TW593703B - High-strength copper alloy - Google Patents

Abstract

This invention relates to a high-strength copper alloy which is excellent in mechanical properties, processability, corrosion resistance, etc. and is satisfactory in profitability. It is a rolled material which has an alloy composition comprising 4 to 19 mass% zinc, 0.5 to 2.5 mass% silicon, and copper as the remainder, the contents of zinc and silicon satisfying the relationship, Zn-2.5xSi=0 to 15 (mass%), and which has a crystal structure having an average crystal grain diameter D of 0.3 to 3.5 mum and has a 0.2% proof stress of 250 N/mm<2> or higher in the recrystallized state.

Description

593703 D. Description of the invention: [Technical field to which the invention belongs] Once the invention relates to wires, connectors, relays, etc. suitable for use in electrical, electronic, communication, information, testing, machinery or automobiles: High-strength steel alloys such as sheets. [Previous technology] Generally speaking, high-strength alloy copper is used as wires, switches, and connectors in electrical, electronic: telecommunications, information, food equipment, or automobiles. . The structural materials of Tsukisuke-ji Temple “are accompanied by the miniaturization, weight reduction, and high performance of the second machine in recent years, and they are also required to have very strict characteristics to improve the structural materials such as wires and open connectors. :: For example, the spring contact part of the connector is extremely inverse, and the south-strength copper alloy that constitutes the two special plates is required to be thin and high-strength, and it is also required to have the strength of the material. Leaded by a high balance with ductility, excellent productivity and economy, as well as electrical conductivity and survivability (financial corrosion cracking resistance, dezincification corrosion resistance, migration resistance), stress relaxation characteristics, weldability, wear resistance No damage will occur. However, as a high-strength copper alloy, in general, beryllium copper, titanium copper, bronze, phosphor bronze, zinc copper, brass, or brass with sn and Ni are known. The following questions cannot meet the above requirements. That is, although wrinkled copper has the highest strength among copper alloys, beryllium is harmful to beans (especially 'in the molten state, beryllium vapor is very dangerous even in extreme 6 u). It is very difficult for γ to dispose of wastes (especially incineration treatment) from the surface of the mouth, and the special features used in manufacturing become extremely high. Therefore, in order to obtain both f and f, melt processing is required in the final stage of manufacturing, which also causes economic problems. And the package 3 system So: to: ΐ :: the strength is second only to beryllium copper, but titanium is the active element, the melting equipment of large scallops, the quality and yield of melting have problems. Therefore, like beryllium copper, a solution treatment is required in the final stage of manufacturing, and the economy is also problematic. The block is: due to the inscription of copper as an active element, households must obtain a complete cast Α, and also have poor weldability. , "Also, the hot workability of Shijie Bronze and Cixi Copper is poor. The dream of hot rolling = difficult. Therefore, __ is generally t, which is achieved by horizontal continuous casting. The energy cost is high, and the rate is also poor. In addition, in high-strength, mouth-type-phosphor bronze for spring yellow or zinc-white copper for spring, including expensive brass and the addition of sn, Nk brass, although low-priced, the corrosion resistance of the f Unable (There is a problem with stress corrosion cracking and dezincification corrosion. As a result, the miniaturization and high performance of the product are not suitable. The general high-strength copper alloy is not described here. After all, it cannot meet the foregoing. 1 gongli, dual performance of various machine parts and components, and the development of new high-strength copper alloys is strongly needed. "牛 Structure 5937703 [Summary of the invention] The inventor focused on 0.2% safety limit stress (The strength at the time of permanent deformation of 0.2% is sometimes referred to as "safety limit stress" below.) Hall Peck, which increases in proportion to the -1/2 power (D_1 / 2) of the crystal grain size D (Hall-petch) relationship (see E. 〇. Hall, Proc. Phys. Soc London. 64 (1951) 747 and NJ Petch, J. Iron Steel

Inst. 1 74 (1 953) 25 ·), it is thought that by refining the grains, a high-strength copper alloy that meets the above-mentioned current requirements can be obtained, and various researches on grain refining have been conducted. As a result, it was found that depending on the type of the additive element, the copper alloy can be recrystallized to achieve grain refining. By refining the grains (recrystallized grains) to a certain degree or less, the safety limit of 0.2% can be achieved. As the main strength, the grain size becomes smaller, and the accompanying strength also increases. In addition, the results of various experiments on the effects of added elements in grain refining show that for Cu—Zn alloys, the addition of Si has the effect of increasing the nucleation sites, and for ㈣—Si alloys The addition of C0 has the effect of inhibiting the growth of crystal grains. By using these effects, it is possible to obtain Cu-Zn-Si series with fine grains. V &gt; rn〇Mn, or Cu-Zn -Si-Co based alloy. That is, 'the increase of nucleation sites' is thought to be caused by the addition of the force si to reduce the energy of the layered defects: =! The inhibition of grain growth 'is thought to be caused by the addition of c "to produce fine precipitates. 夂 This invention' is based on The identified matters are mechanical properties, processability, and ... the purpose is to provide for ^-free surname and other excellent 'economy, there are no new high-strength copper alloys, especially Hm "also, there are questions, ± τ &lt; 〇_ and 疋 适 are suitable to be used as a component material of each material, which tends to be smaller, lighter, and more functional. It can be used for a wide range of applications and is very practical. Needs :: Brother 1 'The main purpose of the present invention is to provide a kind of suitable material for two = Γ materials (plates, strips, wires, etc.) or their processed materials (called: ": mouth: bowed processed products) High-strength copper alloy (hereinafter referred to as "the first invention copper alloy"). In addition, the use of gold as a constituent material is based on the invention of the invention of the copper joints &lt; I mouth, parts, there are portable, small-sized communication devices that require thinning and twisting二 二 里 mu ^ Electrical equipment used for electronic equipment is zero: medical equipment parts, clothing parts, mechanical parts, heat exchanger tubes, cooling devices that are cooled by seawater, or seawater on small ships, etc. Export components, wiring machine parts, various L parts for automobiles, measuring machine parts, game equipment, and supplies, etc., and physical examples include connectors, relays, switches, sockets, springs, gear pin pads Tablets, game tokens, keys, reels (tumble small buttons, hooks, stop metal pieces, diaphragms, bellows f (bellQWS), sliders, bearings, volume sliders, sleeves, fuse clips, Lead frames, instrument panels, etc. Second, the main object of the present invention is to provide a rolled material (plate material) suitable for use as a strength that does not need to reach the level required by the copper alloy of 帛 1 invention, but needs to have a high balance of strength and conductivity. , Strip, wire ) Or its high-strength copper alloy (hereinafter referred to as "the second invention copper alloy") (press-molded product, bent product). It is also suitable for the second invention copper alloy as a constituent material. Among the products and parts, there are various machines for automobiles = parts, information machine parts that require electrical conductivity, measuring machine parts, home appliance parts, heat exchanger tube sheets, cooling devices cooled by seawater 5937303, or in small ships Waiting for the seawater to take in and import machine parts, game parts and daily necessities, "parts, machines, switches, 1 appliances, sleeves, fuse clips, guide two: OK :: connector key, drum, 4 ¥ Wire wood, wiring appliances, 4 relays, buttons, hooks, retaining slides, bearings, game tokens, etc. Corrugated tubes, 帛 3, the main purpose of the present invention is to provide a method suitable for the invention The copper alloy has the same surface as a circle ... :: two-strength extension wire (cut, two-wire, cross-sectional shape is square (square, etc. (/, angle, etc.), etc.) or its processing) Materials, etc.) The high-strength copper-manufactured eight-f bowed product ... A strong copper alloy (hereinafter referred to as "the third invention copper alloy"). It is also suitable to be made of the copper mouth of the third invention and the incineration made of gold. Among the parts used for clothing, there are medical machine parts, construction, mechanical parts, game parts, automotive long-time = parts, clothing parts, and various machine parts and measuring machines for electronics = electronics. , Electrical equipment parts, specifically, including

Connection, key, header love piece, 4 〆A 罘 Lu; pieces, nails (such as nails for Jia opera machines), gaskets, pins, screws, coil springs, insect guides ^. Π, 平 贝贝 螺 螺Talents, Rotary shafts of photocopiers, metal nets (metal nets for farming or fishing), Syria, people c. Fly hunting by the cooling device of the seawater cold department or seawater inlet and outlet filters on small ships, etc. ), Sliding blades, bearings, pins. The basic composition of the "X-Year Copper Alloy" contains Si of ㈠9mass% (preferably 6 ~ 15maSS%, more preferably 7 ~ 13mass%) &, and between these contents With a-2. 5 · ^ = H5maSS% (preferably H2mass%, 2 ~ 9 coffee for a more magical relationship, 10 593703 and the remainder is copper, and the average crystal grains only U is 0.3 / z DS 3. Crystal structure of 5 // m (preferably 0.3 &quot; m $ D $ 2.5 // m, more preferably 0q &lt; n π soil MU ·: 3 / z Dg 2 / zm), recrystallized The 0.2% safety limit stress of the energy n 9q / a sun shape L is more than 25n / _2 (preferably more than 300N / mm2). Also, the steel structure of Ming 2 | Ming's steel alloy contains 4 ~ 17maSS % (Preferably 5 ~ 13 „mss%, more preferably 6 ~ 115_%)

Zn, 0.8 mass% (preferably 0.2 to 〇6raass%, more preferably 0.2 to 〇_5 a) 81 ', and zn—2.5.Sl = H5mass% (4 ~ 12_s% is preferred, Ho · "is more preferred), and the remainder is copper 'and exhibits an average crystal grain size of 0. 0.3 // π ^ 1 ^ 3 · 5μΐη (preferably With a crystalline structure of 〇DS 2. 5 # m), the safety limit stress of the recrystallized state is 250 N / mm2 or more (preferably 300 N / _2 or more). In addition, the copper alloy of the third invention has a basic composition of 66 76 mass ° / 〇 (preferably 68 to 75.5 mass%) Cu, and 2 33 mass% (preferably 22 to 31 mass%) Zn, With 〇2 2mass% (

20.8 ~ 1.8mass% is better, more preferably 17mass%), and there is Cu-5 · Si = 62 ~ 67mass% (with Cu-5 · Si = 63 ~ 66.5inass%) and Zn + 6 · ^ = 32 ~ 38 ^ μ% (preferably Zη + 6 · Si = 33 ~ 37mass%), and the average crystal grain size d is 0-3 ^ in ^ D ^ 3.5 / zin (i, x 0.3 / ^ ~ 2.5 / zm is better) crystalline structure, the recrystallized state of 0. safety limit stress is 250N / mm2 or more (preferably 300N / _2 or more). In each of the copper alloys of the invention, the above-mentioned average crystal grain size D and 0.2% Ann 11 593703 = stress are used to make the alloy structure—partially or completely recrystallized—crystallized.) The material obtained from the last re-treatment (hereinafter referred to as "final recrystallization treatment") (hereinafter, referred to as "re-crystallized material") y <ten average crystal grain size and 0.2% An Wang limits the stress specified. In addition, if only the above-mentioned recrystallization treatment is performed by n. ~ _Person, it is reasonable to take iron, and the Moda ^ ^, μ treatment is the final recrystallization treatment, and the treatment material is a recrystallization material. In the preferred embodiment of each invention copper alloy, generally speaking, the ingot is processed by () including hot working (calendering, extrusion, forging, etc.) and plastic working (= rolling (drawing) wire). The recrystallized material obtained by performing a heat treatment (annealing, etc.) in a predetermined shape in the recrystallization temperature region to recrystallize (suspend, s, re, and next day) treatment (mainly, 帛i and the second invention copper alloy is a rolled material, the third invention copper alloy is a wire rod), &amp; (2) the recrystallized material of the above (1) is processed into a predetermined one by cold working (rolling, wire drawing, forging) The cold-formed material obtained from the shape (mainly, the copper alloy of the first and second inventions is a rolled material, and the copper alloy of the third invention is a wire rod). Λ () The recrystallized material (1) is processed by pressure, Product processing materials obtained by processing into a predetermined product shape such as bending processing, (4) Product processing materials obtained by pressing the cold-processed material (2) described above under pressure, bending processing into a predetermined product shape, Either form. In the copper alloy of the first invention, in order to further improve the characteristics, it contains 0.005 ~ 0.5mass% in step 12 593703 (preferably 0 · (Π ~ 0.3mass%, and more preferably 0.02 ~ O.-ss%) Good) of 〇 and / or 〇3 ~ 15ι ^% (preferably 0.711 ^ 33%, and more preferably 005 ~ 0.5 bribery 33%) of 811 Σ • In this case, the content of Co and Sn is determined in consideration of the combined amount of Sl within the above range. That is, the content of Co is calculated by dividing the content of co by the content of Si The value C0 / Si is determined to be 0.005 to 05 (2 C0 / Sh0. 0, 3, and more preferably, c0 / s, 0. 3 to 2, 2). Also, The content of Sn is determined by the value of the Si content divided by the% content. Si / Sn becomes h5 or more (preferably Si / Sn ^ 2, and more preferably si / sn ^ 3). In the copper alloy of the invention 1, the alloy composition may further contain 0.005 to 0.3 mass% (preferably 0.002 mass%) of Fe and / or 0.005 to 0.3 mass% (0.02 to 0.2maSS). % Is better) Ni as a substitute element of c0 or an element co-added with Co. Here The 'Fe content or Ni content is determined by considering the Si content (in the case of co-addition with Co, the Si content and the co content). That is, the Fe and Ni content are determined by In the case of containing c0, the total content is divided by the content of si (Fe + Ni + c〇) / Si becomes 0.005 to 0.5 (by (? 6 + "+ (: 〇) / 8 〇.〇.〇 1 ~ 0.3 is better, and (Fe + Ni + Co) / Si = 0 · 03 ~ 0 · 2 is more preferred. When making related decisions, the total content (Fe + Ni + C0) is preferably 0.005 to 0.55 mass% (preferably 〇1 to 0.35maSS%, and more preferably 0.02 to 0.25 mass%). 13 593703 In the second invention copper alloy, in order to obtain characteristics To further improve, the alloy composition further contains 0.005 ~ 〇5mass% (preferably 0.001 ~ 〇3 paste ^%, and preferably 0.2 ~ 3mass% (preferably) Sn). 0.02 ~ 0 · 2mass% is better) c0 ~ 2.6 mass%, and h 2 ~ 2 and / or 5 mass% is more in this case, the Co content and the Sn content are considered to be related to $ 丨The relationship between the amount is determined. That is, Co contains Within the above range, the value of the Co content divided by the Si content c0 / Si becomes 0.002 ~ ι 5 (Co / Si = 0.04 ~ 1 is preferred, and C〇 / Si = 〇〇6〜〇 · 5 is better)). The Sn content is within the above range, and the value of Si content divided by the Sn content Si / Sn is 0.5 or less (preferably Si / SnS0.4, and more preferably Si / SnS 0 · 3) To decide. In addition, the copper alloy of the second invention may contain Fe and / or 0.005 to 0.3 mass% (preferably 0 · (Η to 0.2 mass%)) and / or 0.005 to 0.3mass% (preferably 0. 2 to 0.2mass%) Ni. In this case, the Fe content or Ni content is based on the Si content (when co-added with Co, it is Si and Co content) to determine _. That is, the Fe and Ni content is a value obtained by dividing the total content in the case of containing c0 by the content of Si (Fe + Ni + Co) / Si 0.02 ~ 1.5 (preferably (Fe + Ni + Co) / Si: 0.04 ~ 1, and more preferably (Fe + Ni + Co) / Si = 0 · 0 6 ~ 0 · 5) At the time of the decision, the total content (Fe + Ni + Co) is considered to be 0.005 to 0.55 mass% (preferably 0.01 to 0.35 mass%, and more preferably 0.02 to 0_25 mass%). 14 ^^ / 03 For the 1st and 2nd copper alloys, it can be selected from p, Sb, As, Sr, Mg, Y, Cr, La, Ti according to the special seat required for the application. , Zr In, and Hf. At least one of these elements contains It is appropriately determined within the range of 0.003 ~ 0.3mass%. In the third invention, in order to further improve the characteristics, the alloy composition further contains 0.005 ~ 0.3mass% (with 〇 · (Η ~ 0.2mass) % Is better, and 〇2 ~ o.i5mass% is more preferred) c0 and / or 〇3ι · π% (more preferably 0.005 ~ 0.7 maSS%, and more preferably 0.005 ~ 〇 · 5 is better)%

Good 0 Here, the monthly C0 and Sn content are determined in consideration of the si content within the above range. That is, the Co content is such that the value of Co / Si divided by the Si content becomes 0.005 ~ 〇4 (It is better to use C〇 / Si = 〇〇i ~ 〇2, and Co / Si = 0.02 ~ 〇.15 is better) to decide. The Sn content is determined by dividing the content of Sn by the content of Si / Sn to 1 or more (preferably Si / Sng1.5, and more preferably Si / Sn ^ 2).

