TW200930822A - Lead-free, free-machining brass having excellent castability - Google Patents

Abstract

Disclosed is a brass which contains no lead (Pb), and which is excellent in cutting properties, castability, mechanical properties and others. Specifically disclosed is a brass comprising Cu at a content of 55 to 75 wt% (inclusive), Bi at a content of 0.3 to 4.0 wt% (inclusive), and B and Si at such contents that, when the contents of B and Si are represented by y wt% and x wt%, respectively, then y and x fulfill the relationship represented by the following formulae: 0=x=2.0, 0=y=0.3 and y > -0.15x+0.015ab [wherein a is a numeral number of 0.2, 0.85 or 1 when the content of Bi falls within the following range: 0.3=Bi < 0.75 wt%, 0.75=Bi < 1.5 wt% or 1.5=Bi=4.0 wt%, respectively; and b is a numeral number of 1 when the apparent Zn content is not less than 37 wt% and less than 41 wt%, and a numeral number of 0.75 when the apparent Zn content is 41 to 45 wt% (inclusive)], with the remainder being substantially Zn and unavoidable impurities. The brass has excellent castability, cutting properties, mechanical properties and others.

Description

200930822 IX. INSTRUCTIONS OF THE INVENTION [Technical Field] The present invention relates to a lead-free brass, that is, a lead-free brass, and particularly relates to an excellent casting which is particularly suitable for use in a faucet part or the like because it does not contain lead. Casting brass for properties, machinability and mechanical properties. [Prior Art] The faucet parts are usually made of brass or bronze. In order to improve the machinability, 2 to 3 wt% is added to the brass, and 4 to 6 wt% of lead (Pb) is added to the bronze. However, in recent years, attention has been paid to the impact of Pb on the human body, the environment, etc., and countries have actively carried out restrictions on Pb. For example, in California, starting from January 2010, the restriction that the Pb content of the faucet is below 0.25 wt% will come into effect. Moreover, it is reported that the amount of elution for Pb will be limited to about 5 ppm in the future. This limitation is also significant in countries outside the United States, and it is also required to develop materials that can correspond to the above Pb content or the amount of Pb elution. In Japanese Laid-Open Patent Publication No. Hei 7-3 10133 (Patent Document 1), since bismuth (Bi) exhibits characteristics similar to those of Pb in brass, it has been proposed to add Bi instead of Pb. Further, in Japanese Patent Publication No. 2005-290475 (Patent Document 2), it is disclosed that bismuth (B), nickel (Ni) or the like is added in order to improve the machinability of such a type of brass to which Bi is added. In Japanese Patent Laid-Open Publication No. 2001-59123 (Patent Document 3), it is disclosed that the addition of iron (Fe) in the type of brass to which Bi is added can make the crystal finer. However, the brass of this type disclosed in the prior art -4-200930822 still has room for improvement in its castability, especially in the case of casting. Therefore, it can be said that there is still a demand for brass which does not contain Pb and which has excellent castability, machinability and mechanical properties. [Patent Document 1] Japanese Unexamined Patent Publication No. Hei No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. 2001-59. A new insight is that in the brass in which Pb is replaced by adding Bi, B and Si are added in a predetermined relationship, that is, the casting crack can be effectively prevented, and the machinability and mechanical properties are excellent. And brass such as corrosion resistance. Moreover, a new insight is obtained: the addition of elements such as Ni, A1, Sn, etc., which are usually added to improve the properties of the brass, have an effect on the casting rupture, and the Q-ring system can be used in a prescribed relationship. Adding B and Si can prevent casting cracking. The present invention has been developed based on the above findings. Therefore, an object of the present invention is to provide a brass which does not contain Pb and which has excellent castability, machinability, mechanical properties and the like. In addition, the brass disclosed in the present invention is characterized in that the ratio of the crystal structure to the α + 泠 phase is 85 % or more, the Cu content is 55 wt% or more and 75 wt % or less, and the Bi content is 0.3 wt% or more and 4.0 wt % or less. When B and Si are ywt% and xwt%, respectively, the amount is in accordance with the following relationship 200930822, OS 2.0, OS yS 0.3 and y&gt; ·0·15χ + 0.015ab (here, a is 0.3SBi&lt;0.75wt in Bi %, 0.75; 1.5wt%, 1.5SBiS4.0wt%, respectively 0.2, 0.85 and 'b when the apparent Zn content is 37% or more and less than 41%: • 0.75 or more and 45% or less is 0.75 In addition, the remainder is substantially composed of Zn and the unavoidable impurity j 0 . [Embodiment] [Definition] In the present invention, the term "inevitable impurities" means an element having an amount smaller than o.iwt% as long as it is specifically described. Although Sb, P, As, Mg, Se, Te, Fe, Co, Zr, and Cr are contained in unavoidable impurities, the contents thereof are separately added in the specification. The amount of the unavoidable impurities is preferably 0.05% by weight. [α phase · /3 phase] The brass disclosed in the present invention has a total ratio of the α phase to the Θ phase of 85 % or more, and preferably 90% or more. By having a crystal structure of the α phase and the ruthenium main body, it is possible to realize brass having good castability. The present invention is preferably to avoid dendritic crystals of the primary crystal α phase. Further, in the present invention, the total ratio of the α phase and the yS phase is the face in the crystal cross section.

Bi &lt;1;;1, group: first and not Ti 1 and less than the case in the phase, and in the product ratio -6-200930822 as the benchmark, for example: for the photomicrograph taken by the optical microscope image The process is performed to obtain the total area ratio of the α phase and the θ phase. [Bi] The brass disclosed in the present invention contains Bi in an amount of from 0.3% by weight to 4.0% by weight. Since Bi exhibits similar characteristics to Pb in brass, Pb can be imparted with the same machinability instead of Pb. In the present invention, Bi is 0.3% by weight or more in order to obtain good machinability. On the other hand, if Bi is excessive, there is a tendency to cause Bi agglomeration, and since the agglomerated portion may become a starting point of casting cracking, the upper limit is 4.0 wt%. According to a preferred embodiment of the present invention, the preferred lower limit of Bi is more than 0.5 wt%. 'If the machinability is considered, it is preferably 1.0% by weight, and the upper limit is preferably 3.0% by weight or less, and 2.0% by weight. The following is especially good. Further, according to the present invention, good machinability can be achieved even if Pb is not contained at all. It is preferable to have no Pb at all, and even if it is assumed to be contained, it is only limited to it as an inevitable impurity. Specifically, considering that the human body and the environment are 0.5 wt% or less, 〇.1 wt% or less is more preferable. • [B and Si] In the present invention, 'B promotes refinement of crystals (especially, primary crystal phase). As a result, Bi fine dispersion can effectively prevent cracking during casting. Further, 'Sl solid-melt is in the absence phase, and it is presumed that it has a function of alleviating the breakage of the interface between Bi and the phase which is the starting point of the casting fracture. Further, the brass of τκ disclosed in the present invention exhibits good performance for good mechanical properties as a result of the refinement. The brass disclosed in the present invention contains B and Si. When the amount of B and Si is ywt% and xwt%, respectively, the amount is in accordance with the relationship between 〇SyS〇.3 and 〇$x2, and y&gt;-0.15x+0.015ab. Here, the appropriate amounts of B and Si change depending on the amount of Bi added and the apparent Zn content described later. Therefore, the coefficients a and b indicate the correction coefficients. Specifically, the coefficient a varies with the amount of Bi, and is 0.2, 0.85, and 1 when Bi is 〇 〇 75.5%, 〇.75SBi &lt; 1.5 wt%, and 1.5 SBiS 4.0 wt%. Further, the coefficient b changes with the apparent Zn enthalpy, and is 1 when the apparent Zn content is 37% or more and less than 41%, and 0.75 when it is 45% or more. According to a preferred embodiment of the present invention, y and X are in the range of 0SyS0.03 and 0SXS1.8, and are in the range of O^ySO.Ol and 0SxS1.5, and conform to y&gt;-0.l5x + 〇. The amount of 〇15ab relationship is particularly good. Although it is necessary to add B of the above lower limit 为了 in order to achieve the refinement of the crystal, the addition of an excessive amount of B may cause deterioration of the ductility of the alloy. Therefore, the upper limit is 〇.3 Wt% or less, and 0.03 wt% is Preferably, it is preferably o.oiwt% or less. Further, B and Fe, Cr, and the like will form an intermetallic compound, and a pitting will be formed, which may cause problems in the surface processing of the molded article after casting. Therefore, when the surface is required to have smoothness, it is preferable to reduce the amount of addition of B and/or to reduce the content of Fe, Cr, etc., specifically, B is 0.005 wt% or less, preferably 〇〇. 〇〇 3 wt% or less, Fe. And Cr is preferably less than 0.1% by weight. Further, as described later, according to Guillet, the Zn content is 10, and the apparent Zn content is increased, and a hetero phase of -8-200930822 r phase or /c phase transport may be crystallized in the crystal structure. Therefore, the amount of Si added in accordance with the present invention is 2.0 wt% or less, and the upper limit is preferably 1. In the present specification, the apparent Zn content means an amount calculated according to the following formula. This formula is based on the Zn 'addition element which shows the same tendency as the addition of Zn g 〇❾ Apparent Zn content (%) = [(B + tq) / (A + B + tq)] xl〇〇 In the formula, A = Cuwt%, B = Znwt%, t is the amount of added element white, and q means the added amount of the added element wt%. Further, the name Zn equivalent is Si = 10, Al = 6, Sn = 2, Pb = 1, Fe = 0.9, and Ni = -1.3. The Zn equivalent of Bi has not been clearly defined, and in the case of the reference, the calculation is carried out at 0.6. Further, since the element of Xue is small in addition amount, the influence on 値 of Zn equivalent is also Φ, so it is "1". [Cu, Zn and other components] The brass disclosed in the present invention contains copper (Cu) of 55 wt% or less. If Cu is above the above range, cracks may occur due to the dendritic crystals of the two phases. Moreover, if the range of Cu 1 is difficult to be affected by the α phase, the performance of P brass may be obtained. According to a preferred embodiment of the present invention, Cu 6 is preferably 58% by weight, and the upper limit is preferably 70% by weight. 3 - kind of 5wt%, the idea of Zn other than Guillet 'Zn when the element's Μ = 0.5 specification is very small, 1 7 5 wt primary crystal α at the above lower limit is 200930822 In addition, if the apparent Zn can be made When the content is adjusted to 37 to 45% and the ratio of the crystal phase to the α + no phase is 85% or more, the amount of Cu can be utilized in the upper limit portion of the above range. Therefore, the upper limit of the amount of Cu is increased. The brass disclosed in the present invention is such that the remainder of the portion composed of the above components is substantially composed of zinc (Zn). * The brass disclosed in the present invention may contain various added components in order to improve the characteristics of the brass. Moreover, although the presence of impurities which are unavoidable U is not excluded in the present invention, it is preferable to minimize them. According to an embodiment of the present invention, Ni may be added for the purpose of improving strength, corrosion resistance and the like. In order to more effectively obtain the strength and the resistance to uranium resistance caused by the addition of Ni, it is preferable to add Ni 0.3% by weight or more. On the other hand, from the viewpoint of casting cracking, it is preferable to avoid excessive Ni. It is preferably 2 · 0 wt % or less. Further, according to a preferred embodiment of the present invention, the amount of addition of Ni and the amounts of B and Si corresponding thereto are as follows, and can be classified into various cases. φ When B and Si are ywt% and xwt%, respectively, the amount is in the following relationship, 0.1 S Ni &lt; 〇·3 wt% when • • (1) 〇.〇5abSxS0.75ab, 0 &lt;y$〇 .3 (2) 〇.75ab &lt; x S 2.0, 0 S y each 0.3 0· 3 S Ni &lt; 1 -〇wt%, (1) 0.05abSxS0.2ab, -0.15x+〇.〇3ab&lt ;yg〇.3 (2) 0.2ab&lt;xS0.75ab, 〇&lt;yg〇.3 (3) 0.75ab&lt;xS1.75ab, y ^ 0.3 -10- 200930822 (4) 1.75ab &lt; x ^ 2.0 when ' 0 · 0 0 4 x - 0.0 0 7 ( 2 - ab ) &lt; y ^ 0.3 1 · 0 S Ni 刍 2.0wt%, (1) 0.05abSxS〇.2ab when '〇.〇2ab&lt;yS0 .3 (2) 0.2ab&lt;xS0.3ab when '-0.05x+ 0.03 ab&lt;yS0_3 (3) 0.3ab&lt;xS0_5ab, 〇.〇15ab&lt;yS0.3

(4) 〇.5ab&lt; l.Oab when '-〇·〇26χ + 0.028ab< yS O 0.3 (5) 1.0ab&lt;xSl_5ab when '〇.〇llx-〇.〇〇9(2-ab) &lt; y S 0.3 (6) 1.5ab&lt;xS2.0' 〇-〇〇75ab&lt;yS0.3 (here, 'a is 0.3' Bi&lt;〇.75wt%, 0.75SBi&lt;1.5wt%, 1.5SBiS4_0wt% in Bi In the case of 〇·2, 0.85, and 1'b, when the apparent Zn content is 37% or more and less than 41%, it is '_75 when it is 1' 舄 41% or more and 45% or less. Further, according to a more preferred embodiment of the present invention, the amount of addition of Ni and the amount of B and Si corresponding thereto are as follows. When b and si are ywt% and xwt%, respectively, the amount is in the following relationship, 0.1 $ Ni &lt; 0.3 wt% when '(1) 0.05ab$xS〇.3ab' 0_001abSyS0.3 (2) 0 3ab&lt ;x$〇-5ab when '·0·00375χ+0·002125αΙ)^ VS 0.3 (3) 0 5ab&lt; 〇.75ab, -0.001x + 〇-〇〇〇75ab$ y 11 - 200930822 ^ 0.3 (4 0.75ab &lt; x S 2.0, 0 S y S 0.3 0_3 S Ni &lt; 1 .Owt%, (1) 0.05abSxS0.22ab, -0.1 3 75x+ 0.03 1 25abS 0.3 (2) 0.22ab &lt; x ^ 0.3 ab B#, O.OOlab^ 0.3

