MXPA06010239A

MXPA06010239A - Copper alloy

Info

Publication number: MXPA06010239A
Application number: MXPA/A/2006/010239A
Authority: MX
Inventors: Oishi Keiichiro
Original assignee: Sanbo Shindo Kogyo Kabushiki Kaisha
Priority date: 2004-08-10
Filing date: 2006-09-08
Publication date: 2007-04-20

Abstract

A copper alloy, which has a chemical composition, in mass%, that Cu:69 to 88%, Si:2 to 5%, Zr:0.0005 to 0.04%, P:0.01 to 0.25%, and the balance:Zn, wherein with respect to [a]mass%representing the content of the element a, the relationships:f0=[Cu]- 3.5[Si]- 3[P]=61 to 71, f1=[P]/[Zr]=0.7 to 200, f2=[Si]/[Zr]=75 to 5000 and f3=[Si]/[P]=12 to 240 are satisfied, which has a metal structure wherein a phase and ? phase and/or ? phase are present and, with respect to [b]%representing the content of the phase b, the relationships:f4=[a]+ [?]+ [?]=85 and f5=[?]+ [?]+ 0.3[]- [ss]=5 to 95 are satisfied, and which has an average crystal grain diameter of 200 m or less in a macroscopic structure immediately after the solidification of a melt of the alloy.

Description

COPPER ALLOY BACKGROUND OF THE INVENTION 1. FIELD OF THE INVENTION The present invention relates to an alloy based on Cu-Zn-Si having excellent moldability, mechanical properties (toughness, ductility, etc.), corrosion resistance, wear resistance, susceptibility to machining and the like. 2. DESCRIPTION OF THE RELATED ART It has been known that copper alloys are improved in their elastic limit by refinement of grain like common metallic materials, and according to the Hall-Petch law, copper alloys present an improvement in tenacity in proportion to the inverse of the square root of the grain diameter. In addition, copper alloys are generally used for two basic types of grain refinement as follows: (A) when copper alloys melt and solidify, (B) when copper alloys (ingots such as slabs, smelters such as pressure castings, melted castings, etc.), then the melt solidification is subjected to either deformation such as rolling or heating, and the resulting stored energy such as the distorted energy acts as a driving force. In any of the cases of subsections (A) or (B), zirconium (Zr) is known as an element that effectively affects grain refinement. However, in the case of process (A), since grain refinement affects Zr in the melting-solidification stage and is considerably influenced by other elements and their contents, the desired level of grain refinement is not obtained . For this reason, in general, the technique of (B) has been widely used, where grain refinement is facilitated by heat treatment on ingots, smelting and so on after melting-solidification and after endowing of distortion again. According to the teachings of Japanese Examined Patent Application Publication No. 38-20467, a copper alloy containing Zr, P and Ni is subjected to melt processing, cold worked at a rate of 75% and examination of its average grain diameter, in which the average grain diameter decreases in proportion to increase the Zr content, for example, 280 μm when it does not contain Zr, 170 μm (Zr content: 0.05% by mass), 50 μm (content of Zr: 0.13% by mass), 29 μm (content of Zr: 0.22% by mass) and 6 μm (content of Zr: 0.89% by mass). In this document, it is proposed to contain 0.05 to 0.3% by mass of Zr in order to avoid the adverse effect caused by an excessive content of Zr. Furthermore, it is disclosed in Japanese Unexamined Patent Application Publication No. 2004-233952 that when a copper alloy to which 0.15 to 0.5% by mass Zr is added, it is subjected to smelting, melt processing and processing by deformation for addition by distortion, its average grain diameter is refined at a level of approximately 20 μm or less. However, as in the technique (B) this treatment and worked after casting to refine the grain diameter results in increased costs. In addition, some smelters can not be subjected to deformation processing for addition by distortion due to their shapes. As such, the grains are preferably refined by the technique of (A) when the copper alloy melts and solidifies. However, in the case of the technique of (A) which is established in the foregoing, Zr is greatly influenced by other elements and their contents in the melting-solidification stage. Therefore, although the Zr content is increased, the refinement of grain corresponding to the increase is not necessarily obtained. In addition, Zr has a very strong affinity for oxygen. Consequently, when it has melted and added into the atmosphere, Zr easily forms an oxide and is very low in performance. As such, although a very small amount of Zr is contained in products after smelting, it is required to load a considerable quantity of raw material in the casting stage. Meanwhile, when too much is produced during melting, the oxide easily integrates when casting is performed, and there is a likelihood of generating casting defects. In order to avoid oxide production, melting and melting under vacuum and an inert gas atmosphere can be carried out, which causes increased costs. In addition, because Zr is a costly element, its aggregate amount is preferably limited to be as small as it can be from the economic point of view. For this reason, a copper alloy having a Zr content as small as possible is required and simultaneously the average grain diameter refined in the next step after melting-solidification of the casting process. In addition, in the case of an alloy based on Cu-Zn-Si, it serves to improve the mechanical property, etc., but during melting-solidification, it has problems that it is easy to generate a fracture or porosity, that a cavity of Shrinkage is large and it is easy to generate casting defects such as a blowhole. The main reason is that as the Si content increases, the solidification temperature range (a difference between the liquid temperature and the solid temperature) is extended and the thermal conductivity deteriorates. Furthermore, by taking the concept of a solidification structure of a conventional alloy based on Cu, Zn-Si, a dendrite is generated in a branching pattern similar to a tree. The arms of the dendrite make it difficult to discharge the air bubbles generated into the air, which are responsible for the residual blowholes and local generation of a large shrinkage cavity. The present invention provides an alloy based on Cu-Zn-Si capable of significantly improving the properties of copper alloy such as moldability, various mechanical properties, corrosion resistance, machinability susceptibility, workability, etc., by means of refinement of grains and simultaneously a method for manufacturing it.

