EP0560590A2 - Laiton à usinage facile - Google Patents

Laiton à usinage facile Download PDF

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Publication number
EP0560590A2
EP0560590A2 EP93301814A EP93301814A EP0560590A2 EP 0560590 A2 EP0560590 A2 EP 0560590A2 EP 93301814 A EP93301814 A EP 93301814A EP 93301814 A EP93301814 A EP 93301814A EP 0560590 A2 EP0560590 A2 EP 0560590A2
Authority
EP
European Patent Office
Prior art keywords
lead
test
free cutting
bismuth
cutting brass
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP93301814A
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German (de)
English (en)
Other versions
EP0560590A3 (fr
Inventor
Kenkichi c/o Hitachi Alloy Ltd. Yamaji
Rokuro c/o Hitachi Alloy Ltd. Kawanishi
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Hitachi Alloy Ltd
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Hitachi Alloy Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Hitachi Alloy Ltd filed Critical Hitachi Alloy Ltd
Publication of EP0560590A2 publication Critical patent/EP0560590A2/fr
Publication of EP0560590A3 publication Critical patent/EP0560590A3/xx
Withdrawn legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc as the next major constituent

Definitions

  • the invention relates to free cutting brass, and more particularly to, brass with free cutting property having no harmful effect to the quality of water and containing no lead or the minimum amount of lead.
  • Copper alloy containing lead is used in a variety of fields as an industrial material having free cutting property.
  • the increase of machinability by adding lead to a metal is not only used for nonferrous alloy, but also in the field of steel.
  • Copper-Zinc system alloy containing lead is used in the large quantity for parts of life-related machines or devices. In the field of water-contact metal fittings (metallic parts), especially, this tendency is remarkable. On the other hand, the contamination of water in quality which is caused by the change of our living environment, and the use of hot water which is resulted from the popularization of hot water heaters are generalized.
  • free cutting brass comprises :
  • free cutting brass comprises :
  • the content of lead is zero, and a metal element which is gentle for the environment and the quality of water is contained to improve machinability in place of lead.
  • the content of lead is as low as possible, and a selected metal element is contained in the co-existence with a third added metal to provide intermetallic compound therebetween, thereby improving machinability and increasing the elution resistance of lead.
  • Lead in brass does not form solid solution with copper and zinc, and precipitates at grain boundaries at the time of solidification. Consequently, cutting property is effectively improved.
  • Table 1 explains the formation and the non-formation of intermetallic compounds with copper and zinc by the above described candidate elements, and the state of solid solution thereof.
  • bismuth has been selected as a metal element replacing lead.
  • Lead and bismuth are of low melting points (Pb : 327°C and Bi : 271°C).
  • the density of lead is 10.5 g/cm 3 at 800°C and 9.81 g/cm 3 at 1000°C, and that of bismuth is 9.4 g/cm 3 at 800 °C and 9.2 g/cm 3 at 1000°C. These values are considerably high as compared to the density of 7.32 g/cm 3 at 1000°C for mother material of 60/40 brass .
  • Table 2 shows properties of reacting products between Misch Metal (defined "M.M.” hereinafter, and mixture of rare earth elements consisting mainly of cerium and lanthanum ) and each of elements composing a mother material.
  • Misch Metal defined “M.M.” hereinafter, and mixture of rare earth elements consisting mainly of cerium and lanthanum
  • intermetallic compounds of M.M. formed in accordance with the reaction with lead and bismuth are thermodynamically more stable than intermetallic compounds with copper and zinc.
  • M.M. is selected as a third added metal.
  • the preferred embodiments according to the invention are divided into two cases, wherein elution of lead is discussed to be important in free cutting brass in one preferred embodiment, and machinability is discussed to be important in free cutting brass in another preferred embodiment.
  • the free cutting brass in the former preferred embodiment is Cu-Zn-Bi-M.M system alloy, and the free cutting brass in the latter preferred embodiment is Cu-Zn-Bi-Pb-M.M. system alloy in which lead and bismuth are co-existed.
  • Test materials are prepared as set out below.
  • Table 3 explains chemical compositions of Cu-Zn-Bi-M.M. system alloy, and Table 4 explains those of Cu-Zn-Bi-Pb-M.M. system alloy.
  • Table 3 explains chemical compositions of test materials for Cu-Zn-Bi-M.M. system alloy.
  • test materials for the former alloy are prepared in accordance with the steps of casting by using a carbon mold having a diameter of 30 mm, and machining to be a diameter of 25mm, and those for the latter alloy are prepared in accordance with the steps of casting by using a water cooling mold having a diameter of 45 mm, machining to be a diameter of 40mm, extruding at a temperature of 720 °C to be a diameter of 18.5 mm, and cold-drawing with a drawing degree of 10.5 % to be a diameter of 17.5 mm.
  • Dispersion phase is observed by an optical microscope, and is analyzed in distribution state in accordance with the treatment by an image analysis system, intermetallic compounds formed by adding M.M. are observed by an electronic microscope, and is analyzed by an X ray microanalyzer (X-MA), and the behavior of dispersion phase is observed at a high temperature by heating.
  • X-MA X ray microanalyzer
  • Figs. 1A to 1D and 2A and 2B show X-MA analysis images of typical intermetallic compounds observed in the test material A-8 (59.7 Cu-37.32 Zn-2.22 Bi-0.5 M.M.) and the test material C-2 (59.6 Cu-37Zn-1.51 Bi-1.52Pb-0.27 M.M.).
  • the intermetallic compounds of the test material A-8 have nucleus formed by Bi-M.M. and covered in periphery with bismuth.