(3) 0.3ab &lt; x ^ 0.5ab, -0.003 75x+ 0·002 1 25 abS

(4) When 0.5ab &lt; x ^ 0.75ab, -O.OOlx + 0.00075ab ^ y ^ 0.3 (5) 0.75ab&lt;xS1.75ab, 0SyS0.3 (6) 1 ,75ab &lt; x ^ 2.0 , 0.006x-0.0105 ( 2-ab) ^ y ^ 0.3 1 ·〇S Ni S 2.0wt%,

(1) When 0.05ab S x S 0.2ab, 0_0225ab S y S 0.3 ❹ (2) 0.2ab &lt; x ^ 0.3ab, -0.0 5 x + 0.0 3 2 5 ab S y S 0.3

(3) 0.3ab&lt;xS0.5ab, 0.0175abSyS0_3 ' (4) 0.5ab &lt; x S 1 .Oab, -0.029x + 0.032ab S y S 0.3 (5 ) 1.0ab&lt; 1.5ab, 0.0165x -0.0135 ( 2 - ab ) ^ y ^ 0.3 (6) 1.5ab&lt;xS2.0, 0.01125abSyS0.3 (In the foregoing, X, y, a, and b are synonymous with the foregoing.) -12- 200930822 'According to other embodiments of the present invention, A1 may be added for the purpose of improving fluidity, surface properties, and the like. In order to more effectively obtain the improvement of fluidity, surface properties, etc. caused by the addition of A1, it is preferable to add A1 〇.3 wt% or more. On the other hand, from the viewpoint of casting cracking, it is preferable to avoid excessive A1. The upper limit is preferably 2. 〇 wt% or less. Further, according to a preferred embodiment of the present invention, the amount of addition of A1 and the amount of B and Si corresponding thereto are as follows, and can be classified into various cases. Q When B and Si are ywt% and xwt%, respectively, the amount is in accordance with the following relationship, 〇_l$Al&lt;0.3wt%, (1) 0^y^0.3' 0^x^2.0' y &gt; - 0.1 5 x + 0.0 1 5 ab 0.3 S A1 &lt; 1 .Owt%, (1) OSxSO.lab, -0_15x+0.015ab&lt;yS0.3 (2) O.lab &lt; xS 1.5ab 0&lt;yS0.3 (3) 1 .5ab &lt; x ^ 2.0, 0.0〇2x-0_003 ( 2-ab) &lt;y$ 〇0.3 1 ·0 S A1 S 2.0wt%, (1) 0.05abS When xS 0.3ab, 〇.〇〇4ab &lt; y $ 0.3 ' (2 ) 0.3 ab &lt; x S 0· 5ab, -〇·〇1 x + 〇.〇〇7ab &lt; y S 0.3 (3 ) 0.5ab &lt; x ^ 1 .Oab, -〇.〇〇4x+ 0.004ab&lt;y$ 0.3 (4) 1.0ab&lt;xSl_5ab, 〇_〇〇lx-〇_〇〇l(2-ab) &lt; y ^ 0.3 (5) 1.5ab&lt;xS2.0, 0 · 0 0 0 5 ab &lt; y S 0 · 3 -13- 200930822 (here, a is 0.3^Bi&lt;〇.75wt%, 0.75 in Bi When SBi &lt; 1.5 wt % and 1.5 SBi $ 4.0 wt%, respectively, 0.2, 0.85 and 1, b are 1 when the apparent Zn content is 3 7% or more and less than 41%, and 41% or more and 45% or less. 0.75). According to a still further preferred embodiment of the present invention, the amount of addition of A1 and the amounts of B and Si corresponding thereto are as follows, and can be classified into various cases. When B and Si are respectively ywt% and xwt%, the amount is 符合. 1 ^ Al &lt; 0.3wt%, (1) 0^y^0.3' 0^x^2.0' y ^ -0.1 4x + 0.0 1 7 5 ab 0.3 g A1 &lt; 1 .Owt%, (1) OSxS 0.1178 ab, -0·14χ + 0.0175 ab each yS 0.3 (2) 0.1 1 78ab &lt; x S 0.3ab When O.OOlab^ 0.3 (3) 0.3ab &lt; x ^ 〇.5ab, -0.00375x + 0.002 1 25ab ^ 0.3 〇(4) 0.5ab &lt; XS 1.5ab, 0.00025ab each y $ 0.3 ( 5) 1 , 5ab &lt; x ^ 2.0, 0.0 0 2 5 x - 0.0 0 3 5 ( 2-ab ) ^ y ^ 0.3 • 1 . When the guest A1 S 2.0wt%, (1) 0.05ab S x When S 0.3ab, 0.0 0 5 7 5 ab $ y 彡〇. 3 (2) 0.3ab&lt;x'〇.5ab, -0.0 1 3 75x+ 0.009 875 abS 0.3 (3) 0.5ab &lt; x ^ 1 . Oab, -0.0055x+ 0.00575ab^ y ^ 0.3 -14- 200930822 (4) 1 .Oab &lt; x ^ 1 .5ab &gt; 0.0 0 1 x - 〇. 〇〇〇7 5 ( 2-ab ) ^ y ^ 0.3 (5) 1.5ab&lt;x 彡2.0, 0.00075ab 彡yS0.3 (In the foregoing, X, y, a, and b are synonymous with the foregoing.) Further, according to other embodiments of the present invention, In order to improve the resistance to corrosion Plus Sn, but the present invention is disclosed in brass, Sn may cause casting cracking easily occurs. In order to more effectively obtain the improvement of corrosion resistance caused by the addition of Sn φ, it is preferable to add SnO. 3 wt% or more. On the other hand, excessive amount of Sn may cause casting cracking, and the upper limit is 3.0 wt. % below is appropriate. Further, according to a preferred embodiment of the present invention, the amount of addition of Sn and the amount of B and Si corresponding thereto are as follows, and can be classified into various cases. When B and Si are respectively ywt% and xwt%, the amount is in the following relationship: 〇· 1 S Sn &lt; 〇.3wt%, Q ( &quot; 〇SxS〇"25ab, -〇_i6x+0.02 Ab&lt;yS0.3 (2) 0.125ab<xS〇.4ab, when 00&lt;yS〇.3 (3) 0.4ab&lt;xS2.〇, 〇syS〇.3 ' 〇.3SSn&lt;1.5wt%, ( 1) When 0SxS0.25ab, -〇〇8x+〇.〇2ab&lt;yS0.3 (2) 0_25ab &lt; x' 1.25ab, 0 &lt; y S 〇·3 (3) 1.25ab &lt; x S 1.75ab 0 S y S 〇·3 (4) 1.75ab&lt; 2.〇,〇.〇〇2χ-〇·〇〇35 ( 2-ab) &lt; y ^ 0.3 -15- 200930822 1 . 5 S Sn S 3 .Owt%, (1) OSxSO.lab, 0.025ab&lt;y$0.3 (2) 0.1ab &lt; x ^ 〇.3ab, -0·105x+ 0_03 5 5ab&lt; yg 0.3 (3) 〇.3ab&lt ;x$〇.5ab, 0.004ab&lt;y$0_3 (4) 0.5 ab &lt; x $ 1 . 〇ab, 0 · 0 0 7x + 0.0 0 0 5 ab &lt; y $ 0.3 ◎ ( 5) 1 .Oab &lt; x ^ 2.0, 0 · 0 4 5 x - 0.0 3 7 5 ( 2-ab ) &lt; y ^ 0.3 (here, a is Bi in Bi.3SBi &lt; 0.75wt%, 〇.75SBi&lt; 1.5wt%, 1.5SBi, 4.0wt%, respectively, 0.2, 0.85 and 1, b in the apparent Zn content of 37 When the ratio is more than 41% and is less than 41%, it is 1 and when it is 41% or more and 45% or less, it is 0.75). Further, according to a more preferred embodiment of the present invention, the amount of addition of Sn and the amount of B and Si corresponding thereto are as follows. It can be divided into various cases. Q When B and Si are ywt% and xwt%, respectively, the amount is in the following relationship, 0.1SSn &lt;0.3wt%, - (1) 0 ^ X ^ 0.1 246ab, -0.1 925x + 〇· 025 ab ' y € 0.3 (2 ) 〇.1246ab&lt; xS 0.3ab when ' 0 · 0 0 1 ab $ y S 〇· 3 (3) 0.3ab&lt;xS〇.4ab, -0.01x+〇 .〇〇4abSy$〇·3 (4) 0.4ab&lt;xS2.0, 0SyS0.3 〇.3$Sn&lt;1.5wt%, -16- 200930822 (1) OSxSO.lab, -0.1375x+ 0.025ab $yS0.3 (2) 0.1ab&lt;xS 0.286ab, -0.05 5x+ 0.0 1 675ab'y ^ 0.3 (3 ) 0.28 6ab &lt; x S 0.3ab, 0 · 0 0 1 ab S y S 0 · 3 (4) 0.3ab &lt; x ^ 0.5ab, -0 · 0 0 3 7 5 x + 0 · 0 0 2 1 2 5 ab S 0.3 (5) 0.5ab&lt;xS1.0ab, 0.00025ab ^ y ^ 0.3

(6) 1.0ab&lt; 1.25ab, -0.001x+ 0.00 1 25ab^ y ^ 0.3 (7) 1 .25ab &lt; x S 1.75ab, y ^ 0.3 (8) 1,75ab &lt; x ^ 2.0 0.003x-0.00525 ( 2-ab ) ^ 0.3 1 .5 S Sn S 3 .Owt%, (1) OS275SO.lab, 0.0275ab$y$0.3

