ ○ 120 20 ○ 490 35 ▵
    5017 o ○ ○ 121 <5 ○ 573 40 ○
    5018 o ○ ○ 120 <5 ○ 549 39 ○
    5019 o ○ ○ 122 50 ○ 537 30 ○
    5020 o ○ ○ 118 <5 ○ 521 37 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    6001 o ○ ○ 121 30 ○ 512 24 ○
    6002 o ○ ○ 122 <5 ○ 574 31 ○
    6003 o ○ ○ 117 <5 ▵ 501 32 ○
    6004 o ○ ○ 120 <5 ○ 514 26 ○
    6005 o ○ ○ 121 <5 ▵ 525 42 ○
    6006 ○ ○ 115 <5 ○ 514 32 ○
    6007 o ○ ○ 120 <5 ○ 548 27 ○
    6008 o ○ ○ 119 <5 ○ 503 30 ○
    6009 o ○ ○ 117 <5 ○ 522 38 ○
    6010 o ○ ○ 122 <5 ▵ 527 41 ○
    6011 o ○ ○ 119 <5 ○ 536 32 ○
    6012 o ○ ○ 123 20 ○ 478 27 ▵
    6013 o ○ ○ 118 <5 ○ 506 30 ○
    6014 o ○ ○ 118 <5 ○ 525 39 ○
    6015 ○ ○ 114 <5 ○ 503 35 ○
    6016 o ○ ○ 122 40 ○ 526 27 ○
    6017 o ○ ○ 119 <5 ▵ 507 30 ○
    6018 o ○ ○ 121 <5 ○ 589 31 ○
    6019 o ○ ○ 120 <5 ○ 508 25 ○
    6020 o ○ ○ 121 <5 ▵ 504 43 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    6021 o ○ ○ 116 <5 ○ 501 33 ○
    6022 o ○ ○ 120 <5 ○ 547 29 ○
    6023 ○ ○ 119 <5 ○ 523 30 ○
    6024 o ○ ○ 120 <5 ▵ 525 40 ○
    6025 o ○ ○ 120 <5 ○ 496 30 ○
    6026 ○ ○ 114 <5 ○ 518 34 ○
    6027 o ○ ○ 119 <5 ○ 487 28 ▵
    6028 o ○ ○ 118 <5 ○ 524 35 ○
    6029 o ○ ○ 122 <5 ▵ 540 41 ○
    6030 o ○ ○ 118 <5 ○ 511 29 ○
    6031 o ○ ○ 119 40 ○ 519 28 ○
    6032 o ○ ○ 120 <5 ○ 572 32 ○
    6033 o ○ ○ 123 <5 ▵ 515 36 ○
    6034 o ○ ○ 122 <5 ○ 580 35 ○
    6035 o ○ ○ 123 <5 ○ 517 27 ○
    6036 o ○ ○ 121 <5 ○ 503 26 ○
    6037 ○ ○ 117 <5 ○ 536 30 ○
    6038 o ○ ○ 116 <5 ○ 506 30 ○
    6039 o ○ ○ 120 <5 ○ 485 28 ▵
    6040 ○ ○ 116 <5 ○ 528 36 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    6041 o ○ ○ 117 <5 ○ 496 30 ○
    6042 o ○ ○ 120 <5 ▵ 574 34 ○
    6043 o ○ ○ 123 10 ▵ 506 43 ○
    6044 o ○ ○ 115 10 ○ 500 30 ○
    6045 o ○ ○ 119 20 ▵ 485 27 ▵
    6046 o ○ ○ 121 40 ○ 512 24 ○
    6047 o ○ ○ 123 <5 ○ 557 25 ○
    6048 o ○ ○ 120 <5 ○ 526 30 ○
    6049 o ○ ○ 120 <5 ○ 502 24 ○
    6050 o ○ ○ 124 <5 ○ 480 31 ○
    6051 ○ ○ 117 <5 ○ 534 32 ○
    6052 o ○ ○ 123 <5 ▵ 523 38 ○
    6053 o ○ ○ 123 <5 ○ 506 39 ○
    6054 o ○ ○ 115 <5 ○ 485 31 ○
    6055 o ○ ○ 122 <5 ▵ 512 44 ○
    6056 o ○ ○ 120 <5 ○ 480 33 ▵
    6057 o ○ ○ 121 <5 ○ 479 25 ▵
    6058 ○ ○ 116 <5 ○ 525 34 ○
    6059 o ○ ○ 119 20 ○ 482 35 ○
    6060 ○ ○ 118 30 ○ 513 38 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    6061 o ○ ○ 123 30 ○ 530 22 ○
    6062 o ○ ○ 119 10 ○ 538 33 ○
    6063 o ○ ○ 118 <5 ○ 504 37 ○
    6064 o ○ ○ 121 <5 ○ 526 30 ○
    6065 o ○ ○ 123 <5 ○ 565 35 ○
    6066 o ○ ○ 120 <5 ○ 501 25 ○
    6067 o ○ ○ 119 <5 ○ 526 26 ○
    6068 o ○ ○ 122 <5 ○ 502 30 ○
    6069 o ○ ○ 124 <5 ○ 484 28 ▵
    6070 ○ ○ 115 <5 ○ 548 37 ○
    6071 o ○ ○ 118 <5 ○ 530 34 ○
    6072 o ○ ○ 119 <5 ○ 515 30 ○