  • the intermetallic compounds of the test material C-2 are observed to have main bodies of Bi-M.M. covered with lead.
  • the present system alloys are generally processed to be products by hot working (extruding, forging, etc.), cold working, annealing, etc. Due to thermal load at the time of the process, bismuth and lead contained therein as dispersion phase are cohered to be coarse, because they are of low melting points, so that this will be a cause for a problem to occur in the alloys.
  • test materials are prepared from a forging material and an extruding material (extruding temperature less than 720°C) to investigate the state of dispersion phase.
  • Table 5 shows the behavior of dispersion phase prior to thermal load and thereafter observed in accordance with the treatment by an image analysis system.
  • test material B-1 The conventional free cutting brass (test material B-1) is observed to be remarkable in thermal effect. In accordance with the result, it is understood that lead of dispersion phase is cohered to be coarse. Comparing the test materials B-3 and B-9, thermal effect of dispersion phase for the latter test material is considerably suppressed. Considering the composition of the test material B-9, the alloy is Cu-Zn-Bi-M.M system alloy having the added M.M., although the Bi-content is constant. As discussed in the metallurgical investigation, it is considered that this is because Bi-M.M. compounds which are high in thermal stability are formed by the addition of M.M. Comparing the test materials D-1 and D-4, the influence of thermal load to dispersion phase for the latter test material is considerably suppressed. This phenomenon is for the same reason as discussed above.
  • the workability is studied mainly in regard to cutting property (machinability) and ductility.
  • the marginal compressibility factor is obtained by measuring a deformation amount of a test piece having a size of 10mm diameter and 10mm length immediately prior to the occurrence of crack under the condition that a load is applied to the test piece, which is prepared by machining a cold drawing material having a diameter of 17.5mm, by a compression test machine.
  • the marginal compressibility factor MCF is defined by the below equation. where He is a height of the test piece prior to the test, and H is that of the test piece after the test.
  • Table 6 explains one example of the test results.
  • the Cu-Zn-Bi-M.M. system alloy and the Cu-Zn-Bi-Pb-M.M. system alloy provide better compression workability than the conventional free cutting brass, and, especially, the Cu-Zn-Bi-Pb-M.M. system alloy represents excellent property.
  • Test materials for the cutting test are mainly casting materials
  • test materials for the bore formation test are mainly cold drawing materials.
  • Figs. 3A to 3E show cutting conditions and the configuration of a bits (cutting tool), and the evaluation of the cutting property is made dependent on the size and the configuration of chips.
  • Table 7 explains bore formation test conditions. In the test, a time required to form a bore having a depth of 5mm is measured to evaluate the bore formation property.
  • the bore formation is carried out as shown in Fig. 4.
  • Figs. 5A to 5E are pictures showing the appearance of the chips of each test material, wherein the test material A-1 is 60/40 brass, the test material A-2 is the conventional free cutting brass, and the test materials A-4, A-5 and A-6 are the free cutting brasses in the preferred embodiment.
  • the curling diameter of the chips for the test materials A-4, A-5 and A-6 is slightly larger than those for the test material A-2, and the length thereof is similar to each other for those test materials. This means that the free cutting brass of the invention provides a stable cutting property.
  • Figs. 6A and 6B are for pictures showing the appearance of the chips of each test material.
  • the configuration (curling diameter and chip length) of the chips for the test materials in the preferred embodiment represents cutting property equivalent to that of the conventioned free cutting brass.
  • Table 8 explains the measurement results of the bore formation test.
  • the bore formation property is improved in proportion to the content amount of bismuth.
  • the content amount of bismuth is greater than 2%, a considerably good property is obtained.
  • it is considered that a good property is obtained in the present system alloy containing bismuth and M.M. as compared to an alloy containing no M.M., but bismuth, because compound formed by bismuth and M.M. is uniformly dispersed.
  • Fig. 7 shows the state of bore formation property for alloys in which a bismuth content is constant, but a M.M. content is changed. In accordance with the results, the aforementioned tendency is confirmed.
  • Table 9 explains the measurement results of the alloy. In accordance with the results, it is confirmed in the present system alloys that a good bore formation property is obtained as confirmed in the aforementioned cutting property. Even in a composition having a considerably less content of dispersion phase, the bore formation property approximately equivalent to the conventional free cutting brass is obtained. This is because bismuth and lead are co-existed, so that eutectic of a low melting point is formed, and dispersion phase is uniformly depersed in accordance with the formation of intermetallic compounds by the addition of M.M.
  • a first type of free cutting alloy containing no lead according to the invention results in no effect or influence to the quality of water, and a second type of free cutting alloy containing the minimum amount of lead results in no decrease of free cutting property.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Domestic Plumbing Installations (AREA)
  • Powder Metallurgy (AREA)
EP93301814A 1992-03-10 1993-03-10 Laiton à usinage facile Withdrawn EP0560590A2 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP8646392A JPH05255778A (ja) 1992-03-10 1992-03-10 快削性黄銅合金
JP86463/92 1992-03-10