BRIEF DESCRIPTION OF THE INVENTION In order to carry out the objective, the present invention proposes a copper alloy and a method for manufacturing the same, as follows: First, the present invention proposes a copper alloy (hereinafter referred to as a copper alloy). "first copper alloy") consisting essentially of Cu: 69 to 88% by mass (preferably 70 to 84% by mass, more preferably 71.5 to 79.5% by mass, and most preferably 73 to 79% by mass ), Yes: 2 to 5% by mass (preferably 2.2 to 4.8% by mass, more preferably 2.5 to 4.5% by mass, and more preferably 2. 7 to 3.7% by mass), Zr: 0.0005 to 0.04% by mass (preferably 0.0008 to 0.029% by mass, more preferably 0.001 to 0.019% by mass, more preferably 0. 0025 to 0.014% by mass and much more preferably 0.004 to 0.0095% by mass), P: 0.01 to 0.25% by mass (preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass, and much more preferably 0.04 to 0.12% by mass), Zn: remainder and satisfying the following conditions (1) to (7). In the first copper alloy, it is preferable that it additionally meet the following conditions (10) to (15), including conditions (1) to (7). When the first copper alloy requires cutting, it is preferable that it additionally meet condition (17), including conditions (1) to (7) and (10) to (15). Secondly, the present invention proposes a copper alloy (hereinafter referred to as "second copper alloy") containing at least one Sn, As and Sb element in addition to the constituent elements of the first copper alloy, it is to say, that it consists essentially of Cu: 69 to 88% by mass (preferably 70 to 84% by mass, more preferably 71.5 to 79.5% by mass, and most preferably 73 to 79% by mass); Yes: 2 to 5% by mass (preferably 2.2 to 4.8% by mass, more preferably 2.5 to 4.5% by mass, and more preferably 2.7 to 3.7% by mass), Zr: 0.0005 to 0.04% by mass ( preferably 0.0008 to 0.029% by mass, more preferably 0.001 to 0.019% by mass, more preferably 0.0025 to 0.014% by mass and much more preferably 0.004 to 0.0095% by mass), P: 0.01 to 0.25% by mass mass (preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass, and much more preferably 0.04 to 0.12% by mass), at least one element that is selected from Zn: 0.05 a 1.5% by mass (preferably 0.1 to 0.9% by mass, more preferably 0.2 to 0.7% by mass and much more preferably 0.25 to 0.6% by mass), As: 0.02 to 0.25% by mass (preferably 0.03 to 0.15% by mass), and Sb: 0.02 to 0.25% by mass (preferably 0.03 to 0.15% by mass); and Zn: remainder and that satisfies the following conditions (1) to (7). In the second copper alloy, it is preferable that it additionally satisfy the following conditions "(10) to (15), including conditions (1) to (7)." When the second copper alloy requires cutting, it is preferable that it additionally satisfy condition (17), including conditions (1) to (7) and (10) to (15) Thirdly, the present invention proposes a copper alloy (hereinafter referred to as "third copper alloy") which contains at least one element selected from Al, Mn and Mg, in addition to the constituent elements of the first copper alloy, ie, consisting essentially of Cu: 69 to 88% by mass (preferably 70 to 84% by weight) dough, more preferably 71.5 to 79.5% by mass, and much more preferably 73 to 79% by mass); Si: 2 to 5% by mass (preferably 2.2 to 4.8% by mass, most preferably 2.5 to 4.5% by mass, and much more preferable 2.7 to 3.7% by mass); Zr: 0.0005 to 0.04% by mass (prefer preferably 0.0008 to 0.029% by mass, more preferably 0.001 to 0.019% by mass, still more preferably 0.0025 to 0.014% by mass and much more preferably 0.004 to 0.0095% by mass), P: 0.01 to 0.25% in bulk (preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass, and much more preferably 0.04 to 0.12% by mass); at least one element that is selected from Al: 0.02 to 1.5% by mass (preferably 0.1 to 1.2% by mass), Mn: 0.2 to 4% by mass (preferably 0.5 to 3.5% by mass) and Mg: 0.001 to 0.2 % in mass; and Zn: remainder and that satisfies the following conditions (1) to (7). In the third copper alloy, it is preferable that it additionally meet the following conditions (10) to (15), including conditions (1) to (7). When the third copper alloy requires cutting, it is preferable that it additionally meet condition (17), including conditions (1) to (7) and (10) to (15). Fourth, the present invention proposes a copper alloy (hereinafter referred to as "fourth copper alloy") containing at least one element that is selected from Sn, As and Sb and at least one element that is selected from Al, Mn and Mg, in addition to the constituent elements of the first copper alloy, that is, consisting essentially of Cu: 69 to 88% by mass (preferably 70 to 84% by mass, more preferably 71. 5 to 79.5% by mass, and more preferably 73 to 79% by mass); Yes: 2 to 5% by mass (preferably 2.2 to 4.8% by mass, more preferably 2.5 to 4.5% by mass, and much more preferably 2.7 to 3.7% by mass); Zr: 0.0005 to 0.04% by mass (preferably 0.0008 to 0.029% by mass, more preferably 0.001 to 0.019% by mass, still more preferably 0.0025 to 0.014% by mass and much more preferably 0.004 to 0.0095% by mass mass), P: .0.01 to 0.25% by mass (preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass, and much more preferably 0.04 to 0.12% by mass); at least one element that is selected from Sn: 0.05 to 1.5% by mass (preferably 0.1 to 0.9% by mass, more preferably 0.2 to 0.7% by mass and much more preferably 0.25 to 0.6% by mass), As: 0.02 to 0.25% by mass (preferably 0.3 to 0.15% by mass) and Sb: 0.02 to 0.25% by mass (preferably, 0.03 to 0.15% by mass); At least one element that is selected from Al: 0.02 to 1.5% by mass (preferably 0.1 to 1.2% by mass), Mn: 0.2 to 4% by mass (preferably 0.5 to 3.5% by mass) and Mg: 0.001 to 0.2% by mass; and Zn: remainder and that meets the following conditions (1) to (7). In the fourth copper alloy, it is preferable that it additionally meet the following conditions (10) to (15), including conditions (1) to (7). When the fourth copper alloy requires cutting, it is preferable that it additionally meet condition (17), including conditions (1) to (7) and (10) to (15). Fifth, the present invention proposes a copper alloy (hereinafter referred to as "fifth copper alloy") containing at least one element that is selected from Pb, Bi, Se and Te in addition to the constituent elements of the first copper alloy, that is, consisting essentially of Cu: 69 to 88% by mass (preferably 70 to 84% by mass, more preferably 71. 5 to 79.5% by mass, and much more preferably 73 to 79% by mass); Yes: 2 to 5% by mass (preferably 2.2 a 4. 8% by mass, more preferably 2.5 to 4.5% by mass, and much more preferably 2.7 to 3.7% by mass); Zr: 0.0005 to 0.04% by mass (preferably 0.0008 to 0.029% by mass, more preferably 0.001 to 0.019% by mass, still more preferably 0.0025 to 0.014% by mass and much more preferably 0.004 to 0.0095% by mass mass), P: 0.01 to 0.25% by mass (preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass, and much more preferably 0.04 to 0.12% by mass); at least one element that is selected from Pb: 0.005 to 0.45% by mass (preferably 0.05 to 0.2% by mass and more preferably 0.005 to 0.1% by mass), Bi: 0.005 to 0.45% by mass (preferably 0.005 to 0.2% by mass and more preferably 0.005 to 0.1% by mass), Se: 0.03 to 0.45% by mass (preferably 0.05 to 0.2% by mass), and more preferably 0.005 to 0.1% by mass), and Te: 0.01 to 0.45% by mass (preferably 0.03 to 0.2% by mass and more preferably 0.05 to 0.1% by mass) dough); and Zn: remainder and that meets the following conditions (1) to (8). In the fifth copper alloy, it is preferable that it additionally meet the following conditions (9) to (16), including conditions (1) to (8). When the fifth copper alloy requires cutting, it is preferable that it additionally comply with condition (17), including conditions (1) to (8) and (9) to (16). Sixth, the present invention proposes a copper alloy (hereinafter referred to as "sixth copper alloy") containing at least one element that is selected from Sn, As and Sb in addition to the constituent elements of the fifth alloy of copper, that is, consisting essentially of Cu: 69 to 88% by mass (preferably 70 to 84% by mass, more preferably 71.5 to 79.5% by mass, and most preferably 73 to 79% by mass); Yes: 2 to 5% by mass (preferably 2.2 to 4.8% by mass, more preferably 2.5 to 4.5% by mass, and much more preferably 2.7 to 3.7% by mass); Zr: 0.0005 to 0.04% by mass (preferably 0.0008 to 0.029% by mass, more preferably 0.001 to 0.019% by mass, still more preferably 0.0025 to 0.014% by mass and much more preferably 0.004 to 0.0095% by mass mass), P: 0.01 to 0.25% by mass (preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass, and much more preferably 0.04 to 0.12% by mass); Pb: 0.005 to 0.45% by mass (preferably 0.005 to 0.2% by mass and more preferably 0.005 to 0.1% by mass), Bi: 0.001 to 0.45% by mass (preferably 0.005 to 0.2% by mass and most preferably 0.005 to 0.1% by mass), Se: 0.03 to 0.45% by mass (preferably 0.05 to 0.2% by mass), and more preferably 0.05 to 0.1% by mass); Te: 0.01 to 0.45% by mass (preferably 0.03 to 0.2% by mass and more preferably 0.05 to 0.1% by mass); at least one element that is selected from Sn: 0.05 to 1.5% by mass (preferably 0.1 to 0.9% by mass, more preferably 0.2 to 0.7% by mass and much more preferably 0.25 to 0.6% by mass), As: 0.02 to 0.25% by mass (preferably 0.03 to 0.15% by mass) and Sb: 0.02 to 0.25% by mass (preferably 0.03 to 0.15% by mass); and Zn: remainder and that satisfies the following conditions (1) to (8). In the sixth copper alloy, it is preferable that it additionally meet the following conditions (9) to (16), including conditions (1) to (8). When the sixth copper alloy requires -cutting, it is preferable that it additionally comply with condition (17), including conditions (1) to (8) and (9) to (16). • Seventh, the present invention proposes a copper alloy (hereinafter referred to as "seventh copper alloy") containing at least one element that is selected from Al, Mn and Mg, in addition to the constituent elements of the fifth copper alloy, ie, consisting essentially of Cu: 69 to 88% by mass (preferably 70 to 84% by mass, more preferably 71.5 to 79.5% by mass, and much more preferably 73 to 79% by mass) dough); Yes: 2 to 5% by mass (preferably 2.2 to 4.8% by mass, more preferably 2.5 to 4.5% by mass, and much more preferably 2.7 to 3.7% by mass); Zr: 0.0005 to 0.04% by mass (preferably 0.0008 to 0.029% by mass, more preferably 0.001 to 0.019% by mass, still more preferably 0.0025 to 0.014% - by mass and much more preferably 0.004 to 0.0095% in bulk), P: 0.01 to 0.25% - by mass (preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass, and much more preferably 0.04- to 0.12% by mass); Pb: 0.005 to 0.45% by mass (preferably 0.005 to 0.2% by mass and more preferably 0.005 to 0.1% by mass), Bi: 0.005 to 0.45% by mass (preferably 0.005 to 0.2% by mass, and more preferably preferable 0.005 to 0.1% by mass), Se: 0.03 to 0.45% by mass (preferably 0 -.05 to 0.02% by mass), and most preferably 0.05 to 0.1% by mass); Te: 0.01 to 0.45% by mass (preferably 0.03 to 0.2% by mass and more preferably 0.05 to 0.1% by mass); at least one element that is selected from Al: 0.02 to 1.5% by mass (preferably 0.1 to 1.2% by mass), Mn: 0.2 to 4% by mass (preferably 0.5 to 3.5% by mass) and Mg: 0.01 to 0.2% by mass; and Zn: remainder and meet the following conditions (1) to (8). In the seventh copper alloy, it is preferable that it additionally meet the following conditions (9) to (16), including conditions (1) to (8). When the seventh copper alloy requires cutting, it is preferable that it additionally comply with condition (17), including conditions (1) to (8) and (9) to (16). Eighth, the present invention proposes a copper alloy (hereinafter referred to as "octave copper alloy") which contains at least one element which is selected from Sn, As and Sb and at least one which is selected from Al , Mn and Mg, in addition to the constituent elements of the fifth copper alloy, ie, consisting essentially of Cu: 69 to 88% by mass (preferably 70 to 84% by mass, most preferably 71.5 to 79.5% by mass mass, and much more preferably 73 to 79% by mass); Yes: 2 to 5% by mass (preferably 2.2 to 4.8% by mass, more preferably 2.5 to 4.5% by mass, and much more preferably 2.7 to 3.7% by mass); Zr: 0.0005 to 0.04% by mass (preferably 0.0008 to 0.029% by mass, more preferably 0.001 to 0.019% by mass, still more preferably 0.0025 to 0.014% by mass and most preferably 0.004 to 0.0095% by mass ), P: 0.01 to 0.25% by mass (preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass, and much more preferably 0.04 to 0.12% by mass); Pb: 0.005 to 0.45% by mass (preferably 0.005 to 0.2% by mass and more preferably 0.005 to 0.1% by mass), Bi: 0.005 to 0.45% by mass (preferably 0.005 to 0.2% by mass and most preferably 0.005 to 0.1% by mass), Se: 0.03 to 0.45% by mass (preferably 0.05 to 0.02% by mass), and more preferably 0.05 to 0.1% by mass); Te: 0.01 to 0.45% by mass (preferably 0.03 to 0.2% by mass and more preferably 0.05 to 0.1% by mass); at least one element selected from Sn: 0.05 to 1.5% by mass (preferably 0.1 to 0.9% by mass, more preferably 0.2 to 0.7% by mass and more preferably 0.25 to 0.6% by mass), As : 0.02 to 0.25% by mass (preferably 0.03 to 0.15% by mass), and Sb: 0.02 to 0.25% by mass (preferably 0.03 to 0.15% by mass); at least one element that is selected from Al: 0.02 to 1.5% by mass (preferably 0.1 to 1.2% by mass), Mn: 0.2 to 4% by mass (preferably 0.5 to 3.5% by mass) and Mg: 0.001 to 0.2 % in mass; and Zn: remainder and that fulfills the following conditions (1) to (8). In the eighth copper alloy, it is preferable that it additionally meet the following conditions (9) to (16), including conditions (1) a (8) When the eighth copper alloy requires cutting, it is preferable that it additionally comply with condition (17), including conditions (1) to (8) and (9) to (16). In the following description, [a] represents the content of an element a, where the content of element a is represented by [a]% by mass. For example, the content of Cu is expressed as [Cu]% by mass. Further, [b] represents a content in terms of a phase area rate b, where the content (area ratio) of phase b is expressed by [b]%. For example, the content (area rate) of the phase, a, is expressed by [a]%. In addition, the area rate content of each phase b is measured by an image analysis and is obtained particularly by binarization using WinROOF image processing software (available from TECH-JAM Co., Ltd.), and is a value average of the area rates measured with three views. (1) fO = [Cu] - 3.5 [Si] - 3 [P] + 0.5 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) - 0.5 ([Sn] + [As ] + [Sb]) -1.8 [Al] + 2 [Mn] + [Mg] = 61 to 71 (preferably fO = 62 to 69.5, most preferably fO = 62.5 to 68.5, and most preferably fO = 64 to -67). Also, in the case of fO, [a] = 0 with respect to a non-contained element. (2) fl = [P] / [Zr] = 0.7 to 200 (preferably fl = 1.2- to 100, preferably fl = 2.3 to 50 and more preferably di = 3.5 to 30). (3) f2 = [Si] / [Zr] = 75 to 5000 (preferably f2 = 120 to 3000, more preferably f2 = 180 to 1500 and more preferably d2 = 300 to 900). (4) f3 = [Yes] / [P] = 12 to 240 (preferably f3 = 16 to 160, more preferably f3 = 20 to 120, and most preferably f3 = 25 to 80). (5) Which contains phase a and phase K or phase? and f4 = [a] + [y] + [K] >; 85 (preferably f4 >.95). In addition, in the case of f4, [b] = 0 with respect to a phase b not contained. (6) f5 = [y] + [K] + 0.3 [μ] - [ß] = 5 to 95 (preferably f5 = 10 to 70, more preferably f5 = 15 to 60 and more preferably f5 = 20 to 45). In addition, in the case of f5, [b] = 0 with respect to phase b not contained. (7) Having an average grain diameter of 200 μm or less, preferably 150 μm or less, more preferably 100 μm and much more preferably 50 μm or less) in a macrostructure during melt-solidification. Here, the average grain diameter in the macrostructure (or microstructure) during melt-solidification refers to an average value of grain diameters in a macrostructure (or microstructure) in a state where the deformation (extrusion, lamination, etc.). ), or heating are not carried out after melt-solidification by melting (which includes various conventionally known castings such as permanent mold casting, sand casting, horizontal continuous casting, casting up (upper casting), semi-solid metal casting, semi-solid metal forging, and fusion forging), welding or fusion cutting. In addition, the term "smelting" or "smelting" used herein refers to any object in which the whole or part is melted and solidified, and for example, includes sand casting, casting in a metal mold, casting at low pressure, die-casting, lost-wax casting, semi-solid casting (eg thixofunding, re-casting, casting of a semi-solid metal, compression casting, centrifugal casting and continuous casting (for example with a rod, a hollow rod, an irregularly shaped rod, an irregularly shaped hollow rod, a coil, a wire, etc., made by continuous horizontal casting, casting up or upper casting) or a casting made by forced fusion (direct forging), metallization sprinkling, coating or overlaying, which includes a laminate or an extrusion ingot, a slab and a billet. it is understood that welding is included in the foundry in a broad sense because a base metal partially melts, solidifies and joins. (8) tß = [Cu] - 3.5 [SI] - 3 [P] + 3 ([pb] + 0. 8 ([Bi] + [Se]) + 0.6 [Te]) 1/2 > 62 (preferably f6 > 63. 5) and f7 = [Cu] - 3.5 [Si] - 3 [P] - 3 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) 12 < 68.5 (preferably f7 < 67). Also, in the case of f6 and f7, [a] = 0 with respect to a non-contained element. (9) f8 = [?] + [K] + 0.3 [μ] - [ß] + 25 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) 1/2 > 10 (preferably f8 > 20) and f9 = [y] + [K] + 0.3 [μ] - [ß] - 25 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te] 1 2 £ 70 (preferably f9 <50) In addition, in the cases of f7 and f8. [A] = 0 p [b] = 0 with respect to an element not contained or a phase b not contained. (10) A primary crystal generated during fusion-solidification is in phase A. (11) Generation of a peripéctic reaction during fusion-solidification. (12) During fusion-solidification, have a crystalline structure where the dendrite network is divided and a grain whose two-dimensional form is a circular shape, a non-circular shape close to a circular shape, an elliptical shape, a cross shape, an acicular shape or a polygonal shape. (13) Having a matrix whose phase a is finely divided and whose phase K or phase? Are uniformly distributed. (14) A semi-molten state that has a solid phase fraction of 30 to 80%, which has a crystalline structure where the network den drita divides into at least one solid phase whose two-dimensional shape is a circular shape, a non-circular shape close to the circular shape, an elliptical shape, a cross shape or a polygonal shape. (15) A semi-molten state having a 60% solid phase fraction, having a solid phase of an average grain diameter of 150 μm or less (preferably 100 μm or less, more preferably 50 μm or less, and much more preferably 40 μm or less) or of a maximum average length of 200 μm or less (preferably 150 μm or less, more preferably 100. μm or less, and much more preferably 80 μm or less). (16) In the case that there is a content of Pb or Bi, which has a matrix in which the particles of Pb or Bi of a fine and uniform size are evenly distributed, where the Pb or Bi particles have a diameter of average grain of 1 μm or less (but preferably has a maximum grain diameter not exceeding 3 μm (preferably 2 μm). (17) In the case where the cutting is carried out in a dry atmosphere by a lathe equipped with a depth of an angle of attack: -6 ° and a tip radius: 0.4 mm under the conditions of a cutting speed: 80 to 160 m / min, a depth of cut: 1.5 mm and a feed speed : 0.11 mm / rev., That has generated chips that acquire a small segment shape (figure 5A) of a trapezoidal or triangular shape, a ribbon shape (Figure 5B) having a length of 25 mm or less or an acicular shape (Figure 5C). In addition, in the first to eighth copper alloys, Cu is a major element of each copper alloy, and is required to contain 69% by mass or more in order to ensure corrosion resistance (corrosion resistance by zinc elimination and resistance to fracture by stress corrosion) and mechanical properties as an industrial material. However, when the content of Cu exceeds 88% by mass, the toughness and the wear resistance are deteriorated so that there is a probability of preventing the refinement effect of grain by coaddition of Zr and P as described in the following . In considering this, the content of Cu is required to be 69 to 88% in bulk, preferably 70 to 84% by mass, more preferably 71.5 to 79.5% by mass and most preferably 73 to 79% by mass. Furthermore, in order to facilitate the refinement of grain, it is necessary to produce a large account of relationship with the other elements that are going to be contained in order to comply with the condition (1). In other words, the content of Cu and the other constituent elements is required to meet the ratio of fO = [Cu] - 3.5 [Si] - 3 [P] + 0.5 ([Pb] + 0.8 (Bi) + [Se ]) + 0.6 [Te]) - 0.5 ([Sn] + [As] + [Sb]) -1.8 [Al] + 2 [Mn] + [Mg] = 61 to 71, preferably fO = 62 to 69.5, of more preferably fO = 62.5 to 68.5 and more preferably fO = 64 to 67. In addition, a lower limit of fO is a value that indicates whether a primary crystal is a phase or not, and the upper limit is a value that indicates if the peritectic reaction is generated or not.