(2) 0.1 ab &lt; x ^ 0.2ab, -0.075x+ 0.035abSyS 〇 0.3

(3) 0.2ab&lt; 0.3ab, -0.1425x+ 0.0485abSyS 0.3 (4) 0.3ab &lt; x S 0.5ab, 0.00575ab S y S 0.3 (5) 0.5ab&lt; l.Oab, 0.011x + 0.00025 Ab$ 0.3 (6) 1 .Oab &lt; x ^ 1.25, 0.0 7 5 x - 0.0 6 3 7 5 ( 2 -ab ) ^ y ^ 0.3 (In the foregoing, X, y, a and b are as described above -17- 200930822 In addition, when Ni, Al, and Sn coexist, it is sufficient to set them according to the respective addition amounts of the elements that coexist, in a range that satisfies the predetermined range as described above. That is, according to other embodiments of the present invention, a brass is provided, wherein the crystal structure has a total ratio of the α phase and the A phase of more than 85 %, and the Cu content is 55 wt% or more and 75 wt% or less, and the Bi is contained in the crucible. 3 wt% or more and 4.0 wt% or less, and further, ❹ B and Si, and from 0.1% by weight or more of 2.0% by weight or less of Ni, 0.1% by weight or more and 2.0% by weight or less of A1 and 0.1% by weight or more and 3.0% by weight. At least two components selected from the group consisting of Sn below %, the remainder consisting essentially of Zn and unavoidable impurities, characterized in that = B and Si are respectively yWt% and xwt%, At the same time, at least two relational expressions specified in claims 2 to 10 of the patent application scope of the present application corresponding to the respective amounts of at least two elements of the group consisting of the Ni, A1, and Sn are satisfied. In the brass disclosed in the present invention, when Μη is added to increase the strength, an intermetallic compound of Μη and Si is generated to consume Si, and therefore, casting cracking may occur. When Μη is not used, the upper limit is made less than 0.3 wt% in order to suppress the influence on the casting fracture property. On the other hand, in the case of effectively utilizing the strength increase due to the addition of Μη, it is only necessary to sufficiently increase the amount of addition of Si. That is, when the addition of Μη is 0.3% by weight or more, the influence on the casting fracture property caused by the addition of Μη can be suppressed by satisfying the above-specified range and 0.7 &lt;Si$2.0 wt%, -18-200930822. Further, excessive addition of Μη increases the amount of the intermetallic compound and lowers the machinability, so the upper limit is 4.0% by weight. In the brass disclosed in the present invention, it is also possible to select additional elements according to different purposes to add other components, for example, Sb, P, etc., which are beneficial to _ to improve corrosion resistance by a small amount of addition, and a trace amount of addition as a refinement The agent can improve the casting crack, and can improve the strength of Fe and the like. The addition of the above component to the amount of 0 may have an effect on the castability, but by adjusting B and Si, the influence can be suppressed. That is, in the type of brass in which casting cracking occurs, the influence can be suppressed by further increasing the amount of B within the above range, or conversely increasing the amount of Si further, or both. According to a preferred embodiment of the present invention, the brass of the present invention may further contain one or more selected from the group consisting of Sb, P, As, Mg, Se, Te, Fe, Co, Zr, Cr, and Ti. The content of the element is preferably 0.01 to 2% by weight. According to another preferred embodiment of the present invention, in order to improve corrosion resistance and corrosion resistance, one or more elements selected from the group consisting of Sb, P, As, and Mg may be contained, and the suitable content thereof, Sb The P and As are 0.2% by weight or less, and the Mg is 1% by weight or less. Further, according to another preferred embodiment of the present invention, Se or Te may be contained in an amount of 1 wt% or less in order to improve machinability. According to another preferred embodiment of the present invention, in order to improve the strength, one or more elements selected from the group consisting of Fe, Co, Zr, Cr and Ti may be contained, and the suitable content thereof, Fe and Co The ratio is below 1 wt%, and the other elements are below 5% by weight. -19- 200930822 [Use] The brass disclosed in the present invention does not contain Pb, and on the other hand, its castability, machinability and mechanical properties have the same or better performance as those of Pb-containing brass, and therefore, it is very suitable for use. For faucet parts materials. Specifically: It is suitable for use as a faucet part, a drain part, a valve, etc. [Manufacturing Method] The molded article made of the brass disclosed in the present invention can be produced by metal casting or sand casting because of its good castability, but it is more preferable in metal casting. Good castability. Further, the brass disclosed in the present invention is also excellent in machinability, and can be subjected to cutting after casting. Further, the brass disclosed in the present invention can also be used as a cutting bar or a forging bar which is extruded after continuous casting, and can also be used as a wire formed by drawing. [Examples] The present invention will be described in more detail based on the following examples, but the present invention is not limited to these examples. [Evaluation Test] The details of each evaluation test in the following examples are as follows. (1) Casting cracking test The casting cracking property was evaluated by the two-end restraint test method. -20- 200930822 The shape of the metal mold 1 used is as shown in Fig. 1. In Fig. 1, the heat insulating material 2 is provided at the center portion so that the cooling rate at the center portion is slower than the both end restraining portions 3, and the distance between the ends (2L) is 100 mm, and the length of the heat insulating material (21) is 7. 0mm. In the test, the restraining portion 3 was rapidly cooled and both ends were restrained, and in the state of the state, the central portion was further solidified, and the resulting solidification shrinkage stress was used to investigate: at the center of the test piece which became the final solidified portion. Whether or not there is a crack to proceed. As a result, it was judged as ◎ when there was no rupture, and it was judged to be 〇 when a partial rupture occurred but did not reach the fracture, and was judged to be X when the rupture occurred and was broken. (2) Machinability test An ingot having a diameter of 35 mm and a length of 100 mm was produced by metal casting, and the outer diameter portion was subjected to turning processing to evaluate the machinability. Specifically, the machinability was evaluated by the number of cutting resistance fingers of three types of brass castings (JIS CAC203). The cutting conditions were a peripheral speed of 80 to 175 m/min, a feed amount of 0.07 to 0.14 mm/rev, and a feed amount of 0.25 to 1 mm, and the cutting resistance index was calculated by the following formula. * Cutting resistance index (%) = cutting resistance of CAC203 / cutting resistance of test piece χίοο As a result, the cutting resistance index is 70% or more and is judged as ◎' 50% or more and less than 70%. The judgment is 〇' less than 50%. It is judged as X. -21 - 200930822 (3) Mechanical property test An ingot of 35 mm in diameter and 100 mm in length was cast by metal casting, and machined into a test piece of JIS Z 220 1 1 4A and subjected to a tensile test. That is, 0.2% proof stress, tensile strength, and elongation at break were measured, and 0.2% proof stress was l〇〇N/mm2 or more, tensile strength was 245 N/mm2 or more, and elongation at break was 20% or more. When all three items are met, it is judged as ◎, and when it is two items, it is judged as 〇, and only one item is selected. (4) Corrosion resistance test An ingot with a diameter of 35 mm and a length of 100 mm, which was cast by metal mold casting, was prepared as a test piece, and was carried out according to the technical standard JBMA T-303-2007 of the Japan Copper Association. test. The maximum erosion depth is judged to be ◎ below 15 〇 μηη, and more than 15 〇 /zm is determined to be 〇' exceeds 300 &quot; m is 300 or less. (5) Measurement of Crystallization Comparative Example The image S was obtained from the photograph of the crystal structure photographed by the optical microscope, and the area ratio of the α phase and the Θ phase was determined. Examples 1 to 5 1 5 : Brass having the composition components described in the following tables were cast. That is, 'electrolytic Cu, electrolytic Ζη, electrolytic Bi, electrolytic Pb, electrolytic Sn, Cu-30% Ni master alloy, electrolytic Ab Cu-15%Si master alloy, Cu-2%B master alloy-22- 200930822, Cu-30%Mn master alloy, Cu-10%Cr master alloy, Cu-15%P master alloy and Cu-10% Fe master alloy are used as raw materials, and are also melted by composition adjustment while high-frequency melting furnace First, casting was carried out in a test metal mold at both ends of the test and the foundry fracture was evaluated. Next, casting was carried out in a cylindrical metal mold to prepare an ingot having a diameter of 35 mm and a length of 100 mm, and the ingot, the mechanical properties, the corrosion resistance, and the crystallization ratio were measured using the ingot as a sample. f) Display the results of the evaluation in the table below. [Table 1] Μο· Cu Ζη Β ί Pb S 1 Β AIS η Ν i Zinc equivalent mm Cracking machinability mechanical characteristics 1 60.60 38.10 1-0 0 0 0 0 0 0 39.2 X &amp; 2 60.20 37.80 2.0 0 0 0 0 0 0 39.3 X Ο Ο 3 59. eo 37.20 3.0 0 0 0 0 0 0 39.5 X ρ ο 4 61.00 37.00 0 2.0 0 0 0 0 0 39.0 θ ρ ο [Table 2]

Cu 丨Ζη j Βΐ SI BA 1 8n N i Zinc 筲 鋳逭 切削 切削 切削 切削 切削 切削 切削 ΙΚΠϋΙ ΙΚΠϋΙ 00 00 2.00 OLOQ75 2.00 0.05 37.4 κ Ο P ϋ 14 Β3 η 2.6 1.50 i,〇〇TToT 318 6 $ 0 6毒24 ύ 7 25.49 2.0 1.40 αοο?5 1t99 !·拽4αο Ρ 9 9 is 33 S7 8 IIHOl 3),ii 2.0 i,〇〇itW 41.2 $ ψ Ο Islandή 0 37.19 2.0 0.60 aoiso TjiT aol 〇l〇5 42.9 9 φ φ 44 Μ 10 |S5r0Q| ΑΖ.9Ί 2.0 0 άόΜο 0 0.05 rwi 4iS 〇_ι_ _Ω_ 31 ϊ 98 [Table 3]

No. ΤΓ 1Γ 131

Β 1 ΤΓ

Cu ΈΤ00Γ36: 62*00

S 0.S0 0.50 Β 0.S0 0,0050 0.50 ΙΟ,ΙΟΟΟΤ AIS n N 1 Zinc equivalent rupture cutting mechanical properties 0 0.05 0.05 40.4 Ο ρ 0 0.05 0.05 40.4 d _a_ 9 0 0.05 0.05 40.4 θ 0 D. 05 0.05 40.4 ❹ θ Ο SExaEsaEnn β Ο ο 3 X ο -23- 200930822 [Table 4]

No. Cu Zn B i SI Θ At S n N i Zinc | When i 镛 rupture machinability ΤΓ 59.80 39. €0 0.50 0 0 0 0.05 0.05 40.0 X p © IT 59.80 39.60 0.50 0 ΠίΓϊΤΤϊ] Ιι&lt; ·: ΐ ΐ [·! 0 0.05 0.05 40.0 X ο ir 59.80 39.60 0.50 0 0 0.05 0.05 40.0 θ ο &amp; 20 59.80 39.59 0.50 0 0.0075 0 0.05 0.05 40.0 Ο ο ρ 21 59.80 39.59 0.50 0 0.0150 0 0.05 0.05 40.0 e ο &amp; 22 59.90 39.48 0.50 0.02 0 0 0.05 0.05 40.0 X ο &amp; 23 60.10 39.25 0.50 0.05 0 0 O.OS 0.05 40.0 θ ο &amp; 24 «0.40 38.90 6^50 0.10 0 0 0.05 0.05 40.0 ο ο 〇25 € 0.50 38.34 0.S0 0.10 0.0075 0 0.30 0.05 40.0 d ο &amp; 26 €0.50 30.54 0.50 0.10 0.0150 0 0.30 O.OS 40.0 d ο Θ 27 60.90 38.30 0.50 0.20 0 0 0.05 0.05 40.0 d ς&gt; 9 23 60.90 3S.29 0.50 0.20 0.0075 0 0.05 0.05 40.0 θ ο &amp; 29 60.90 38.29 0.50 0.20 0.0150 0 0.0S 0.05 40.0 Q ο 夺 30 61.50 37.60 0.50 0.30 0 0 O.OS 0.05 40.0 p ο 9 31 €1.50 37.59 0.50 0.30 0.0075 0 0.05 40.0 Ο ο θ 32 61.50 37.59 0.50 0.30 άόϊϊ ό 0 0.0S 0.05 40.0 9 ο 33 59.70 39.19 1.00 0 0.0075 0 0-05 a〇5 40.0 X Θ β 34 59.70 39.19 1.00 0 0.0110 0 0.05 0.05 40.0 X d ❾ 35 59.70 39,19 1.00 0 0.0125 0 0.05 a 〇 5 40.0 X φ 36 59.70 39. Id 1.00 0 0.0150 0 0.05 0.05 40.0 Θ θ 37 59.70 39· 18 1.00 0 0.0200 0 0.05 0,05 40.0 p θ θ 38 S9.70 39.17 1.00 0 0.0300 0 0.0S 0.05 40,0 Ο amp &amp; 39 16Ο.ΟΟ 38.85 t.oo 0.05 0 0 0.05 0.05 40.0 X 9 40 60.00 38.83 1.00 0.07 0 0 0.05 0.05 40.1 X φ 〇41 60.30 38.50 1.00 0.10 0 0 0.05 0.05 40.0 &amp; e &amp; 42 60.30 38.49 1.00 0.10 0.0075 0 0.05 0.05 40.0 9 β &amp; 43 60.30 38.49 1.00 0.10 0.015ύ 0 0.05 0.05 40.0 &amp; ❺ ❺ 44 60.80 37.90 1.00 0.20 0 0 0.05 0.05 40.0 e β 45 60. SO 37. of 1.00 0.20 0.0075 0 0.05 O.OS 40.0 ο ❺ Θ 4$ 60.80 37.89 1.00 0.20 0.0150 0 0.05 0.05 40.0 &amp; 47 61.30 ! 37.30 1.00 0.30 0 0 0.05 0.05 40.0 a © Θ

❹ -24- 200930822 [Table 5]

Ho. Cu Zn Β 1 S i Β A 1 S η Ν i Zinc equivalent casting cracking machinability 4B 61.30 37.29 1.00 0.30 0.0075 0 0.05 0.05 40.0 Q Phase capture 61.30 37,29 1.00 0.30 0.0150 0 0.05 0.05 40.0 ❺ &amp; 0 50 59.50 38.39 2,00 0 0.0075 0 0,05 〇,〇5 40.0 X 9 Θ 51 59.50 38.39 2.00 0 0.0150 0 0.(6 0.05 40.0 X 9 〇52 59.50 38.38 2.00 0 0-0200 0 0.05 0.05 40.0 θ 〇53 59.50 38.38 2.00 0 0 0.05 0.05 40.0 〇e ύ 54 59.50 38.37 2.00 0 0 0.05 0.05 40.0 Q p θ 55 60.00 37.8Q 2.00 0.10 0 0 0.05 0.05 40.0 X 9 ρ 56 60.00 37.79 2.00 αιο 0.0075 0 0.05 0.05 40.0 0 θ 57 60.00 37.79 2.00 0.10 0.0150 0 0.05 0.0S 4Q.0 e Capture 58 60.30 37.45 2.00 0.1S 0 0 0.05 0.05 40.0 Capture 59 60.60 37,10 2.00 0.20 0 0 0.05 0.05 40.0 e Θ 60 60.60 37.» 2.00 0.20 0.0075 0 0.05 0.05 40-0 Θ Θ &amp; Sentence 60. SO 37.09 2.00 0.20 0.0150 0 0.05 O.OS 40.0 Q β Q 62 61.10 36.50 2.00 0.30 0 0 0.05 0.05 40.0 Q Θ 9 63 61.10 36.50 2.00 0.30 0.0010 0 0.05 0 .Q5 40.0 Θ Θ 〇64 61.10 36.50 2.00 0.30 0.0020 0 0.05 0.05 40.0 〇〇〇65 61.10 36.50 Ζ.00 0.30 0.0040 0 0.05 0.05 40.0 d 〇 66 61·10 36.49 2.00 0.30 0.0075 0 0.05 0.05 40.0 Q e 67 61.10 36.49 2.00 0.30 0.0150 0 0.05 0.05 40.0 68 61.10 3β.47 2.00 0.30 0.0300 0 0.05 0,05 40.0 Θ Θ ο 69 €2.20 35,20 2.00 0.50 0 0 0.05 0,05 40.0 ί 〇θ &amp; 70 €4.90 &quot;32.00 2.0Q 1.00 0 0 0.05 40.0 〇β &amp; 71 67.60 2B.B0 2.00 1.50 0 0 0.05 0.05 40 Θ 0 72 70.30 25.60 2.00 ΖΟΟ 0 0 0.05 6.05 40.0 〇〇ο 73 59.20 1 37.69 3.00 Ο 0.0075 0 0.05 0.05 40.0 XQ 74 59.20 3.00 0 ΓϊΙΓΤΜιΙ 0 0.05 0.05 40.0 X ❺ θ 75 59.20 3.00 0 0 0.05 0.05 40.0 Φ 〇@ 76 59.20 37.67 3.00 0 0.0300 0 0.05 0.05 40.0 Θ θ 77 59.80 37.00 3.00 0.10 0 0 0.05 0.05 40.0 X -25- 200930822 [Table 6]