In addition, the copper alloy of the third invention may contain F &quot; and / or 〇05 〇3mass% (about 0.00H. 2) —) Ni as a substitute element of c0 or an element added together with c0. In this case, the Fe content or the old content is determined in consideration of the Si content (in the case of co-addition with Co, the content of Si and co). That is, the content of Fe and Ni is a combination of the cases where Co is contained. The value divided by Si content (Fe + Ni + c〇) / si is 0.005-0.4 (a (Fe + Ni + C〇) / Si = 0.01.〇.2 ^ ^, ^ ^ 15 593703 (Fe + Ni + Co) / Si = better 0.02 ~ 0.15). When making relevant decisions_, make the total content (Fe + Ni + c〇) stated in the month "" be 0.005 ~ 0.555mass% 〇2. 〇2mass% is more preferred). ^ Again 'With regard to the copper alloy of the third invention, the alloy composition may further contain a content of 0.0005% 2mass% 2 p,

Sb and As, and the content are 0.03 ~ 0.33 mass% 2 讦, Mg, γ,

In the case where at least one of Cr, La, Ti, Mn, Zr, In, and Hf includes at least one of P, Sb, and As, the total content of these elements is 0.005 to 0.25 mass%. However, as described above, due to the miniaturization of crystal grains (recrystallized grains), the strength is 'especially A 0.2% increase in safety limit stress'. However, the inventors confirmed through experiments that if the average crystal grain size D is 3.5 // m Below, compared with the case where it exceeds 3.5 / zm, a significant increase in safety margin stress can be confirmed. In addition, the average crystal grain size D gradually became smaller from 3. 5 # m, and when it reached 3 # claw two 2.5 # m, m, it was confirmed that the degree of safety limit stress increase drastically changed. According to the matters confirmed by such experiments, in order to ensure the safety limit stress required for the components and materials of electrical components, electronics, communications, and measuring equipment (in general, 250N / _2 or more is preferred, and 3 〇〇N / mm2: better), if the average crystal grain size D is less than 3 · 5 "m, it is necessary to use 2 degrees of strength (safety limit stress), and it is better to be below. In the case of high strength, it is preferable to be below 2.5 m. In particular, in order to increase the strength significantly within the possible range, it is better to make the average grain size k D 纟 2 &quot; m below. 'As the average crystal grain size 16 593703 becomes smaller, although the safety limit stress increases, it has been experimentally confirmed that the minimum average crystal grain size is 0.3 m and the prediction is less than 0.3 m, which is practical. It is difficult to obtain the grade. From this point of view, regarding the copper alloys of the third to third inventions, in order to ensure a safety limit stress of 250N / IM12 or more (preferably 300N / _2 or more) ^ 0 _ 3 / / m SD $ 3 · 5 // The recrystallized structure of m is necessary. That is, in the recrystallized state ( In the state after the final recrystallization treatment), it is necessary that the average crystal grain size D is 0.3 // mgDs3e5 // m and the 0.2% safety margin stress is 25n / _2 X. Furthermore, in the first In the copper alloys of the second and third inventions, when higher strength is required, 0.3 // mSDg 3 // m is more preferable, and 0.3 is more preferable. On the other hand, copper is more than the second and third inventions. The alloy needs to be supplied to the copper alloy of the first invention for high-strength applications, and more preferably 0.3 # mgDg2 // m. The copper alloy of the first to third inventions is subjected to appropriate heat treatment ( One: It is L fire) to recrystallize, and to achieve the above-mentioned micronization of the crystal grains, the micronization of the crystal grains is achieved by making it into the aforementioned alloy composition. That is, 'in the first ~ In the copper alloy of the third invention, the functions of Zn and Si are to reduce the energy of laminated defects, increase the differential density, increase the nucleation location (place) of recrystallized grains, promote the miniaturization of crystal grains, and solid solution. &amp; the function of the matrix to promote the enhancement of the strength of the material (referred to as τ, these two functions are referred to as grain miniaturization and strength enhancement function). The amount of the following reasons based, as previously determined. In other words, in the copper alloy i 17 593703 and the second invention, which are mainly used as rolled materials or processed products thereof, in order to fully exert the functions of Zn-containing grain refinement and strength enhancement, the Zn content is increased. 4mass% or more is necessary. 'In order to make the function more effective, and to increase the strength significantly, the copper alloy of the first invention should preferably be 6mass% or more (preferably 7mass% or more).' Compared with the copper alloy, the copper alloy of the second invention having a slightly lower allowable strength is preferably 5 mass% or more (preferably 6 mass% or more). On the other hand, when the Zn content is too large, the stress corrosion cracking sensitivity increases, and the bending workability also deteriorates. Therefore, considering the relationship between the Si content and the application of rolled materials and the function of suppressing stress corrosion cracking, the Zn content is i9mass% or less (preferably 15mass% or less in the copper alloy of the i-th invention). 13mass% or less is better), the second invention copper alloy needs 17mass% or less (preferably i3mass% or less, u 5mass% or less) as necessary. On the other hand, the function of 'fine grains and strength enhancement by containing Si' requires only a small amount compared with Zn, which is due to the interaction with zn. In addition, the combined addition of Si and Zn has the effect of improving and suppressing stress corrosion cracking. However, excessive addition of s 丨 can reduce the conductivity. Therefore, if these points are taken into consideration, the copper alloy of the first invention, which focuses on strength improvement and grain refinement, needs to have a Si content of 0.5 mass / s or more, and more than 0.0 gmass% (preferably above). Better. However, in the copper alloy of the first invention, if Si is added in excess of 2.5 mass%, the electrical conductivity, hot workability, and cold workability are deteriorated. In order to ensure these characteristics more fully, the content of &amp; % &amp; is better and below 2.2mass% is better. On the other hand, in the copper alloy of the second invention, which emphasizes the balance between strength and electrical conductivity, 'in order to obtain a predetermined strength. The necessary grain refining effect is exerted, and the Si content needs to be at least Q.imass%'. It is better to be 0.2% or more. However, in order to consider the balance with strength and ensure a predetermined conductivity, the Si content must be 〇8raass% or less. To ensure sufficient electrical conductivity, balance the use to 〇6mass%. The following (more preferably 0.5 mass% or less) is preferred. Furthermore, in the copper alloys of the first and second inventions, Zn,

For Si, it is necessary to balance the effect of grain refinement with stress corrosion cracking and strength. In order to achieve this, it is not sufficient to independently determine the content of Zn and Si only within the above-mentioned ranges. Therefore, it is necessary to make The relationship between the amounts of Zn and su is specified as 7n nr 〇 ^ Fu Ma Zn-2 · 5 · Si, and the value of this relationship is within the range of 疋. That is, in order to ensure a predetermined strength by grain refinement, in the 1 S bright copper alloy, Zn-2 · 5 · Si-〇maSS% must be satisfied, and Zn-2.5 · Si ^ lmass% ( Zn—2.5 · Si 2 M is more preferred). In the "invented copper alloy, Zn-2.5.Si" 2 is necessary, and Zn-2.5.Si "mass% (Zn-2.5.Si 2 5mass 〇 /. Even better) is better. On the other hand, if the Zn—2.5 · Si &gt; 15mass% of the copper alloy of the second invention, the stress corrosion cracking will occur remarkably, so 7n C. A «ting The content of Zn and Si needs to be set to Zn-2 · 5 · Si $ 15mass%, ffq ^ T ^ ^ ^. In order to prevent stress corrosion cracking more effectively,

Zn Si $ 12mass% (preferably in the copper alloy of the first invention, ZΠ Sl $ 9mass% ′ in the copper alloy of the second invention, Zn-2. 5 ·

Si-10mass ° / 〇 is preferred. Regarding the copper alloy according to the third invention, the Zn content is naturally the same as that in the first 19

The same as in the 2nd Ming Ming copper alloy, it is necessary to consider the refinement of grain size and the strength improvement target. Moreover, since the 3rd invention copper alloy is mainly used for wire rods or processed products, it is necessary to consider heat. It is determined by the compressibility. Compared with the rolled copper alloy, the copper alloys of the first and second inventions should be in a large amount. In order to fully ensure the hot compressibility, it is necessary to be 21 mass% or more. In order to make the hot-extruded wire better, the Zn content is preferably 22% or more. In addition, the first: copper alloy, compared with the copper alloy of 发明 1 and the second invention, Zn has poor stress corrosion cracking resistance due to the presence of Zn, but compared with the general U

—Zί1 series alloy (for example, JIS—C2700 (65Cu-35Zn)), Zn contains piano

For a small amount of use, it can be fully filled with stress rotten skin 4 f for use as a wire material, etc. However, in the copper alloy of the third invention, in order to ensure the necessary and sufficient stress corrosion cracking resistance and cold working to be used as a wire It is necessary to keep the z content below. That is, if the Zn content exceeds 33maSS%, the / 5 phase and the r phase are likely to remain ', which adversely affects the cold workability, which is also known as stress corrosion cracking and dezincification corrosion. It is better to carry out ㈣stress㈣rupture and cold-guarding performance while squeezing a pull wire, and the content of Zη is preferably 31 mass% or less. In the volume 3 bright copper alloy, in order to ensure hot extrusion and cold workability, it is necessary to consider that ^ Cu contains 1, if the Cu content is less than 66 mass%, the cold phase and γ are compatible. On the contrary, if it exceeds 76 mass%, it is difficult to squeeze south. Therefore, the Cu content needs to be 66 to 76 mass%. In order to fully maintain the cold workability and hot extrusion properties, it is preferably 68 to 75 5 mass%. Knife 'and si are as described above. By adding Zn together with Zn, the grain size is reduced, the strength is improved, and the stress corrosion cracking is improved. ”20 593703, suppression function. Therefore, in the copper alloy of the third invention as the wire rod, if the focus is on the function of crystal grain refinement and strength enhancement, it is also the same as the copper alloy of the first invention, and the Si content needs to be more than 0.5 mass%. As the drawing wire, it is preferably 0.8 mass% or more, and it is most suitable for imass% &. However, if the Si content exceeds 2 mass%, the r-phase and the / 3-phase, which are the most important factors hindering cold workability, will precipitate. Therefore, in order to ensure cold workability, the Si content must be 2 mass% or less. When considering a large amount of Zn, it is preferably 1 mass% or less, and more preferably 17 mass% or less. Furthermore, in the copper alloy of the third invention, in order to sufficiently ensure hot extrusion properties, cold workability, and stress corrosion cracking resistance, it is not sufficient to determine the contents of Cu, si, and Zn individually, and it is necessary to consider Si. The relationship between the content, the Cu content, and the Zn content is determined. In the correlation between the Cu and Si content, it is necessary to set Cu-5Si = 62 to 67 mass% and to make Zn + 6 in the correlation between the Zn and si content. · Si = 32 ~ 38mass% to determine the content of Cu, Sl, and Zn. That is, even if the contents of Cu, Si, and Zn are individually within the above ranges, if the relationship between the contents of Cu and Si is Cu-5Si> 67mass%, or the relationship between the contents of Zn and Si is zn + 6.si & lt 32maSS%, it cannot ensure good hot workability. On the contrary, if 5Si &lt; 62mass / 〇 or Zn + 6 · Si &gt; 38mass%, the concentration of zn and Si at the grain boundary becomes high, or there is no phase or r. Phases are easy to remain, so cold workability is poor, and valleys are prone to stress corrosion cracking. Depending on the application, disengagement can easily occur. In addition, in order to prevent such problems from occurring, and to ensure cold workability and stress corrosion cracking resistance, Cu-5si 21 593703 = 63 ~ 66.5mass% 1 ^ Zn + 6u ~ 37mass% i ^ Cu The content of Si, Si and Zn is better. However, the grain system grows with increasing temperature or time. In the recrystallization process, not all parts are recrystallized at the same time, but the recrystallization starts from the part that is easy to crystallize, until the entire area is recrystallized. End 2 is a long fight. Therefore, at the beginning of the recrystallization process, the growth of the daily grains' will continue until the end of the recrystallization process, and when the entire area of the organization is complete, considerable growth has passed. Therefore, in order to uniformly distribute the recrystallized grains throughout the tissue, the growth of the recrystallized grains is suppressed during the recrystallization process. With this function of suppressing the growth of recrystallized grains, the reason why c0 is added to the third-generation bright copper alloy is this. In other words, a fine precipitate (such as cO2Si, etc. of about 0.1 mm) is formed at the mouth of Co., and the growth of the grains is made. The amount is necessary to be 0.005mass% or more. However, the total amount of C2 added is not all involved in the formation of the above-mentioned precipitates. With one = C0, the financial and thermal properties of the substrate are improved and the stress relaxation characteristics are improved. Give full play to such heat resistance and stress relaxation properties. 'Any of the copper alloys in the third invention: at least one or more, and in the 2nd and 2nd 0.2 face in the 1st and 2nd inventions. In copper alloys, even if Co is added more than

〇 3 ^. . 'In addition, in the copper alloy of the third invention, even if Co is added in excess of 0.3 mass%, the H-reforming effect is necessary for use ^ It is said that the effect of suppressing grain growth, stress relaxation, and special effects have reached the limit and cannot be further It can be raised, the economy reports waste and coarsening of the precipitate, or the bending process 22 593703 may be poor due to the excessive amount of precipitate. Therefore, "c" contains 3 and "$". In the first and second inventions, the copper alloy y 'must be 0.5 mass% or less. ^ — Tl n Bu Fengyi Yao, and in the third invention copper alloy, M 〇 · 3mass% or less is required, i &amp; π. i ”, in order to play the above functions more effectively and ensure that the use of the knife is necessary for the purpose of bowing, it is necessary to add the bow in the first and second rounds:… ': 0.3-down is better, and more preferably 0.2- ^ In the third invention of the copper alloy, the soil is more preferably 0.2maSS% or less, and more preferably 0.15mass% or less. 8 7 υυ… The micronization of the grains of β is closely related to ^ # It is necessary to determine the relationship between the content of Si and the content of Si. In order to obtain the necessary strength improvement for the purpose of using Si to reduce the size of the crystal grains, c I 'tl_ | r / c + &amp; The ratio of each person to eight miles Co / Sl must be U05 or more in the first and third invention copper, and must be 0.2 or more in the second invention copper alloy. That is, if the Co / Si value does not reach these values, the formation of upper precipitates is small and the effect of suppressing grain growth cannot be exerted, and it is difficult to obtain the strength required for the use of the copper alloy of the present invention. Furthermore, the effect of suppressing the growth of the crystal grains is fully exerted and the strength is further improved. In the copper alloys of the first and third inventions, C0 / Si is more preferably 0.001 or more, and 0. 02 or more f is eliminated. In addition, A neodymium 0 w is more preferable, and in the second invention copper alloy, it is more preferably 0.04 or more, and more preferably 0. 06 or more. 2 In the relationship between the content of Co and Si, c0 / Si should be set above the threshold value as described above, but if Co / Si is larger than necessary, it will lead to the coarsening of the above-mentioned precipitates. Impairs bendability. For example, if the copper alloy of the i-th invention as a rolled material exceeds 0.5, and the copper alloy of the third invention as a wire rod or processed product thereof, 23 593703

When Co / Si exceeds 0.4, the bending workability decreases rapidly. In addition, even in the copper alloy of the second invention, which is used for applications that do not need to increase the strength to the level required by the copper alloy of the first invention, if c0 / Si exceeds 1.5, the minimum necessary bendability is ensured difficult. Therefore, the upper limit of c0 / Si should be determined while considering the grain growth suppression effect produced by this point and co, and considering the application, processing experience, and shape provided by the copper alloy of the invention. Specifically, Co / Si The range of Si is determined as follows. That is, the upper limit of c0 / Si is necessary to make Co / Si $ 0.5 in the copper alloy of the first invention, C0 / SiS 0.3 is better, and c0 / Si $ 0.2 is more preferable. In the copper alloy of the second invention, Co / Si $ 1.5 is necessary, Co / Si $ i is more preferable, and Co / Si $ 0.5 is most suitable. In the copper alloy of the third invention, c0 / Si &lt; 0.4 is necessary, Co / Si $ 0.2 is more preferable, and c0 / Si $ 0.15 is most suitable.