In the first to eighth copper alloys, Zn is a main element of each copper alloy along with Cu and Si and acts to decrease the stacking failure energy of the alloy, generate the peritectic reaction and provide refinement of grains in a material melted and solidified, improved fluidity and melting point reduction in a molten metal, prevention of oxidation loss of Zr, improvement of corrosion resistance and improvement of machinability susceptibility. In addition, Zn serves to improve mechanical tenacities such as tensile strength, yield strength, impact resistance and fatigue resistance. In consideration of this, a content of Zn is established to the rest excluding the content of each constituent element. In the first to the eighth copper alloys, when added together with Zr, P, Cu and Zn, Si is an element that serves to decrease the stacking fault energy of the alloy, to extend the range of the composition it takes part in the peritectic reaction and exert a significant effect of refinement of the grains. If it has an effect when its aggregate amount is 2% or greater. However, even when Si is added above 5%, the refinement of grain caused by coaddition with Cu and Zn saturates or deteriorates inversely, and also causes deterioration in ductility. In addition, when the Si content exceeds 5% the thermal conductivity deteriorates and the solidification temperature range is extended, so that there is a probability of deteriorating the moldability. Meanwhile, if it acts to improve the fluidity of a molten metal, avoid oxidation of the molten metal and lower the melting point. In addition, Si serves to improve the resistance to corrosion and particularly the resistance to corrosion by elimination of zinc and the resistance to fracture by stress corrosion. Furthermore, Si contributes to the improvement of the machinability susceptibility as well as the mechanical properties such as tensile strength, yield strength, impact resistance, etc. These actions cause a synergy effect in the refinement of grain foundries. For the purpose of effectively exercising this Si addition function, the content of Si is required to have a range of 2 to 5% by mass, preferably 2.2 to 4.8% by mass, more preferably 2.5 to 4.5% and so much more preferable 2.7 to 3.7% by mass, with the condition of fulfilling condition (1). In the first to eighth copper alloys, Zr and P are coaggregated in order to facilitate the refinement of copper alloy grains, and particularly during melt-solidification. In other words, Zr and P individually facilitate the refinement of copper alloy grains to a degree similar to other usual addition elements, but they exert a very significant function of grain refinement in a state of coexistence. With respect to Zr, this function of grain refinement is exerted at 0.0005% by mass or greater, effectively to 0.0008% by mass or greater, significantly to 0.001% by mass or greater, much more significantly at 0.0025 % by mass or greater and very significantly at 0.004% by mass or greater. With respect to P, this function of grain refinement is exerted at 0.01% by mass or greater, effectively at 0.02% by mass or greater, more significantly at 0.03% by mass or greater and very significantly at 0.04% by mass or older. Meanwhile, when the amount of addition of Zr constitutes 0.04% by mass and that of P constitutes 0.25% by mass, the function of refining grain by coadition of Zr and P is saturated regardless of the classes and contents of other constituent elements. Therefore, the addition amounts of Zr and P which are required to effectively exercise this function are 0.04% by mass or greater for Zr and 0.25% by mass or greater for P. Furthermore, when the addition amounts of Zr and P are small as set in the interval, Zr and P can uniformly distribute a high concentration of Sn, which is assigned to a phase? with priority, in a matrix without continuation by means of a refinement of grain, for example, even when the copper alloy contains Zn without deteriorating the properties of the alloy exerted by the other constituent elements, so that it is possible to avoid fractures of casting, obtaining a good casting having low porosity, shrinkage cavities, blowholes and microporosity and improving the working performance such as stressing or cold drawing performed after casting and therefore it is possible to further improve the properties of the alloy of interest. Furthermore, from an industrial point of view of adding a very small amount of Zr, the effect of grain refinement is not yet exercised even when Zr is added in excess of 0.019 mass%. The grain refinement effect can be damaged when Zr exceeds 0.029% by mass, and clearly is lacking when Zr exceeds 0.04% by mass. In addition, because Zr has a very strong affinity for oxygen, it is easy to generate oxide and Zr sulfide - when Zr melts in the air or scrapings are used as raw material. When Zr is added in excess the viscosity of the molten metal increases causing casting defects by inclusion of the oxide and sulfide during casting, so that it is easy to generate the blowhole or microporosity. In order to avoid this, melting and melting under vacuum or in a complete atmosphere of inert gas can be considered. In this case, the versatility disappears and the copper alloy costs are considerably increased when simply adding Zr as the refining element. In this regard, the amount of Zr addition which has not been formed of the oxide and the sulfide is preferably set to be 0.029 mass% or less, more preferably 0.019 mass% or less, even more preferably 0.014% by mass or less and much more preferably 0.0095% by mass. Furthermore, when the amount of Zr is established in this range the generation of the Zr oxide or sulfide decreases even when the corresponding copper alloy is melted in the air as a recycle material without new addition of a virgin material (or is melted using the raw material consisting only of the corresponding recycling materials). In this way it is possible to obtain the first to eighth good copper alloys formed of fine grains again. In this regard, it is required that the addition amount of Zr be in a range of 0.0005 to 0.04 mass%, preferably 0.0008 to 0.029 mass%, more preferably 0.001 to 0.019 mass%, even more preferably 0.0025 to 0.014% by mass and much more preferably 0.004 to 0.0095% by mass. In addition, P is added to exert the function of refining grain by coaddition with Zr and exerts an influence on corrosion resistance, moldability and etc. In this way, when considering the influence exerted on corrosion resistance, moldability, etc., in addition to the function of refining grain by coaddition with Zr, it is required that the amount of addition of P has a range of 0.01 to 0.25% by mass, preferably 0.02 to 0.2% by mass, more preferably 0.03 to 0.16% by mass and much more preferably 0.04 to 0.12% by mass. P has an important relation with Zr, but it is not favorable even when it is added in excess of 0.25% by mass, the refining effect is small and rather the ductility is damaged. In addition, the effect of refining grain by the coaddition of Zr and P is not exercised solely by individually determining the contents of Zr and P in the aforementioned range, but it is required to satisfy condition (2) in their mutual contents. The refinement of grain is obtained by causing a nucleation rate of the phase of the crystallized form of primary crystal from a melt which is melted to be even higher compared to the growth rate of a dendrite crystal. In order to generate this phenomenon, it is insufficient to individually determine the addition amounts of Zr and P, and it is necessary to consider a coadition ratio of (f1 = [P] / [Zr]). By determining the contents of Zr and P to have an appropriate addition rate in an appropriate range, it is possible to significantly facilitate the crystallization of the a phase of the primary crystal by means of the coaddition or interaction function of Zr and P. As a As a result, the nucleation of the corresponding phase ot exceeds the growth of the dendrite crystal. When the contents of Zr and P are within the appropriate range and their combined ratio [P] / [Zr]) is stoichiometric, the addition of Zr reaches several ppm which allows intermetallic compounds of Zr and P to be generated (eg ZrP , ZrP? - ?, etc.) in the crystal of the phase and the nucleation speed of the corresponding phase a increases as the value f1 of [P] / [Zr] reaches a range of 0.7 to 200, increases more when fl = 1.2 to 100, increases significantly when fl = 2.3 to 50 and increases markedly when fl = 3.5 to 30. In other words, the coadition ratio of Zr and P is a factor important for facilitating grain refinement and crystal nucleation during melt-solidification that greatly exceeds crystal growth when fl is within the range. Furthermore, in order to produce fine grains, the coaddition proportions of Zr and Si and of P and Si (f2 = [Si] / [Zr] and f3 = [Si] / [P]) are sufficiently important and it requires that they be considered. In addition, when solidification-fusion is carried out to increase a fraction of the solid phase, crystal growth begins to occur frequently. This begins to generate amalgamation of grain in part. In general, the grains of phase a gradually increase in size. Here, while the fusion solidifies, a peritectic reaction occurs. Then a solid-liquid reaction is generated between the melt that is in the molten state that remains without having solidified and the solid phase is generated, so a β phase is created when the solid phase is consumed. As a result, the phase is enclosed by the β phase and therefore the grain of the a phase itself begins not only to have a diminished size but also to acquire an elliptical inclined shape. In this way, when the solid phase acquires the fine elliptical shape, it is easy to escape in gases and shrinkage is generated uniformly with tolerance to fracture resulting from solidification shrinkage as it solidifies, which has a good influence on various properties such as tenacity, resistance to corrosion, etc., at room temperature. Of course, when the solid phases acquire the fine elliptical shape, the fluidity decreases and therefore it is optimal to use one. solidification of semi-solid metal. When the solid phase of the thin elliptical form and the molten melt melt in the final solidification stage, the solid phase and the molten melt are supplied sufficiently in each nook and corner even when a mold has a complicated form, so that a casting is formed in a good way. That is, the foundry conforms almost to the net form (NNS). Furthermore, whether or not it takes part in a peritectic reaction is generally generated in a composition wider than that of a state in equilibrium, unlike the state of equilibrium from the practical point of view. Here, a fO relationship plays an important role and an upper limit of fO has a major relationship with the size of a grain after fusion-solidification and a criterion capable of taking part in the peritectic reaction. A lower limit of fO has a major relationship with the size of a crystal after fusion-solidification and a limit value where a primary crystal is a phase a or not. Since fO is in the preferable interval mentioned above (fO = 62 to 69.5), the most preferable interval (fO = 62.5 to 68.5) and the much more preferable interval (fO = 64 to 67), the primary crystal, the phase a, increases in quantity and therefore the peritectic reaction generated in a reaction that is not in equilibrium is still activated more. Consequently, the grain that is obtained at room temperature becomes smaller. Of course, this series of melting-solidification phenomena depends on the rate of cooling. Specifically, in a rapid cooling where the cooling rate has an order of 105 ° C / sec or more, there is no time to perform nucleation of the crystal, so that there is a probability that the grain is not refined. In contrast, in a slow cooling where the cooling rate has an order of 10"3 ° C / sec or less, the grown grain or grain amalgamation is promoted, so that there is a possibility that the grain is not refined., the equilibrium state approach causes the range of composition that does not take part in the peritectic reaction to become narrow. More preferably, the cooling rate in the melt-solidification step has a range of 10"2 to 10 ° C / sec and more preferably a range of 10" 1 to 103 ° C / sec. Between this cooling rate range, the closer the upper limit of the broader cooling rate is reached, the longer the range of the composition where the grain becomes refined, so that the grains are further refined. The generated β phase and the peritectic reaction serve to suppress grain growth. However, when the ß phase remains in the metal structure at high temperature and when the phase K or the phase? are precipitated and generated by a reaction in solid phase, in this way the phases? they constitute a large fraction of the total structure, crystal growth is suppressed and the grain OI becomes finer. The conditional expressions for this are the following: f4 = [a] + [?] + [K] and f5 = [?] + [K] + 0.3 [μ] - [ß]. Since f5 is - in the preferable interval mentioned above (f5 = 10 to 70), the most preferable interval (f5 15 to 60) and the much more preferable interval (f5 = 20 to 45), the grain becomes finer . In condition (8), f6 and f7 are similar to fO, and in condition (9) f8 is similar to f5. In this way, satisfying conditions (8) and (9) leads to satisfying condition (1) for fO and condition (6) for f5. In addition, phase K and phase and formed in the Cu-Zn-Si-based alloy having the range of composition specified in the present invention are Si-rich hard phases. When cut, these phases K and y act as a source of stress concentration and generate thin cutting chips of a shearing type, so that splitting chips are obtained, and consequently at the same time a low resistance to cut.