Cu Ζπ B i Si BA 1 Sn N i Zinc-making rupture machinability 78 59.80 36.99 3.00 0.10 0.0075 0 0.05 0.05 40.0 9 79 59.8Q 36.99 3.00 0.10 0.0150 0 ~άοΓ 0.05 40.0 夺 9 p 80 60.10 36.65 3.00 0.15 0 0 α坜0.05 40.0 1 Θ 9 ρ 81 60.30 36.40 3.00 &amp;20 0 0 0.05 0.05 40.0 ! θ ❼ 82 towel 11_1丨[.来FI 3.00 0.20 0.0075 0 0.05 0.05 40.0 夺 夺 9 83 3.00 0.20 0.0150 0 0.05 0.05 40.0 e &amp; 〇84 ιπη&gt;ι 35.70 3.00 0.30 0 0 0.05 0.0S 40.0 Q ! &amp; 〇85 ΚΟΙΜ 35.69 100 0.30 0.0075 0 O.QS 0-05 40.0 ❺ pd 86 60.90 35.69 3· 00 0.30 0.0150 0 0.05 0.05 40.0 e 9 87 59.00 36. β9 4.00 0 0.0075 0 0.05 0.05 40.0 X 9 ❶ 88 59.00 36.8S 4.00 0 0.0150 0 0,05 0.05 40.0 X [Θ 89 5». 00 36.88 4.00 0 0.0200 0 0.06 0.05 40.0 &amp;〇ΓΤ&quot; 90 59.00 3β.87 4.00 0 0.0300 0 0.05 0.05 40.0 win 0 91 69.50 36.30 4.00 0.f0 0 0 0.05 a. os 40.0 X φ 9 92 59.50 36.29 4.00 0.10 0.0075 0 a. 〇5 0.05 40.0 Q 〇〇 93 59.50 36.2d 4.00 0.10 0.0150 0 0.05 0.0 5 40.0 0 θ 94 59.80 35.95 4,00 0.15 0 1 0 0.05 0.05 40.0 ❽ θ 〇95 60.10 Fflm 4.00 0.20 ❶ 0 0.05 0.05 40.0 ® θ 〇96 6Q.10 loo 0.20 0.0075 1 0 0.05 0.05 40.0 丨Θ θ 97 60.10 KMm 4.00 0.20 0.0150 0 0.05 0.05 40.0 Θ ❺ 0 98 60.60 n-wn 4.00 0.30 0 ! 0 nor 0.05 40.0 &amp; Θ 99 ί?ί_]ΐ:ί·Ιΐ^)^_ΐ·ΙΙΒΜ1ί·ΐ1ί·【0ΐ·: ·73·!Μϊ1Ιϊ]^ΐρΗΙίΗ1·7Ο 3 9 EED 19 | $ Θ

[Table 7]

No. Cu Zn B i Si 1 BA 1 Sn N i Zinc-making rupture machinability Mechanical properties Tor 65.00 32.57 2.0 0.30 1 0.0300 0 0.05 0.0S 36.2 X 6 Θ mm I·乂101 tx·:·] 33.57 2.0 0.30 0.0300 0 0.05 0.05 37.2 Q &amp; 34. S7 2.0 0.30 0.0300 0 0.05 a 〇5 38.1 ρ Q 0 104 61.00 36.57 2.0 0.30 0.0300 0 0.05 0.05 40.1 ο 105 59.00 38.57 2.0 0.30 0.0300 0 0.05 0.05 42.1 9 &amp; 106 58.00 39.57 2.0 0.30 0.0300 0 0.05 0.05 43.0 Win 0 ο 107 56.00 41.57 2.0 0.30 a〇3〇o 0 0.05 o.os 45.0 &amp; § ο 108 61.50 36.39 2.00 0 0.0075 0 0.05 0.05 38.0 X 0 ❹ 109 61.50 35.39 2.00 0 0.0150 0 0.05 0.05 38.0 X $ 110 61.50 36.38 2.00 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 62.00 3S.80 2.00 0.10 0 0 0.05 0.05 38.0 X θ 9 m 62.00 3 %.79 2.00 0.10 0.0075 0 0.05 D.0S 38.0 &amp; 9 &amp; 115 62.00 35.79 2.00 0.10 0.0150 0 0.05 05 38.0 〇116 62.30 35.45 2.00 0.15 0 0 0.05 0.05 38.0 3 ο 117 62. 35.10 2.00 0.») 0 0 0.05 0.05 38.0 Θ ο 118 62.60 35.09 2.00 0.20 0.0075 0 0.05 0.05 38.0 $ 〇❹ 1t9 62.60 魟铋2.00 0.20 0.0150 0 0.05 0.05 38.0 &amp; 〇Θ 120 57.50 40.39 2.00 D 0.0075 0 0.05 0. 坶 42.0 X 0 d 121 57.50 40.39 2-00 0 a οι io 0 0.05 0.05 42.0 X 〇Ο 122 57.50 40.39 2.00 0 0,0125 0 0,05 0.05 42.0 9 9 123 57.50 40.39 2.00 0 0.0150 0 0.05 0.05 42.0 〇〇ο 124 57.50 40.38 loo 0 0.0200 0 0.05 0.05 42.0 $ θ ο 125 57.50 40.37 2.00 0 0.0300 0 0.05 o.os 42.0 θ 〇ρ 126 I 57.80 IcH 2.00 0.05 0 0 0.05 0.05 42.0 X ο ο 127 57.90 2.00 0.07 0 0 6.05 0.05 42.0 X Ο ο 128 58.00 30.80 2.00 0.10 0 0 0.05 0.05 42.0 ❺ ο e 129 58.00 39.79 2.00 0.10 0.007S 0 0.05 0.05 42.0 〇9 9 130 58.00 1 39.7$ 2.00 0.10 0.0150 0 0.05 42.0 ❹ ο 131 S8.50 39,20 2.00 0.20 0 0 0.05 0.05 42.0 〇ο d -26- [Table 8]

No. C u 2n B i Si BA 1 Sn -. N i Zinc antimony equivalent casting fracture machinability 132 58.50 39.19 2.00 0.20 0.0075 0 0.05 0.05 42.0 Ο ❺ 133 133 134 135 136 AH Z.00 0.20 0.0150 0 0.05 42.0 9 Θ I just 2.00 0 0.0075 0 0.05 0.05 44.0 X Θ 14*1*1 42.39 2.00 0 0.0110 0 a 〇5 0.05 44.0 X θ Q 42.39 2.00 0 0.0125 0 0.05 0.05 44.0 &amp;&amp; 137 55.50 42.39 2.00 0 0.0150 0 0.05 0.05 44.0 ο &amp; 9 138 55.50 42.3S 2.00 0 0.0200 0 0.05 0.05 44.0 9 &amp; β 139 55.50 42.37 2.00 0 0.0300 0 0.05 0.0S 44.0 Ο &amp; 0 140 55.80 4^05 2.00 0.05 0 0 0.05 44.0 X 令 9 141 55.90 41.93 2.00 0.07 0 0 0.05 0.05 44.0 X Θ β 142 56.00 41.60 2.00 α. io 0 0 0-05 0.05 44.0 &amp; ο 143 56.00 41.79 2.00 0.10 0.0075 0 0.05 0.05 44.0 Ο &amp; ά 144 56.00 41.79 2.00 0.10 0.0150 0 0.05 0.05 44.0 Ο Θ ο 145 56. SO 41.20 2.00 0.20 0 0 O.OS 0.05 44.0 &amp;&amp; @ 146 56. SO 41.19 2.00 0.20 t,霣,:〇rH [•除.] 0 0.05 0.05 44.0 Q 6 0 147 56.50 41.19 2.00 0.20 0 0.05 1 0.0S 44.0 Q &amp; ο [Table 9]

Cu Ζη B i 1 S i BA 1 S n N i Zinc when the shovel is broken and machinable mechanical properties W 59.80 3λ 99 I 2.00 0 0.0075 0.10 0.05 0.05 40.0 X ◎ 149 150 2.00 0 IWTRil [* gamma 1 0.10 0.05 a 〇 5 40.0 X © 2.00 0 0.10 0.05 0.05 40.0 ◎ © © W 37.97 2.00 0 0.0300 0.10 0.05 0.05 40.0 ◎ @ © Τ52 ΙίΛΜ 37.40 2.00 0.10 0 0.10 0.05 0.05 40.0 X © @ 153 60.30 37.39 2.00 0.10 0.0075 0.10 0.05 0.05 40.0 @ © ◎ Rain 60.30 37.39 2.00 0.10 0.0150 0.10 0.0S 0.05 40.0 ◎ ◎ 155 60.60 37.05 2· 00 0. (5 0 0.10 0.05 0.05 40.0 ◎ ◎ ◎ Μ 60.90 36.70 zoo 0.20 0 0.10 0.05 0.05 40.0 @ 157 60.90 36.69 2.00 0.20 0.0075 0.10 0.05 0.05 40.0 ◎ ◎ 158 60.90 36.69 2.00 0.20 0.0150 0.10 0.05 0.05 40.0 © 159 61.40 36.10 2.00 0.30 0 0.10 0.05 0.05 40.0 @ @ 160 61.40 36. t0 2.00 0.30 0.0040 0.10 0.05 0·05 40.0 © Θ © 161 61.40 36.09 2.00 0.30 0.0075 0.10 0.05 0.05 40.0 © 162 61.40 36.09 2· 00 0.30 0.0150 0.10 0.0S 0.05 40.0 © @ 163 62.50 34.80 zoo 0.50 0 0.10 0.05 0.05 40.0 3 ◎ 164 65.20 31.60 2.00 1.00 0 0.10 0.05 0.05 40.0 © © 165 67.90 28.40 2,00 1.50 0 0.10 O.OS 0.05 40.0 ◎ © 166 70.60 25.20 2.00 2.00 0 0.10 0.05 O.OS 40.0 φ © o («7 60.40 37.19 2.00 0 0.0075 0,30 0,05 0.05 40.0 X ◎ 168 60.40 37.19 2.00 0 0.0150 0.30 0.05 O.OS 40.0 X © ® 169 60.40 37.18 2.00 0 0.0200 0.30 0.05 0.05 40.0 @ © @ 170 60.40 37.17 2.00 0 0.0300 0.30 0.05 0.05 40.0 © ◎ @ 171 60.90 36.60 2.00 0-10 0 0.30 0.05 0.05 40.0 X © ◎ 172 60.90 36.59 2.00 0.10 0.0075 0.30 O.OS O.OS 40.0 © &amp; 173 60.90 3β. 59 2.00 0.10 0.0150 0.30 0.05 0.05 40.0 © ◎ 174 61.50 35.90 2.00 0.20 0 0.30 0.05 0.05 40. a X ◎ ◎ 175 61.50 35.89 2,00 0.20 0.0075 0.30 0.05 0.05 40.0 @ p ◎ 176 61.50 35. &amp;9 2.00 0.20 0.0t50 0.30 0.05 0.05 40.0 © @ 177 62.00 35.30 2.00 0.30 0 0.30 0.05 0.05 40.0 X © © 17Β 2.00 0.30 RRiRi] 0.30 0-05 0.05 40.0 ◎ I ◎ © 179 卞 · ·]·1·°, 1 2.00 0.30 0.30 0.05 0.05 40.0 ◎ © -27- [ Table 10]

Cu Zn B i si BA 1 Sn N i Zinc-casting rupture machinability mechanical properties 180 62.00 35.29 2.00 0.30 0.007S 0.30 0.05 a. 〇5 40.0 © © ◎ 181 62.00 35.29 2.00 0.30 1&gt;λ»κι»ι·] Mm 甽 甽 UMOH·] Ι·]|·:.Ν*] Ι«ν*Ιι!ί)1 mm [·Μ»ΙΟΜ nw*rwii mm 0.30 0.05 0.05 40.0 © ◎ 182 62. οα 35.27 2.00 0.30 0.30 0.05 0.05 40.0 © © 183 63.10 34.00 2.00 0.50 0.30 0.05 0.05 40.0 X © ◎ 184 63.10 34.00 2.00 0.50 0.30 0.05 0.05 40.0 © ◎ 185 63.10 34.00 2.00 0.50 0.30 0.05 0.05 40.0 © © ◎ 1B6 63.10 34.00 Too&quot; 0.50 0.30 0.05 0.05 40.0 @ © ◎ 187 63.10 34.00 2.00 0.50 0.30 0.05 0.05 40.0 © © ◎ 188 65.80 30.80 2.00 1.00 0.30 0.05 0.05 40.0 X © ◎ 189 65.80 30.80 2.00 1.00 0.30 0.05 0.05 40.0 © ◎ ◎ 190 65. BO 30.80 2.00 1.00 0.30 0.05 40.0 ◎ © 191 65.80 30.80 2.00 1.00 0.30 0.05 0.05 40.0 © © 192 68.50 27.60 2.00 1.50 0.30 0.05 0.05 40.0 X ◎ 193 68.50 27.60 2.00 1.50 IOIiIiH·】 wmm IOIiWW ϊϊΜϋίΓΓϋ [WKHIt ] 0.30 0.05 0.D5 40.0 @ © ◎ 194 68.50 27.60 2.00 K50 0.30 0.05 0.05 40.0 ◎ ◎ © 195 71.20 U.AO too 2.00 0.30 0.05 0.05 40.0 X 〇196 71.20 24.40 2.00 2.00 0.30 0.05 0.05 40.0 X © 〇197 71.20 24.40 2.00 2.00 0.30 0.05 0.05 40.0 X ◎ 〇198 71.20 24.40 ZOO 2.00 0.30 0.05 0.05 40.0 @ ◎ 〇199 62.50 34.39 2.00 0 1.00 0.05 0.05 40.0 X © @ 200 62.50 34.39 2.00 0 1.00 0.05 0.05 40.0 X 丨◎ 201 62.50 34.38 2.00 0 1.00 0.05 0.05 40.0 X ◎ 丨 ◎ 202 S2.50 34.37 2.00 0 1,00 0.05 0.05 40.0 X ◎ 203 63.00 33.80 2.00 0.10 mm l··“丨I buckle 1 Μ·side Ε· t_) niorPi mm 1·Λ_] ΙΛΊίΜ ΓϊΙϊΤΡϊϊΙ ΜΙ·7_ΙΝ 1.00 0.05 ! 0.05 40.0 X ◎ ◎ 204 63.00 33.79 2.00 0.10 1.00 0.05 0.05 40.0 © © 205 63.00 3.00 0.10 1.00 0.05 0.05 40.0 © ◎ 206 63.60 3110 2.00 0.20 ! 1.00 0.05 0.05 40.0 X © ◎ 207 63.60 33.09 2.00 0.20 1.00 0.05 0.05 40.0 © ◎ © 208 63.60 33.09 2.00 0.20 1.00 0.05 0.D5 40.0 ◎ 209 64.10 3Z50 2.00 0.30 1.00 0.05 0.05 40.0 X © ◎ 210 64.10 32.50 2.00 0.30 1.00 0.05 0.05 40.0 X © 211 64.10 32.49 2.00 0.30 1.00 0.05 0.05 40·0 ◎ ◎ ◎ 212 213 嗣32.49 2.00 0.30 1.00 0.05 0.05 40.0 @ ◎ 31.20 ί 2.00 0.50 1.00 0.05 0.05 40.0 X ◎ ◎ [Table 11]