    6073 o ○ ○ 121 <5 ▵ 579 35 ○
    6074 o ○ ○ 117 <5 ○ 517 32 ○
    6075 o ○ ○ 117 <5 ○ 513 38 ○
    6076 o ○ ○ 122 40 ○ 535 28 ○
    6077 ○ ○ 119 <5 ○ 490 30 ○
    6078 o ○ ○ 122 <5 ▵ 513 40 ○
    6079 o ○ ○ 118 <5 ○ 524 30 ○
    6080 o ○ ○ 123 <5 ○ 482 35 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    6081 o ○ ○ 118 <5 ○ 536 34 ○
    6082 o ○ ○ 123 <5 ○ 510 25 ○
    6083 o ○ ○ 119 <5 ○ 504 32 ○
    6084 o ○ ○ 117 <5 ○ 533 34 ○
    6085 o ○ ○ 118 10 ○ 501 30 ○
    6086 o ○ ○ 117 <5 ○ 545 37 ○
    6087 o ○ ○ 119 <5 ○ 503 34 ○
    6088 ○ ○ 115 <5 ○ 526 36 ○
    6089 o ○ ○ 119 <5 ○ 514 39 ○
    6090 o ○ ○ 121 20 ▵ 480 35 ○
    6091 o ○ ○ 122 30 ○ 516 24 ○
    6092 o ○ ○ 118 <5 ○ 532 30 ○
    6093 o ○ ○ 119 <5 ○ 539 34 ○
    6094 ○ ○ 117 <5 ○ 528 32 ○
    6095 o ○ ○ 119 <5 ○ 507 30 ○
    6096 o ○ ○ 122 <5 ○ 508 22 ○
    6097 o ○ ○ 117 <5 ○ 510 31 ○
    6098 o ○ ○ 117 <5 ○ 527 32 ○
    6099 o ○ ○ 116 <5 ○ 529 34 ○
    6100 o ○ ○ 119 <5 ○ 515 32 ○
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) 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
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    7001 o ○ ▵ 138 ○ 670 18
    7002 o ○ ▵ 136 ○ 712 20
    7003 o ○ ○ 132 ○ 783 23
    7004 o ○ ○ 138 ○ 736 21
    7005 o ○ ○ 136 ○ 785 23
    7006 o ○ ▵ 139 ○ 700 24
    7007 ▵ ○ 138 ○ 707 23
    7008 o ○ ○ 131 ○ 805 22
    7009 o ○ ○ 136 ○ 768 19
    7010 o ○ ○ 135 ○ 778 23
    7011 ▵ ○ 137 ○ 677 23
    7012 o ○ ○ 134 ○ 800 21
    7013 o ○ ○ 133 ○ 819 22
    7014 ▵ ○ 138 ○ 641 21
    7015 o ○ ○ 134 ○ 764 23
    7016 o ○ ○ 129 ○ 759 20
    7017 ▵ ○ 139 ○ 638 18
    7018 o ○ ○ 135 ○ 717 20
    7019 o ○ ○ 136 ○ 694 24
    7020 ▵ ○ 138 ○ 712 25
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    7021 o ○ ○ 130 ○ 754 24
    7022 o ○ ▵ 134 ○ 780 23
    7023 o ○ ○ 133 ○ 765 22
    7024 o ○ ○ 135 ○ 772 23
    7025 ▵ ○ 138 ○ 687 24
    7026 o ○ ○ 135 ○ 718 24
    7027 o ○ ▵ 136 ○ 742 18
    7028 ▵ ○ 138 ○ 785 20
    7029 o ○ ○ 134 ○ 703 23
    7030 o ○ ○ 135 ○ 820 18
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    8001 o ○ ○ 132 ○ 655 15
    8002 o ○ ○ 129 ○ 708 17
    8003 o ○ ○ 127 ○ 768 20
    8004 o ○ ○ 128 ○ 785 18
    8005 o ○ ○ 131 ○ 714 16
    8006 o ○ ○ 134 ○ 680 16
    8007 o ○ ○ 132 ○ 764 17
    8008 o ○ ○ 130 ○ 673 16
    8009 o ○ ○ 132 ○ 759 18
    8010 o ○ ○ 132 ○ 751 15
    8011 o ○ ○ 134 ○ 767 17
    8012 o ○ ○ 128 ○ 796 18
    8013 o ○ ○ 129 ○ 784 18
    8014 o ○ ○ 129 ○ 802 17
    8015 o ○ ○ 133 ○ 679 15
    8016 o ○ ○ 130 ○ 706 16
    8017 o ○ ○ 129 ○ 707 18
    8018 o ○ ○ 131 ○ 780 16
    8019 o ○ ○ 128 ○ 768 16
    8020 o ○ ○ 132 ○ 723 19
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    8021 o ○ ○ 134 ○ 765 16
    8022 o ○ ○ 132 ○ 770 16