Consequently, when the phases K and? they are uniformly distributed even without the presence of soft Pb or Bi particles as machinability susceptibility enhancing elements (ie, without containing the machinability susceptibility enhancing elements such as Pb, Bi, etc.), a susceptibility to machining that is industrially satisfactory. A condition for exerting an effect of improving the machinability susceptibility that does not depend on these Pb machining susceptibility enhancing elements, etc., is condition (1) and condition (6) for f5. However, today, there is a demand for a high speed cut. For this purpose, the hard phases K and? and the soft particles Pb and Bi are evenly distributed in a matrix. This coexistence exerts a sudden effect of synergy, particularly under the condition of high speed cutting. In order to exert this co-add effect, it is required to satisfy condition (8) and preferably to further satisfy condition (9). As noted above, in the first to eighth copper alloys by satisfying at least conditions (1) to (6), even the molten solidified substance can facilitate the same grain refinement as a hot worked material or a recrystallized material and by satisfying the condition (10) it is possible to facilitate the elaboration of an even finer grain. In addition, in the fifth to eighth copper alloys, by satisfying condition (8) (preferably condition (9) in addition to condition (8)), it is possible to facilitate grain refinement together with an improvement in the machinability susceptibility by addition in traces of Pb, etc. Also, when phases K and? they have a higher concentration of Si compared to the phase and when the three phases do not constitute 100%, the rest generally includes at least one of the phases β, μ and d. - In quino to eighth copper alloys, as is well known, Pb, Bi, Se and Te improve the machinability susceptibility and simultaneously exert excellent wear resistance by improving the formability and susceptibility to sliding to the other member in a member of abrasion coupling such as a bearing or the like. For the purpose of exercising this function, addition of Pb mass, etc. is required, but when condition (8) fulfills the addition in traces of Pb, etc., it is carried out without the addition of Pb mass, etc. , so that it is possible to ensure the machinability susceptibility that can be industrially satisfactory along with grain refinement. In order to further facilitate the improvement of the machinability susceptibility in the trace addition of Pb, etc., it is preferable to fulfill conditions (9) and (16) in addition to condition (8). By satisfying these conditions, the grains become finer and by distributing the Pb particles, etc., in the matrix into a finer uniform size, it is possible to improve the machinability susceptibility without the addition of Pb mass, etc. These effects are exerted in a remarkable way under the condition, particularly, of a high speed cut together with the existence of hard phases K and? and soft non-solid melting Pb and Bi, which are formed within the present effective composition range for machinability susceptibility. In general, Pb, Bi, Si and Te undergo individual addition or common addition by any combination of Pb and Te; Bi and Se or Bi and Te. In this regard, under the condition of satisfying condition (8), etc., it is required that the amount of addition of Pb be in a range of 0.005 to 0.45% by mass, preferably 0.005 to 0.2% by mass and much more preferably from 0.005 to 0.1% by mass. In addition, the amount of addition of Bi that is required has a range of 0.005 to 0.45% by mass, preferably 0.005 to 0.2% by mass and more preferably 0.005 to 0.1% by mass. In addition, the amount of Se addition that is required has a range of 0.03 to 0.45% by mass, preferably from 0.05 to 0.2% by mass and more preferably from 0.005 to 0.1% by mass. In addition, the amount of Te addition that is required has a range of 0.01 to 0.45% by mass, preferably from 0.03 to 0.2% by mass and more preferably from 0.05 to 0.1% by mass. Pb and Bi do not enter the fusion of the solid at room temperature, it exists since the Pb particle or the Bi particle are also distributed in a granular form in a molten state in the melt-solidification stage and exist between solid phases. The more particles there are of Pb and Bi, the easier it is to generate a fracture in the melting-solidification stage (by generating tensile stress depending on the shrinkage by solidification). In addition, Pb and Bi exist mainly at the grain boundary in the molten state after solidification, so that when their particles increase, it is easy to generate a solidification crack. In order to solve this problem, it is very efficient to refine the grain to release tension (i.e., increase an area of grain boundary) and cause the Pb and Bi particles to decrease in size and distribute evenly. In addition, Pb and Bi have an adverse influence on the properties of copper alloy except the susceptibility to machining, as stated in the above. With respect to the ductility at room temperature, the stress is concentrated on the particles of Pb and Bi so that the ductility is damaged (it is unnecessary to mention that when the grain is large, the ductility is geometrically damaged). Attention should be paid to this problem which can be corrected by grain refinement. In the second, fourth, sixth and eighth copper alloys, Sn, As and Sb are added to improve mainly the erosion resistance of cavitation, the resistance to corrosion (in particular the resistance to corrosion by elimination of zinc). This function is exercised by adding 0.05% by mass or more of Sn and 0.02% by mass or more of Sb and As. However, although Sn, As and Sb are added in excess of a certain amount, it is impossible to obtain an adequate effect by the additional amount and rather impairs the ductility. Sn has only a small influence on the refining effect but can exert the refinement function of the grain under the existence of Zr and P. Sn is to improve the mechanical properties (tenacity, etc.), corrosion resistance and wear resistance . In addition, Sn serves to more efficiently perform the peritectic reaction by expanding the Cu and Zn composition range which divides the dendrite arm to generate the peritectic reaction and decreases the stacking failure energy of the alloy and thus leads to more effectively granulate and refine the grain. Sn is a metal with a low melting point, which forms a concentrated Sn phase or a concentrated part to prevent moldability even if added in a small amount. However, when Sn is added under the addition of Zr and P, it has the effect on the refinement of grain by Sn and simultaneously this refinement of grain causes the concentrated phases h and Sn to be distributed evenly despite the formation of the concentrated part in Sn and in this way provide excellent resistance to cavitation erosion without greatly damaging the moldability or ductility. In order to exert an effect of resistance to cavitation erosion, Sn requires the addition of an amount of 0.05% or more, preferably 0.1% or more and more preferably 0.25% or more. Meanwhile, when exceeding 1.5%, the amount of addition of Sn causes problems regarding moldability or ductility at room temperature regardless of how fine the grain has been made and preferably is 0.9% or less, more preferably 0.7% or less and more preferably 0.6% or less. The amount of addition of Sn is necessary to be established in a range of 0.05 to 1.5% by mass, preferably • from 0.1 to 0.9% by mass, more preferably from 0.2 to 0. 7% by mass and much more preferably 0.25 a 0. 6% in mass. In addition, the addition amounts of As and Sb are necessary to establish them in a range of 0.02 to 0.25% by mass and preferably from 0.03 to 0.15% by mass considering their toxicity that has an adverse influence on the human body. In the third, fourth, seventh and eighth copper alloys, Al, Mn and Mg are added mainly to facilitate the improvement of the tenacity, improvement of the melting fluidity, deoxidation, desulfurization effect, improvement of the erosion resistance of cavitation under a high speed flow and improvement of wear resistance. In addition, Al forms a thin, corrosion-resistant, hard film of Al-Sn over the melt surface to improve wear resistance. In addition, Mn has the effect of generating a thin film resistant to corrosion between itself and Sn. In addition, Mn is combined with Si in the alloy to form an intermetallic compound of Mn-Si (atomic ratio: 1: 1 or 2: 1) and has the effect of improving the wear resistance of the alloy. However, scraping material (eg a poorly used heating tube, etc.) is often used as part of the copper alloy feedstock and an S component (sulfur component) is often contained in this scraping material. When the S component is included in a molten metal, Zr, an element of the grain refinement forms a sulfide. In this way, there is a probability that the effective grain refinement function by Zr is lost. In addition, melt flow is deteriorated and it is therefore easy to generate casting defects such as blowholes, fractures, etc. Mg has the function of improving the melting fluidity in the foundry when scraping material containing this S component is used as the alloy raw material, in addition to the function of improving the corrosion resistance. In addition, Mg can remove the S component in the form of MgS, which is more innocuous, where MgS is not harmful to the corrosion resistance even if it remains behind in the alloy and can effectively prevent the decrease in corrosion resistance caused by the S component contained in the raw material. In addition, when the S component is contained in the raw material, there is a likelihood that because S is easy to exist at the grain boundary, intergranular corrosion is generated. However, intergranular corrosion can be effectively prevented by the addition of Mg. In addition, Al and Mn also act to eliminate the S component included in the molten metal although it is less than Mg. In addition, when there is a large amount of oxygen in the molten metal, there is a probability that Zr forms an oxide and therefore the refinement function of the grain is lost. However, Mg, Al and Mn have an effect in preventing the formation of Zr oxide. In consideration of this, the content of Al, Mn and Mg is established in the aforementioned range. In addition, there is a likelihood that the S concentration of the molten metal will increase and therefore the Zr will be consumed by S, but when Mg is contained in 0.001% by mass or more in the molten metal before loading Zr, the S component of the molten metal is separated or fixed in the form of MgS, and therefore this problem does not arise. However, when Mg is added in excess of 0.2% by mass, Mg is subjected to oxidation similar to Zr and the molten metal increases its viscosity, and there is a likelihood of generating casting defects, for example, by inclusion of the oxide. Considering this and the improvement in toughness, resistance to cavitation erosion and wear resistance in general, the amount of Al addition is necessary to be established in a range of 0.02 to 1.5% by mass, and preferably 0.1 to 1.2% by mass. In addition, considering the effects of improvement of wear resistance by Si formation and an intermetallic compound of MnSi (in an atomic ratio of 1: 1 or 1: 2) in the alloy as a whole, the amount of addition of Mn is necessary to be established in a range of 0.2 to 4% by mass and preferably is 0.5 to 3.5% by mass. It is necessary that Mg is added in a range of 0.001 to 0.2% by mass. In the first to eighth copper alloys, by adding Zr and P, the refinement of the grain is carried out. By satisfying condition (7), that is, by establishing the average grain diameter in a macrostructure during the melt-solidification at 200 μm or less (preferably 150 μm or less, more preferably 100 μm or less and much less). more preferably 50 μm or less in a microstructure) a high casting quality can be obtained and the supply and practical use of casting by continuous casting such as horizontal continuous casting, ascending casting (top casting), etc. are possible. When the grain is not refined, a heat treatment is required several times with the purpose of eliminating the dendrite structure characteristics of the foundry or facilitating the division, subdivision of the K phase and the phase y and its surface condition becomes bad because the grain gets thicker. In contrast, when the grain is refined as stated in the above, it is not necessary to perform this heat treatment because the segregation is simply microstructural and the surface condition becomes good. In addition, the K phase and the y phase are present mainly at the phase boundary with the phase oi. In this way, the more grains are distributed in a tiny and uniform way, the smaller the lengths of the phases. For this reason, a peculiar processing procedure to divide the K phase and the phase? they are not required or can be minimized even if required. In this way, it is possible to significantly reduce the number of process required for production and therefore decrease production costs as much as possible. Furthermore, by satisfying the condition (7) the following problems do not occur and excellent properties of the copper alloy are exerted. In other words, when the K phase and the phase? A difference in toughness from the phase to the matrix is not evenly distributed, it easily generates a fracture and damages the ductility at room temperature. In addition, since there are Pb or Bi particles at the boundary with phase a or at the grain boundary, a large-sized phase easily generates a solidification fracture and damages ductility at room temperature. In addition, when the phases K and y of the particles Pb and Bi satisfy the condition (13) (and additionally condition (16) of the fifth to eighth copper alloys) are evenly distributed in the matrix in a uniform size and in a form fine, it is natural to improve cold handling. As such, smelters from the first to eighth copper alloys can be used appropriately for application requiring caulking (for example, in the case of a hose nipple, caulking is often carried out when installed). In addition, in the foundries of the first to eighth copper alloys, there are many cases of use of scraping material in the raw material. In the case of use of this scraping material inevitably impurities exist which is tolerated from the practical point of view. However, in the case where the scraping material is a nickel coating material or the like, when Fe or Ni exists as unavoidable impurities, it is necessary to limit its content. That is, this is due, when the content of their impurities are high, to which Zr P useful for the refinement of the grain are depleted by Fe or Ni. For example, this is because, although Zr and P are added excessively, there is the problem of preventing the refining action of the grain. Consequently, when there is a content of either Fe and Ni, its content is preferably limited to 0.3 mass% or less (preferably 0.2% by mass or less, more preferably 0.1% by mass or less and much more preferably 0.05% by mass or less). In addition, when Fe and Ni are contained together, their total content is preferably limited to 0.35% by mass or less (preferably 0.25% by mass or less, more preferably 0.15% by mass or mnos and much more preferably 0.07% by mass or less).