No. Cu Zn B i S i BAIS n N 1 Zinc-casting rupture cutting property 214 65.20 31.20 200 0.50 0.0020 1.00 0.05 0.05 40.0 X @ ◎ 215 65.20 31.20 2.00 0.50 0.0040 1.0D 0.05 0.05 40.0 @ © © 216 67.90 28.00 2.00 1.00 0 1.00 0.05 0.05 40.0 X © ◎ 217 67.90 28.00 2.00 1.00 0.0005 1,00 0.05 0.05 40.0 ◎ © 218 67.90 28.00 100 1.00 0.0010 1.00 0.05 0.05 40.0 ◎ © ◎ 219 67.90 28.00 2.00 1.00 0.0020 1.00 0.05 0.05 40.0 © © 220 67.90 28.00 2.00 1.00 0.0040 1.00 0.05 0.05 40.0 ◎ ◎ © m 70.50 24.80 2.00 1.50 0.0005 1.00 0.05 0.05 40.0 X ◎ @ 222 70.60 24.80 zoo 1.50 Q.0010 1.00 0.05 0.05 40.0 © © @ 223 70.60 24.80 2.00 1.50 0.0020 1.00 0.05 0.05 40.0 © © @ 224 73.30 21.60 zoo 2.00 0.0005 1.00 0.05 0.05 40.0 X © 〇225 73.20 21.60 zoo 2.00 0.0010 1.00 0.05 0.05 40.0 © 〇226 73.30 21.60 2.00 2.00 0.6020 1.00 0.05 0.05 40.0 ◎ 〇227 63.50 32.57 2.00 ; 0. 30 il · 跃OCUIH l··氺 "I·] 1.50 0.05 0.05 41.9 @ © © 228 65.00 30.57 2.00 ! 0. 30 1 2.00 0.05 0.05 ; 41.9 © © 〇 -28- 200930822 [Table 12]

Cu 2η Β 1 Si Β A 1 Sn N j Zinc; Equivalent rupture and machinability Mechanical properties 229 59,50 3β.34 2.001 0 0.0075 0 0.10 0.05 40.0 X ◎ ◎ 230 231 Ι4·Ι(^Ι 38.34 100 0 Γιϊ· Ϊ́ί.1»1 0 0.10 0.05 40.0 X ◎ β 38.33 2.00 0 0 0.10 0.05 40,0 X © 232 59.50 38.32 2.00 0 0.0300 0 0.10 0.05 40.0 ; ◎ © @ 233 60.10 37.65 2.00 0.10 0 0 0.10 0.05 40.0 X Item} @ 234 60.10 37.65 2.00 0.10 0.0040 0 0.10 0.05 40.0 X ◎ © 235 60.10 37.64 2.00 0.10 0.0075 0 0.10 0.05 40.0 © @ 236 60.10 37.64 2.00 0.10 0.0150 0 0.10 0.05 40.0 © @ ◎ 237 60.60 37.05 2.00 0.20 0 0 0.10 0.05 40.0 X © © 238 Ιδίό1 37.05 2.00 0.20 0.0020 0 0.10 0.05 40.0 © @ 239 60.60 37.05 ZOO 0.20 0.0040 0 0.10 0.05 40.0 ◎ © 240 60.60 37.04 2.00 0.20 0.0075 0 0.10 0.05 40.0 © 241 61.10 36.45 100 0.30 0 0 0.10 0.05 40.0 X © 242 61.10 36.45 2.00 0.30 0.0020 0 0.10 0.05 40.0 @ © @ 243 61.10 36.45 2.00 0.30 0.0040 0 0.10 0.05 40.0 @ @ ◎ 244 61.10 36.44 2.00 0.30 0.0075 0 0.10 0.05 40.0 @ ρ ◎ 245 62.20 35.15 2.00 0.50 0 0 0.10 0.05 40.0 ◎ © 246 62.20 35.15 2.00 0.50 0.0005 0 0.10 0.05 40.0 ◎ © 247 62.20 35.15 2.00 0.50 0.0010 0 0.10 0.05 40.0 ◎ © ◎ 248 62.20 35.15 2.00 0.50 Q.0020 0 0.10 0.05 40 , 0 © © 249 64.90 31.95 2.00 1.00 ^~τ~ 0 0.10 0.05 40.0 © @ © 2S0 64.90 31.95 2.00 1.00 0.0005 0 0.10 0.05 40.0 © @ ◎ 251 64.90 31.95 2.00 1.00 0.0010 0 0J0 0.05 40.0 © ◎ © 252 67.60 28.75 2.00 1.50 0 0 0.10 0.05 40.0 ◎ © @ 253 ¢7.60 28.75 2.00 1.50 0.0005 0 0.10 0.05 40.0 © @ ◎ 254 67.60 28.75 2.00 1.50 0.0010 0 0.10 0.05 40.0 © @ ◎ 255 70.30 25.55 2.00 2.00 0 0 0J0 0.05 40.0 © ◎ 〇256 59.60 38.04 2.00 0 0.0075 0 0.30 0.05 40.0 X &lt; φ © 坜7 S9.60 FH«I1 2.00 0 0.0150 0 0.30 0.05 40.0 X ◎ ◎ 258 59.60 Rrnrwi 2.00 0 0.0200 0 0.30 0.05 40.0 X @ ◎ 259 Ι^'Χίί ·! 2.00 0 0.0300 0 0.30 0.05 40.0 ◎ ◎ ◎ 260 ΕΤΐΚϋ 100 Ο.ίΟ 0 0 0.30 0.05 40.0 X ί ◎ ◎

❹ -29- m i3]

Ko. Cu Zn B i Si BA 1 Sn N i Zinc equivalent casting fracture mechanical properties 2§Γ 60.20 37.34 2.00 0.10 0.0075 0 0.30 0.05 40.0 X © © 262 60.20 37.34 2.00 0.10 0.0150 0 0.30 0.05 40.0 @ ◎ © 263 60.70 36.75 2.00 0.20 0 0 0.30 0.05 40.0 X ◎ 264 60.70 36.75 2.00 0.20 0.0040 0 0.30 0.05 40.0 X @ ρ 265 60.70 36.74 2.00 0.20 0.0075 0 0.30 0.05 40.0 @ © ◎ 266 61.20 36.15 2.00 0.30 0 0 0.30 0.05 40.0 X © ◎ 267 6Κ30 36.05 2.00 0.30 0.0020 0 0.30 0.05 40.0 ◎ ◎ ◎ 268 61.30 36.05 2.00 0.30 0.0040 0 0.30 0.05 40.0 p ◎ © 269 61.30 36.04 2.00 0.30 0.0075 0 0.30 0·坜40,0 @ © ◎ 270 62.30 34.85 2.00 0.50 0 0 0.30 0.05 40.0 X © ◎ 271 €2.30 34.85 2.00 0.50 0.0005 0 0.30 0.05 40.0 。 © © 272 62.30 34. B5 2.00 0.50 0.0010 0 0.30 0.05 40.0 © 273 62.30 34.85 2.00 0.50 0.0020 0 0.30 0.05 40.0 Θ 274 65.(10) 31.昉2.00 1.00 0 0 0.30 0.05 40.0 X @ ◎ 275 65.00 31.65 2.00 1.00 0.0005 0 0.30 0.05 40.0 ◎ @ © 276 65.00 31.65 2.00 1.00 0.0010 0 0.30 0 .05 40.0 © © 277 67.70 28.45 2.00 1.50 0 0 0.30 0.06 40.0 © 278 €7.70 28.45 2.00 1.50 0.0005 0 0.30 0.05 40.0 @ ◎ 279 67.70 28.45 2.00 1.50 0.0010 0 0.30 0.05 40.0 © @ ◎ 280 70.40 25,25 2.00 2.00 0 0 0.30 0.05 40.0 X 〇281 70.40 25.25 2.00 2.00 0.0005 0 0.30 0.05 40.0 X ◎ 〇282 70.40 25.25 2.00 too 0.0010 0 0.30 0.05 40.0 @ ◎ 〇283 60.40 36.04 2.00 0 0.0075 0 1,50 0.05 40.0 X @ ◎ 284 60.40 36.04 2.00 0 0.0150 0 1.50 0.05 40.0 X ◎ © 285 60.40 36.03 2.00 0 0.0200 0 1.50 0.05 40.0 X 286 60.40 36.02 2.00 a 0.0300 0 1.50 0.05 40.0 ◎ © 287 60.90 35.45 2.00 0.10 0 0 1.50 0.05 40.0 X © ◎ 28S 60.90 35.44 2.00 0.10 0,0075 0 1.50 0.05 40.0 X ◎ 289 60.90 35.44 2.00 o.to 0.0150 0 1.50 0.05 40.0, X ◎ © 290 60.90 35.43 2.00 0.10 0.0250 0 1.50 0.05 40.0 X ◎ ◎ 291 60.90 35.42 2.00 0.10 0.0300 0 1.50 0.05 40.0 ◎ ◎ ◎ 292 6Ϊ.40 34.85 100 0.20 0 0 1.50 0.05 4Q.0 X © ◎ 293 , 61.40 34.84 2.00 0,20 ην»ϊίΐιΐ 0 t.50 0.05 40.0 X ◎ 294 I 61.40 34.84 2.00 0.20 0 1.50 0.05 40.0 X ◎ @ -30- 200930822 [Table 14]

Cu 2n B i Si θ A 1 Sn N i Zinc when casting rupture machinability 295 61.40 34.83 2.00 0.20 0.0250 0 1.50 0.05 40.0 ◎ ◎ 296 62.00 34.15 2.00 0.30 0 0 1.50 0.05 40.0 X © © 297 62.00 34.15 2.00 0.30 0.0040 0 1.S0 0.05 40.0 X ◎ ◎ 298 62.00 34.14 2.00 0.30 0.0075 0 1.50 0.05 40.0 @ @ ; ◎ 299 62.00 34.12 2.00 0.30 0.0300 0 t.50 0.05 40.0 ◎ ❽1 〇300 63.00 32.95 2.00 0.50 0.0010 0 1.50 0.05 40.0 X @ 301 63.00 32.95 2.00 0.50 0.0020 0 1.50 0.05 40.0 X ◎ 3021 63.00 32.95 Too1 0.50 0.0040 0 1.50 0.05 4D.0 X 303 63.00 32.94 2.00 0.50 0.0075 0 1.50 0.05 40.0 @ © @ 304 65.70 29.75 2.00 1.00 0.000S 0 1.50 0.05 40.0 X 〇〇305 65.70 29.75 2.00 1.00 0.0010 0 1.50 0.06 40.0 X 〇〇306 65.70 29.75 2.00 1.00 0.0020 0 1.50 0.05 40.0 X 〇〇307 65.70 29.75 2.00 1,00 0.0040 0 1.50 0.05 40.0 X 〇〇308 65.70 29.74 100 1.00 Q.0075 0 1.50 d〇5 40.0 X 〇〇309 65.70 29.74 2.00 1.00 0.0Ϊ50 0 1.50 0.05 40.0 ◎ 〇〇310 68.40 26.55 2.W) 1. 50 0 0 1.50 0.05 40.0 X 〇〇311 68.40 26.55 2.00 1.50 0.0005 0 1.50 0.05 40.0 X 〇〇312 68.40 2G.55 2.00 1.50 0.0010 0 1.50 0.05 40.0 X 〇〇313 68.40 26.55 2.00 1.50 0.0040 α 1.50 0.05 40.0 X 〇〇 314 68.40 26.54 2.00 1.50 0.0075 0 1.50 0.05 40.0 X 〇〇315 68.40 26.54 2.00 t.50 0.0150 0 1.50 0.05 40.0 X 〇〇316 68.40 26.52 2.00 1.50 0.0300 0 t.50 0.05 40.0 X 〇〇317 71.10 23.35 2.00 2.00 0 0 1.50 0.05 40.0 X 〇〇31d 71.10 23.35 2,00 2.00 0.0005 0 1.50 0.05 40.0 X 〇〇31d 71.10 23.35 2.00 2.00 0.0010 0 1.50 0.05 40.0 X 〇〇320 71.10 23.35 2.00 2.00 0.0040 0 1.50 0.05 40.0 X 〇〇321 71.10 23.34 2.00 2.00 0.0075 0 1.50 0.05 40.0 X 〇〇322 71.10 23.34 2.00 2.00 0.0150 0 1.50 0.05 40.0 X 〇〇323 71.10 23.32 2. 00 2.00 0.0300 0 1.50 0.05 40.0 X 〇〇324 2.00 ESEIEXSE] ΚκΜμι Marriage 0.30 2.00 0 41.2 © ◎ 〇325 2.00 0.30 3.00 ! 0 Gift 7 © 〇〇200930822 [Table 15]