Publications (2)

Publication Number Publication Date
EP0560590A2 true EP0560590A2 (fr) 1993-09-15
EP0560590A3 EP0560590A3 (fr) 1994-02-02

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Family Applications (1)

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EP93301814A Withdrawn EP0560590A2 (fr) 1992-03-10 1993-03-10 Laiton à usinage facile

Country Status (2)

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EP (1) EP0560590A2 (fr)
JP (1) JPH05255778A (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5487867A (en) * 1993-04-22 1996-01-30 Federalloy, Inc. Copper-bismuth casting alloys
WO2011012931A1 (fr) * 2009-07-31 2011-02-03 Elsan Hammadde Sanayi Anonim Sirketi Alliage de laiton à faible teneur en plomb contenant des lanthanides
WO2011067682A1 (fr) 2009-12-03 2011-06-09 Elsan Hammadde Sanayi Anonim Sirketi Alliage de laiton à faible teneur en plomb

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3485502B2 (ja) * 1999-08-24 2004-01-13 日立アロイ株式会社 無鉛快削性銅合金材
JP2001280757A (ja) * 2000-03-30 2001-10-10 Sanyo Electric Co Ltd 冷凍装置
JP2002069551A (ja) * 2000-09-04 2002-03-08 Sumitomo Light Metal Ind Ltd 快削性銅合金
KR100389777B1 (ko) * 2001-01-09 2003-06-27 이구산업 주식회사 고강도 절삭성이 우수한 무연쾌삭 황동합금
JP2003277855A (ja) * 2002-03-22 2003-10-02 San-Etsu Metals Co Ltd 無鉛快削黄銅合金材及びその製造方法
JP2006097074A (ja) * 2004-09-29 2006-04-13 Dowa Mining Co Ltd 快削黄銅
KR100861488B1 (ko) * 2007-03-21 2008-10-02 대창공업 주식회사 동합금으로부터 납 또는 비스무트를 제거하는 방법
CN104711450A (zh) * 2015-04-03 2015-06-17 北京金鹏振兴铜业有限公司 高强度高延展性镁黄铜合金

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS54135618A (en) * 1978-04-13 1979-10-22 Sumitomo Metal Mining Co Cuttable presssformable brass bismuth alloy
US4879094A (en) * 1987-10-16 1989-11-07 Imi Yorkshire Fittings Limited Cu--Sn--Zn--Bi alloys
WO1992015718A1 (fr) * 1991-03-01 1992-09-17 Olin Corporation Alliages de cuivre usinables a teneur reduite en plomb

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS54135618A (en) * 1978-04-13 1979-10-22 Sumitomo Metal Mining Co Cuttable presssformable brass bismuth alloy
US4879094A (en) * 1987-10-16 1989-11-07 Imi Yorkshire Fittings Limited Cu--Sn--Zn--Bi alloys
WO1992015718A1 (fr) * 1991-03-01 1992-09-17 Olin Corporation Alliages de cuivre usinables a teneur reduite en plomb

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
ADVANCED MATERIALS AND PROCESSES vol. 10, 1991, pages 23 - 27 PLEWES, J.T. AND LOIACONO 'Free-Cutting Copper Alloys contain no Lead' *

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5487867A (en) * 1993-04-22 1996-01-30 Federalloy, Inc. Copper-bismuth casting alloys
WO2011012931A1 (fr) * 2009-07-31 2011-02-03 Elsan Hammadde Sanayi Anonim Sirketi Alliage de laiton à faible teneur en plomb contenant des lanthanides
WO2011067682A1 (fr) 2009-12-03 2011-06-09 Elsan Hammadde Sanayi Anonim Sirketi Alliage de laiton à faible teneur en plomb

Also Published As

Publication number Publication date
EP0560590A3 (fr) 1994-02-02
JPH05255778A (ja) 1993-10-05

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