    8023 o ○ ○ 131 ○ 746 18
    8024 o ○ ○ 132 ○ 816 19
    8025 o ○ ○ 129 ○ 759 18
    8026 o ○ ○ 130 ○ 726 17
    8027 o ○ ○ 133 ○ 703 17
    8028 o ○ ○ 132 ○ 737 18
    8029 o ○ ○ 129 ○ 719 20
    8030 o ○ ○ 133 ○ 645 23
    8031 o ○ ○ 129 ○ 764 22
    8032 o ○ ○ 131 ○ 790 19
    8033 o ○ ○ 133 ○ 674 20
    8034 o ○ ○ 131 ○ 748 23
    8035 o ○ ○ 129 ○ 777 22
    8036 o ○ ○ 131 ○ 725 23
    8037 o ○ ○ 128 ○ 770 21
    8038 o ○ ○ 131 ○ 815 18
    8039 o ○ ○ 127 ○ 739 24
    8040 o ○ ○ 130 ○ 721 22
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    8041 o ○ ○ 128 ○ 735 23
    8042 o ○ ○ 127 ○ 822 18
    8043 o ○ ○ 131 ○ 780 18
    8044 o ○ ○ 126 ○ 726 21
    8045 o ○ ○ 128 ○ 766 22
    8046 o ○ ○ 127 ○ 712 23
    8047 o ○ ○ 128 ○ 674 21
    8048 o ○ ○ 129 ○ 753 24
    8049 o ○ ○ 127 ○ 768 22
    8050 o ○ ○ 132 ○ 691 17
    8051 o ○ ○ 131 ○ 717 17
    8052 o ○ ○ 128 ○ 739 21
    8053 o ○ ○ 128 ○ 730 22
    8054 o ○ ○ 127 ○ 735 20
    8055 o ○ ○ 134 ○ 818 15
    8056 o ○ ○ 132 ○ 812 16
    8057 o ○ ○ 131 ○ 755 18
    8058 o ○ ○ 133 ○ 659 20
    8059 o ○ ○ 132 ○ 740 17
    8060 o ○ ○ 130 ○ 714 19
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    8061 o ○ ○ 129 ○ 705 21
    8062 o ○ ○ 131 ○ 690 22
    8063 o ○ ○ 133 ○ 811 18
    8064 o ○ ○ 131 ○ 746 17
    8065 o ○ ○ 133 ○ 652 19
    8066 o ○ ○ 130 ○ 758 19
    8067 o ○ ○ 129 ○ 734 19
    8068 o ○ ○ 131 ○ 710 17
    8069 o ○ ○ 131 ○ 767 20
    8070 o ○ ○ 131 ○ 753 18
    8071 o ○ ○ 129 ○ 792 19
    8072 o ○ ○ 131 ○ 736 21
    8073 o ○ ○ 130 ○ 767 22
    8074 o ○ ○ 132 ○ 679 19
    8075 o ○ ○ 134 ○ 728 17
    8076 o ○ ○ 133 ○ 795 16
    8077 o ○ ○ 133 ○ 716 18
    8078 o ○ ○ 132 ○ 809 18
    8079 o ○ ○ 129 ○ 758 22
    8080 o ○ ○ 130 ○ 724 21
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    8081 o ○ ○ 132 ○ 706 23
    8082 o ○ ○ 130 ○ 768 23
    8083 o ○ ○ 128 ○ 774 25
    8084 o ○ ○ 129 ○ 765 22
    8085 o ○ ○ 130 ○ 729 23
    8086 o ○ ○ 133 ○ 687 24
    8087 o ○ ○ 131 ○ 798 20
    8088 o ○ ○ 132 ○ 699 23
    8089 o ○ ○ 130 ○ 740 21
    8090 o ○ ○ 132 ○ 782 18
    8091 o ○ ○ 129 ○ 763 22
    8092 o ○ ○ 130 ○ 680 22
    8093 o ○ ○ 131 ○ 655 23
    8094 o ○ ○ 128 ○ 714 21
    8095 o ○ ○ 132 ○ 638 24
    8096 o ○ ○ 128 ○ 689 22
    8097 o ○ ○ 129 ○ 711 21
    8098 o ○ ○ 130 ○ 693 20
    8099 o ○ ○ 127 ○ 702 21
    8100 o ○ ○ 129 ○ 724 18
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    8101 o ○ ○ 131 ○ 685 18
    8102 o ○ ○ 132 ○ 690 21
    8103 o ○ ○ 133 ○ 744 17
    8104 o ○ ○ 130 ○ 726 17
    8105 o ○ ○ 133 ○ 751 19
    8106 o ○ ○ 130 ○ 752 21
    8107 o ○ ○ 131 ○ 760 21
    8108 o ○ ○ 132 ○ 748 22
    8109 o ○ ○ 130 ○ 807 18
    8110 o ○ ○ 133 ○ 739 16
    8111 o ○ ○ 132 ○ 717 17
    8112 o ○ ○ 134 ○ 763 20