Fe and Ni are those exhibiting the same grain suppression effect as Co (more precisely, the effect of Fe and Ni is at or below the same level as Co). Therefore, Fe and Ni can be contained as substitute elements of Co. Of course, by adding Fe, Ni, and Co together, it is expected that the above effects will be further enhanced.

In the case where Fe and / or Ni replaces Co or is added together with Co, it can reduce the content of expensive Co, so it is economically effective. In the case, the content is based on the amount of: :: 系 (Co + Fe + For NO / Si, the Co content is equal to the &amp; Si content. Co / Si, for the same reason and basis as described above, in the "-Fe and Nl content of the copper alloy of the third invention" Same as the content of c〇: Let (Fe 舰 〇) / Sl be the same as Co / Sl. That is, Feng + c〇) / si, 24 593703 In the first invention, the copper alloy is 0.005. 0 · 002 02 ～ 1. 5 ， 为 0. 04〜1 是 为 ， 0.5 （为 0.01〜〇 · 3 is better, and the invention copper alloy is 0. 02 ~ 1. 5 （以 0 · 06 ~ 〇 · 5 is better), 0.005 ~ 0 · 4 (preferably 0.01 ~ 0.2, in terms of Fe, Ni, Co as a substitute element of the invention, the copper alloy is more preferably 0.02 ~ 0 · 15) The other 'is a thing that performs the same function as Co, so even in the case of adding ", ..., etc. together: its total content' should be equivalent to the case where the above-mentioned Co is only added separately. Content). However, in common In the case where two or more kinds of Fe, Ni, and c are added, 'If solid solution and precipitation are taken into consideration, the upper limit of the common addition content # (total content) of Fe, Ni, and c 0 may be allowed to be expanded to C. The content is about 0.05 mass% more. From this point of view, when two or more kinds of Fe, Ni, and c are added together, the total content (Fe + Ni + c〇) has a problem with Co, so that It is preferable that the upper limit value is extended by 0.05 mass% 2. That is, the total content (Fe + Ni + c〇) is 0.05 to 5555 mass% in the i-th and second invention steel alloys. (Preferably 0.001 to 035, more preferably 0.02 to 0.25 mass%). In the copper alloy of the third invention,

u 0.005 ~ 0.35 mass% (preferably 0.025 mass%, more preferably 0.002 ~ 0.2 mass%).

Sn is a substance that exerts the functions of improving strength, miniaturizing grains, and improving functions of stress relaxation properties, corrosion resistance, and abrasion resistance. However, in the copper alloys of the first and third inventions, in order to give full play to the strength-enhancing function, the function of crystal grain miniaturization, the heat-resistant improvement function of the matrix, the stress relaxation characteristic, and the improvement function of margin and wear resistance, It is necessary to set the Sn content to 0.03 mass% or more, and it is preferable to set the Sn content to 0.05 mass% or more.鈇 25 593703 And if the Sn content exceeds 1 · 5 mass% in the copper alloy of the first invention as a rolled material, and if it exceeds 1 mass% in the copper alloy of the third invention as a wire rod, The bendability deteriorates sharply. Therefore, in order to ensure the bending workability, the Sn content is required to be 15 claws or less in the copper alloy of the third invention 'and it is necessary to make it lmass% or less in the copper alloy of the third invention. Regardless of whether in the copper alloys of the first and third inventions, in order to more fully ensure the bending workability, the Sn content is preferably set to 0.7 mass% or less, and set to 0.5 mass% or less. Most suitable. On the other hand, in the second invention copper alloy having the lowest required strength lower than the first and third inventions_ the copper alloy of the second invention, considering the relationship with the content of Si, the strength is increased by adding Sn, and the grains are fine 4 inch improvement in stress relaxation, stress corrosion cracking resistance, corrosion resistance, and abrasion resistance are improved. This product should have a Sn content of 0.2 mass% or more. According to the required strength, make it Above lmass%, even above 12mass% is preferred. However, if Sn is added in an amount of more than 3 mass%, hot workability and bending workability are impaired. Therefore, in order to ensure the workability /% content, it must be less than 3maSS%. In order to ensure better hot workability and bending workability, it is better to be less than 2.6maSS%, and to be more than 2.5_SS. good. In addition, when adding Sn, the relationship between the content of Sn and the content of si (si / Sn) must be considered. In the case of the u-th bright copper alloy with a focus on strength improvement, when the content of si is to be increased to obtain high strength, if si / Sn &lt; 1.5 is less than, the ductility including bending workability is significantly reduced. Therefore, in the copper alloy of the first invention, it is necessary to set the Sn content to Si / Sr ^ 26 593703: It is better to ensure the ductility 1 Si / core 2 as described above, and it is appropriate to restrain: two. Also, 'If the content is smaller than that of the copper alloy of the first invention, J is a slightly smaller amount of the copper alloy of the third invention, from the same reasoning as above: If the content is to be determined with the heart 1, in order to fully determine' As mentioned above, Si / Sr ^ .5 is better, and Si / Sn ^ 2 is better. On the other hand, the second invention, copper alloy, which requires a balance between conductive properties and strength, has limited addition of Si. Therefore, in order to ensure high strength without causing too much ductility loss, it is necessary to make the Sn content and

In the relationship, Si / Sn &lt; 05 was used. In order to prove that w A-Feng has improved the ductility and strength, so that

Sl / Sns 0.3 is preferable, and Si / Sns 03 is most suitable. P, Sb, AS, Sr, Mg, Y, Cr, U, Ti, Mn, Zr, In,

Hf is added based on the alloy's material. It is mainly used to make crystal grains finer, improve hot workability, improve residual resistance, and harmless trace elements (S, etc.) which are unavoidably mixed. Effects such as reducing stress and improving stress relaxation properties. This effect can hardly be expected when the content of each element is less than 0.0003%. On the contrary, even if it exceeds 0.3maSS% ', the effect corresponding to the added amount cannot be obtained, and it becomes economical. 'Waste' and detrimental to bendability. However, in the copper alloy of the third invention with a high content of 纟 &amp;, particularly P, Sb, and As are added for the purpose of improving the resistance to dezincification and the cracking of the stress corrosion button. The effects of p, Sb, and As added for this purpose are the same as those described above, and the addition of less than G._ hardly functions. On the other hand, if the p content is ㈣, the cold and cold workability will be damaged. Therefore, in the case of adding p, Sb, and red 'in the third I copper port *', 27 is required so that the content is between 0.005 and 0.2 mass%, and two or more kinds of P, Sb, and As are added together. It is necessary to make the total content be 0 005 to 0.25 mass%. However, the heat treatment (recrystallization treatment) to obtain the recrystallized material is generally performed by maintaining the plastically processed material at 200 to 600 ° C for 20 minutes to 10 hours as mentioned in (1) above. Instead, annealing is performed. The heat treatment is carried out in batches, but if the heat treatment takes a long time, those who recrystallize in the initial stage of heat treatment will slowly grow even if the crystal growth suppression effect is exerted by the addition of Co, which is a hindrance. The crystal grains may be uniformly refined. However, when there is such a concern, the molding material is subjected to a short-term heat treatment (rapid high-temperature heating treatment) at a higher temperature than the general annealing temperature (object temperature of the molding material). Of course, it is not necessary to add c0. . Even in the case where rhenium is not added, growth of recrystallized grains at the initial stage can be prevented, and fine grains can be finely refined by recrystallization. That is, by applying a high thermal energy source for a short period of time, it is possible to recrystallize in a large number of nucleation sites for a short period of time and to recrystallize them at the same time, without giving time margin for crystal growth. Specifically, for example, the aforementioned plastically-processed material is completely recrystallized by heat treatment (rapid high-temperature treatment) under conditions of 450 to 75 ° C. (1,000 seconds). , The third invention steel alloy, a, a, a, +,, and work for another, as described, as (1) of the recrystallized material, (2) of a, cold working material or (3 ) (4) is manufactured by processing the product. By adding force 1 and adding the following treatments in this process, the alloy properties such as strength can be improved. ^ For example, if you get stronger, you can say, "亍" In the cold processing before Dan, Kou, and Japanese materials, the processing is more than 30% (preferably more than 60%), 丄 j is specific and g, and 28 of (1) is obtained.

In the production process of 2 f raw processing materials, by performing cold working with a reduction rate (e.g., more than 60%) of the rolling rate or wire drawing rate, the grain size can be promoted, and the grain size can be further refined by the grain size. Effectively seek to increase strength. That is, in order to make the crystal grains fine, the nucleation position is necessary. # The nucleation position is increased by processing as described above with the processing rate = 2; the higher the processing rate, the more the increase amount of nucleation position H, Recrystallization is caused by the release of strain energy. Therefore, by increasing the shear strain by the above-mentioned cold working, more fine-grained results can be obtained: 'Results' From the miniaturization of crystal grains, a stronger rise can be achieved more effectively. On the other hand, as a plastic processing material for the final recrystallization treatment, flat: the crystal grain size (average crystal grain size before recrystallization) is preferably smaller, the volume is 5, the average crystal grain size is less than 2G lG // m or less is preferred) The smaller the average grain size of the recrystallized steel is, the more the heat treatment will be performed in the next step, and the position of the recrystallized nuclei will increase, especially the dense packing between the grain boundaries: w'Yugu It is easy to become a nucleation site. However, due to the average crystal grain size, the strength: t times 'the energy cost required to manufacture a high-strength copper alloy' also takes manufacturing time. Therefore, the material of plastic working materials described in ⑴ = Average crystal grain size If the strength is insufficient in the state of the recrystallized material, the cold rolling or cold drawing line with a processing rate of 10 to 60% can be applied to the recrystallized material. In addition, in the case of obtaining the aforementioned plastic processing material, when a rolling calendering or wire drawing process is performed, 'the τ pressure rate or the wire drawing rate is set to be larger (15% or more (25% or more) Good)) is better. By cold working with a high reduction rate and high draw ratio, the increase in shear strain and nucleation position can be achieved, and the 29 recrystallized particles can be further refined. In addition, if a small caliber roll or Conversely, the caliber is extremely large for calendering, or the wire drawing is performed with a wire drawing mold with a large mold angle, or the wire drawing is performed with a very small wire drawing mold with a very large mold angle. It is effective to increase and realize the refining of the recrystallized grains. Furthermore, even if the calendering process is performed by a different-circle-speed calendering method, that is, by using upper and lower rolls with different diameters, the rolls are changed while changing the speed. Rolling, or The rolled material is given a large shear strain, and the recrystallized grains can be miniaturized. In addition, according to the purpose of each invention, the copper alloy is subjected to an appropriate heat treatment that does not recrystallize it (generally, 150 ~ 600t, L fire from i seconds to 4 hours), can significantly improve the elastic yellow limit value and stress relaxation characteristics. Specifically, for the cold-worked materials (2) (including the cold-worked materials mentioned in (4)) or (3) The processed product of (4) is heat-treated under the conditions of 20 (rc, 2 hours or 600 ° C, 3 seconds.) [Embodiment] As Example 1, Tables 1 to 4 The copper alloy of the composition shown was solved in the atmosphere. 'I know a square column ingot with a thickness of 35_, a width of 80mm, and a length of 200mm. Then' this ingot was subjected to hot rolling (85 times of TC (4 times) to obtain a thick After pickling the intermediate sheet, it is cold rolled and rolled into a final sheet with a thickness of 1 mm. Each final sheet is then recrystallized at a temperature at which it can be 100% (hereinafter referred to as "recrystallization temperature"). ”) Heat treatment (annealing) 丨 hour, that is, a complete recrystallization treatment of the structure is performed to obtain the copper alloy N of the first invention · 1〇 BU No. 186. In the recrystallization process, beforehand, test pieces taken from each of the final plates of 30 593703 (one side is a 20mm &amp; right square plate piece) 'are started from 300 ° C, and the temperature is changed every 5 (rc Hold the strip for i hours ^ annealing, find the lowest temperature when the test piece is completely recrystallized, and use this as the recrystallization temperature (refer to Table 1 5 to Table 17).… Again, by using and After the same process as above, to obtain the final materials of the same material (same shape and same composition) as the final materials of the alloys No. 107, No. 111, No. 111, No. 154, No. 18o, etc., The final sheet was recrystallized under conditions different from those described above to obtain ν〇 · 102, Ν〇 · 1G7, No. 111, ν〇 · 154, Νο · 175, and the compositions were the same as those described above. No. 1〇2Α, No. 1〇7A, No. 111A, No. 154A, No. That is, the first! Invention such as ⑽ ^ 如 丽 ^ ⑴ 八, · No. 154A, No. 180A is by Refining the final sheet at a temperature much higher than the reheating temperature: the temperature is increased for a short time to recrystallize the material (rapidly high / JEL plus Treatment), its temperature a (° C) and heating time b (seconds) are as described in "a (b)" in the "recrystallization temperature" column of Table 15 and Table 17. For example, in Table 15, No. "480 (20)" is described in the column "Recrystallization temperature" of 102A, which means that the final sheet is kept at 4800 (heating and holding for 20 seconds) and L is used as Example 2 and Tables 5 to Table The copper alloy with the composition shown in Fig. 8 was disintegrated in winter to obtain a square column-shaped ingot having a thickness of 35 mm, a width of 80 mm, and a length of 200 mm. Then, the ingot was subjected to hot rolling (4 times) at 85 ° to obtain Houda. After pickling the middle plate, it is cold-rolled and rolled to a thickness of 1 mm. After the plate, each final plate is heat-treated at a temperature at which it can recrystallize 100%, that is, the recrystallization temperature ( Annealing) 丨 hours (recrystallization treatment) 31. The copper alloy No. 201 to No. 281 of the second invention is known. The recrystallization temperature and degree are determined in the same manner as in the first embodiment beforehand (see Table 丨 8 to Table 20) Furthermore, the constituent materials and alloys of Alloy No. 202 No. 209, No. 250, and No. 265 were obtained by the same process as above. After a homogeneous final sheet, the final sheet is subjected to the aforementioned rapid high-temperature heat treatment to recrystallize, to obtain No. 202, No. 209, No. 250, No. 265, and, and the same as the above No. 2〇2A, Ncx 209A, No. 250A, No. 265A. That is, rapid high-temperature heat treatment of each alloy No. 2〇2α, ν〇 · 209A, No. φ 250A, and No. 265A was obtained. The conditions (temperature) and heating time b (seconds) are described in the same manner as in Table 15 to Table 17, and are listed in the "recrystallization temperature" column of Tables 18 to 20 as "a (b)". In Example 3, an alloy having a composition shown in Tables 9 to 12 was melted in the atmosphere to obtain a cylindrical ingot having a diameter of 95 mm and a length of 180 mm. This ingot was heated to 78 (rc, and an extruder (500 t) was used to obtain a round rod of 12 mm. 胄 After the round rod was washed, the wire was processed to straight # 8 随, and then After heat treatment at 50 CTC and i hours, the wires are washed and drawn into spring-shaped wires (formed materials). Then, each wire is recrystallized at a temperature at which it can be 100%, that is, the recrystallization temperature. The heat treatment (annealing) is performed for one hour (recrystallization treatment) to obtain the third invention copper alloy No. 3 (η to No. 397. In addition, when the recrystallization treatment is performed, the wire rod will be removed from each wire rod beforehand. The test piece (a wire piece with a length of about 20mm (diameter 4_)) is annealed from 30 (rc) and kept for 5 hours (TC units) to find the lowest value when the test piece is completely recrystallized. The temperature was used as the recrystallization temperature mentioned above (refer to Table 32 593703 21 to Table 24). The constituent materials of alloy No. 302, No. 314, and ν〇 · 338 were obtained by the same process as above. After the final wire of the same quality (forming material), the final plate is subjected to the aforementioned rapid high temperature heat treatment to recrystallize 'To obtain No. 302, No. 314, No. 338, and No. 302A, No. 314A, and No. 338A, which have the same composition as above, and obtain the rapidity of each alloy No. 302A, No. 314A, and No. 338A. The high-temperature heat treatment conditions (temperature a (° c) and heating time b (seconds)) are described in the same manner as in Tables 15 to 17 and described in "a (b)" in Tables 2i to 24. Recrystallization temperature ". As Comparative Example 1, the same process as in Example 丨 was used to obtain the composition of Table 13! Comparative Example Alloy No. 4〇i ~ n〇. 422. Also As a comparative example, the second comparative example alloy No. 423 ~ No. 431 having the composition shown in Table μ was obtained by the same process as that of the third embodiment. Also, the first comparative example soft alloy No. 401 ~ No. 4〇7, which is the same as the individual specifications of CDO〇, 乂: 2〇 :, ⑵00, Yi, C2_, coffee. And ⑽ &quot; 目 同 组 组 jislai: 2 ^ car 乂 example The gold No. 423 and No. 424 are C2600 and C27OO phases of the JIS standard, respectively, 1 and 19 persons U, and completed products. Also, in Table 12, 3 has c0 and Does not contain! ^ Μ. Λ / ς. ★ 1 by the -l 'the system "(Co + Fe +