In the exemplary embodiment, the first to eighth copper alloys are provided, for example, as a foundry obtained in the casting process or a plastic worked material which additionally performs plastics work on the casting once again. The foundry is provided as a wire, a rod or a hollow bar which is melted by continuous horizontal casting, ascending casting or upper casting, as well as casting in an almost pure form. In addition, the casting is provided as a foundry, a semi-solid metal foundry, a semi-solid metal formed material, a forged cast material or a die-cast shaped material. In this case, it is preferable to satisfy conditions (14) and (15). When the solid phase in a semi-molten state is granulated, it is natural that the moldability of the semi-solid metal becomes excellent and therefore it is possible to carry out the melting of the semi-solid metal. In addition, the melt fluidity includes the solid phase in the final solidification stage is dependent mainly on the solid phase form in the semi-molten state and the viscosity or composition of the liquid phase. However, with respect to a good or bad conformability (high precision) or a complicated form required in the casting, the first (the shape of the solid phase) has a greater influence with respect to a suitable casting that can be melted or not. In other words, when the solid phase in the semi-molten state begins to form a network of dendrites, the melt that includes the solid phase is difficult to disperse at all corners. In this respect, the formability by the casting deteriorates and therefore it is difficult to obtain the casting having a high precision or a complicated shape. Meanwhile, the solid phase in the semi-molten state of granulate and as the solid phase becomes more spheroidal (the circular shape in a two-dimensional shape) and the smaller the grain diameter, the moldability that includes the moldability of the semi-solid metal becomes excellent and it is possible to obtain a suitable casting having a high precision or a complicated shape (of course, to obtain the semi-cast iron that has the high precision). Therefore, by knowing the shape of the solid phase in the semi-molten state, it is possible to evaluate the moldability of the semi-solid metal. By means of a good or bad moldability of the semi-solid metal it is possible to verify the good or bad of another moldability (moldability of complicated form, precision moldability and melting forge capacity). In general, the half-solid state having a solid phase fraction of 30 to 80%, the dendrite network has at least one split crystal structure.

Also, when the two-dimensional form of the solid phase has a non-form. circular near the circular shape, an elliptical shape, a cross shape or a polygonal shape, the moldability of semi-solid metal is good. In addition, in particular, in the semi-molten state having a 60% solid phase fraction when the corresponding solid phase descends to at least one having an average grain diameter of 150 μm or less (preferably 100 μm or less, most preferably 50 μm or less and more preferably 40 μm or less) and one having a maximum average length of 300 μm or less (preferably 150 μm or less, more preferably 100 μm or less and much more preferable 80 μm or less) (particularly in the elliptical form, when the average ratio of a major side to the minor side is 3: 1 or less (preferably 2: 1 or less), the moldability of semi-solid metal is excellent. In addition, the plastic worked material is provided, for example, as a hot extruded material, a hot forged material or a hot rolled material. In addition, the plastic worked material is provided as the wire, the rod or the hollow bar formed by drawing the casting. In addition, when the plastic worked material is provided as a plastic worked material that is obtained by cutting, ie, a cut material, it is preferable that it satisfies the condition (17), specifically it is preferable that, when the cutting is performed in an atmosphere dries by a lathe using a depth with an angle of attack of -6o and a tip radius of 0.4 mm under the conditions: cutting speed from 80 to 160 m / min, a depth of cut of 1.5 mm and a feed speed of 0.11 mm / rev, the cut chips have a small trapezoidal or triangular segment shape, and an acicular shaped tape having a length of 25 mm or less is generated. This is because the processing (collection or reuse) of the cut splinters adhere to the depth, damaging the cutting surface or the like. The first to eighth copper alloys are provided as a contact coupling in water that is used in contact with water at all times or temporarily. For example, the coupling in contact with water is provided as a connecting sleeve, a hose coupling sleeve, an adapter sleeve, an elbow, a very short cylinder, a tap tap, a threaded reducer, a joint, a gasket , a collar, a check valve, a suction valve, a slit valve, a gate valve, a check valve, a ball valve, a diaphragm valve, a constriction valve, a ball valve, a valve needle, a miniature valve, a release valve, a main tap, a hand tap, an acorn tap, a two-way tap, a three-way tap, a four-way tap, a gas tap, a valve ball valve, a safety valve, a release valve, a pressure reducing valve, an electromagnetic valve, a steam trap, a water meter, a flow meter, a hydrant, a water sprayer, a stop spigot from water, an oscillating faucet, a mixed spigot, a corporation spout, a spout, a branched spigot, a check valve, a forked valve, a hinge valve, a three-way tap, a shower, a shower hook, a male tap, a zarubo, a. irrigation nozzle, a sprinkler, a tube. of heating for a water heater, a heating tube for a heat exchanger, a heating tube for a heater, a trap, a fire hydrant valve, a water supply orifice, an impeller, a drive shaft or a pump casing or its constituent members. In addition, the first to eighth copper alloys are provided as a frictional coupling member that performs relative movement in contact with the other member at all times or temporarily. For example, the frictional coupling member is provided as a gear, a sliding bushing, a cylinder, a piston shoe, a bearing, a bearing part, a bearing member, an axle, a rotating joint part, a bolt , a nut or the body of a screw or its constituent parts. Further, it is provided as a pressure sensor, a temperature sensor, a connector, a compressor part, a carburetor part, a cable coupling, a part of a mobile telephone antenna or a terminal. In addition, the present invention proposes a casting method of a copper alloy foundry having excellent machinability, toughness, corrosion resistance and wear resistance, characterized in that, in the case of producing the first to eighth alloys of copper, Zr is added (content for the purpose of an even greater refinement of a grain and stable refinement of the gain) in the form of a copper alloy material that contains the same just before casting or in a final stage of melting. raw material in a process of melting raw material in a casting process, thereby preventing Zr from being added to a form of an oxide or sulfide in the foundry. Regarding the copper alloy material containing Zr, Cu-Zn alloy, Cu-Zn-Zr alloy and additional alloys containing at least one that is selected from P, Mg, Al, Sn, Mn and B are preferable In other words, in the process of casting the first to eighth copper alloys or components thereof (materials to be shaped), the loss of Zr, generated while adding Zr, is reduced as much as possible when adding Zr as an intermediate alloy material (copper alloy material) in the form of a granular material, sheet-like material, rod-like material or wire-like material just prior to casting. Afterwards, Zr is not added in the form of oxide or sulfur when casting is carried out, so that the amount of Zr necessary and sufficient to refine the grains can be obtained. In addition, in the case of adding Zr just before casting in this way, since the melting point of Zr is 800 to 1000 ° C higher than that of the corresponding copper alloy, it is preferable to use a material with an alloy low melting material that is an intermediate alloy material that conforms similar to granules (grain diameter of approximately 2 to 50 mm), thin sheet (thickness of approximately 1 to 10 mm), rod (diameter of approximately 2 to 50 mm) or wire and having the melting point close to that of the corresponding copper alloy and many of the necessary components (for example Cu-Zn alloy or Cu-Zn-Zr alloy containing 0.5 to 65% by mass of Zr or the alloys which also contain at least one element (containing 0.1 to 5% by mass each) which are selected from P, Mg, Al, Sn, Mn and B). In particular, in order to lower the melting point to facilitate melting and simultaneously avoid any oxidation loss of Zr, it is preferable that it be used in the form of an alloy material based on the Cu-Zn-Zr alloy which it contains 0.5 to 0.35% by mass of Zr and 15 to 50% by mass of Zn (more preferably 1 to 15% by mass of Zr and 25 to 45% by mass of Zn). While they are dependent on a combined proportion of themselves and coaggregate P, Zr is an element that prevents electrical thermal conductivity as an intrinsic property of copper alloy. However, when the amount of Zr that does not take the form of oxide or sulfide is less than 0.04% by mass and particularly 0.019% by mass, almost no reduction in electrical thermal conductivity is caused by the addition of Zr. For example, even when thermal conductivity is reduced, the reduced rate will do so if it is a very low rate compared to the case of not adding Zr. In addition, in order to obtain the first to eighth copper alloys in satisfying condition (7), it is preferable to properly determine the melting conditions, particularly a melting temperature and a cooling rate. Specifically, in terms of melting temperature, it is preferable to determine that it is greater than a liquid temperature of the corresponding copper alloy at 20 to 250 ° C (more preferably 25 to 150 ° C). In other words, the melting temperature is preferably determined in the following range: liquid temperature + 20 ° C) < . Casting temperature < . (liquid temperature + 250 ° C), and more preferably (liquid temperature + 25 ° C) < Casting temperature < . (liquid temperature + 150 ° C). In general, although it depends on the components of the alloy, the melting temperature is less than 1150 ° C, preferably 1100 ° C and more preferably 1050 ° C. The lower side of the casting temperature is not particularly limited insofar as a molten metal is filled at all corners of a mold. However, since the casting is performed at a lower temperature, a tendency is shown that the grain is refined. It should be understood that these temperature conditions are varied according to the amount of each constituent element of an alloy.

BRIEF DESCRIPTION OF THE DRAWINGS Figures IA and IB are photographs of a recorded surface (cut surface) of a copper alloy number 79 of one embodiment, wherein Figure 1A illustrates a macrostructure and Figure IB illustrates a microstructure; Figures 2A and 2B are photographs of a recorded surface (cut surface) of a copper alloy number 228 of a comparative example, wherein Figure 2A illustrates a macrostructure and Figure 2B illustrates a microstructure; Figure 3 is a photomicrograph of a semi-solidified solid state in a semi-solid metal moldability test of a copper alloy number 4 of one embodiment; Figure 4 is a photomicrograph of a semi-solidified solid state in a semi-solid metal moldability test of a copper alloy number 202 of a comparative example; Figures 5A-5G are perspective views showing a shape of a cut splinter generated in a cutting test; Figure 6 is a perspective view showing a foundry C, D, Cl or DI (body of a running water meter); Figure 7 is a sectional plan view showing the bottom of the casting C, D, Cl or DI (body of the running water meter) shown in Figure 6; Figure 8 is an enlarged plan view of a major interior portion (a shrinkage portion corresponding to a portion M of Figure 7) of a foundry C, a copper alloy number 72 of one embodiment; Figure 9 is a cross-sectional view (corresponding to a cross-sectional view taken along the line N-N of Figure 7) of an important portion of a foundry C, a copper alloy number 72 of one modality; Figure 10 is an enlarged plan view of an important interior portion (a shrinkage portion corresponding to a portion M of the figure 7) of a foundry C, a copper alloy number 73 of one embodiment; Figure 11 is a cross-sectional view (corresponding to a cross-sectional view taken along the line N-N of Figure 7) of an important portion of a foundry C, a copper alloy number 73 of one modality; Figure 12 is an enlarged plan view of an important interior portion (a shrink portion corresponding to a portion M of the figure 7) of a foundry Cl, a copper alloy number 224 of a comparative example; and Figure 13 is a cross-sectional view (corresponding to a cross-sectional view taken along the line NN of Figure 7) of an important portion of a foundry Cl, a copper alloy number 224 of a .

DESCRIPTION OF THE MODALITIES As a modality, the copper alloys numbers 1 to 92 of the compositions shown in Tables 1 to 8 are obtained as foundries A, B, C, D, E and F and a material G worked plastic . Furthermore, as a comparative example, the copper alloys numbers 201 to 236 of the compositions shown in tables 9 to 12 are obtained, such as Al, Bl, Cl, DI, El, Fl and Gl castings and a plastic worked material. G2 Smelters A (copper alloys numbers 1 to 46) and Al smelters (copper alloys numbers 201 to 214) are rods having a diameter of 40 mm, which are melted continuously at low speed (0.3 m / min) using a casting apparatus in which the horizontal continuous casting machine is attached to a melting furnace (60 kg melting capacity). In addition, smelters B (copper alloy numbers 47 to 52) and smelters Bl (copper alloy numbers 217 and 218) are rods having a diameter of 8 mm which were melted continuously at low speed (1 m / min) using the casting apparatus where the continuous horizontal casting machine is attached to the melting furnace (60 kg melting capacity). In any case, casting is performed continuously using a graphite mold while adjusting and adding an additional element so that it becomes a predetermined component, if necessary. In addition, in the casting process of smelters A, B, Al and Bl, when casting is performed, Zr is added in a form of a Cu-Zn-Zr alloy (containing Zr of 3% by mass) and simultaneously a melting temperature is established to be greater than the liquid temperature of a material constituting the corresponding foundry at 100 ° C. In addition, Al smelters (copper alloy numbers 215 and 216) are horizontal continuous rods having a diameter of 40 mm, which are placed on the market (where number 215 corresponds to CAC406C). Any of the foundries C (copper alloys numbers 53 to 73), the smelters D (copper alloys numbers 74 to 78), the smelters Cl (copper alloys numbers 219 to 224) and the smelters DI (copper alloys number 225) and 226) are obtained by casting at low pressure (molten metal temperature of 1005 ° C + 5 ° C, pressure of 390 mbar, pressurization time of 4.5 seconds and retention time of 8 seconds) of the actual operation and is a casting product having the body of a paired running water meter, as shown in figure 6. In addition, castings C and Cl are melted using a metal mold, while foundries D and DI are melted using a mold of sand. The smelters E (copper alloys numbers 79 to 90) and the smelters (copper alloys numbers 228 to 233) are ingots of a cylindrical shape (diameter of 40 mm and length of 280 mm), each of which is obtained from melting a raw material in an electric furnace and then melting the molten metal in a pre-heated metal mold at a temperature of 200 ° C. The foundry F (number 91) and the cast iron Fl (number 234) are large size castings (ingots having a thickness of 190 mm, a width of 900 mm and a length of 3500 mm) obtained by casting at low pressure of real operation. The material G worked with plastic (copper alloy number 92) is a rod having a diameter of 100 mm which is obtained by hot extrusion of an ingot (billet having a diameter of 240 mm). Any of the Gl worked plastic materials (copper alloys numbers 235 and 236) is a stretched and extruded rod (which has a diameter of 40 mm) which is placed on the market. In addition, number 235 corresponds to JIS C3604 and number 236 corresponds to JIS C3711. In addition, in the following description, the foundries A, B, C, D, E and F and the material G worked plastic are referred to as the "material of the mode" while the castings Al, Bl, Cl, DI, El, Fl and Gl as well as the plastic worked material G2 are referred to as the "material of the comparative example". In addition, the test specimens number 10 in JIS Z2201 sample from the materials of the modalities A, B, C, D, E, F and G and the materials of the comparative example Al, Bl, Cl, DI, El, Fl, Gl and G2. In terms of the test specimens, a stress test is performed by the Amsler universal test machine and the tensile strength (N / mm2), the 0.2% elastic limit, are measured.