    8113 o ○ ○ 129 ○ 745 22
    8114 o ○ ○ 132 ○ 722 20
    8115 o ○ ○ 130 ○ 706 17
    8116 o ○ ○ 133 ○ 684 19
    8117 o ○ ○ 132 ○ 740 18
    8118 o ○ ○ 133 ○ 765 16
    8119 o ○ ○ 128 ○ 733 22
    8120 o ○ ○ 131 ○ 819 19
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) elongation (%)
    8121 o ○ ○ 130 ○ 788 20
    8122 o ○ ○ 131 ○ 755 22
    8123 o ○ ○ 127 ○ 711 21
    8124 o ○ ○ 130 ○ 763 20
    8125 o ○ ○ 131 ○ 687 18
    8126 o ○ ○ 134 ○ 706 17
    8127 o ○ ○ 128 ○ 730 22
    8128 o ○ ○ 130 ○ 702 23
    8129 o ○ ○ 132 ○ 727 21
    8130 o ○ ○ 130 ○ 701 24
    8131 o ○ ○ 129 ○ 745 22
    8132 o ○ ○ 132 ○ 749 21
    8133 o ○ ○ 130 ○ 826 18
    8134 o ○ ○ 128 ○ 770 20
    8135 o ○ ○ 129 ○ 828 17
    8136 o ○ ○ 129 ○ 746 20
    8137 o ○ ○ 130 ○ 784 23
    8138 o ○ ○ 131 ○ 779 21
    8139 o ○ ○ 128 ○ 710 22
    8140 o ○ ○ 131 ○ 717 22
    No. machinability hot workability mechanical properties
    form of chippings condition of cut surface cutting force (N) 700°C deformability tensile strength (N/mm2) 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
    Figure 00800001
    Figure 00810001
    Figure 00820001
    No. 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 (µm) 700°C deformability tensile strength (N/mm2) elongation (%)
    13001 o ○ ○ 128 140 ▵ 521 39 ○
    13002 o ○ ○ 126 130 ▵ 524 41 ○
    13003 o ○ ○ 127 150 ▵ 500 38 ○
    13004 o ○ ○ 127 160 ▵ 508 38 ○
    13005 o ○ ○ 128 180 ○ 483 35 ○
    13006 o ○ ○ 129 170 ○ 488 37 ○
    Figure 00840001
    Figure 00850001
    Figure 00860001
    Figure 00870001
    Figure 00880001
    Figure 00890001

    Claims (13)

    1. A lead-free, free-cutting copper alloy which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; and the remaining percent, by weight, of zinc.
    2. A lead-free free-cutting copper alloy which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; at least 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 the remaining percent, by weight, of zinc.
    3. A lead-free free-cutting copper alloy which comprises 70 to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by weight, of silicon; at least one element 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.
    4. A lead-free free-cutting copper alloy which comprises 70 to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by weight, of silicon; at least one element 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; at least 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 the remaining percent, by weight, of zinc.
    5. A lead-free free-cutting copper alloy which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; at least one element selected from among 0.3 to 3.5 percent, by weight, of tin, 0.02 to 0.25 percent, by weight, of phosphorus, 0.02 to 0.15 percent, by weight, of antimony, and 0.02 to 0.15 percent, by weight, of arsenic, and the remaining percent, by weight, of zinc.