"Ni) / Si" is not changed to "c0 / Si". On the other hand, regarding the alloy No. 427 and plate 431 of the comparative example, the following processes, such as .425 and plate, were produced in the process_, so the production was abandoned. , That is, the stage of hot rolling that cannot be carried out produces a large Yu No. 421, a large crack in the casting, about 425 is unable to heat 33 593703 extrusion, about No. 427 and No. 431 In order to break in the drawing process, ▲ no one can carry out the subsequent process, and give up production. Then 'for the first invention copper alloy No. 10, No. 186, No. 102A, No. 107A, No. 111A, No. 154A, No. 180A, and the second invention copper alloy No. 201 to No. 281, No. 202A, No. 209A, No. 250A, No. 265A, and the third invention copper alloy No. 3 (H ~ No. 397,

No. 3 02A, No. 3i4A, No. 338A, and copper alloy No. 401 to No. 431 of Comparative Examples of the first and second inventions (excluding No. 421 'No-425, No. 427, No. 431, waiving production) The average crystal grain size in the recrystallized structure of 9) was 9 D (// m), and was measured based on a cutting method (JIS-H050 1) using an optical image. The results are shown in Tables 15 to 26. In addition, the first invention copper alloy No. 101 ~ No. 186, No. 102A, No ·, No. 111A, No. 154A, No. 180A, and the second invention copper alloy No. 201A ~ No. 281A, No. 202A, No. 209A, No. 25〇A, No. 265A and the first comparative example copper alloy No. 401 to No. 421 (excluding No. 421), and the conductivity was measured. The results are shown in Tables 15 to 20 and 25. In addition, the conductivity (% I ACS) is the percentage ratio of the volume specific resistance of the international standard soft copper (1 7. 241 X 1 0-9 // Ω · m) divided by the volume specific resistance of the alloy.

In addition, for the first invention copper alloy No. 10B No. 186, No. 102A Λ Νπ • 107A, No. 111A, No. 154A, No. 180A, and the second sun-drum steel alloy No. 201A to No. 281A, No. 202A, No. 209A, No. 2 5 〇δ No. 265A, and the first comparative example copper alloy No. 401 to No. 421 (No. 421), using Arm The Armsler universal testing machine performs 34 tensile tests to determine the safety limit stress (0.2% safety limit stress), tensile strength and elongation. Furthermore, each alloy was cold-rolled to a thickness of 0.7_ (3⑽), and this rolled material (hereinafter referred to as "post-processed material") was subjected to the same tensile test as described above to determine the safety limit stress (0.2%). Safety limit stress), tensile strength and elongation, and evaluation of bending workability and stress corrosion cracking test. The results are shown in Tables 15 to 20 and Tables =. In addition, the copper alloys No. 1101 to No. 186, No. 102, No. 1a, No. 154A, No. 18OA of the first invention, and the second invention copper Renjin No. 201A ~ No. 281A, No. 2〇2A, No. 20gA, &amp; 25〇 / Ν〇 · After 30% calendering, the processed material obtained is of course also the n of the present invention Strength copper alloy. The evaluation of the bow σ workability is to bend the test piece obtained from the post-processed material in the vertical direction to the rolling direction to bend into a W shape, and the fracture degree R / t (R: in the bending part) The radius of curvature (mm) on the inner peripheral side is the thickness of the test piece (with). In 2 ~ Table 17 and Table 22, those who did not break at t 0.5 days were those with excellent bending workability.

◎ "indicates that no cracking occurs at R / t = 1 e ^ 1.5%, but those with cracking at 〇.R / t:.: Are those with good bending workability (not indicated by" 〇 "in practice In ^ = 2.5, the temple does not produce cracks, but. 1 · 5 $ R / ts 2 · 5 produces cracked earth ^ d 'is a person with ordinary bending workability, although there are problems, but it is practical) to 4… / “△” indicates that it is generated at R / t-2.5; 4 indicates bending workability 丨 Wang Buk (difficult to use), and “X” indicates. Also, the "stress rot worm rupture 4 _ A clothing 4 test" is specified in JIS H3250: the test container and the test solution come from the wood, and use the same amount of ammonia and water mixed with 35 sides: "" &lt; Environmental exposure time and stress relaxation rate (on the post-processed material table, the stress of the post-processed material tg is 80% of the full limit stress value of the female of the post-processing material). In the table ... and; the exposure time of 75 cuts and the stress relaxation rate is m or less, is the one with excellent corrosion resistance and crack resistance, exposed π 丨 卩 士 ± ◎ "shows that the stress relaxation rate is under the exposure '% Of 7 exceeds 20%, and 20% or less at the time of 30 hours of exposure' are those with good anti-corrosive money rupture properties (there is no problem in practical use). Those who are 2 times below the corrosion resistance (may have '&quot;, Hachichang, J Yuejian have asked, but there is no problem in using them), △ "said' exceeded at 12 hours of exposure time Those with poor rupture (practical difficulty) are indicated by "X". For the third invention, the copper alloy No. 301 to No. 397, ν〇. 4 No. 314A, No. 338A, and the second comparative example alloy No. to No. 431 (excluding the N of abandoned production) 〇 · still, n〇.milk and version use an Amsler type universal testing machine to perform a tensile test to determine the safety limit stress (G. 2% safety limit stress), tensile strength, and elongation. The alloy wire is drawn to a diameter of 3.35_. For this wire (hereinafter referred to as "post-processed material"), the same tensile test as described above is performed to determine the safety limit stress, tensile strength, and elongation, and bend processing is performed. Evaluation of the properties and stress corrosion cracking test. The results are as shown in Table 2 and Table 24 and Tables 2 and 6. The copper alloy of the third invention such as .30, such as .397, and version 3.02A No. 314A, No. 338A drawn wire after processing, of course, is also the high-strength copper alloy of the present invention. The evaluation of bending workability is to use a V-shaped block to bend the post-processed material 36 593703 90 degrees In this case, the degree of bending R / t (R: radius of curvature (_) of the inner peripheral side in the bent portion) at the time of rupture •• The sheet thickness (_)) of the test piece is used. In Tables 18 to 22, when R / d = 〇, no crack will occur, and those who are good for bending processing are indicated by "◎", and R / d = 〇 · 25, no rupture occurs, but the rupture occurred at O'R / d ^ O.25, which is a good one (there is no problem in practical use), which is indicated by "〇 本 一 -d" ° ", in When R / d = 0.5, the person who has no leather clothes and ruptures at 0.25 ^ R / t ^ 0 · 5 is a person with ordinary bending workability (though right ny ^, with rice R / t &n; n &quot; / (Although it has been asked, but it is practical), it is indicated by "△", and those who have fractured ~ are those with poor bending workability (Practical are indicated by "X". U has (difficulty to use), labor, The stress corrosion cracking test is for the above-mentioned 90-degree bending of the processed material after bending and adding R / d = 1.5, using JIS H3250 Song Xi 4 AX &lt; 曲 # equal amount of ammonia water Toilets, two persons, three persons, containers and test liquids were used to evaluate the rupture of the rot. In; whether the two burnt offerings were cracked, and there was no break during the time of financial stress ^ ^ Table 20 and Table 25 towels, When exposed The wearer is resistant to corrosion and breakage "means 'breaker when exposed for 40 hours' in ◎ days, without breakage at that time, it is no problem if the break time of the corrosion-resistant button is 15 minutes), with" 〇 # ^ 丨 生Good person (practical rupture, but when the exposure time is 6 hours ^ day = time 15, there is a general-like corrosion cracking resistance (can be no rupture, it is with "" at the exposure time 6 Hours but practical) '# "△ Poor cracking (difficult to apply), and those who have cracked are corrosion resistant X". 37 593703 It can be seen from Table 15 to Table 26 that the first to third invention copper alloys can be obtained with respect to the first and second comparative example alloys that do not have a specific alloy composition and recrystallization structure at the beginning. The miniaturization can greatly improve the mechanical properties including the safety-limiting stress and the bending workability. It can be used as a plate, a bar, or a wire even in applications where conventional high-strength alloys are difficult to use. In addition, it is known that the recrystallization treatment can be performed by rapid high-temperature heating treatment to further refine the grain D and increase the strength. In addition, although it is not described in Tables 15 to 26, it has been confirmed that the following processed materials (re-crystallized rolled materials and wire rods are further processed; human calenders and wire rod processors) are at 150 to 600 °. C, heat treatment from 1 second to 4 hours | 'The spring limit value and stress relaxation characteristics can be greatly improved.