(N / mm2), the elongation (%) and the fatigue resistance (N / mm2). The results are as shown in Tables 13 to 18 and it is identified that the modal materials are excellent in mechanical properties such as tensile strength, etc. In addition, in terms of the C, D, Cl and DI smelters, the test specimens are shown for a slider portion K shown in Figure 6. In addition, in order to compare and identify the machining susceptibility of the Mode materials and materials of the comparative example, the following cutting tests are performed to measure a main force cutting component N. Specifically, the outer circumferential surfaces of the sampled specimens of the materials of mode A, B, E and G and the materials of Comparative Example Al, Bl, El and Gl are cut dry by a lathe equipped with a straight sharp pointed tool (having an angle of attack of -6 ° and a tip radius of 0.4 mm) under the conditions: a cutting speed of 80 m / min, a depth of cut of 1.5 mm and a feeding speed of 0.11 mm / rev, and under the conditions: a cutting speed of 160 m / min, a depth of cut of 1.5 mm and a feed rate of 0.11 mm / rev, measured by a three-component force dynamometer attached to the depth, and calculated in terms of the main force cutting component. The results are as shown in tables 13 to 18. In addition, the states of the cutting chips generated by the cutting test are observed. Splinters are classified into seven, according to their forms: (a) small trapezoidal or triangular segment shape (figure 5 (A)), (b) form of tape that has a length of 25 mm or less (figure 5 (B)) ), (c) acicular shape (figure 5 (C)), (d) form of ribbon that has a length of 75 mm or less (excluding (b)) (figure 5 (D)), (e) spiral shape that it has three turns (turns) or less (figure 5 (E)), (f) a ribbon shape that exceeds a length of 75 mm (figure 5 (F)) and (g) a spiral shape that exceeds three turns (figure 5) (G)) and subjected to evaluation of machinability susceptibility. The results are shown in tables 13 to 18. In these tables, the cutting splinter whose shape belongs to (a) is represented by the symbol ("®", (b) by the symbol "O", (c) by the symbol "•", (d) by the symbol "D", (e) by the symbol "?", (f) by the symbol "x" and (g) by the symbol "xx". cut they take the forms (f) and (g), the handling (harvesting or reuse) of the cut chips becomes difficult as well as a good cut can not be carried out due to the problems that said cutting chips adhere to the depth damaging the cutting surface or Similary. When the cutting chips acquire the forms (d) and (e), the big problems are not generated as in (f) and (g), but the handling of the cut splinters is not easy either, and when the cut is made Continuously, the generated chips can adhere to the depth or damage the cutting surface or similar. In contrast, when cutting chips acquire the forms (a) a (c), the aforementioned problems are not generated and the handling of cutting chips is easy insofar as the volume is not increased as in (f) and (g) (that is, because it does not increase) the volume) . However, with respect to (e), the cutting chips often slip to a sliding surface of the machine tool such as the lathe to generate a mechanical obstacle according to the cutting conditions or accompanying hazards, for example to be embedded in the fingers or the eyes of an operator. In this way, regarding the evaluation of the machinability susceptibility, (a) is the best, (b) is the second best, (c) is good, (d) is slightly good, (e) is only acceptable, ( f) is inadequate and (g) is the most inappropriate. It is identified from the main force cutting component and the shape of the cutting splinter that the materials of the modality are excellent. In addition, the following wear test is performed in order to compare and identify the wear resistance of the materials of the embodiment with the materials of the comparative example. First, annular test specimens having an outer diameter of 32 mm and a thickness of 10 mm (length of an axis direction) of the materials of mode A and E and the materials of comparative example Al, El and Gl when making the cut and perforation on these materials. Sequentially, in the state where each test specimen is coupled on a rotational axis and simultaneously a SUS304 roller (having an outer diameter of 48 mm) is brought into rotational contact with the outer circumferential surface of the annular test specimen under a load of 50 kg, the rotational shaft is rotated at 209 rpm while allowing multiple oil to drip onto the outer circumferential surface of the test specimen. And, when the number of rotations constitutes 100,000 times, the rotation of the test specimen is stopped. The weight difference between before and after rotation is measured, specifically a loss by wear (mg). As the wear loss becomes small, the copper alloy is excellent in its wear resistance. The results are shown in Tables 19, 20, 22, 23 and 24. It is identified that the modal materials are excellent in their resistance to wear and susceptibility to sliding. In addition, the following erosion corrosion tests I to III, zinc elimination corrosion test specified in "ISO 6509" and strain corrosion fracture test specified in "JIS H3250" are performed in order to compare and identify the corrosion resistance of the materials of the modality and the materials of the comparative example. That is, in the erosion corrosion tests I to III, an erosion corrosion test is carried out when hitting sampled cast specimens of the materials of the modalities A, C, D and E and the materials of the comparative example Al, El and Gl with a test melt (30 ° C) at a flow rate of 11 m / sec in a direction perpendicular to the axes of the specimens from the nozzle having a diameter of 1.9 mm. The mass loss (mg / cm2) is then measured after a predetermined time T has elapsed. As the test melt, 3% saline fused is used for test I, a mixed saline fused mixture of CuCl2.H20 (0.13 g / 1) with the 3% saline fused, which is used for the test II, and a mixed melt to add a very small amount of hydrochloric acid (HCl) to sodium hypochlorite (NaClO), is used for test III. Mass loss is the amount per cm2 (mg / cm2) that extracts a specimen weight after impact in the melting test for a time T from the weight of the specimen before starting the test, and the impact time is set to T = 96 in any of the tests I to III. The results of the erosion corrosion tests I to III are as shown in Tables 19 to 24. In addition to the zinc removal corrosion tests of "ISO 6509", the sampled specimens of foundries of the materials of the modalities A, C, D and E and the materials of the comparative example Al, El and Gl are joined to phenolic resins in the state where the exposed specimen surfaces are perpendicular to one direction of extension, and then the specimen surfaces are polished by an emery paper of up to 1200. The polished specimens are dried after ultrasonic cleaning in pure water. The corrosion test specimens are thus immersed in a copper (II) chloride dihydrate (CuCl2.2H20) 1.0% water melt, maintained for 24 hours under a 75 ° C temperature condition and removed from the melted water. Then the maximum corrosion depth value of zinc removal is measured, specifically the maximum corrosion depth of zinc removal (μm). The results are as shown in tables 19 to 24. In addition, in the stress corrosion fracture test of "JIS H3250", plate-like specimens (width of 10 mm, length of 60 mm and thickness of 5 mm) sampled from foundries B and Bl are bent into shape in V of 45 ° (radius of the curved portion of 5 mm) (in order to apply residual tension by traction) and undergo degreasing and drying. In this state, the specimens are kept in an ammonia atmosphere (25 °) in a desiccator in which water contains 12.5% ammonia (ammonia is diluted with the same amount of pure water). And at a point of time, when a predetermined retention time (exposure time) has elapsed, the specimens are removed from the desiccator and cleaned with 10% sulfuric acid. In this state, they are observed with a microscope (10 increases) where any fracture in the corresponding specimen is observed or not, so the specimens are evaluated. The results are as shown in Tables 21 and 23. In the corresponding table, the specimen whose fracture is shown after 8 hours of retention time has elapsed in the ammonia atmosphere, but clearly shows when 24 hours have elapsed, represented by the symbol "?" and the specimen whose fracture is never shown after 24 hours has passed is represented by the "O" symbol. It was identified from these results of the corrosion resistance test that the modal materials are excellent in corrosion resistance. In addition, the following cold compression test was carried out in order to compare and evaluate the cold handling of the materials of the modality and the materials of the comparative example. That is, from smelters A, B and Al, cylindrical specimens having a diameter of 5 mm and a length of 7.5 mm are sawn and sampled by means of a lathe and subjected to compression with a universal test machine. Amsler and the evaluation of cold compressibility manageability is performed due to the existence or nonexistence of a fracture, according to the relation with compressibility (work rate). The results are shown in Tables 19, 20, 21 and 23. In these tables, the specimen that generates the fracture at a compressibility of 30% is considered to be bad in its handling of cold compression, and is therefore represented by the symbol "x", the specimen where the fracture is not generated at a compressibility of 40% is considered to be excellent in its handling of cold compression and therefore it is represented by the symbol "O" and the specimen where the fracture is not generated at the compressibility of 30% but is generated at the compressibility of 40%, it is considered to be good at the handling of cold compression, and therefore it is represented by the symbol "?". The good or bad of the cold compressibility can be evaluated by the good or bad of the caulking maneuverability. When the evaluation is given the symbol "O", it is possible to perform caulking with ease and high precision. When is the symbol "?" common caulking is possible. When the "x" symbol is provided, it is impossible to perform an adequate caulking. It has been identified that, among the materials of the modality, some are represented by the symbol "?", The largest. part of which is represented mainly by the symbol "O" and therefore the materials of the modality are excellent in cold compressibility manageability, that is, caulking manageability. In addition, the following high temperature compression test was carried out in order to compare and evaluate the hot forging capacity of the materials of the modality and compare it with the modalities of the comparative example. From smelters A, E and El and plastic worked material Gl, cylindrical specimens having a diameter of 15 mm and a height of 25 mm are sampled using a lathe. These specimens are kept for 30 minutes at 700 ° C and then subjected to hot compression after changing the rate of work and evaluation of hot forging susceptibility based on the relationship between the work rate and the fracture. The results are as shown in tables 20, 22 and 24. It is identified that the materials of the modality are excellent in their susceptibility to hot forging. In these tables, the specimen where a fracture is not generated at an 80% work rate is considered excellent in its hot forging capacity and is therefore represented by the symbol "O", the specimen where it is generated slightly a fracture in the 80% work rate but it is not generated at a rate of. 65% work is considered to be good in its hot forging capacity and therefore it is represented by the symbol "?", and the specimen where a fracture is generated in a remarkable way at a 65% work rate it is considered to be bad in its forging capacity and therefore it is represented by the symbol "x". In addition, in order to compare and identify the cold stretchability with respect to the materials of the embodiment and the materials of the comparative example, cold stretchability is evaluated based on the following. Castings similar to bars B and Bl (diameter of 8 mm) are subjected to cold drawing. It evaluates one capable of being cold stretched without generating a fracture up to a diameter of 6.4 mm by a single stretch (36% work rate) and it is evaluated as excellent in its cold stretching, one capable of being stretched cold without generate a fracture up to a diameter of 7.0 mm for a single stretch (rate of work of 23.4%) is evaluated that is normal in its cold stretchability, and one that is able to be cold drawn with generation of a fracture when the cold drawing is performed once to a diameter of 7.0 mm, it is evaluated that it is bad in its cold stretching. The results are as shown in Tables 21 and 23. One that is evaluated as excellent in its cold stretchability is represented by the "O" symbol, one that is evaluated. which is normal in its cold stretchability is represented by the symbol "?" and one that is evaluated as bad in its cold stretchability is represented by the symbol "x". As it is understood from tables 21 and 23 it is identified that the modal materials are excellent in their cold stretchability as compared to the materials of the comparative example. In addition, its moldability is evaluated with respect to the modal materials and the materials of the comparative example. First, in terms of smelters B and Bl, the superiority or inferiority of moldability is evaluated when performing the following moldability valuation test. That is, in the moldability evaluation test, when casting B is obtained in the mode while the casting speed is varied in two stages, high and low, 2 m / min and 1 m / min (or when the casting Bl is obtained in the comparative example), the superiority or inferiority of the moldability is evaluated as high or low in the casting rate at which a defect-free wire is obtained by continuously melting a wire (rod) having a diameter of 8 mm under the same condition and apparatus compared to those used to obtain casting B in the mode (or to obtain cast iron Bl in the comparative example.) The results are shown in tables 21 to 23. Once obtains a wire free of defects with the high casting speed of 2 m / min is considered to be excellent in its moldability and therefore it is represented with the symbol "O." A material where the defect-free wire is not obtained au At high casting speed but it is obtained at a low casting speed of 1 m / min, it is considered normal in its moldability and therefore it is represented by the symbol "?". Bl casting wire free of defects even at a low casting speed (1 m / min) is considered to be of poor moldability and therefore is represented by the symbol "x", in Second, the bottom L (see FIG. 6) of the casting C or Cl is cut and the shrinkage portion M (see FIG. 7) is observed within the cutout portion. The moldability is evaluated by existence or non-existence of defects in a depth of shrinkage. The results are as shown in Tables 21 to 23. In these tables, a sample where there are no defects present in the M portion of shrinkage and the shrinkage is shallow is considered to be excellent in its moldability, and so both are represented by the symbol "O". In addition, a material in which no clear defects are present in the M portion of. Shrinkage and shrinkage is not very deep, it is considered to be good in moldability, and therefore it is represented by the symbol "?". However, one in which there are clear defects in the portion M of shrinkage or shrinkage is deep, is considered to be bad in moldability and is therefore represented by the symbol "x". Examples of the shrinkage portion M are shown in FIGS. 8 to 13. That is, FIG. 8 is a cross-sectional view of the shrinkage portion M in copper alloy number 72 of the embodiment and FIG. 9 is an enlarged plan view of the corresponding shrinkage portion M. In addition, Figure 10 is a cross-sectional view of the shrinkage portion M in the copper alloy number 73 of the embodiment and Figure 11 is an enlarged plan view of the corresponding shrinkage portion M. Figure 12 is a cross-sectional view of the shrinkage portion M in copper alloy number 224 of the comparative example and Figure 13 is an enlarged plan view of the corresponding shrinkage portion M. As you can see from figures 8 to 13, the surfaces of the shrinkage portions M in copper alloys numbers 72 and 73 are very smooth and free from defects, while in copper alloy number 224 clear defects are present in the M. portion of shrinkage and depth The shrinkage is deep. Furthermore, since copper alloy number 224 has almost the same composition as copper alloys numbers 72 and 73, except that it does not contain Zr, it can be understood from figures 8 to 13 that the refining of grain by coadition is facilitated. of Zr and P and therefore the moldability is improved. Third, the following semi-solid metal moldability test is performed in order to compare and evaluate the modal materials and materials of the comparative example with respect to the moldability of semi-solid metal. That is, the raw materials used when castings A, Al and El are melted, loaded in a crucible, heated to a semi-molten state (solid phase fraction of approximately 60%), maintained for 5 minutes at that temperature and undergo cooling (cooling with water) and the moldability of the semi-solid metal is evaluated by investigating the shape of a solid phase in the semi-molten state. The results are as shown in Tables 19, 23 and 24. It is identified that the materials of the modality meet the conditions (14) and (15), and are excellent in moldability of semi-solid metal. In these tables, one where an average grain diameter of the corresponding solid phase is 150 μm or less, or an average of the maximum length of a grain is 300 μm or less is evaluated as excellent in the moldability of semi-solid metal , and therefore it is represented by the symbol "O". A material in which a grain of the corresponding solid phase does not satisfy these conditions, but a remarkable dendrite network is not formed, is evaluated as having a good one. oldeability of semi-solid metal sufficient to be industrially satisfactory and therefore represented by the symbol "?". A material in which a dendrite network has been formed is evaluated as being bad in moldability of semi-solid metal and is represented by the symbol "x". Examples where the modal materials satisfy conditions (14) and (15) are shown. That is, Figure 3 is a photomicrograph of a semi-solidified solid state in a semi-solid metal moldability test for copper alloy number 4 of the modal material, which clearly satisfies conditions (14) and (15). In addition, Figure 4 is a photomicrograph of a semi-solidified solid state in the semi-solid metal moldability test of copper alloy number 202, the comparative example material, which does not satisfy conditions (14) and (15). In addition, with respect to the materials of the A to G mode and the materials of the Comparative Example Al to Gl, the average grain diameters (μm) are measured when they melt and solidify. In other words, in the cut state the. Modeling materials and the materials of the comparative example and the engraving of the cutting surfaces with nitric acid, the average grain diameters (average grain diameter) are measured in macrostructures arising from the engraved surfaces. Further, with respect to the foundries C, D, Cl and DI in the cut state of an inlet flow outlet J (see Figure 6) of a running water meter body and its cutting surface is recorded with nitric acid , an average diameter of a grain on the engraved surface is measured in the same way as indicated in the above. This measurement is based on a comparison method of an average grain size test of a stretched copper product of JIS H0501. The cutting surface is etched with nitric acid. Then, a material whose grain diameter exceeds 0.5 mm is observed with the naked eye, one whose grain diameter is less than 0.5 mm is observed with a magnification of 7.5 times and one whose grain diameter is less than 0.1 mm is recorded with a molten mixture of hydrogen peroxide and water with ammonia and then observed with a 75-fold magnification by means of an optical microscope. The results are as shown in Tables 13 to 18. Any of the materials of the modality satisfies condition (7). Also, in terms of the materials of the example. Comparative, it is identified that all present a primary phase crystal when they melt and solidify. In addition, it is identified that the materials of the modality satisfy the conditions (12) and (13). Their examples are shown in Figures 1 and 2. Figure 1 is a macro-structure photograph of copper alloy number 79, the modal material (Figure IA) and a microstructure photograph (Figure IB). Figure 2 is a macro-structure photograph of copper alloy number 228, the comparative example material (Figure 2A) and a microstructure photograph (Figure 2B). As is clear in Figures 1 and 2, it should be understood that the comparative example material number 228 does not satisfy conditions (12) and (13), while the material of mode number 79 satisfies conditions (12) and (13) ). It is identified from the above that the materials of the modality improve notably in their susceptibility to machining, mechanical properties (tenacity, elongation, etc.), wear resistance, moldability, semisolid metal mouldability, cold compressibility handling, hot forging capacity and corrosion resistance to having each constituent element contained in the aforementioned range and upon compliance the conditions (1) to (7) (with respect to the fifth to eighth copper alloys, additionally, the condition (8)) compared to the materials of the comparative example which does not comply with at least part of these conditions . Furthermore, it is identified that the improvement of these properties can be effectively facilitated by meeting conditions (10) to (15) in addition to the above conditions (with respect to the fifth to eighth copper alloys, additionally conditions (9) to ( 16) It has been identified that the above fact is equally valid for the large size smelter F (number 91) and the effect of refining grain by the coadition of Zr and P and the resulting effect of the property improvement are guaranteed without In addition, with respect to the large smelter (number 234) which has almost the same composition as copper alloy number 91 except that it does not contain Zr, these effects are not present, and a difference of the smelters is clear In addition, with respect to foundries C, Cl and DI containing Pb, a lead leak test is performed based on "JIS S3200-7: 2004 Water Supply Equipment Performance Test for Leachability". or is, in this test it is used as a water leaching solution (quality: pH 7.0 + 0.1, hardness: 45 + 5 mg / l, alkalinity: 35 + 5 mg / l, residual chlorine: 0.3 + 0.1 mg / l) where the pH is adjusted, with sodium hydroxide melt, to the water adding. Sodium hypochlorite melt, a sodium acid carbonate melt and a calcium chloride melt in an appropriate amount, and the C, Cl and DI smelters are subjected to predetermined cleaning and conditioning and then a hollow portion of the corresponding smelters. , Cl and DI (specifically, a measuring body of running water in itself, see figure 6) is filled with the leachate solution at 23 ° C and sealed, and then the smelters are allowed to stand for 16 hours with the solution retained at 23 ° C and then the amount of exudation (mg / l) of Pb contained in the leachate solution is measured. The results are shown in tables 21, 23 and 24. It is identified that the amount of Pb exudate is extremely small and the materials of the mode and foundries may be used as couplings in contact with water such as a meter of running water, without any problem. In addition, a K portion of slide is sampled (see FIG. 6) of casting C of copper alloy number 54 and a copper alloy is melted using the sampled portion of the slide as raw material (Zr: 0.0063 mass%). That is, the corresponding slide portion K is remelted under a cover of activated carbon at 970 ° C. it is maintained for 5 minutes and under the anticipation that an amount of oxidation loss of Zr when melted can constitute up. 0.001% by mass, an alloy of Cu, Zn, Zr containing 3% by mass of Zr is added as well as the amount of oxidation loss of Zr which is melted in a metal mold. As a result, in the obtained foundry, a Zr content is almost equal (0.0061% by mass) to that of the raw material, the copper alloy number 54 and an average grain diameter, which is measured, - is of 25 μm, which is almost equal to that of the original copper alloy number 54. It is identified from the foregoing fact that the copper alloy of the present invention is capable of effectively utilizing excess or unnecessary portions such as portion K of slides generated in its foundry as a raw material for recycling without damaging the effect of grain refinement. Thusit is possible to use the surplus or unnecessary portions such as the portion K of the slide as supplementary raw material loaded under the continuous operation and to carry out the continuous operation very efficiently or economically. The copper alloy of the present invention is subjected to grain refinement in the melt-solidification stage, so that it can resist shrinkage as it solidifies and decrease the generation of melt fractures. In addition, in terms of the holes or the porosity generated in the solidification process, they escape outwardly with. ease so that a good casting is obtained free of casting defects (because the casting defect such as porosity is not present, and because the dendritic network is not formed, the casting has a smooth surface and the Shrinkage cavity is shallow as possible). Therefore, in accordance with the present invention, it is possible to provide the foundry having a very abundant practical use or a worked plastic material by performing plastic work on the casting. In addition, the grains crystallized in the solidification process take the form in which the arm is divided, preferably such as a circular shape, an elliptical shape, a polygonal shape and a cross shape instead of a branch-like structure which is typical for a foundry structure. As such, the fluidity of the molten metal is improved, so that the molten metal can be dispersed to all corners of the mold even though the mold has a thin thickness and a complicated shape. The copper alloy of the present invention can accommodate a remarkable improvement in terms of machinability, toughness, wear resistance, slip susceptibility and wear resistance exerted by the constituent elements by means of grain refinement and uniform distribution of the phases (phases K and? generated by Si) except phase a or particle Pb and appropriately, can practically be used as a coupling in contact with the water used in contact with tap water at all times or temporarily (for example in water spigot couplings or water supply pipes, valve taps, gaskets, collars, water spigot couplings, residential installations and drainage mechanisms, connection couplings, water heating parts, etc.), the frictional coupling performs relative movement in contact with the other member (rotational axis, etc.), at all times oo temporarily (for example, of a bearing, a gear, cylinder, bearing retainer, impeller, valve, open-close valve, pump parts, bearings) or a pressure sensor, a temperature sensor, a connector, compre parts, sweep compre parts, a high pressure valve, a conditioned air valve and a valve that opens and closes, carburetor, a cable accey, a mobile phone antenna part, a terminal or these constituent members . Furthermore, according to the method of the present invention, grain refinement can be carried out by the coarsening effect of Zr and P without causing any problem caused by the addition of Zr in the form of oxide or sulfide, and from this way is able to melt the copper alloy casting in an efficient and favorable way.