    6. A lead-free free-cutting copper alloy which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; at least one element selected from among 0.3 to 3.5 percent, by weight, of tin, 0.02 to 0.25 percent, by weight, of phosphorus, 0.02 to 0.15 percent, by weight, of antimony, and 0.02 to 0.15 percent, by weight, of arsenic; at least 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 the remaining percent, by weight, of zinc.
    7. A lead-free, free-cutting copper alloy which comprises 62 to 78 percent, by weight, of copper; 2.5 to 4.5 percent, by weight, of silicon; at least one element selected from among 0.3 to 3.0 percent, by weight, of tin, 0.2 to 2.5 percent, by weight, of aluminum, and 0.02 to 0.25 percent, by weight, of phosphorus; and at least one element selected from among 0.7 to 3.5 percent, by weight, of manganese and 0.7 to 3.5 percent, by weight, of nickel; and the remaining percent, by weight, of zinc.
    8. A lead-free free-cutting copper alloy which comprises 62 to 78 percent, by weight, of copper; 2.5 to 4.5 percent, by weight, of silicon; at least one element selected from among 0.3 to 3.0 percent, by weight, of tin, 0.2 to 2.5 percent, by weight, of aluminum, and 0.02 to 0.25 percent, by weight, of phosphorus; and at least one element selected from among 0.7 to 3.5 percent, by weight, of manganese and 0.7 to 3.5 percent, by weight, of nickel; at least 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 the remaining percent, by weight, of zinc.
    9. A lead-free free-cutting copper alloy which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; and 0.02 to 0.25 percent, by weight, of phosphorus; and the remaining percent, by weight, of zinc.
    10. A lead-free free-cutting copper alloy which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at least one element selected from among 0.02 to 0.4 percent, by weight, of chromium and 0.02 to 0.4 percent, by weight, of titanium; and the remaining percent, by weight, of zinc.
    11. A lead-free free-cutting copper alloy which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at least 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 the remaining percent, by weight, of zinc.
    12. A lead-free free-cutting copper alloy which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at least one element selected from among 0.02 to 0.4 percent, by weight, of chromium, and 0.02 to 0.4 percent by weight of titanium; at least 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 the remaining percent, by weight, of zinc.