38 593703 [Ls

Alloy composition (ma ss%) (Co + Fe + Ni) / Si 0. 108 0.079 0.079 0.056 | 0.070 0.055 0.060 0.005 0.040 | 0.213 0.044 o 0.071 0.020 | ο. Ιοί | 0.066 Zn-2.5Si 丨 7.550 6.550 o CO ΙΛ (• ds CD LT &gt; LO cs LO lo CSI &lt; 〇CO 4.350 LO Csi LO-LO CSi LO Seven LO 05 〇14.275 s 6.400 〇 Xj · &lt; d 8.200 in in 5.075 Ο in 〇CVJ 6,425 〇 CO CD 〇IT ) oo o 14.625 10.450 6.475 in inch ai &lt; x &gt; CO 0.03 JO 0.03 FREE 〇 &gt;-0.02 0. 05 cu 〇0.03 0.07 0.12 0. 11 0. 12 CM omo 〇o to ο 5 〇0. 06 CO CVI ooo 0. 09 0.98 SS CO lO CO &lt; 〇csi csi CO CO csi CO os CM LO Csj lO E〇o csi Csi CO csi CM LO m oo LO 〇 &gt; CO csj 5 〇 &gt; CO o CO r5 10.0 CO 〇CO 〇CO ai d LO 00 cy &gt; 0¾ 00 &lt; 6 CQ oo eg 〇CSI d 00 a &gt; O LO 〇CN4 oc〇〇 &gt; CO 00 CO CO eg O CM oa CO &lt; 5 Residual Residual Residual Residual | Residual Residual Residual Residual Residual Residual Residual Residual Residual Residual Remains 107A go II 111A CM CO inch LO &lt; 〇 卜 00 〇 &gt; CO CSJ 39 593703 [CVJ skimming] (o / os S BE) ^ S &lt; ^ such as Si / Sn 4.824 I 1.545 22.400 o oo 5. 095 inch Csi δ xr 5. 241 5.433 6. 680 Z ss 〇s CO sso 〇 If in: LO s 〇5 ogs oo s CO CO § ss CO &lt; £ &gt; o σ &gt; LO os CM + 〇oooo 〇oo dd o 'ooooooooood 〇CO LO eg LO CM CO uo wins osgo LO rj- LO CM cn o § s 〇〇s LO CVJ UD p- ooo 8 LO CSJ LO CO os LO § CO o 8 o § LO o LO 05 LO o JO o § ΙΛ CM LO LO CM CO rS ΙΛ ur &gt; co LT &gt; CD &lt; b in co a &gt; cd — — eg 00 lO to evi to cd &lt; d cb 10 LO c 0. 03 ivj S 〇S δ o Ο s o 'o capacity a &gt; CM to ΓΟ CD CVJ s U &gt; eg oooooo 〇ο O 2: 04 CN CNJ s CVi g 5 O s § O' o 〇oo 〇ooooooog 〇 &gt; s 04 gosod 〇〇dooooo 〇 &gt; CO gosg CD g two sogo CSi r- S ο o 〇oooo 〇oooooooo &lt; D ο o CO un CT &gt; 0. 88 04 CO o 04 c〇CO art OQ in &lt; £ &gt; CO CO CVJ CO CO CO CO CO Si Si CO oss CM 04 vs csi 0.57 eg to 2 &lt; 〇〇6 10. 3 | CO ur &gt; oi 10.0 〇r &gt; 〇〇O CO ai 00 04 CSO σ &gt; 00 cb 〇6 CO uS CNi o to ai 〇 &gt; CO &lt; 〇o 04 od CO &lt; 〇oo o CO o &lt; £ &gt; 〇i 00 ai 3 §Q Insertion §n Insertion § □ Insertion 锸Insertion § □ Insertion 镝 镝 镝 §a § □ Insertion § □ Flame mm flame m flame flame m m * mm * mmm Stimulation mm Stimulation 0 CM CO CS4 CM S 04 ΓΟ CO CO 5 ΙΟ CO CO CO CO 00 00 CO 0¾ CO o 5 CO 5 &lt; o CO § s in z 40 593703 [s] Alloy composition (ma ss %) Si / Sn 4.969 8.000 6.286 6.286 3.447 4.317 16. 250 8.050 5.286 10.111 6.885 | o CO 4. 786 4.182 6.400 5.500 19.875 12.083 9 · 000 | 14.364 10.714 8.167 10.333 5. 321 6. 200 6.154 10.045 (Co + Fe + Mi) / Si 0.069 0.011 0.034 0.034 0.051 0.338 0. 050 0.072 0. 066 0.045 0.068 0.060 0.203 0.050 0. 055 0.069 0.028 0.037 0.070 0.053 0.068 0.218 0.074 0.057 0.050 0.050 Zn-2. 5Si 4.675 o 〇4.300 S 〇 &gt; Seven 5.475 6. 850 5.475 10.525 S CO CO 0. 425 5.600 4.975 7.850 os LO LO to L〇6.525 7.675 4. 850 S CO iO 6.250 9. 525 o Bu 5.975 to OJ CO L〇5.300 4. 675 0.02 rvi oo 0.02 | 003 Ml Bu 0.08 | 0.04 | 0.07 0. 02 0.08 0. 05 CL · 0. 03 0. 32 0.23 CO C \ lo 0. 28 0.47 0. 41 0. 08 j 0. 20 | o 0.18 0.26 | 0. 82 I 0.42J 0.33 0. 25 0.30 0. 08 oo 0.12 0. 28 0. 25 0.26 0. 22 4.12 0.28 0. 08 0.06 002 0.01 0.04 0.05 CM 〇0.08 0.09 so Ml 0.03 0.04 0.05 0.05 &lt; s 0.11 0.02 0.06 0.06! 0 09 Ϊ 0.44j 0.08 0.08 0.06 | 0.04 | 0.03 | 0.03 0.07 0.03 0.05 0.21 0.09 0.08 0.04 006 CO 1.59 1.84 1.76 CO 〇g &lt; 〇 &lt; 〇2 CsJ 00 &lt; N CO ο csi 00 CO S to CO a &gt; la Csl CO τ— CO to s CVI 5 LO in 1.60 2. 21 rS 10.7 σ &gt; to COCO 卜 00 O σ &gt; 〇 &gt; cr &gt; LO ai CO CO CNJ CO σ &gt; σ &gt; οα ο ο CO o O) buai LO o CO σ &gt; GO 00 cri oo CN CO CO cri ir &gt; a &gt; CO cn CNJ o 3 Residuals Residuals Residuals Residuals Residuals Residuals; Residuals i Residuals Residuals Residuals Residuals Residuals Residuals Residuals Residuals Residuals Residuals Residuals Residuals Residuals Residuals Residuals Alloys No. cvi LO ss 154A in LO CO LC 〇〇LO r— in § τ— 3 ss IX &gt; &lt; 〇I sr— § σ &gt; CO t— o CO LO CO r- * Bu 41 593703 [Table 4] Alloy composition (mass 1%) No. Cu Zn Si Co Fe Ni Sn Zn- 2.5Si (Co + Fe + Ni〉 / Si Si / Sn 178 stub 6. 9 1. 19 0. 15 0. 14 0. 54 3.925 0.244 2.204 179 stub 8.9 1.68 0.09 0.02 0. 09 4.700 0.065 18. 667 180 stub 14.2 1.65 0. 03 0.09 0.20 10. 075 0.073 8.250 Xiao 180A stub 14.2 1.65 0.03 0.09 0.20 10. 075 0.073 8. 250 181 stub 9.4 1.62 0. 06 0.01 0.02 0. 18 5.350 0.056 9.000 Example 182 stub 10.1 0.89 0 03 0. 02 0.01 0.24 7. 875 0.067 3. 708 1 183 stub 11.8 1.45 0,01 0,03 0.02 0.33 8.175 0.041 4. 394 184 stub 8.3 1.20 0.31 0. 07 0.05 5.300 0.317 24.000 185 stub 9.5 1.70 0. 15 0. 07 5.250 0.129 186 stub 9.5 1.70 0.10 0.30 5.250 0.059 5.667 42 593703 [9 lazy]? Φ φ &lt; 0 ί class &lt; η 0) U. b 00 to o 〇o CM oo CVJ o CM cr &gt; 〇 § o CVJ u &gt; o 'CO CO CO o 00 oo OJ o CO os 〇so LO 〇CO oos Csl C &gt; &lt; 〇CO o a &gt; 00 o 'sois Cj4 M 8 〇 &gt; in oo oo oo in CO cri 8 &lt; 0 in CNi om 04 〇 &gt; uo csl CT &gt; S bu 00 s r- od s Cvi 〇0 · s in s 〇 &gt; to oo 00 l〇o oo so LO &lt; NJ BU · § cJ 8 CVJ a &gt; in CM in 〆LA Csl OO cd IA 〇r &gt; 8 &lt; S »BU 'm 00 a &lt; P s 00 04 〇 二 so ώ 〇v5 S o 'Q. so O sogol £ S o S og O sos O sd CM O CM O oo § ogooooos 〇o § ogoa O oo so 5 o σ &gt; o to o 〇CM LO 〇 cr &gt; CO O ar &gt; T— * ooomoso CSI to oso JO o CO CO o CO ooo CO ooo CM to 〇rj o 〇 &gt; CO opoo CO oso oo T- · o rS oooooo 〇 &gt; to 〇 卜 o — CsJ o cn a &gt; oooo LO 〇 &gt; oo CD CO o bu a &gt; σ &gt; oo LO ir &gt; oo CO ΙΛ o bu CO oo a &gt; oo ai CO od oo CN od oo &gt; od &lt; 3 Niobium Interferential Interferential Interferential Interferential Excitation §nm 镝 Flame Excitatory §n Interferential Sm ffi m Interfering m 镝 m §n Interferential Interfering m Interfering Interfering m Sn m Flame §§ m Interfering Flame §n 尨 尨 · Juan 〇 &lt; α ζ ss CM 5 s CO 8 tr &gt; S s CM g CsJ S s c &lt; \ &lt; go 04 CO inch ΙΛ &lt; 〇 卜 cs CO Csl σ &gt; s CSJ a 04 Csl CM CO Oi csl CNJ Ά CM fc 镅 pon w 43 593703 [9 «] Alloy composition (ma ss%) Si / Sn 0.305 0. 090 0.101 0.073! 0.108 0.451 0.474 0.183 0.183 0.169 0.173 0.146 0.146 0.467 0.467 (Co + Fe + NO / Si 1.200 0.918 0.211 0.554 0.316 0.136 0.167 0.128 ! 0.460 0.191 0.286 〇 0 o 0.140 0.344 0.273 0. 400 0.345 0.179 〇ϊ o 0.171 Zn-2. 5Si 8.450 7.275 6.850 8. 700 10. 325 8.050 7.600 13.825 | 3,550 7.325 9. 300 7.000 9.375 8. 625 3 Bu 8.000 7.325 ! 8.525 11.025 9.350 8 6.375 6. 750 8. 400 8.400 | 8.650 S d rvi δ o 0.03 BU 0.07 &gt; »I 0.05 | so 0.02 0.03 o cvi σ &gt; a &gt; cvi CM csi CO 00 CO o LO s OO &lt; x &gt; CVJ σ &gt; Si s-| 0.02 0.06! 0.04 I 0.03 I 0.02 0.05 0.02 I 0.03 | so £ s 〇0. 06 0.05 0.02 0.21 '' | 0.04 0.02 0.02 0.05 0.36 0.45 0. 02 0.26 0.04 | 0,03 0. 04 0.04 I 0.03 I 0.01 〇0.09 | Csj r- · ooogo 0.05 [C4 O oo 0.30 0. 49 0.38 0.56 0.19 CO to o 0 48 〇 &gt; CO oso 0.47 | 0.28 '0.44 LO o CO o 00 oso LO 1— o 0 23 0.51' 0.18 0. 32 CO CO o 0. 30 0. 29 0. 28 0.28 | 0.70 r5 CNI cr &gt; L 〇CO 00 'Τ Ο 00 o aa &gt; 00 00 〇0 — CO Seven LO Ό〇 10.0 CXD oo o a &gt; C \ J 00 LT &gt; OO crcr &gt; CO csi CO σ &gt; CT &gt; C \ l LD 〇 &gt; cri σ &gt; To o 3 stub stub stub stub stub stub stub stub: stub stub | stub stub stub stub stub stub stub stub stump CSI CM 00 C \ J CSi CNI CM o CO csi CO CN CV I CO CM CO CO &lt; NI m CO CM c〇 CO CM CO oo CO CVJ σ &gt; CO &lt; N o CVJ CNI CO s CM ΙΛ &lt; N s CO s 〇 &gt; o to 04 I 250A j

44 593703 [Arithmetic]

Alloy composition (ma ss%) Si / Sn 0.203 0.127 0.200 0.142 0.140 0.100 0.483 0. 205 5 〇0.173 0.229 0.216 0.454 0.129 0.129 0.122 0.135 I 0.202 0.228 0.328 0.215 0. 262 0.236 0.116 J 0.169 0.228 0.180 (Co + Fe + Ni ) / Si 0.563 0.556 0.286 0. 048 0.344 0.333 0. 357 0.219 0.286 0. 261 0.150 0.229 0.108 0.346 0.346 0. 333 0.322 0.500 0.194 0.316 0.250 0.136 0.212 0.364 0.214 0.217 0.244 Zn-2.5Si! 7. 700 7. 125 丨6.525 8.275 7,600 LO CM 10.250 14,300 〇CO 8.625 8,000 4. 025 6. 450 7. 050 7. 050 6. 425 I 7.625 | 5,800 j 7.900 | 8.825 7.000 10. 200: 7.875 10.050 7.000 5. 900 11.475 0.06 &gt;-0.02 0.02 0. 05 Ml 1.58 2.12 in 〇〇CM cvi JZ OJ 0.29 jm oo 00 CO CO ΙΛ SS 2.02 sc \ i CM CSJ csi ^ 00 ″ CO c \ i S 0.58 S 〇S &lt; jD S 2. 28-0.06 0. 08 0.08 so 0. 05 1 0.03 1 0.05 so 0. 03 0. 01 0.05 〇ogo 0.06 〇 0.02 0.03 0.01 0.01 | 0.05 | 0.02 0.06 0.03 0.02 0.05 0.18 0.15 0.10 0.01 0.11 0.09 0.05 j 0.07 0.07 0.06 0.08 I 0 · 21 0.02! 0.04 0.03 0.03 0.05 0.12 CO 0.32 0.27 LO CO o CD 0.32 1 1 eg 〇o CM CO d OO o CO CM o 0.40 LO CO 〇d CO CvJ o &lt; £ &gt; eg 〇ooo 0.36 〇0.32 0.44 CO CO o CM CM 〇CO CSJ O 0.36 0.41 i〇od CO 0000 OD CO 〇〇 &lt; 〇O LO oo od CSJ σ &gt; 〇 σ &gt; 〇r &gt; xr CO oo bu bu bu bu · bu · CO 00 σ &gt; co 00 CO CO 〇 &gt; · OO bu · CO od CD 〇 OO OO &lt; 0 LO oi 8 Remnant Remnant Remnant Remnant Remnant Remnant: Remnant: Remnant! Stub 丨 j stub stub stub stub stub stub stub stub stub i stub stub stub stub stub stub 0 &lt; αζ CvJ to CM CO LO CSJ tn LO CM CO LO CM r- LO CM 00 s σ &gt; uo CM 1 04 CO Csl ro CO C ^ J to &lt; 〇 &lt; N 265A ΙΟ r ^. CO CM oo CO CSJ 〇 &gt; to CN4 o CM δ CSJ CO CSJ ID CO CM CM 45 593703 [Table 8] Alloy No. Alloy composition (mass%) Cu Zn Si Co Fe Ni Sn P Sb Zn-2. 5Si (Co + Fe + Ni) / Si Si / Sn Example 2 278 Residual 7.7 0.26 0.01 0. 04 0.02 1.77 7.050 0.269 0.147 279 Residual 8.3 0. 34 0.09 0. 03 1.73 0.05 0. 03 7.450 0.353 0.197 280 stub 9.0 0.35 0. 13 2.10 8.125 0.371 0.167 281 stub 9.0 0.40 0,26 2.00 8.000 0.650 0.200 cn S s oo 3 5 00 sos 〇 § § ssss &lt; 〇τ- co os CO o 04 s I OJ a &gt; CM ① Ll. oo o 'oooo 〇ooooo 〇 oooo 〇o 〇CO S g &lt; £ &gt; CP s CO CN OO CO in s CM ir &gt; 00 CO &lt; J〇oo &lt; 〇oo 吕 CO &lt; 〇 Another oo Ch a CO C QS 〇 + r5 ιη CO &lt; ό CO CO to CO ui co LO CO CO 00 &lt; x &gt; CO CO c6 oo ui co s ι CO CO to CO cS S s ΙΛ CO s P &gt; CO CO 1 S Cf &gt; 8 σ &gt; s 05 o cs XT 8 00 8 00 oo CO § Another s CO s CO O to LO sogo S OQ os &lt; 〇S CM 〇〇 &gt; 5 gssoo 8 S CO CO ssss CP &lt; £ &gt; CO LO &lt; £ &gt; ΙΛ &lt; · 〇cvj &lt; £ &gt; CO co s uS CO to CO S ui CD s to &lt; 〇LO &lt; 〇ss LO &lt; 〇ss LO &lt; 〇Ξ so Φ CM ( Λ o (0 S ε o &lt; α soso 吕 oooo § &lt; N CN os if oo 〇o c &gt; ooss CO eg two CO sg ra sso CO oooo ο 〇ooooooooo Ίλ CO CO co CO CO uo to oo &lt; £ &gt; s CO CO 00 CO CO &lt; a to to uo in co ιο o CM co 5 5; s ΙΛ i〇 one production o 'strict production r- production Producing r- r— r- o ′ Producing o Strict r— Producing o ′ γ5 〇0000 ΙΟ o σ &gt; o CO Γ- σ &gt; CO LO LO o CNJ a &gt; olol〇 卜 CO o 00 κ s KS in cvj 00 CvJ 00 CM C £ &gt; CSI ui CVJ, CNJ cvj c \ i &lt; 〇c \ i ur &gt; c \ i uS CNi &lt; d CM id C \ i cd CSI to &lt; N cd CM oc \ l csi ss 3 — 〇〇00 r- to &lt; 〇CVI o LO OJ uo CVJ Bu σ &gt; 〇 &gt; xr strict &lt; 〇CO oo CO CVI CO to F: 00 CO factory 〇co f: in 04 evi co c ^ i 00 CD 5 ui csi 00 &lt; 〇〇〇Au zs CO so co CO S co L〇CO P— g CO σ &gt; o CO co CNJ CO CO CO &lt; CO LO &lt; 〇CO co co oo co 〇 &gt; co s CO s CN CN CO CO eg co s CO LO cs co 1 «; Jin co 46 593703 [0 i]