No. Cu 2n B i Si B Al Sn N \ Zinc when casting rupture machinability 326 59.40 38.44 2.00 0 0.0075 0 0.05 0.10 40.0 X ◎ 327 5d.40 38.44 2.00 0 0.0150 0 0.05 0.10 40.0 X ◎ © 328 59.40 38.42 2.00 0 0.0300 0 0.05 0.10 40.0 X © © 329 60.00 37.75 2.00 0.10 0 0 0.05 0.10 40.0 X © © 33? 60.00 37.75 2.00 0.10 0.0040 0 0.05 0.10 40.0 @ © © 331 332 ΕΪΕΙΙΣΕΙ t^StWfKn 2.00 0.10 0.0075 0 0.05 0.10 40.0 ◎ @ 2.00 0.10 0.0150 0 0.05 0.10 40.0 © © 333 60.50 37· 15 2.00 0.20 0 0 0.05 0.10 40.0 X © © 334 60.50 37.14 2.00 0.20 0.0075 0 0.05 0.10 40.0 © © ◎ 335 60. SO 37.14 2.00 0.20 0.0150 0 0.05 0.10 40.0 @ 336 61.00 36.55 2.0D 0.30 0 0 0.05 0.10 40.0 X ◎ ◎ 337 61.0D 36.55 2.00 0.30 0.0020 0 0.05 0.10 40.0 ◎ 338 61.00 36.55 2.00 0.30 0.0040 0 0.05 0.10 40.0 ◎ ◎ 339 61.00 36.54 2.00 0.30 0.0075 0 0.05 0.10 40.0 © © 340 6t.0Q 36.54 2.00 0.30 0.0150 0 0.05 0-10 40.0 ◎ ◎ 34t 62.10 35.25 2.00 0.50 0 0 0.05 0.10 40.0 X © 34 2 62.10 35.25 2.00 0.50 0.0005 0 0.05 0.10 40.0 ◎ © 343 62.10 35.25 2.00 D.50 0.0010 0 0.05 0.10 40.0 ◎ © © 344 62.10 35.25 2.00 0.50 0.0020 0 0.05 0.10 40.0 © © 345 64.80 32.05 2.00 1.00 0 0 0.05 0.10 40.0 ◎ © ◎ 346 64.80 32.05 2:00 1.00 0.0005 0 0.05 0.10 40.0 ◎ @ @ 347 67.50 28.85 2.00 1.50 0 0 0.05 0.10 40.0 ◎ © 348 67.50 28.85 2.00 1.50 0.0005 0 0.05 0.10 40.0 @ ◎ 70.20 25.65 ZOO 2.00 0 0 0.05 0.10 40.0 ◎ 〇◎ 59.10 38. B4 2.00 0 0.0075 0 0.05 0.30 40.0 X © Ι Ι1Ι·Ι 38.54 2.00 0 0.0150 0 0.05 D.30 40.0 X @ 鼸38.53 2.00 0 0.0200 0 0.05 0.30 40.0 X ◎ ◎ 59.10 38.52 2.00 0 0.0300 0 0.05 0.30 40.0 X © © 354 59.70 37. 85 2.00 0.10 0 0 0.05 0.30 40.0 X © © 355 59.70 37.84 2.00 0.10 0.0075 0 0.05 0.30 40.0 X © ◎ 356 S9.70 37.84 2.00 0.10 0.0150 0 0.05 0.30 40.0 X © ◎ 357 59· 70 37.83 2.00 o.to 0.0200 0 0.05 0.30 40.0 © © 358 59.70 37.82 2.00 0.10 0.0300 0 0.05 0.30 40.0 @ ©

❹ -32- [Table 16]

No. Cu 2n B 1 Si BA 1 S n N i Zinc-casting rupture machinability 359 60.20 37.25 2.00 0.20 0 0 0.05 0.30 40.0 X ◎ 360 60.20 37.24 2.00 0.20 HOW k·Jia 0 0.05 0.30 40.0 © © w 60.20 37.24 2.00 0.20 0 0.05 0.30 40.0 © © ◎ 3S2 60.20 37.23 2.00 0.20 0.0200 0 0.05 0.30 40.0 @ ◎ 363 60.20 37.23 2.00 0.20 0.0250 0 0.05 0.30 40.0 ◎ ◎ 364 60.20 37.22 2.00 0.20 0.0300 0 0.05 0.30 40.0 ◎ ! © 365 60. SO 36.55 2.00 0.30 0 0 0.05 0.30 40.0 X ◎ ◎ 366 60.80 36.55 2.00 0.30 0.0020 0 0.05 0.30 40.0 © ◎ ί 367 60.80 36.55 100 0.30 0.0040 0 0.05 0.30 40.0 @ © © 3es 60.80 36.54 2.00 0.30 0.0075 0 0.05 0.30 40.0 © @ 369 60.80 36.54 2.00 0.30 0.0150 0 0.05 0.30 40.0 © © 370 60.80 36.52 2.00 0.30 0.0300 0 0.05 0.30 40.0 © © 371 6K80 35.35 2.00 0.50 0 0 0.05 0.30 40.0 X ◎ ◎ 372 61.80 35.3S 2.00 0.50 0.0005 0 0.05 0.30 40.0 @ ◎ 373 61.fi0 35.35 2.00 0.50 O.OOfO 0 0.05 0.30 40.0 ◎ ◎ 374 61.80 35.35 2.00 0.50 0.0020 0 0.05 0.30 40.0 ◎ @ © 375 64. SO 32.15 2.00 1.00 0 0 0.05 0.30 40.0 © ◎ 376 64.50 32.15 2.00 1.00 0.0005 0 0.05 0.30 40.0 ◎ @ 377 64.50 32.15 2.00 i.oa o.ooTo 0 O.OS 0.30 40.0 ◎ @ © 378 67.20 28.95 2.00 1.50 0 0 0.05 0.30 40.0 ◎ 379 67.20 28.95 too 1.50 0.0005 0 0.05 0.30 40.0 © @ @ 380 67.20 28.95 2.00 1.50 0.0010 0 0.05 0.30 40.0 © © ◎ 381 69.90 25,75 2.00 2.00 0 0 0.05 0.30 40.0 X 0 © 382 69.90 25.75 2.00 2.00 0.0005 0 0.05 0.30 40.0 X 〇◎ 383 69.90 25.75 2.00 2.00 0.0010 0 a 05 0.30 40.0 X 〇ρ 384 69.90 25.75 2.00 2.00 0.0020 0 0,05 0.30 40.0 ◎ 〇◎ 385 58.20 3B. 74 2.00 a 0.0075 0 0.05 1.00 40.0 X ◎ © 386 58.20 38.74 2.00 I 0 0.0150 0 0.05 1.00 40· 0 X ◎ 387 58.20 38.72 2.00 0 0.0300 0 0.05 1.00 40.0 X © ◎ 3Bd 58.70 38.15 2.00 0.10 0 0 0.05 1.00 40.0 X © @ 369 58.70 38.14 100 0.10 0.0075 0 0.05 1.00 40.0 X ◎ ◎ 390 58.70 38.14 100 0.10 0.0150 0 0.05 1.00 40.0 X &amp; ◎ 391 58.70 38.13 2.0D 0.10 0.0200 0 0.05 1.00 40.0 X ◎ ◎ 392 58.70 38.12 2.00 0.10 0.0300 0 0.05 1.00 40.0 © ◎ 393 59.25 37.50 2.00 0.20 0 0 0.05 1.00 40.0 X © 394 59.25 37.49 2.00 0.20 0.0075 0 a. 05 1.00 40.0 X @ 395 59.25 37.49 100 0.20 0 a. os t. Oo 40.0 X ◎ ! © 39$ !59.25 37.48 2.00 0.20 0 0.05 K00 40.0 X ◎ i © -33- 200930822 [Table 7]

Cu 2n B i si BAIS n N i Zinc equivalent i mm Rupture machinability mechanical surface ED 59.25 37.48 2.00 0.20 0.0250 0 0.05 1 00 40.0 ύ © 59.25 37.47 2.00 0.20 0.0300 0 0.05 1.00 40.0 p © ΕΞ fFP] 59.80 36.85 2.00 0.30 0 〇0.05 1 00 40.0 X © , @ 59.80 36. 84 2.00 0.30 0.0075 0 0.05 1.00 40.0 X © ΕΙΏ 59.80 36.84 2.00 0.30 0.0150 0 0.05 1.00 40.0 X ◎ © ca 59.80 36.83 2.00 0.30 0.0200 0 0.05 1.00 40.0 φ @ cna 59 ΘΟ 36.83 2.00 0.30 0.0250 0 0.05 1 00 40.0 @ ◎ 59. SO 36.82 2.00 0.30 0.0300 0 0.05 1 00 40.0 Credit © © ESS 60.90 35.55 2.00 0.50 0.0040 0 0.05 1 00 40.0 X ◎ 60.90 35.54 2.00 0.50 0.0075 0 0.05 1 00 40.0 X © ◎ ΕΙΏ 60.90 35.54 2.00 0.50 0.0150 0 0.05 1.00 40.0 X ◎ © EM:I 60.90 35.53 2.00 0.50 0.0200 0 0.05 1.00 40.0 © @ © m BE 63.60 32.35 2.00 1.00 0.0010 0 0.05 1. 00 40.0 X © ◎ 63.60 32.35 2.00 i.oa 0.0020 0 0.05 1.00 40.0 X © ◎ 411 63.60 32.35 2.00 1.00 0.0040 0 0.05 1. 00 40.0 © @ ◎ AM 63.60 32.34 2.00 1.00 0.0075 0 0.05 1.00 40.0 ◎ ◎ 413 66.30 29.15 2.00 1.50 0.0010 0 0.05 1.00 40.0 X ◎ ◎ 414 66.30 29.15 2.00 1.50 0.0020 0 0·诋a 00 I 40.0 X © © 4t5 66.30 29· 15 2.00 1.50 0.0040 a 0.05 1.00 40.0 X 1 © © 416 66.30 29.14 2.00 1.60 0.0075 0 0.05 ί.00 40.0 X ◎ ◎ 417 66.30 29.14 2.00 1.50 0.0150 0 0.05 1.00 40.0 © 1 © © 418 69,00 25· 95 2.00 2.00 0.0005 0 0.05 1.00 40.0 X 〇◎ 419 69.00 25.95 2.00 2.00 0.0010 0 0.05 ΓΣ ΟΟΊ 40.0 X 1 〇 ◎ 420 69.00 25.95 2.00 2.00 0.0020 0 0.05 ;1.001 40.0 X 〇421 69.00 25.94 ZOO 2.00 0.0075 0 0.05 [I 00 40.0 X 1 〇◎ 422 69.00 25.94 2.00 2.00 0.0150 0 0.05 [T ^5~ 40.0 © 〇423 PrKTil ΙΊ#Μ 38.82 2.00 0.30 o. 0300 0 0.05 I 1.50 I 41.8 ◎ ◎ ◎ 424 38.92 ZOO 0.30 0.0300 0 0.05 a MJ 4T.8 ◎ 1 ◎ 〇

m is] μη C a IZ n B t Si BA 1 Sn N i F· P Kn P b Zinc equivalent casting cracking machine « ηη. fit.00 38.3&amp; 2.0 0.20 O.OOGO 0.15 0.05 0.05 0 0 0.20 0 40, p i&gt; 9 Φ E1E1 2.0 0.20 0.0050 0.15 o.os ΌΓ 0 0 0.30 0 39.9 9 ο 2.0 0.60 0.0010 Q.SS O.OS 0.05 0 0 0.20 0 40.0 ό e &quot;42Γ 63.70 32.9S Following 0.0010 0.35 0.05 0. Station 0 0 0.30 0 40.0 X ό 429 5S.20 29.70 ^.0 0.0015 ι,ρο 0.05 O.OS 0 0 0.30 0 40.0 X 9 ο &quot;430Ί S6.20 Ά. 60 IP oM O.OOT5 1.00 0.05 A〇5 0 0 0.4D 0 39.9 X 0 -Ο- nr 67.20 28.50 2.0 ar9〇0.0015 1.00 0.05 0.D5 0 0 0,30 0 40.0 Ο Ο W »7.20 28.40 2.0 0.90 0.0015 1.00 0.05 0.05 0 0 0.40 9 40, p Ο φ ο IS- (6.60 29.19 1.5 1.50 0.0075 6.10 0.05 0.05 0 0 1.00 0 41.0 9 ο 1 ς Τ5Γ $6.30 214Ϊ %5 i.io 0.007S ΤΤΓ 0.05 0.05 0 0 2.00 〇«1.0 ρ 〇ο EM wmi 1.S I. so 0.007S 0.10 0.05 0.05 0 0 3.00 〇! 4t.0 ρ ο 〇1.S 1.50 0.0075 0.10 0.05 0.05 0 0 4.00 0 ' 41.0 〇Ls_ ο -34- 200930822 [Table 19]

❹ [Table 20] ❹ 161001 lei.SOi

1 62.00J 36J#

2, CO

[Sn I N I I i T 5〇 n~ 〇5 I 8b

Pb 欢 鼸 .70 L» L20

3S.$S 36.lt is^y ΙΠΓ t.25 _L50 Ϊ.25 0,35 035 00075 cai? Ejtumaoa catuzanAJw^ioa ΕΏί·ϋΙ^ΙΜΑ^·ΙΙ-^Ε^Ι_ pjiiaEii^iKEiiaaiHEaa_ traiiKviEazi|^a ^Q|CE5stxn D3i9E3E3EZl^MBQ^^SOS· [51 mi υ·ϊϋ Em it .- [Table 21]