    13. A lead-free free-cutting copper alloy as defined in claim 1, claim 2, claim 3, claim 4, claim 5, claim 6, claim 7, claim 8, claim 9, claim 10, claim 11 or claim 12, which is subjected to a heat treatment for 30 minutes to 5 hours at 400 to 600°C.
    EP98953071A 1998-10-12 1998-11-16 Leadless free-cutting copper alloy Expired - Lifetime EP1045041B1 (en)

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    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    WO2004022805A1 (en) * 2002-09-09 2004-03-18 Sambo Copper Alloy Co., Ltd. High-strength copper alloy
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    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    US7056396B2 (en) 1998-10-09 2006-06-06 Sambo Copper Alloy Co., Ltd. Copper/zinc alloys having low levels of lead and good machinability
    US8506730B2 (en) 1998-10-09 2013-08-13 Mitsubishi Shindoh Co., Ltd. Copper/zinc alloys having low levels of lead and good machinability
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    WO2024090037A1 (en) 2022-10-28 2024-05-02 日本碍子株式会社 Lead-free free-cutting beryllium copper alloy
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    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
    US1954003A (en) * 1930-03-31 1934-04-10 Vaders Eugen Copper alloy for chill and die casting
    CH148824A (en) * 1930-03-31 1931-08-15 Hirsch Kupfer & Messingwerke Process for the production of chill moldings and injection molded parts.
    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 (en) * 1951-01-19 1953-06-22 Alloy usable in dentistry
    DE1558470A1 (en) * 1967-02-02 1970-03-19 Dies Dr Ing Kurt Extruded part
    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 (en) * 1984-12-03 1986-06-20 Showa Alum Ind Kk Cu base alloy for bearing superior in workability and seizure resistance
    JPS62297429A (en) * 1986-06-17 1987-12-24 Nippon Mining Co Ltd Copper alloy having excellent corrosion resistance
    JPH0368731A (en) * 1989-08-08 1991-03-25 Nippon Mining Co Ltd Manufacture of copper alloy and copper alloy material for radiator plate
    JPH09143598A (en) * 1995-11-22 1997-06-03 Chuetsu Gokin Chuko Kk Brass alloy material for heating device
    JP3956322B2 (en) * 1996-05-30 2007-08-08 中越合金鋳工株式会社 One-way clutch end bearings and other sliding parts
    FR2765243B1 (en) * 1997-06-30 1999-07-30 Usinor AUSTENOFERRITIC STAINLESS STEEL WITH VERY LOW NICKEL AND HAVING A STRONG ELONGATION IN TRACTION

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    EP1600517A3 (en) 2005-12-14
    EP1045041A4 (en) 2003-05-07
    DE69838115T2 (en) 2008-04-10
    DE69832097T2 (en) 2006-07-06
    JP2000119775A (en) 2000-04-25
    DE69832097D1 (en) 2005-12-01
    CA2314144A1 (en) 2000-04-20
    KR20010033073A (en) 2001-04-25
    TW421674B (en) 2001-02-11
    EP1559802A1 (en) 2005-08-03
    DE69839830D1 (en) 2008-09-11
    DE69840585D1 (en) 2009-04-02
    EP1045041B1 (en) 2005-10-26
    DE69838115D1 (en) 2007-08-30
    EP1600516A3 (en) 2005-12-14
    AU1054199A (en) 2000-05-01
    WO2000022182A1 (en) 2000-04-20
    EP1559802B1 (en) 2014-01-15
    AU744335B2 (en) 2002-02-21
    KR100352213B1 (en) 2002-09-12
    EP1600517A2 (en) 2005-11-30
    EP1600516A2 (en) 2005-11-30
    EP1600516B1 (en) 2007-07-18
    EP1600515B8 (en) 2008-10-15
    EP1600515B1 (en) 2008-07-30
    CA2314144C (en) 2006-08-22
    EP1600517B1 (en) 2009-02-18
    EP1600515A2 (en) 2005-11-30
    EP1600515A3 (en) 2005-12-14
    JP3734372B2 (en) 2006-01-11

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