(% sse οι) 迤 迤 α C CO CO oo Csl g csi oo in CM Csi CO CM c \ io 8 uo c \ 4 &lt; 〇〇 &gt; CSJ csi CO 5 o in &lt; Ni l〇〇 0 T &quot; · to CO CO 00 s &lt; 〇 &lt; · 〇ai s CO 00 § o 00 CSI LO 00 CO CNJ CM CsJ CVJ ζ ΐ &gt; lu b CO o &lt; £ &gt; in oo 3 ooc \ i if oso LO sosoo in so LO go oo go oo CO oo S o Csi CO odoo 〇 &gt; soo CO so Γ— 〇l〇osoo CO O osd CM S 〇S o CO CO rr5 g L〇CO g LO CO s ui oo s LO CO g K § to CO g ub CO 00 m ub CO Another cd CO &lt; £ &gt; CSJ σ &gt; CN CO &lt; Nui CO sssg CsJ 05 sss CO CO &lt; 〇CO ΙΛ CO FIN CO CO CO CO 〇LO CO CNJ CO id CO o &lt; 〇CO iO &lt; £ &gt; OJ ur &gt; CO &lt; 〇CO LO 1 3 to 00 s CO CO s 0¾ CsJ sss CN CO oss s' o CO s S co CO CVJ CD to CD LO CO CN &lt; x &gt; t K ub &lt; JD R; i0 CO s LO 2 CM C7 &gt; s &lt; £ &gt; CD IX &gt; CO in s' csi &lt; 0 &lt; £ &gt; in &lt; 〇ss 〇2 s CO CO CO in CD &lt; 〇 &lt; 〇s 5 ud &lt; 〇s o 'Ren Art o Μ s 〇oo JO s 〇 &gt;-soso Cs4 CSJ o CO dgo CO o oo ooogo CO o CO CM ogo CO 〇 LO O '8 or— r— oo &lt; 〇o § o ζ soooso CO ooosos o 'o O s O' sooso oo 芒 osdso LO oo 〇O 'g O o' 〇SO sogdsososdsdod to osogogo ur &gt; CD o CO o CO CO uo CM 5 ΙΛ 00 uo LO L〇TO CO CO uo uo 5 CSJ to CD L〇σ &gt; LO g £ σ &gt; to CsJ 00 s O) r— lO m ιο o; 5 〇 &gt; uS CM 00 csi o K CO cb CM &lt; £ &gt; LO CD CVi Osi &lt; 〇csi CO so to s 00 CO cvl CD CM 〇ub csi o id CM CSi in CM to to C \ J CO 16 CM 00 csi csl a &gt; cd eg o &lt; d CM CO CSi CO CD CVI ui 04 S pair &lt; £ &gt; CM bu csi &lt; N 5 CO c ^ i CO o LO f: r- CM Csi bu CO o bu CVi c〇CVJ 〇 2 o CO 00 csi σ &gt; pi to in plant 00 bu 〇 &gt; plant LO eg CvJ Bu CO 00 Factory to te. &Lt; α ζ CO CM CO Bu CM CO 00 CN CO 0¾ &lt; Ni CO R CO CO CO CVJ CO CO CO CO CO CO LC CO CO CO CO CO ζ〇CO 00 CO CO s CO CO σ &gt; CO CO o CO CO CO 5 CO ΙΛ CO CD CO CO § oo § CO s ro E CO 47 593703 [L Yishu]

Si / Sn 6.905 11.429 8. 778 13.583 17.889 CO CO 10.286 13. 583 6. 273 8.947 un co ur &gt; Bucc &gt; s CO σ &gt; CM 9.333 12. 600! (Co + Fe + Ni) / Si | 0.062 0.056 0.063 0.055 0.062 0. 041 0.063 0. 043 0.159 0.053 0.063 0.064 0.160 0.075 0.060 0.286 0.042 0.052 0.047 0.081 0.048 0.048 0.074 0.044 0.048 0.054 Zn + 6Si 35.30 34. 50 34.78 34.58 34.76 34.76 33.18 34.84 35. 28 35.08 35.40 32.44 34.86 33.10 33.46 34.46 . 98 36.08 34.70 I 35.00 | 35.38! 35. 32 35.20 35. 96 34.92 34. 82 35. 08 35.16 34. 78 1 Alloy composition (ma ss%) Cu_5S ί 64.400 65. 270 64.920 65.170 65.013 66.152 64.930 64.530 64.480 64.320 66.550 | 64.840 I 66.250 65.700 64.740 63.690 65.270 64.860 64.552 64.470 64.680 63.840 64.930 65.030 64.763 64.730 65. 090 0.02 | Λ oo &gt; 0. 03 0.02 &lt; h 0.02 Q- s 〇0,14 oo 0.12 0.05 | 0.27 0.08 0.06 | 0.09 | 0.03 1 0.04 〇 oo o CM 〇g 〇cn to o 〇CNJ 〇OJ CN 〇 &lt; y &gt; o 04 〇 &gt; o CN4 〇CO o CM 00 o 0.18 0.05-O o 0.04 0.05 soso 0.06 0.05 oo 0.02 〇oo 0.03 5 〇ιί 005 007 0. 07 0.05 1 0. 06 CO o 0.06 0.03 0.02 0.02 007 0.04 Ί 0.13 0.02 0.05 0 03 so 0.02 0,03 0.04 0.04 o 0.05 0 02 0.02 CN 〇§ o 0.02 0.12 0.06 0.09 0.07 0.07 0.06 005 GO | Λ S CO LO CO &lt; 〇CO oo CO CO CO o 5 ΙΛ 〇00 CO &lt; JO oo to &lt; 〇T- CO S r- rj &lt; NI CM ss 2 r5 &lt; 〇CSi 〇 &gt; s CO ib CM CO s to CM 〇 &gt; CVi CM LO LO CN oo C £ &gt; CVI CM uo CM 00 oo C \ J 26.4 28.6 s CO CN4 CO 26.3 LO CVi 26.8 25.0 26.2 26.3 «£ &gt; CN to 5 25.9! 25.2 24.7 3 CO CO 00 00 og CO CO CO in 04 Cvi inch CO csi oo CO σ &gt; 70.0 o CO OO cb C £ &gt; ro c6 c6 CM 〇 &gt; CO 72.4 o CO ID CO ¢. Juan Such as z CNJ CO CO CO 〇〇lO CO in LO CO CO LO CO to co CO LO CO cr &gt; uo CO S CO s CO &lt; N CO CO CO CO CO i LO cr &gt; CO CO r ^ CO CO oo c〇 Γ0 a &gt; &lt; 〇 CO 〇 CO CO CO CO CO L £ &gt; CO &lt; £ &gt; CO r- K 00 00 M

48 593703

[CVJLS alloy composition (ma ss%) Si / Sn 5.536 1.519 10. 67 19,25 CO 7.818 8. 471 [14.36 I 7.684 4.571 1-938 | 3.378 2,125 7.048 (Co + Fe + Ni) / Si 0,057 0. 050 0.032 0.056 0.086 0.047 0.057 0, 088 0.056 0.065 0.045 0.048 0.064 0.052 0.054 Zn + 6Si | 35.80 32.78 35.10 35.94 34.50 33.52 33.74 35.08 35.16 35.20 34.80 34. 96 35.18 35.50 | 35.40 34.56 | 33.70 34.28 | 35. 58 Cu-5 860 66. 300 64.610 63. 850 65. 270 66. 052 65. 943 64. 660 64.472 64. 750 65.100 64.900 64. 700 64. 350 64 200 64. 700 65.750 64.850 64 · 100 0.07 0.03 0.06 T ~ ol〇. 02 004 〇 * r— 〇0.02 so 0.08 0. 07 so CL 0. 06 I 0.04 0.06 0.08 006 0.08 0.06 j 0.05 | 0.06 0.05 0.03 0,28 j 0.81 uo Τ Ο 0.08 0.14 0.22 0. 17 Ί— ^ o σ &gt; T &quot; ... o ΙΛ CO 〇LO &lt; £ &gt; o 〇C &gt; 4 〇O-〇 丨 0.06] 0.03 0.04 0. 05 0.07 Τ Ο I 0.03 〇o 0.08 0.02 0.07 0,08 0. 02 0.01 0. 06 0.09 go 0. 11 I 0 07 I 0.06 0.06 so CO CVI *? — Ssgr— CN T · &quot;-5 S r— un LO r— O CD CVJ CO CO LO in r—- g &lt; 〇CS1 lo CSJ CO in T— · CO 26.5 25.4 25.5 &&lt; £ 5 Csl 24.9 CN CO &lt; N T1 &quot; &quot; L〇CN 25.6 26.4 25.9 24.6 id CM &lt; NJ CSJ | 25.8 27.0 CSJ QD CSi r · ** LO CM 26.7 &lt; 5 CO jr * ^ uo r— ^ CO 卜 CO 卜 3 CN 00 Factory uo &lt; 〇CO CM VW Cvj CM o 72.0 LO Csj in 1 ?. 〇 &lt; QZ 0¾ CO § CO T— GO CO Cvf 00 CO CO 00 CO Ye 00 CO uo 00 CO &lt; £) CO CO r ^ 00 CO CO 〇〇CO a &gt; 00 CO 〇σ &gt; CO T &quot; &gt; * OD CO &lt; N4 0¾ CO CO σ &gt; co CO L〇〇 &gt; CO a &gt; CO r · '»Cn CO

49 593703 [CoLs alloy composition (ma ss%) Si / Sn 4.720 6.857 0.297 | ir &gt; a &gt; 0,571 0.189 0. 257 (Co + Fe + Ni) / Si 0.063 0.096 0.063 0.250 0.031 0.522 0.504 I 0.764 I_ 0. 527 0.059 0.106 1.556 Zn-2.5Si to 10.20 14. 90 20. 60 30.10 34. 80 s 〇r &gt; 16-80 -0.85 | ------- i 16.30 16. 60 ss oo 4. 38 00 in S 00 s od CO ΙΛ &lt; 0 00 CO cb S 8.15 7.68 O- 0.08 12 · 10 I 0. 25 丨 0.21 ″ in 00 CM r— 1.33 3. 50 j £ &gt;-in to o 0. 26 | 0.28 0.62 | 0.26 &lt; s 0.09 0.05 0. 03 δ o 0.08 0.59 | 0.17 0.09 0,07 0.42 Ίλ 0. 32 00 5 t— CSJ LO 〇0. 48 0.04 S cvi CO T— CO CVJ r— CN O 'CO in CO o 0.66 ΙΛ 〇r5 CO iri CM O &lt; J &gt; 00 lO CT &gt; c〇c \ i 〇 &gt; CT &gt; &lt; y &gt; oo csi OO CJi oo CQ o oo σ &gt; CM 〇σί 00 OO 00 &lt; 3 94 . 70 89.80 | 85.10 i 79.40 69. 90 65.20 88.32 82. 08 96. 47 78.36 79.78 96. 69 LT &gt; CO 5; 86.41 | 87. 88 | 87.05 | 8 8,43 88.20 I 86.90 88.51 85 · 97 88.30 ί ?. Copper 〇 &lt; πζ o CNJ o CO o I ogogo 〇 5 5 CN T— CO 5 5 in 5 &lt; 〇5 5 5 oo 5 σ &gt; 5 § τ — 50 593703 [Table 1 4] Alloy material No. Alloy composition (mass%) Cu Zn Si Co Sn Cu-5Si Zn + 6Si (Co + Fe + Ni) / Si Si / Sn ratio 423 69.80 30.2 69.80 30.20 424 64.90 35.1 64.90 35.10 425 74.97 23.8 1.23 68.82 31.18 426 66.81 31.9 1.25 0.04 60.56 39.40 0.032 Comparative example 2 427 74.74 23.0 2.21 0. 05 63.69 36.26 0.023 428 65.85 32.8 1,25 0. 10 59,60 40.30 0.080 429 67, 12 32.5 0. 35 0. 03 65.37 34. 60 0.086 430 68.80 29.3 0. 92 0. 05 0.95 64.20 34.82 0. 054 0. 968 431 73.31 23.7 1.80 0. 04 1,15 64.31 34,50 0.022 1.565

51 593703 [s Ls hanging mm CO Ο ί &lt; 〇cvj CSJ Cn4 csi CM C \ J o O o &lt; 〇CO cn CO CO 2 o CO CO CO CO σ &gt; «〇 二 Oi CO m • R m Miscellaneous m Jian〇〇〇oooo 〇〇 @ ◎ ◎ &lt; 3 o © ◎ ❾ © ◎ o @ ◎ ◎ &lt; oooo @ ◎ 〇 (Q ηη S SS Η SS @ o O oo ◎ o &lt; 1 o &lt; O ◎ © ◎ ◎ &lt; &lt; 〇〇〇 o &lt; 〇o &lt; &lt; &lt; 1 &lt; 3 o ϊ M- s: M vn two CM two: CO CM CO OO σν CM CO CO CO CO oo Ο Ok CO 二 aoo a &gt; 00 OO os Μ Another MM mm cone \ E ',. 2 mm Csj tn CO Si &lt; £ &gt; CO oo &lt; 〇IA € 0 to 〇g Q0 OO oo &lt; 〇 卜 m r- ir &gt; cs | r- ^ i un c〇sn S s &lt; 〇1 60 s »CO CO to CM 〇 &lt; 〇〇 &gt; CO &lt; 〇in oa o CO eh in s 〇〇 &gt; CO to LO &lt; 0 \ E ·, zmmi in r- vn Csi O CO at ur &gt; CSI 〇 »m &lt; 〇in ο r- 2 09 Oi WO CO 1Λ CO CVJ U) CO (〇to CSi &lt; 〇 &lt; 〇 € \ J ① u &gt; iO UU) &lt; 〇CO CO o LO CM CM 09 s ΙΛ CO mo «σ C \ J (〇iO s CO tx &gt; CO OO oo u &gt; ii &gt; iO 鲰 m η 5 I #: in 5 Ln right 5 5 5 c〇〇oo ci 5 &lt; hc〇〇o CO CO oo n?; CO e〇〇ϊ Γ〇 cT ε E, z m &lt; 〇cn Ol CO σ &gt; CO 00 CQ 09 CS | ΙΑ OJ 4Λ 00 ir &gt; CM «〇00 〇 &gt; s ΙΛ CM \ r &gt; eg sm 〇0 ir &gt; U) ot〇〇 &gt; S CM i〇 2 CO 00 in Oi LO CO 〇 &gt; LO CO CD in s 00 m ① in 〇5 E, z Peng 00 CO C \ J ns CO 〇 &gt; CO CO GO CM w C3 s CO s ▼ ir &gt; ir &gt; c 〇cr &gt; CO CO u * &gt; CO 5 5 0000 CO i cn CO ro CM Ch 〇 &gt; CO Oi O u &gt; ss CO ooo CO la 〇 &gt; CO σ &gt; C4 卜 ro Ci mm bS slope w 5 g CO g CO s 1 § o S CO s S CO g CO S CO S ΓΟ oo CO SL〇O ooo S cn oooosc〇o 〇S osg SJ Η, a csi &lt; N | 00 〇〇σ &gt; Bu 〇 CvJ 卜 m 1 «&lt; 〇« 〇csi BU Yan CO CO CNJ ir &gt; QO o CNI CM eg u &gt; σ &gt; Bowl 4 »&lt; α 0 z 〇s &lt; sssoggso-&lt; CM ro ΙΛ c〇〇0 Ch% £ &gt; Bu 00