Cu oaoaoaoai-o··——e—psheoe· n^EsaoEMiiQioEmMaimacHKHKEOKK ΜΏί·1ΒΒ^||^3Β$3Ι ΙΚ·Μ KiJKtI 03 10.0078 0,30 0.30 0.30 4ft» 40.9 o 0.15 0.2S &quot;els Os 〇'》 0.05 0.05

O.OS

T« OiOS 0.05

0.05 T〇f Tw ToT 0.0S oor 40.7 0.P2

¥U lay &lt;0.7 15T 40.1 1ST a o 3r 31 o 〇r &quot;g&quot; Ϊ

Mn C

Sb Pb Ε3Ε1ί3ΒΜ1Κ]^·α^Η^ΗΡΕΐυΕΕ1ΙΡΕ1ΕΕ3 ^lll^l^lJK19Cia[iX^KSLJE13EX3iEX^ crag]^ji^trigHRM^^rnr^〇aiEr^giT^ir_ir^nmrnnr^ ΡιΊΕΙΕϋϋΐπ ΙΠΙ^ΙΤΤΊ FTT^[Yes· Nrai gT'Tl FTI··»ΓΤίΙ ΡϋίίϋιΙιΙί^ΙΐΜΪ^ΚίΑίΡΙΒ^ΐΏόΚΙΚΑ^ΜΤ^-ΜίΓίΓΤϋ^υΐιΐίΙιΐιΙ1!1^! ου ir^i eiii mM eei ckj κ;πι oa eei ίΕ3 Elga 031^1 ESa Wka K Ί 】 ΓΤ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^| [:·Ίΐ:η·?*υ»¥:.ΐΓΓ&lt;Γ.τ.^π·, ι^.·Γ^ιπ^·Γττ·ηΓΤ·ίΕΐιιΖ3Κ3^ EiEOigciBEigiFiinTMnaEcagT^wi^oiJM^vT^ODacEi E^ia^lfrfelWFniO^lPUfi)·骨ί·_·»1[.··ι 霣iV)|g?y?l·丨π··υ_η:·1 [3CgiiJE:&lt;aijn.imnriTrMu.)^ iKir'^_〇iLjr]acCT.;tg-i CIIEOEilZigl^irmEEiaglUglBlEaiinnEJOillClga E3 οκι pjZjanEiEnranrirnTOngy^gi^ Eiii oaioaoEa ΓΕ3 only ^ΕΚΙ^^^ΠΓ^ΠΓ^ΟΙίΙΟ^ΓΤΐΙΙ^ ΤΤ^ΙΜΓΤΜυ.ίΙι:] ί〇] hmu i^oi kif3 γτ^ττί Frymr· 0:11 E!&3 ·*τι· l: '· ml FTTl F 逦·: ί:.丨FED Etl mf ΙΠΓ ··ΓΤ71 l·! .i .[j mi Β·Ί#ν;1&gt;^^ΐΜ1ί^ΤΤτί^η»:ιΐΡ!·ιΕ^ί*&gt;(Ί-ΐΓΠ^^&gt;^&gt;νΜί&gt ;ΜΤιΒ&gt;ί'ΊιΐίΠ7Γ^ίι^ιΐί

ICL0Q20I LOOS CoS'

DE2I [®23 HU aos Ά- 0.1 ROS aS! 0.05 otoi ¢. QlOI 0. CL0T~sr

M 4〇r 40.8 40. a 4tt5 40.5

40.B 41.2 41.2 41.3⁄4 41.2 Machine s

40. S

40.S 4〇ue 41.? 41.2 .2 m o o o o o ft o ft o 〇

O 〇 e o o ❼ o

Q e o

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D -35· 200930822 m 22]

No. Γ1Γ zn B ϊ SI Β A 1 $ η N i F· P Μ π [Ej Sb j Zinc when ft 9jnm &quot;49Γ Ui.io 36.44 JJT 0.35 0.0075 0.30 (LOS a〇5 0 0 ~ΤΊ mtm « msm EEl wjem Esn csn EK9 13⁄43⁄4 KDca ixa EXH ντη 40.9 ά -jsr 3S: 49« isr 言 ΊΒΓ &50&gt; 50» ί S10 jiL # 51畜οκά CK] ΓΟΕΆ K^rm Era KKJ mca EEK3 KiS3 D3K1 3S. M TIT 0.3$ 0.0075 0.20 ΚΕΛ HK1 0*3 WSlE no E3 Kl¥3 EX3 KiX3 EK3 inra V^lt^ki oa BEEl EXZ1 lilffl EDEK1 rf^l 0^1 gT!-l KX!ll KX3 0^1 EK3 cxa Aos 0 0 &quot;fH 40.备_δ- 3S.59, 1,2S_ 0.3S 0.0075 0.20 0.0^ 0 0 〇1 0 4|.2 This 3B.191 Step D.C07S 0.10 9.05 0 fi ΖΣΖ 6 41? -4- 32.34 1,5? 0.0075 1.00 0.05 0 0 ζ±ζ i 40.0 JL·- ;%$4 t.70 0.3S 0,007$ 2.00 ao$ 0 0 0 0 Φ If: Rm u? 0,35 0.001⁄2 3.00 0.05 0 0 0&quot; QT〇T 9 9 20.3^ 0.35 0.0300 WEimKJM 0 0 0 a 4gtp 0 9 2€·η 1.70 夂0300 ?r〇5 0 0 0 0 40r0 o 19.39 1.70 9,0150 4.00J £〇S 0 0 ρ ό 4p, 〇ό }lr}} 1.2S 0.0015 ΤΐΓ 0.50 0.01 TW 0.00S 0.0026 αοοβ 4o. d 4 1.2S 1.00 Οόΐ? Ύ1Γ\ 1.00 0.01 0.005 0.00$ ♦•0025 ό,ύάβ 46J δ 5 ikz4 lT 2$ 0,00 沾1.00 0.50 0.01 aoos ΌΚ&quot; ύ.0025 pB^ ^io LiHJ KOCH R^tn LtAU WLim mm imi K*a tsca KiM^M Kldl 26.09 iU ιτ6〇0.0015 1.25 a5Q o.ot 0.00$ αοδΤ 〇5S aoos 42.6 9 0 TOT 12f 1.90 o.ooi6 1.50 0.50 0.01 aoos 0.00$ α〇029 o.oos 43.1 Ten IST^ v8 ^7?&quot; 0.6015 1.50 0:70 0.03 &amp;.01 0.01 0.005 o.6i 41fo ο ο 24. B3 1t3〇0.00IS 1.50 0.7C 0.03 0.03 0.03 0.03 0.0! Τ?Γ ΓΙΤλΙΚΪΊ· KU ra Κπα KTO 6 i 2ft. S3 ila 1,00 O.OOIS !.00 0.70 exh IX·Siam! DLilJl't'il φ 十ίΑ,ύ 1,2S 1.00 0.0015 100 0.70 0.01 0.005 wxm nu κη κη κη m iU HOI KiM 5pf nrsr ι.βό 0.0015 1.60 0.5Q 0.01 0.01 0.005 0.01 4T.0 ο ο 26.03 ι.ΰύ 0.0015 t.SO 1.00 0.03 0.01 0.01 0.005 〇T?1 I 41.0 ο— ο 25.1β -LgL 1.PQ 0.0010 1.50 0.70 0.03 ΤδΓ 0.01 α.οω ΟγΨι ^40.0 ο ο 2 乂46 1r00 0.0010 iTso 9,70 0.03 ΌΓ &quot;ΡΓ 0.005 oW [Ά0 ο ο 27 .3⁄4 33⁄4 0.BS 0.0015 1.$D aso 0.03 ΤοΓ 0.01 0.005 Ml 27.48 αϊΓ 0.0015 1.5D 0.70 1 0.05 1 0.03 aot 0.01 0.005 0.01 rttTi t 卞

-36- 200930822 οο [ezs corrosion resistance 0 IS 0 machinability 0 rupture X ID o total eo 5 O other SOCS o ω 1 0,0080 I CL 1 0.05 1 in 1 0.11 I &lt; oz "0.05 | β U. oc &lt;0 n 〇c N "38·1 l ED s CO Pb I O.UO I Sb oa 〇s -37- 200930822 Examples 1 to 4 For adding in Cu/Zn = 60/40 brass 2% Pb of brass does not undergo casting cracking. However, when B i is added to replace the Pb of the machinability component, casting cracking occurs. Although Bi and Pb can improve the machinability, it is obviously prone to casting. Example 5~10 0 Although the casting crack of the brass to which Bi is added can be prevented by adding B and Si, as shown in Example 5, when Cu exceeds 75 wt%, casting cracking easily occurs. 'Although the occurrence of casting cracking was not found even if Cu was reduced to 55 wt% 'but the increase in the proportion of Zn/3 phase was increased', and the decrease in ductility of the material was found. Thus, Cu was 75 in order to obtain good casting fracture. Below wt%, and in order to also obtain good mechanical properties at the same time, make Cu 5 5 wt % or more. ❹ Example 1 1~1 6 If the addition amount of B and Si is increased, the effect of preventing casting cracking is higher. But 'If B is excessively added, the material becomes hard and becomes brittle. That is, 'cutting resistance At the same time, the ductility of the material is reduced. If the influence on machinability, mechanical properties, etc. is taken into consideration, the amount of B added is 〇.3 wt% or less, and it is preferably 0.03 wt% or less, preferably 〇〇lwt% or less. Example 17~100 -38- 200930822

The more the amount of Bi added, the higher the machinability, and the effect can be obtained by adding 〇 3 wt % or more. However, since it is an expensive element, the material cost becomes high when it is excessively added, and therefore, it is preferably suppressed to 4 wt% or less. Further, since Bi is a starting point for occurrence of casting fracture, the ease of occurrence of casting fracture varies depending on the amount of addition. The more the amount of addition, the higher the risk of occurrence of casting cracking. Therefore, in order to prevent cracking, it is preferred to increase the amount of B and Si added.

When the amount of addition of Bi is less than 1.5% by weight, the amount of B and Si added may be reduced in order to prevent cracking, and if the amount of B and Si required for Bi is 1.5 S BiS 4 wt%, the shell IJ Bi is 0.3 SBi &lt; When it is 0.7 times at 0.75 wt%, the addition amount of 0.85 times at 〇.75SBi &lt; 1.5 wt% can prevent casting cracking. Example 1 0 1 to 1 4 7 Examples 101 to 107 show that the apparent Zn equivalent is 37 to 45%. Good castability is obtained. When the Zn equivalent is less than 37%, dendritic crystals of the primary crystal α phase are generated, and casting cracking easily occurs. On the other hand, when the Ζη* equivalent exceeds 45%, the ratio of the /3 phase increases, and the ductility of the material decreases. • Further, Examples 108 to 147 show that the ease of occurrence of casting fracture also changes depending on the apparent Ζη equivalent. The apparent Ζιι high is difficult to cause casting cracking, thereby reducing the amount of B and Si added to prevent casting cracking. If the amount of cerium and Si required for the apparent Ζη content is 39% or more and less than 41%, it is 1% when it is 37% or more and less than 39%, and is - when it is 41 or more and 45% or less. 39- 200930822 0.75 times the amount added to prevent casting cracking. Example 1 4 8~2 2 8 Although the addition amount of 0.1% by weight or more and less than 〇.3 wt% of A1 was not found to affect the rupture of _, it became easy to occur when it became 〇.3 wt% or more. Casting cracks require an increase in the amount of B and Si. Moreover, if the amount of addition of B and S i is increased, the amount of A1 added can be increased, but the ductility of the material is lowered when A1 is excessively added, and therefore, it is necessary to suppress a 丨 to 2 wt% or less. Example 229~325

The addition of 〇.1 wt% or more of Sn may affect the casting cracking, and in particular, when Sn becomes 1.5 wt% or more, casting cracking easily occurs, which can be suppressed by increasing the amount of addition of B and S i . Example 326~424

When Ni is added in an amount of 0.1% by weight or more, there is a possibility that the influence of casting cracking is exerted, and especially when Ni is added, the influence can be eliminated by adding Si. Like A1 or Sn, Ni also tends to cause casting cracking as the amount of addition increases, and it is preferable to increase the amount of addition of B and Si. Examples 425 to 436 Although Μη has an effect on the casting rupture, as long as it is less than 0.3% by weight, the influence can be eliminated. When Mn is added in an amount of 0.3% by weight or more, -40 to 200930822 is preferably used to increase the amount of Si added to 0.7% by weight or more. Examples 437 to 454 These examples show that the presence of unavoidable impurities can be tolerated, and by increasing the amount of addition of B and Si, the inevitable amount of impurities is increased. Although Sb causes casting cracking to occur easily, the addition amount is 0.2 wt% or less by raising B or Si. Further, it is also possible to add Fe of 1 wt% or less, Pb of 0.5 wt% or less, and P of less than 2 wt%. If the addition amount of B and S i is increased above the listed examples, it is shown that the above elements can be added more. Example 45 5 ~ 467 If the addition amount of B and Si is increased, the casting cracking can be effectively prevented, but if it is excessively added, the machinability, mechanical properties, and the like are deteriorated. Example 45 The composition shown in 5 to 467 is an example in which the castability Q, machinability, and mechanical properties can be maintained in a balanced manner. * Examples 468 to 490 As described above, B forms a compound with Fe, Cr, etc., and if such a compound is formed, it may cause a poor appearance when subjected to surface processing such as honing. Therefore, it is preferable to reduce the content of Fe, Cr, etc. as much as possible, and to reduce the amount of addition of B as much as possible for the decorative part to be subjected to the final refining. Although the reduction of B will become prone to casting cracking, on the other hand, it is possible to prevent casting cracking by increasing the amount of Si added. The components shown in Examples 468 to 490 are examples in which good machinability and surface processability can be obtained without deteriorating machinability and mechanical properties. Example 4 9 1~5 1 5 * Corrosion resistance is improved by the addition of Sn. By adding Sn as