[Table 1] 8 fifteen twenty (? or? r > L? H rH [Table 3] 00 fifteen [Table 4] oo fifteen [Table 5] oo fifteen OR LD rH H [Table 6] 00 VD fifteen un in [Table 7] I fifteen o m o L m rH CN L? [Table 9] YOU L? fifteen [Table 10 VD n fifteen [Table 11] YOU fifteen O -ID LD H H [Table 12] 15 Table 13 I-1 or o fifteen a c ID Table 14 OR fifteen O LD ID H H Table 15 H O Or L? o ID H H CN Table 16 h-1 or fifteen or L? L? H Table 17 o oo fifteen or ID ID H rH Table 18 or i 15 O ID ID H DO 15 O ID ID H H H F > 15 O ID ID H M H C? fifteen O ID LO H H I-1 oo 15 O ID ID H H O 15 O ID LD rH rH ID ID H t LO 15 O ID ID rH Industrial Applicability In particular, the copper alloy of the present invention can be suitably used for the following applications: 1. Mechanical parts in general that require moldability, conductivity, thermal conductivity and a high mechanical property. 2. Electrical terminals that require high conductivity and thermal conductivity, conductors and electrical parts in which copper welding and welding can be easily performed. 3. Parts of instruments that require excellent moldabilidad. 4. Water supply couplings, construction couplings and the need to seal them, which require an excellent mechanical property. 5. Marine impellers, shafts, bearings, valve housings, valve rods, clamping couplings, clamps that connect couplings, door knobs, pipe clamps and cams that require high toughness and hardness and excellent resistance to corrosion and tenacity . 6. Valves, pins, bushings, endless gears, arms, cylinder parts, valve housings, stainless steel shaft bearings and pump impellers. which require high tenacity, hardness and wear resistance. 7. Valves, pump bodies, impellers, hydrants, mixed spigots, tap water valves, gaskets, sprinklers, taps, water meters, spigots to stop water, sensor parts, sweep type compressor parts, high-pressure valves pressure and sleeve pressure containers which require resistance to pressure, wear resistance, machinability susceptibility and moldability. 8. Sliding parts, hydraulic cylinders, cylinders, gears, fishing reels and aircraft clamps that require excellent hardness and wear resistance. 9. Bolts, nuts and pipe connectors that require excellent toughness, corrosion resistance and wear resistance. 10. Mechanical chemical parts and industrial valves which are suitable for a large, simple shaped cast iron and which require high tenacity and excellent resistance to corrosion and wear resistance. 11. Welding pipes of a desalination apparatus, water supply pipes, pipes • heat exchangers, heat exchanger tube plates, gas pipe pipes, elbows, marine structural members, welding members and welding materials. which require a resistant union, accumulation spray, coating, overlap, corrosion resistance and moldability. 12. Couplings in contact with water (joint flanges) union sleeves, hose couplings, adapters, elbows, very short cylinders, tap cores, threaded reducers, unions, gaskets and collars. 13. Couplings in contact with water (valve taps) stop valves, suction artichokes, slith valves, gate valves, check valves, ball valves, diagram valves, constriction valves, ball valve, needle valves, miniature valves, release valves, plug tap, hand taps, acorns, two-way taps, three-way taps, four-way taps, gas taps, ball valves, valves of safety, release valves, pressure reducing valves, electromagnetic valves, steam traps, water meters, running water meters) and flow meters. 14. Couplings in contact with water (water spigot couplings) water spigots (hydrants, water sprays, water spigots, oscillating taps, mixed spigots and corporation spouts), spouts, branched spouts, check valves , bifurcated valves, flap valves, three-way taps, showers, shower hooks, tap males, zarubos, irrigation nozzles, sprinklers. 15. Couplings in contact with water (drainage mechanisms in residential installations), (installation of residential equipment)) traps, fire hydrant valves and water supply holes. 16. Drive pumps, covers, connection couplings and sliding bushings. 17. Equipment related to automobile valves and gaskets; pressure switching sensors, temperature sensors and connectors; bearing parts; compressor parts; carburetor parts and cable accessories. 18. Home accessories parts for a mobile phone antenna, terminal connectors, front screws, motor bearings (fluid bearings), copier shaft rollers, valve steam nuts for air conditioners and sensing parts. 19. Members of frictional coupling piston shoes of hydraulic pneumatic cylinders, sliding parts of bushing, cable fittings, high pressure valve seal, shafts or sprocket gear shafts, bearing parts, pump bearings, valve shoes , hexagonal top nuts and header hydrate parts.