52 593703 [9 r skimming] Electrical conductivity (% IAGS) Two CO LO CSJ CNi CSJ CM co CM CO CO csl Two CO o 200 00 CM CM cvl C \ J Two CSi c &gt; 4 Stress corrosion cracking resistance ◎ ◎ 〇 ◎ ◎ O o ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ o ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ o ◎ Twisting workability 1 (post-processed material) &lt; ◎ ◎ ◎ ◎ o ◎ &lt; ◎ ◎ o &lt; 1 ◎ &lt; 3 &lt; 1 ◎ 〇 ◎ ◎ ◎ ◎ ◎ 〇〇o 〇o &lt; ◎ | Mechanical properties (post-processed material) | Elongation (%) CNJ CS-〇 &gt; 〇 &gt; a &gt; 〇 &gt; CM r- in CvJ 〇 &gt; CO CO o two two CM-CM CSJ two o.-| Tensile strength (N / mm2) CO CSJ s iO BU s S BU CO § 〇 &gt; Gans «〇〇 &gt; 00 &lt; 〇ss CO o oo a CO § m 窆 CO LO Γ- S 卜 o S CO s CM &lt; 〇a &gt; &lt; 〇to m cT ε ε ζ • R Am m CO &lt; a to &lt; £ &gt; ci (O a &gt; sgs &lt; 〇00 &lt; 〇i CO along o K CM CNJ to s CO 00 m in S 8 CN Γ * · ¢ ^ 4 eg mo &lt; £ &gt; LO along ss§ CO § &lt; 〇00 LO ς〇s u &gt; § s &lt; 〇I mm 1 elongation (%) 00 η o Ο o 筅 o V〇CO o co oo 00 CO CSj o to o CO § 1 tensile strength (N / mm2) y CN S CO t— CO s in smol〇s in s σ &gt; ΙΛ LO i £ &gt; m pair 0 &gt; α &gt; &lt; N pair i CO 8 ss u &gt; Ώ s r- s CNi to in sm CO m CO LA § LO Ε Ε 2 m CSI Csl an co LO co CO CO CO co 8 5 Pair CO Γ ^ · LO CO σ &gt; 00 CO LO CSI CO m &lt; 〇g CQ CO 5 ol〇s CTJ 04? CO CO &lt; 〇CO 〇 &gt; cS I recrystallization temperature (° C) i 〇o § io wear io 1 1 so wear o § s CO S co S CO O guide i 〇 wear i 〇 5 oio wear 1 i 710 (5) | o iO oiso Wear average crystal grain size (U m) LO LO Bu CO CO 04 CO Inch CO o CO 〇 &gt; Bu CO csi CO Strict CO csi CM CO CO CO OJ cs c ^ i CO 00 CO Alloy No. 5 g 5 2 &lt; 〇CO CO &lt; 31 CO § 5 CO 5 ΪΛ TO ο ssssss 154A | gs K s

53 593703 u i] i) Hydrazine &amp; suspect m ΤΓ

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Icol hi &quot; ΤΓ CNIl oi hi ΤΓ zi m ^ .00 UJUi / z) 乸 网 ¾¾ 0089 ss 1 / N) 14af (%) Hanging% 劁 loou m § 80b 5 hb C5 i § § εεζ. § Icnlu 1S19 s 01 01 1 § Igl os 69 69 so i — lol ssl la9 i C9S isi 5 0 εΐ9 § 9U § § IUP119 § ICOIS9 si i1§1 s 59 § i 1819 091101 §

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on 691 891 bu 91 991 ltn9l Isll Isll Islt 191 091 6SI sst m 0 0 ISl support § lq &gt; la loola s 汔 a sa ί m 0 W SI- 54 593703

[Οοί] Conductivity (%! ACS) c5 CT &gt; CN S5 C ^ J 〇 &gt; CM s Si cO CM Si IX) OJ s to C »4 &lt; 〇OJ? 5 Stress corrosion cracking resistance 0 〇〇〇〇 〇〇 &lt; 〇oo 〇〇〇〇〇〇 ◎ &lt; o &lt; 〇〇〇0 0 &lt; 1 〇〇〇〇 5 irs ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ○ o ◎ o ◎ ◎ ◎ &lt; 1 ◎ ◎ ◎ ◎ &lt; &lt; 1 1 mechanical properties (post-processed material) fe elongation (%) 1 LO inch ΙΛ CO-CM o CVJ CO c〇CO 〇a &gt; oo &lt; NI eg &lt; Λ Γ0 CM c \ i CM 〇 &gt; cn 1Tensile strength (N / mm2) IS other to iO 馨 in XT JCSJ ΙΛ s LO o uo CO L〇S om lO CO to sgom oo s CO s CM in CM s ΙΟ m S 〇ms Csl Csf s II E £ ',, Z -P Am ms S Γ ^-5% to s ΙΩ 00 inch 8 LO to 10 LA S s uo 〇s to s to s oo CQ QD 5 a &gt; co CO LO oo lean ΙΛΛ | mechanical properties 1 elongation (%) CJ 茺 〇o; oi? § VO CO wear § CO LO Γ0 1 tensile strength (N / mm2) cS CO device &gt; CO s CO s ro a &gt; g CO $ CO &lt; N CO eg CO C \ J lean s oo s to CO CNJ s 04 J〇CO 寸 inch 〇CO CO LT3 CO a &gt; o &lt; 〇CO OO 〇 &gt; CO § s CO 1 Q0 CO Μ Ε ε 、. ζ -R 4m m δ ο, &lt; N | s C \ JJ £ &gt; CSi s C ^ J s CM S Csi 〇0 &lt; 〇CM 0 ^ 4 CM CO LO sn CM w CSJ 04 CM s CO &lt; 〇CM g CO CVJ Bu LoCVJ in Csj CM CM CO &lt; 〇in CM CO 00 CM s C \ J § 1 s CO recrystallization temperature (° C) s CO s CO 53005) iis CO s CQ I gs to 520 0 00) s S o Xinhan ss CO ii § io wear iii 1 o wear 5 average crystal grain size (/ im) CS &lt; CO CO csj CO csj 00 00 CO co c \ i &lt; N eg 00 c \ ic \ i CSJ V eg in CM * LO c \ i &lt; \ i CO Csi oc \ i O CO GO evi inch 00 evi &lt; NJ alloy No, gs CM 202A s CM I in s 1 § oo s § ca 209A o &lt; νϊ 04 OJ CO 04 u &gt; OJ 04 Bu CN oo CM 〇 &gt; OJ s CNJ &amp; csl Csj cv »CM s C \ i eg% Csl C \ J 55 593703 [6 ί]

1 lead ratio ι | (HiACS) 1 CO LO CM 1Λ CM CO CM GO eg CM CSI Cv | Qb CO CM stress corrosion resistance 1 corrosion cracking | ◎ 〇〇o O 0 ◎ oco 0 ooo 0 〇o 〇 ◎ ◎ ◎ ◎ oo OO ◎ ◎ | Bending workability | (Post-processed material) | ◎ ◎ ◎ ◎ ◎ 〇〇 ◎ ◎ @ ◎ o 〇〇 ◎ ◎ o ◎ ◎ 0 o ◎ ◎ ◎ &lt; ◎ 0 ◎ | Mechanical properties ( Post-processed material) I 1 elongation (%〉 | 〇CO CO = CO CO CO CO CNi-Csi CM 二 CO Ro n-CM 〇r &gt; = o-EE mm #: CO swallow a &gt; u〇ur &gt; 〇 &gt; xr oo LO to 00 m uu &gt; CM LO o LO CO U) LO with 10 m LO with L〇ο &lt; 〇CVi u &gt; 1 s &lt; x &gt; ΙΛ &lt; 〇through co to ss co CO Cp CO K〇CO CO% 〇 &lt; 〇w E ε z • P m to 荽 〇〇5 eg i u &gt; K p · | 474 I a &gt; σ &gt; co CM uo Another LO 〇lS CO LO ί; U- &gt; lO 5 i oo s 1 σ &gt; σ &gt; ir &gt; QO 00 LO i & &lt; 〇s LO Ob un g * 〇I Mechanical properties | elongation (%) o CO nn 〇Ojl oo ο &lt; n General CO CO 00 n wear 00 M | tensile strength ( N / mm 2) &lt; 〇1 04 V CO σ &gt; s CO eg OJ Xi CO Male LO CO CD CO o Xi CO 8 Xi &gt; to co &lt; v &gt; 5 3 GO to cn CO ro 1 co per iM E 8. 、, z • F mms 00 σι uo CSi § 8 CM CM s CSJ to CM to CM CO ς〇 (NJ CO CO co CO ro CO ίο Γ〇co CO in CN s CO CO m co co &lt; 〇CO s CO u &gt; a &gt; co Lf &gt; o CO s CO I recrystallization temperature i ° C) 8 o 5 $ 1 i 1 8 to ss 8 inch 8 § s CO 8 § 8 s to s CO s CO 1 8 i § I 520 (20) | I Xin § 1 圏 i a? E (5 Csl csi cn csi &lt; N 00 CO to CO CO CO cn 〇CO 00 c \ i 00 csi bu csi CO CO CO 00 00 CO bu Bu 00 I alloy 0 z? 5 CV4 §3 eg nest CNJ cs CO CSJ CM LO Csi ^ £ &gt; CO CM ro ro CM oo η CSI CSI § S CM CVJ co csi 3 to OJ s GO CM Ol CM s CJ 250A | ίο C \ J s CSI CO eg 3 CVJ 56 593703 【03 术】 m § mi to 04 CNi CO CM CN? 2 g OO s CM 04 m CM ro 04 CS &gt; CM r &gt; cnj ro mm 0 0 〇〇 &lt; 3 〇O 0 ◎ ◎ 〇〇 ◎ ο ◎ 〇〇〇〇〇o 〇〇 ◎ 〇 ◎ ◎ ◎ ◎ 1¾ srS ◎ ◎ &lt; 1 ◎ &lt; 1 〇 ◎ o ◎ &lt; ◎ ◎ 〇 ◎ 〇 ◎ ◎ ◎ o ◎ ◎ ◎ ◎ ◎ ◎ ◎ ○ i HH m 1 inch per m CM 〇2 CO C \ J CM C \ J 〇 &gt; CM eg CM CO two C »J to CO CM CO CM Csi: 〇 &gt; ro = &lt; NJ σ &gt; (s〇iUJ / N &gt; 萆 藤 封 冴 | CM m &lt; J &gt; VO s (O o to 〇D LO CM n &lt; 〇s uo 00 CO CD 2 to s (O sc〇8 Bu cp in g LO sc〇% m «〇〇00 Ln c〇00 ΙΛ ss &lt; 〇〇 $ s Γ ε ε ri m rr § «〇 &lt; 〇ss to oo tr &gt; R u &gt; to to s inch CO tr &gt; to m aluminum to s to OO CO € 〇oo to s CO s CM 75 s to S 茭 UD L〇CM ϊΰ s un 1 in 茺 CO 鲰 m π I ί u 5--o fj CV | oo § Wear 0 o Wear n LT3 CO cv ε E, zm Proto CP CO cn Cvj s ξ 5 1 § SI fs 1 a 1 ^ r CO i CO l〇go section LO i Han lf &gt; CNrf 〇 &gt; N Ε Ε ,,, ΐ Am ms CO (〇〇 &gt; CO i 3 CSJ is ers s CO ms CO iO ss CO CO § CO Γ0 s 8 CO S CO s CO oc〇§ CO CO CSI CO CO s § s CO stub CO iS P ms CO iii 1 1 i I siis § cold LO i 8 ii 1 I i I § i I is inch (uii〇s 猓 习 鞞 刼 鞞 刼 ro oo CSl o CM o iT &gt; OO 卜 卜 00 〇CO o evi cr &gt; eg o eg GO to o csi 卜卜 CO t ?. Remove 〇 ^ α z LO U) CM s CM in eg s CM s CM s CN4 s CNJ s CN cs stub CM &lt; 〇CM 〇) &lt; 〇CM s CM so Csi δ CM CSl CSi in «Ν4 CO OJ 00 CM Λ CM s C \ J oo eg 57 593703

[T 3 operation] (SOVI%) CO CO CO CO CO Osi &lt; 〇IX &gt; Γ0 CN4 C \ j-CO CNJ CSI csl CM C \ | P— eg CO two Csl CNJ 00 Csi m iy mm 0 &lt; &lt; 0 〇 &lt; 1 &lt; &lt; 〇〇〇〇 〇〇〇〇〇〇 &lt; 〇 &lt; 〇 &lt; 〇 &lt; 〇 &lt; 〇Si SHS e 4 | W »r S 〇〇〇 〇o 〇〇〇o &lt; 〇 &lt; &lt; 〇ooo 〇o O o 〇0 oo 〇 &lt; o H • S 1¾ mnm 1 t: «Q« 〇to CO CO &lt; 〇in &lt; 〇to in CO CO r- &lt; 〇 &lt; 〇b &lt; 〇LA &lt; 〇ur &gt; &lt; 〇 &lt; 0 (zUjuj / N) 萆 藤 靱 冴 1 Oi CM &lt; a to oo CD IjO p * (O b i bu CNi &lt; 〇bu cS oo zs oo 斉 〇% 04 CM oo &lt; 2 &lt; M cn oo CO &lt; 〇to s eg s § i NE ε -P mm u &gt; CO to oo in (O CO s CO in 00 CO m 00 CO 〇 &gt; s eg CQ KO &lt; 0 CO p: O) OJ CM § &lt; 〇in CNJ 00 CM CO CO o &lt; 〇S a &gt; LO uo U) &lt; 〇1 CO LO CO CO Csl 窆 m co oo Assign m% m? U t: Domain CO CO ΙΛ CO CO to ro LO CO CO CO cn CO ΓΟ n to CO LO CO C £ &gt; CO &lt; 〇CO to Γ0 l / &gt; CO Cst co 〇 &gt; CO &lt; £ &gt; CO 茺 LO CO to ΓΟ cS CO in co CM E, ε 2 m network CN in 00 ίο ΙΛ ro so ir &gt; ID s e &gt; ur &gt; inch LO 5 in σ &gt; LO § to s ΙΛ ςρ s ID S «〇〇 &gt; l〇m CO &lt; 〇in &lt; n to CO to CO 5 15 Ln to mss LLn CM EE., Z -P mmo ccsi oo This CO in CO C \ J LO CO I s &lt; Ni LO and ΓΟ S CO CO CO s CO &lt; £ J ns CO CM CO | £ &gt; co &lt; D CO oo CO CO σ &gt; co co LO C \ i σ &gt; co os CM 〇CSI s CO CO 〇 &gt; CM smm ^ 〇 〇8 P m 8 〇i LO Xia 〇co s CO 1 〇g Cl s 0¾ s CO sc ^ &gt; sns co s CO s CO 0 1 m S CO s CO s CO 〇§ 1 s CO s CO § s CO s CO s CO s CO (Uirt) CM o 〇 &gt; oo O) CO cn r ^-CM CO 〇 &gt; &lt; 〇co 04 CO csl cn oi csi CO 卜 cv CO c ^ i oo c \ i «〇csi oo c \ ic \ i 诨. Copper 〇 &lt; nzi 8 s CO s co LO CO o% CO S oo &lt; r &gt; C \ J CO 〇5 «! To co? 〇r- 60 &lt; Λ s co CO CM CO Si c〇in eg co s CO 58 593703