Good corrosion resistance can be obtained above Iwt%. Moreover, as shown in Examples 495 to 498, the corrosion resistance of uranium can be improved by increasing Cu. As shown in Examples 499 and 500, if Cu is added and Sn is added, the corrosion resistance can be greatly improved, and the composition shown in Example 5 0 1 to 5 15 can prevent machinability, mechanical properties, and surface. An example in which the workability is deteriorated and good castability and corrosion resistance are obtained. Further, all of the comparative examples of the α phase + the cold phase of the above Examples 1 to 5 15 except for Example 5 were at 85% or more. © [Simplified description of the drawings] Fig. 1 is a view showing the shape of the metal mold 1 used in the evaluation of the casting fracture property in the two-end constraint type test. [Description of main component symbols] 1 : Metal mold 2 : Insulation material 3 : Constraints at both ends -42-

Claims (1)

200930822 X. Patent application scope 1--type brass, characterized in that: the total proportion of the crystal structure is α phase and /3 phase is above 85 %, Cu is 55 wt% or more and 75 wt% or less, and Bi is contained in 〇. 3 wt% or more and 4.0 wt% or less, when B and Si are respectively ywt% and xwt%, the amount is in accordance with the following relationship, OS 2.0, OS 0.3, and y&gt; -0·15χ + 0.015ab where a is 0.3SBi&lt;0.75wt%, 0.75SBi&lt;1.5wt%, 1.5SBi$4.0wt%, respectively 0.2, 0.85 and 1; b is 1' when the apparent Zn content is 37% or more and less than 41%. When the % is more than 45%, it is 0.75. In addition, the rest is substantially composed of Zn and unavoidable impurities. 2. Brass, characterized in that: the total proportion of the crystal structure is α phase and the phase is above 85% 'Cu contains 55 wt% or more and 75 wt% or less, and Bi contains 0.3 wt% or more and 4 wt wt % or less, including When Ni is more than 0.1% by weight and less than 〇_3wt% 'B and Si are ywt% and xwt%, respectively, the amount is in the following relationship' (1) 0.05abSx$0.75ab, 〇&lt;yS〇.3 'And (2) 0.75ab &lt; X $ 2.0, 〇$ y $ 〇·3 Here, a is 0.3SBi&lt;0-75wt%, 0.75 more Bl&lt;-43- 200930822 1.5wt%, 4_0wt % is 〇·2, 0_85 and 1; b is 0.75 when the apparent Zn content is 37% or more and less than 41%, and is 41% or more and 45% or less, and the rest is substantially Zn and Consistent of impurities. 3. Brass, characterized in that: the crystal structure is a total ratio of the α phase and the Lu phase is above 85 % 'Cu contains 55 wt% or more and 75 wt% or less, and Bi contains 0.3 wt% or more and 4.0 wt% or less. When Ni is more than 0.3 wt% and less than 1.0 wt%, and B and Si are ywt% and xwt%, respectively, the amount is in accordance with the following relationship: (1) 0.05abSxS0.2ab, -0.15x+0.03ab&lt; yS〇-3 (2) 0.2ab&lt;xS0.75ab, when 00&lt;y$0.3 (3) 0.75ab&lt;xS1.75ab, 0SyS0.3, and (4) l_75ab&lt;x$2.0, 0.004x-0.007 ( 2-ab) &lt; y ^ 0.3 Here, a is 0.2, 0.85, and 1 when Bi is 0.3SBi &lt; 0_75 wt%, 0.75SBi &lt; 1.5 wt%, 4.0 wt%; b is an apparent Zn content of When 37% or more and less than 41%, when 1' is 41% or more and 45% or less, it is 0.75. Further, the remaining portion is substantially composed of Zn and unavoidable impurities. 4. A brass characterized in that: -44 - 200930822 has a crystal structure in which a total ratio of the α phase and the yS phase is 85 % or more, Cu contains 55 wt% or more and 75 wt% or less, and Bi contains 0.3 wt% or more and 4.0 wt. % or less, containing Ni in an amount of 1.0% by weight or more and 2.0% by weight or less, and when B and Si are respectively ywt% and xwt%, it is an amount satisfying the following *, (1) 0.02ab &lt; y when 0.05abSxS0.2ab ^ 0.3 ❹ (2) 0.2ab&lt;xS0.3ab, -0.05x+0.03 ab&lt;yS0 (3) 0.3ab&lt;xS0.5ab, 0.015ab&lt;yS0.3 (4) 0.5ab &lt; x S 1 . Oab, -0.0 2 6 x + 0 · 0 2 8 ab &lt; y lan (5) 1 .Oab &lt; x ^ 1 .5ab, 0.011x-0.009 ( 2-ab) S 〇.3 , and (6) When 1.5ab&lt;xS2.0, 0.0075ab&lt;yS〇.3 Here, a is when Bi is 0.3S Bi&lt; 〇.75wt%, 0.75S 1.5wt%, 1.5S BiS 4.0wt%, respectively 0.2, 0_85, and 1 ❹ b is 0.75 when the apparent Zn content is 37% or more and less than 41%, and is 41% or more and 45% or less, and the remainder is substantially composed of Zn and unavoidable impurities. . 5. Brass, characterized in that the crystal structure has a total ratio of α phase and phase of more than 85 %, Cu content of 55 wt% or more and 75 wt% or less, and Bi content of 0-3 wt% or more and 4.0 wt% or less, including A1. Above O.lwt% and less than 〇.3wt%, relationship =0.3 &lt; y Bi &lt; 1 &gt; Group -45- 200930822 When B and Si are ywt% and xwt%, respectively, 'is the following relationship Quantity, 0^y^0.3' 0^x^2.0' y&gt;-0.l5x+0.015ab where 'a in Bi is 〇.3SBi&lt;〇.75Wt%, 〇.75SBi&lt;1.5wt%, 1.5SBi$4.0 When wt% is '0.2, 0·85, and 1' 'b, respectively, when the apparent Ζη content is 37% or more and less than 41%, it is 1, and when it is 41% or more and 45% or less, it is 0.75' 0. In addition, the rest It consists essentially of Ζη and unavoidable impurities. 6. Brass, characterized in that the crystal structure has a total ratio of α phase and /5 phase of more than 85 % 'Cu contains 55 wt% or more and 75 wt% or less 'Bi content is 0.3 wt% or more and 4.0 wt% or less 'With A1 above 0.3wt% and less than 1.〇wt% 'B and Si are ywt% and xwt% respectively, 'is in line with the following relationship ,, (1) OSxSO.lab when ' -0.15x+0.015 Ab&lt;y$0.3 (2) 0.1ab&lt;xS1.5ab, 0 &lt;yS0.3' and • (3) 1 .5ab &lt; XS 2·0, 0.002χ-0·003 ( 2-ab ) &lt; Yg 0.3 where a is 0.2, 0.85, and 1 when Bi is 0.3SBi &lt; 0.75 wt%, 〇.75SBi &lt; 1.5 wt%, 1.5 SBiS 4.0 wt%, respectively; b has an apparent Zn content of 37% When the amount is less than 41%, it is 1, and when it is 41% or more and 45% or less, it is 0.75, and -46 - 200930822. In addition, the remaining portion is substantially composed of Zn and unavoidable impurities. 7. Brass, characterized in that: the crystal structure has a total ratio of α phase and /3 phase of 85% or more 'Cu containing 5 5 wt% or more and 75 wt% or less, and Bi containing 0.3 wt% or more and 4.0 wt% or less , A1 is less than 1.0% by weight of 2.0% by weight, and when B and Si are respectively ywt% and xwt%, the amount is in accordance with the following relationship: (1) 0.05ab 刍x$0.3ab when ' 0.004ab&lt;yS0. 3 (2) 0.3ab&lt;xS0.5ab, -0_〇lx+〇.〇〇7ab&lt;y'0.3 (3) 0.5ab&lt;xS1.0ab, -0.004x+ 0.004ab&lt;yS0.3 (4) 1 .Oab &lt; x ^ 1.5ab, O.OOlx-O.OOl (2-ab) &lt;y S 0.3, and (5) 1 .5ab &lt; x S 2.0, 0 · 0 0 0 5 ab &lt; y S 0 · 3 Here, a is 0.2, 〇·85 and 1 when Bi is 〇.3$Bi&lt;0.75wt%, 〇.75SBi&lt;1.5wt%, 1.5SBiS4.0wt%, respectively; b When the apparent Zn content is 37% or more and less than 41%, when 1' is 41% or more and 45% or less, it is 〇·75, and the remainder is substantially composed of Zn and unavoidable impurities. 8. Brass, characterized in that: the crystal structure has a total ratio of α phase and β phase of 85% or more 'Cu contains 55 wt% or more and 75 wt% or less, -47- 200930822 Bi contains 〇. 3 wt% or more 4.0 Below wt%, 'Sn is above O.lwt% and less than 〇.3wt%' When B and Si are ywt% and xwt%, respectively, 'is the quantity that meets the following relationship, (1) OSxS〇.125ab, -0.16 x+0.02ab&lt;yS0.3 (2) 0.125ab&lt;xS0.4ab, 〇&lt;yS〇.3' and (3) 0.4ab&lt;xS2.0 when '0'yS〇.3 here, a When Bi is 0.3SBi&lt;0.75wt%, 〇.75SBi&lt;1.5 rating 1%, 1.5'81$4.0 rating 1:%, respectively, 〇.2, 0.85 and 1'b have an apparent Zn content of 37% or more. When it is less than 41%, it is 1'. When it is 41% or more and 45% or less, it is 0.75'. In addition, the remainder is substantially composed of Zn and unavoidable impurities. A brass characterized in that the crystal structure has a total ratio of the α phase and the /S phase of 85% or more, and the Cu content is 55 wt% or more and 75 wt% or less, and the Bi content is 0.3 wt% or more and 4.0 wt% or less. When Sn is more than 0.3% by weight and less than, when B and Si are ywt% and xwt%, respectively, 'is an amount that satisfies the following relationship, (1) 〇Sx 彡0.25ab when '-〇.〇8x+0.02ab&lt;yS 〇.3 (2) 0.25ab&lt;xSl-25ab' 0&lt;y each 0·3 (3) 1.25&amp;1&gt;&lt;parent $1.75315' 〇Sy$0·3, and (4) 1.75ab&lt; 2.0 When ''.〇〇2x-0.〇〇35(2-ab) &lt; y -48- 200930822 ^ 0.3 Here ' a in Bi is 〇3 $ Bi &lt; 0.75wt %, 0.75 S Bi &lt; 1.5 When wt% and 1.5 SBig 4 〇wt%, 〇2, 〇85 and b are respectively 1 when the apparent Zn content is 37% or more and less than 41%, and 〇75 when ψ 舄 41% or more and 45% or less. In addition, the rest is essentially composed of Zn and unavoidable impurities. 〇 ι〇·—Brown, characterized by: The crystal structure is 0. The total ratio of the phase and the cold phase is above 85 %, the Cu content is 55 wt% or more and 75 wt% or less, and the Bi content is 0.3 wt% or more and 4.0 wt. % or less, when Sn is 1.5 wt% or more and 3.0 wt% or less, and when B and Si are respectively ywt% and xwt%, the amount is in accordance with the following relationship: (1) When OSx 彡O.lab, 〇.〇25ab&lt; y$0.3 ® ( 2 ) 0· lab &lt; x S 〇.3ab, -〇·1〇5χ + 〇.〇3 5 5ab &lt; y S 0.3 (3) 0.3ab&lt;xS〇-5ab when '〇. 〇〇4ab&lt;yS〇.3 (4) 0.5ab&lt;xSl.〇ab, 〇.〇〇7x+〇.0〇〇5ab〈y$0.3 'and (5) l.〇ab&lt;xS2.0' 〇.〇45x-0.〇375 ( 2_ab) &lt;y$ 0.3 Here, a is when Bi is 〇.3SBi&lt;〇.75wt%, 〇.75SBi&lt; i-Swt%, 1.5SBi$4.0wt%, respectively 0.2, 0.85, and 1; -49- 200930822 b is 1 when the apparent Zn content is 37% or more and less than 41%, and 0.75 when it is 41% or more and 45% or less, and the rest is substantially composed of Zn and Consistent of impurities. ' 1 1 . A kind of brass, * The crystal structure is a total ratio of α phase and stone phase of more than 85 % 'Cu contains 55 wt% or more and 75 wt% or less, and Q contains Bi of 0.3 wt% or more and 4.0 wt% or less ' Further, B and Si, and at least two selected from the group consisting of 〇·1 wt% or more and 2.0 wt% or less of Ni, 0.1 wt% or more and 2.0 wt% or less of A1 and 3.0 wt% or less of Sn. The component 'the remainder is substantially composed of Zn and unavoidable impurities' is characterized by: when the amounts of B and Si are ywt% and xwt%, respectively, 'the same as Q corresponds to the composition of Ni, Al and sn described above. The respective quantities of at least two elements in the group are 'at least two relations' as defined in items 2 to 10 of the patent application scope. ' 12. Brass, which is characterized in that the brass 'addition 〇 · 3 wt % or more 4.0 \ ¥ 1% or less as described in any one of the claims 1 to 11. ^11, and 〇.7'^% or more 2_0\¥1% of the amount of 31 〇13.-type brass, characterized by: for any of the patent scope table 1 to item 1 The brass 'adds less than 0 · 3 wt % of the amount -50 - 200930822 of Μη. A faucet part comprising the brass according to any one of claims 1 to 13. 15. The faucet part of claim 14, wherein the faucet part is cast in a metal mold. -51 -