Claims

1. Copper alloy consisting essentially of Cu: 69 to 88% by mass, Si: 2 to 5% by mass, Zr: 0.0005 to 0.04% by mass, P: 0.01 to 0.25% by mass and Zn: the rest that has a ratio, in terms of a content of an element a, (a) mass in%, fO = [Cu] - 3.5 [Si] - 3 [P] = 61 to 71, fl = [P] / [Zr] = 0.7 a 200, f2 = [Yes] / [Zr] = 75 to 5000 and f3 = [Yes] / [P] = 12 to 240; form a metal structure that contains phase a and phase K or phase? and that has a relation, in terms of a phase b content, of [b]% in a proportion in area, f4 = [] + [y] + [K] 85 and f5 = [y] + [K] + 0.3 [μ] = [ß] = 5 to 95; and having an average grain diameter of 200 μm or less in a macrostructure when it melts and solidifies.

2. Copper alloy as described in claim 1, additionally containing at least one that is selected from Pb: 0.005 to 0.45% by mass, Bi: 0.005 to 0.45% by mass, Se: 0.03 to 0.45% by mass and Te: 0.01 to 0.45% by mass; which has a relation, in terms of content of element a, of [a]% by mass, fO = [Cu] 3.5 [Si] - 3 [P] + 0.5 ([Pb] + 0.8 ([Bi] + [Se ]) + 0.6 [Te]) = 61 to 71, fl = [P] / [Zr] = 0.7 to 200, f2 = [Yes] / [Zr] = 75 to 5000, f3 = [Yes] / [P] = 12 to 240, tß = [Cu] - 3.5 [SI] - 3 [P] + 3 ([pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) 1 2 > 62 and f7 = [Cu] - 3.5 [Si] - 3 [P] - 3 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te] 12 £ 68.5 ([a] = 0 relative to element not contained a) forming the metal structure containing the phase a and the phase K or the phase y and having a relation, in terms of the content of phase b, [b]% at an area rate, f4 = [ a] + [y] + [K] > 85 and f5 = [y] + [K] + 0.3 [μ] - [ß] = 5 to 95 ([b] = 0 with respect to phase b) not contained and having an average grain diameter of 200 μm or less in a macrostructure when it melts and solidifies

3. Copper alloy as described in claim 1, which additionally contains at least one that is selected from Sn: 0.05 a 1.5% in mass, As: 0.02 to 0.25% in mass and Sb: 0.02 to 0.25% in mass, which has a relation, in terms of the content of element a, of [a]% by mass, fO = [Cu] - 3.5 [Yes] - 3 [P] - 0.5 ([Sn] + [As] + [Sb]) 0 61 to 71, fl = [P] / [Zr] = 0.7 to 200, f2 = [Yes] / [Zr] = 75 to 5000 and f3 = [Yes] / [P] = 12 to 240 ([a] = 0 with respect to the element not contained a); forming the metal structure containing the phase a and the phase K or the phase yy having a relation, in terms of the content of phase b, of [b]% at an area rate, f4 = [a] + [y] + [K] _ > 85 and f5 = [?] + [K] + 0.3 [μ] - [ß] = 5 to 95 ([b] = 0 with respect to phase b) not contained; and having an average grain diameter of 200 μm or less in a macrostructure when it melts and solidifies.

4. Copper alloy as described in claim 2, which additionally contains at least one that is selected from Sn: 0.05 to 1.5% by mass, As: 0.02 to 0.25% by mass and Sb: 0.02 to 0.25% by mass; which has a relation, in terms of the content of element a, of [a] in mass%, fO = [Cu] - 3.5 [Si] - 3 [P] - 0.5 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) - 0.5 ([Sn] + [As] + [Sb]) = 61 to 71, fl = [P] / [Zr] = 0.7 to 200, f2 = [Yes] / [Zr] = 75 to 500, f3 = [Yes] / [P] = 12 to 240, f6: [Cu] - 3.5 [Si] - 3 [P] + 3 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) 1/2 > 62 and f7 = [Cu] -3.5 [Si] - 3 [P] - 3 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) 1 2 < 68.5 ([a] = 0 with respect to element a) not contained); forming the metal structure containing the phase a and the phase K or the phase yy having a relation, in terms of the content of phase b, of [b]% at an area rate, f4 = [a] + [y] + [K] > 85 and f5 = [y] + [K] + 0.3 [μ] - [ß] = 5 to 95 ([b] = 0 with respect to phase b) not contained; and having an average grain diameter of 200 μm or less in a macrostructure when it melts and solidifies.

5. Copper alloy as described in any of claims 1 to 4, additionally containing at least one that is selected from Al: 0.02 to 1.5% by mass of Mn: 0.2 to 4% by mass and Mg: 0.001 a 0.2% in mass; which has a relation, in terms of the content of the element a, of [a] in mass%, fO = [Cu] -3.5 [Si] - 3 [P] - 0.5 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) -0.5 ([Sn] + [As] + [Sb]) - 1.8 [Al] + 2 [Mn] + [Mg] = 61 to 71, fl = [P] / [Zr] = 0.7 to 200, f2 = [Yes] / [Zr] = 75 to 5000 and f3 = [Yes] / [P] = 12 to 240 ([a] = 0 with respect to element a) not contained); to form the metallic structure that contains the phase a and the phase K or the phase? and that has a relation, in terms of the content of phase b, of [b]% at an area rate, f4 = [a] + [y] + [K] > 85 and f5 = [y] + [K] + 0.3 [μ] - [ß] = 5 to 95 ([b] = 0 with respect to phase b) not contained; and having an average grain diameter of 200 μm or less in a macrostructure when it melts and solidifies.

6. Copper alloy as described in any of claims 2, 4 and 5, which has a ratio, between the content of element a, of [a]% by mass and the content of phase b, [b]% in an area ratio, f8 = [y] + [K] + 0.3 [μ] - [ß] + 25 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te]) 1/2 > 10, and f9 = [?] + [K] + 0.3 [μ] - [ß] -25 ([Pb] + 0.8 ([Bi] + [Se]) + 0.6 [Te] 1/2 <70 ( [a] = [b] = 0 with respect to a non-contained element or a phase b)

7. Copper alloy as described in any of claims 1 to 6, wherein either of Fe and Ni is contained as an impurity inevitable, the content of either Fe and Ni is less than 0.3% by mass, and when Fe and Ni are contained as an unavoidable impurity, a total content of Fe and Ni is less than 0.35 mass%. as described in any of claims 1 to 7, wherein, when melting and solidifying, a primary crystal is phase a 9. Copper alloy as described in any of claims 1 to 7, wherein, when melted and solidifies, a peritectic reaction is generated 10. Copper alloy as described in any of claims 1 to 7, wherein, when melted and solidified a network of dendrites has a crystalline structure. idida and a two-dimensional shape of a grain has any of a circular shape, a non-circular shape similar to a circular shape, an elliptical shape, a cross shape, an acicular shape and a polygon shape. 11. Copper alloy as described in any of claims 1 to 7, wherein the phase a of a matrix is finely divided, and at least one of the phases K and? they are evenly distributed in the matrix. 12. Copper alloy as described in any of claims 2, 4, 5 and 7, wherein, when either one of Pb and Bi is contained, any one of the particles of Pb and Bi has a uniform size thin is distributed evenly in a matrix. 13. Copper alloy as described in any of claims 1 to 12, having any of a foundry that is obtained in a casting process and a plastic worked material that additionally performs plastic work on the casting at least once. 14. Copper alloy as described in claim 13, wherein, when the plastic worked material is cut by a lathe using a depth of an angle of attack: - ß ° and a tip radius: 0.4 mm under a condition of Cutting speed: 80 to 160 m / min, a cutting depth: 1.5 mm and a feeding speed: 0.11 mm / rev, a cutting chip generated is a worked cutting material that has a small segment shape shape trapezoidal or triangular and a tape of acicular shape that has a length of 25 mm or less. 15. Copper alloy as described in claim 13, wherein the casting is a wire, a rod or a hollow bar foundry by horizontal continuous casting, ascending casting or upper casting. 16. Copper alloy as described in claim 13, wherein the plastic worked material is a hot extruded material, a hot forged material or a hot rolled material. 17. Copper alloy as described in claim 13, wherein the plastic worked material is a wire, a rod or a hollow bar formed by tensioning or cold drawing the casting defined in claim 15. 1

8. Copper alloy as described in claim 13, wherein the casting is a foundry, a semifinished casting, a semi-cast shaped material or a forged material of molten metal or a material formed by die casting wherein at least one network of dendrites has the crystalline structure divided into a semi-molten state of an in-phase fraction solid from 30 to 80% and the two-dimensional form of the solid phase has any of a circular shape, the non-circular shape close to the circular shape, the elliptical shape, the cross shape, the acicular shape and the polygon shape. 1

9. Copper alloy as described in claim 18, wherein, in the 60% solid phase fraction, an average grain diameter of the solid phase is less than 150 μm or a maximum average length of the corresponding solid phase is less than 200 μm 20. Copper alloy as described in claim 18 or 19, wherein the copper alloy is melted to an almost pure form. 21. Copper alloy as described in any of claims 13 to 20, wherein the copper alloy is a coupling in contact with water that is used in contact with water at all times or temporarily. 22. Copper alloy as described in claim 21, wherein the copper alloy is a connecting sleeve, a hose coupling sleeve, an adapter sleeve, an elbow, a very short cylinder, a tap male, a threaded reducer, a joint, a gasket, a collar, a stop valve, a suction valve, a slit valve, a gate valve, a check valve, a ball valve, a diaphragm valve, a constriction valve, a ball valve, a needle valve, a miniature valve, a release valve, a plug tap, a hand tap, an acorn tap, a two-way tap, a three-way tap, a four-way tap tracks, a gas tap, a ball valve, a safety valve, a release valve, a pressure reducing valve, an electromagnetic valve, a steam trap, a running water meter, a flowmeter, a hydrant, a aspersi spigot a water spout, a water stop tap, an oscillating tap, a mixed spigot, a corporation spigot, a spout, a forked spout, a check valve, a forked valve, a hinge valve, a three way tap , a shower, a shower hook, a tap tap, a spout, an irrigation nozzle, a sprinkler, a heating tube for a water heater, a heating tube for a heat exchanger, a heating tube for a heater, a trap, a fire hydrant valve, a water supply orifice, an impeller, a drive shaft or a pump cover or its constituent members. 23. Copper alloy as described in any of claims 13 to 20, wherein the copper alloy is a frictional coupling member that performs a relative movement in contact with water at all times or temporarily. 24. Copper alloy as described in claim 23, wherein the copper alloy is a gear, a slidable bushing, a cylinder, a piston shoe, a bearing, a bearing part, a bearing member, an arrow or shaft, a roller, a rotary joint part, a bolt, a nut or the body of a screw or its constituent members. 25. Copper alloy as described in. any of claims 13 to 20, wherein the copper alloy is a pressure sensor, a temperature sensor, a connector, a compressor part, a sweep compressor part, a high pressure valve, a value valve Open-closed for an air conditioner, a carburetor part, a cable accessory, a mobile phone antenna part or a terminal. 26. Method for producing a copper alloy as described in any of claims 1 to 25, in which, in a casting process, Zr is added to a form of a copper alloy material containing Zr and Zr is prevented from being added to a form of an oxide or a sulfide when the casting is performed. 2 . Method as described in the claim 26, wherein the copper alloy material containing Zr is a copper alloy which additionally contains at least one which is selected from P, Mg, Al, Sn, Mn and B based on the Cu-Zr alloy, a Cu-Zn-Zr alloy or its alloys.