[3ZS conductivity (% (ACS) CO CM CM Cs &lt; Cj CO CM 22 OsJ CM CM CM CM-CM co cn OJ CNJ 2 CN 2 CM CM stress corrosion cracking resistance &lt; 3 &lt; 〇 &lt; 〇0 &lt; 3 oo 〇〇〇〇〇〇〇〇〇〇 &lt; 〇 &lt; O o 〇〇〇〇〇〇〇 bending workability (post-processed material) 0 o 0 &lt; 1 0 o 〇 0 0 o 0 〇0 〇o 〇 &lt; o 〇 &lt; 0 〇〇o 0 &lt; 〇0 | Mechanical properties (post-processed material> 1 1 Elongation (%) | CO CO VO to ir &gt; CO uo LO CO «〇Γ-« 〇 &lt; a CO m to C £ 3 LO CO ur &gt; I tensile strength (N./mm2) &lt; 〇in CM &lt; y &gt; s 8 00 s CO s CO CO 〇 &gt; oo § Bu CD 〇 &gt; (〇s Nuo Cxi S3 CO CO 00 〇 &gt; CM OO LO UP oo r ^-s p- s 1 σ &gt; Bu oo 〇00 〇co oo ✓ ** N CSJ ε ε ζ R mmm to CO σ &gt; TO CO CO 〇 &gt; CO &lt; D oo Cf &gt; CO $ C £ &gt; o eo CD CO oo &lt; D a〇00 &lt;〇2; eg VCO CVJ OO ss ggs QD LO ss co &lt; 〇O) s ⑦ CQ ς 〇 § s § 1 Mechanical properties 1 Elongation (%) &lt; 〇ro u &gt; CO WO ro CM ΓΓ) tn CO in CO CO CO LO CO &lt; 〇cn CO ro &lt; x &gt; CO 荛 CM CO cn kO CO co co to CO co co CO 茗 o co 1Tensile strength (N / mm2) i £ &gt; CO LQ 〇 &gt; Wear to S PAN U &quot; &gt; ir &gt;c; m un LT5 CD LO ΙΛ &lt; SJ s A u &gt; in LA § eo QD Cb CO in LO s ur &gt; LO &lt; 〇CO ΙΛ ΙΛ s 00 ffi s CO s P ^ CSI in 1A O in m CM CO ur &gt; Ε Ε-, 、 z pmm cn CM CO 泽 CO 笃 CO s CO% ns CO S CO ςPi CD CD CS CSJ LO CO L〇 &lt; 〇CO i in CO CO oo o CO &lt; 〇 &lt; 〇CO Tung et al. CO s CO s CO co 09 s CO co C9 CO (OO) Ln 07 Recrystallization temperature &lt; ° 〇〇m CO s CO s ΓΟ s CO s CO S g CO s CO s CO s ro s CO s CO 640 (5) s CO s CO 〇ur &gt; co oo 〇in ro s co s CO s CO s CO 〇in CO s co s CO os CO s CO average crystal Particle size (/ im) CO cvi CO cvi in inch to &lt; Q 00 Csj oo c \ i bu c \ i CO csi CV 〇j CSI cvi CSi CSJ 04 cvi 00 ro csi &lt; £ &gt; cvi o co csi tn cvi oo C &gt; 4 cc \ i bu csi 〇 &gt; in cvi CNi c \ i Alloy No, CO CO CM c〇σ &gt; CSI ro r〇co CM CO ro CO CO C O CO CO CO CO co CO CO CO 茺 ro 338A CO § s C? Ro co &lt; y &gt; u &gt; co &lt; 〇 OO S bud C7 cn c? S CSI LO CO 〇〇 ΙΛ

59 593703 [ε3 «]

Conductivity (% IACS) CM CVJ CVI Two CM C \ J c \ &lt; Two CNi CO Inch Two &lt; 〇csj 04 0 * 4 &lt; M CSJ CM CO CNj csi CM eg Csj C \ 4 Stress corrosion cracking resistance 〇〇〇〇〇〇〇 &lt; oo 〇 &lt; &lt; 〇 &lt; o OO 〇ooo 〇〇o O ooo Bending workability (post-processed material) o 〇o &lt; O 〇oo &lt; oo &lt; ο &lt; oooooooooo O 0 &lt; o I Mechanical properties (post-processed material) _ rate (%) m LO mc〇 (〇l〇CO CO LO &lt; 〇CO CO &lt; 〇to &lt; x &gt; LO &lt; 〇CO &lt; 〇 &lt; 0 CO &lt; 〇m | Tensile strength (N / mm2) i〇CO 00 &lt; 〇CO CO m CO 00 00 1 s 00 § i OO 5 s LO (O 00 CO cn &lt; 〇 S3 BU CO CO 00 s QD wso BU CO os CO CSI CO 00 r- CSJ s co 00 Γ EE, -P fine m LO 04 CM co CO σ &gt; capacity oo 〇 &gt; § § in 〇 &gt; LO &lt; 〇CO to 07 eg &lt; 〇I 〇 &lt; 0 00 &lt; 〇tr &gt; CO 〇 &gt; 8 &lt; 〇 &lt; 〇 窆 s CNJ &lt; 〇 &lt; 〇tn o &lt; 〇§ | Mechanical properties Elongation (%) CO CO 荛 un CO CO n CM ro Li 00 CO &lt; JD 07 r- CO c〇co (〇CO in ro ro CO m to CO to oo LO 00 荛 CO ro CO CO | Tensile strength (N / mm2) o to CSi IT) QO in OQ〇in s ΙΩ s &lt; £ &gt; to in order LT3 s 1 Ln CO ΙΛ CO oss CO CO in lf &gt; to 00 s ts ts CO m CO to 0¾ s 00 tn lo in &lt; 〇CO LO CO in m &lt; 〇s CM ε 2 Am m oo J £) CO S 00 s 00 QO CO 00 to CD 00 CO to CO 5 CO in s 〇 &gt; CVi CO σ &gt; co CO; 00 CO CO LC 00 in CO co CO nest CO to 00 co 〇 &gt; ro CO CD CO CO recrystallization temperature (0〇sos CO s CO CO s CO s CO s CO o U7 CO s cn o u &gt; C5 s CO ss CO o U3 CO I s CO s CO 〇to CO s co s CO 〇CO s CO om CO o to co s CO s CO S CO s CO Average crystal grain size (μm) CJ CO xr Γ0 xf CO CD CVI ro CNi CNJ CO σ &gt; csi bu csi LO eg CO CXI evi to c ^ i &lt; QC ^ j OO 04 csi ya C \ J CO c \ i bu c \ i bu evi c \ j Alloy No. so to to LO CO in co 00 s CO s CO &lt; 〇CO CM ro c〇V c〇 &lt; s ro &lt; 〇 &lt; 〇ro bu os CO a &gt; &lt; 〇ro 〇co ro cr &gt; co art r〇LO CO &lt; 〇ro 00 c〇 CO O oo CO W Medical CO

60 593703 [inch 3 skimming]

Electrical conductivity (% IACS) CNi CM two CM CM C \ l CM CXJ CO CM CNi csi CO two csl Stress corrosion cracking resistance 〇〇〇〇〇〇o 〇 &lt; 〇〇〇〇〇〇〇〇3H »pS 〇〇 &lt; 3 o 〇〇0 o 〇 &lt; 〇o &lt; 1 〇 &lt; 3 〇1 mechanical properties (post-processed material) 1 I elongation (%) CO CO ur &gt; C £ &gt; CO (D &lt; 〇 &lt; £ &gt; &lt; 〇LO LO in to uo | Tensile strength (N / mm2) 1 CM OO CD uo GO ΓΟ S s OO σ &gt; CSJ OO o ΙΛ bu s OO OO OO 〇 &gt; w sound s OO in OO &quot; ε ž • mm mm CM a &gt; CD &lt; J〇r- co GO 〇 &gt; CD s CI7 Ln r- 00 CO CO OO g? LO LO CS BU 1) 00 &lt; £ &gt; CO CD CO CD i / d Ui r- S 1 Mechanical properties 1 Elongation (%) n CO Pi CO LO CO Pi cn r &gt; CO c? CM CO in co P &gt; CO io CO 1 tensile strength (N / mm2) 〇 &gt; CO mm 00 l〇l〇CO LO LD cs CO LO isoLO in to in cs in CO CO LO CM tr &gt; ΙΛ m to omi this in cT E z -P Am mg in σ &gt; 茺 to CO σϊ L 〇CO OO (O CO OO CO ΓΟ Csl Nu CO Csl gs CO CO lO CO CSJ LO CO CO S CO Recrystallization temperature (° C) s CO s CO s CO s co s CO g CO i 1 s CO s CO s Γ0 s CO s ro s OO s CO s ro average crystal particle size (pm) in CN m cvi CVJ CO cvi vs. C'J CVJ o CO σ &gt; c \ i CO CO csi cvi CO cvi CO c \ ic \ j a &gt; LO csi Alloy No. CO co OO CO Xi CO CO UP &gt; 00 CO 00 CO OO CO CO OO ro σ &gt; CO CO § cn 5 &gt; CO CVJ 〇 &gt; OO CO 〇 &gt; CO σσ &gt; ro 〇 &gt; CO s CO s &gt; CO 61 593703 [93 »] m £ CM CO s CO 04 L〇CNJ CM ς〇GO CO &lt; am CM I mm 趄 ◎ 〇 &lt; XXX &lt; X © XX ◎ 〇〇〇〇oooo 〇〇1 〇hr Ig irS ◎ ◎ ◎ oo &lt; &lt; 〇 ◎ XX ◎ ◎ XXXXXXX 1 XH Fu an 鹚 S i i CO nt CSJ o 00 CSI LO in to &lt; 〇CO LO CO m LO oo 1 L〇cT EE, z00 茺 LO CM to s LA CO m in oo in § to GO a &gt; f: & lt 〇CO toto s 00 CM oo CM CM to oo oo &gt; COCO s 1 00 NEE 2 mmm Ά 00 CO u &gt; Order co 5; § to to CSJ LD ^ sr 3 OO GO &lt; 〇CM CO cn O CO a &gt; CO 卜 CNJ s &lt; 2 &lt; 〇CO CO (Ο i in CO to 1 s 〇〇mmm I if t: cut 5 in o through CO CO CO CO m CO «Ο CSJ CO?; 00 CO 1 CM CO C4 E 5 mm &lt; 〇CS | CM cs n CO m CD CQ 〇 &gt; &lt; 〇1 00 OO CO s CO 00 〇 &gt; IX &gt; &lt; M CM u &gt; 00 CNj CO CO CM «£ &gt; o in § OO CO to to CM IX) 1 oi? CVJ ε, E z Fine m oo CJ &gt; s CM o og CSI s CM TO CM i: CO CO o cn CO 1 &lt; £ &gt; «〇CO LO (P CO vs r ^ · k〇CQ I LO 〇 &gt; CO m Rl ^ Tank pmww S CO S co s CO s CO 1 § s CO s cr &gt; S o § o guide o guide s ro ossos pair o wear s CO 1 s &lt; E m 5i welcome w in &lt; d O one in tn LO LA o 〇 ¥ in Cvi CO in tn m CO CO &lt; 〇CM CSI oc \ j 1 &lt; £ &gt; 芘. Pin 0 &lt; α ζ is | s 1 iio CM CO L〇 &lt; 〇r- CO a &gt; inch 62 593703 [9 3 hemp] Electrical conductivity (% IACS) oo cvj 1 ro I CO CM 1 Stress corrosion cracking resistance XX 1 XIXX &lt; J 1 Bending workability (post-processed material) 〇o 1 X 1 X o X 1 | Mechanical properties (post-processed material) 1 1 Elongation (%) ί 1 cs 1 csi Bu csi 1 1 Tensile strength (N / mm2) 1 σ &gt; s 1 CO l £ &gt; 1 CO m &lt; £ &gt; &lt; 〇b 1 cT ε, bow ζ-ρ mm CO C9 ID ΙΛ 1 LO s 1 SB c〇C \ 4 LC 1A CO c〇1 | Mechanical properties 1 Elongation (%) J OO CO 1 oo c \ i 1 〇 &gt; eg 1 ㈧ Ε ε ζ mm 闼 〇 &gt; 1 in 1 s I 1 Ε, Ε 5 Am Peng CO CO CSJ CO Csj 1 CO CO CO 1 CO C7 oo &lt; Q CO CO 1 recrystallization temperature (° 〇1 § 1 s CO 1 s CO s CO s CO 1 average crystal grain size (i / m) in to 1 oo csi 1 b o 〇 &gt; csi 1 Alloy No. CO CM 5 § CD CM s OO CSI 〇 &gt; CM i 5 擗 Sex 63

Claims (1)

593703 Patent application scope: 1. A high-strength copper alloy 'characterized in that the alloy composition contains 4 to 19 mass% of Zn and 0.5 to 2.5 mass% of Si (the gates of these contents have Zn-2.5 · Si = 〇 ~ 15maSS%), and the remainder is copper; it has a crystalline structure with an average crystal grain size D of 0.3 // mg D ^ 3.5 // m, and it is safe at the end of the resentment. The limiting stress is above 250 N / mm2. 2. The high-strength copper alloy according to item 1 of the scope of patent application, wherein the composition of the master alloy further contains 0.005 to 0.005 mass% of c0, so that the value of c0 content divided by Si content Co / Si becomes 0. 〇〇5〜〇.5. 3. The high-strength copper alloy according to item 1 of the patent application range, wherein the alloy composition further contains 0.03 to 1.5 mass% of Sn, so that the value of the Si content divided by the Sn content becomes si / Sn of 15 or more. 4. If the high-strength copper alloy according to item 2 of the patent application scope, wherein the gold composition system further contains 0,03 ~ l 5mass% 2 Sn, the value of &amp; content divided by the content of Sn Si / Sn Become ι 5 or more. 5. High-strength copper alloys, such as in the scope of patent, item 1, where: σ to the composition system-further containing 005 ~ 0.3mass% Fe and / or U05 ~ 0.3 hidden Nl, so that the total content divided by the value of the content (Fe + Ni) / Si becomes 0.005 ~ 〇6. As stated in the patent claim 3, a high-strength copper alloy, wherein the alloy composition is further-further containing 0.005 ~ 0.3maSS% Fe and / or 0.005 ~ 0.3 to discuss Nl, so that The value obtained by dividing the total content by the content of si (Fe + Ni) / Si is set to 0.005 to 0.05. 7. As stated in the patented high-strength copper alloy for workers, the 64 593703 alloy composition further contains 0.005 to 0.003 mass% Fe with Ώ, and / or 0.005 to 0.3 mass% Ni, so that A value obtained by dividing the total content of these with c0 by the content of s · (Fe + Ni + Co) / Si becomes 0005 to 0.5. 8. If the high-strength copper alloy according to item 4 of the scope of the patent application, in the meaning, the alloy composition further contains 0.005 ~ 0 · 3mass% Fe and 或 and / or 0.005 ~ 0 · 3mass% Ni is such that the total of these and c0 contains | ^ | divided by the Si content (Fe + Ni + Co) / Si is set to 0.005 ~ 0.5. 9. A high-strength copper alloy, characterized in that the alloy composition contains 4 ~ 17mass% of Zri and 0 · 1 ~ 0 · 8maSS% of Si (there is _ηZη-2.5 · Si = 0 between these contents) (Relationship of ~ 15mass%), and the remainder is copper, exhibiting a crystalline structure with an average crystal grain size D of 0.33.5 // m, and the 0.2% safety limit stress in the recrystallized state is 250N / mm2 or more. 10. The high-strength copper alloy according to item 9 in the scope of the patent application, wherein the alloy composition further contains 0.005 to 0.5 mass% ic0, and the value of the content of c0 divided by the content of Sic0 / Si It becomes 〇 · 〇2 ~ 1.5. 11. The high-strength copper alloy according to item 9 of the scope of the patent application, wherein the alloy composition further contains Sn of 2 to 3 mass%, so that the value of Si content divided by the Sn content Si / Sn becomes 0 or less. . 12_ The high-strength copper alloy according to item 10 of the scope of the patent application, wherein the alloy composition further contains Sn of 0.2 to 3 mass%, and the value of Si content divided by Sn content is Si / Sn to be 0.5 the following. "1 3. The high-strength copper alloy according to item 9 of the scope of the patent application, wherein the alloy composition further contains 0.005 to 0.3 mass% Fe and / or 0.005 to 0.3 mass% Ni, A value obtained by dividing the total content by the Si content 65 (Fe + Ni) / Si is 〇_〇2 ～ i 5 14 · As in the scope of the patent application] 弟 W 11 high-strength copper alloy, where: The alloy composition is further to the right a ^ 0 · 005 ~ 〇3mass% Fe and / or 0.005 ~ 0.3mass% Ni, and the value of the total content divided by the Si content (Fe + Ni) ) / Si becomes 0.02 ~ 1 already 1 5 · As applied for a patent Wei Wei n high-strength copper alloy according to item 10, where the alloy composition further contains right η 3 ^ 0 · 005 ~ 0. 3massG / 〇Fe and / or 0 · 005 ~ 0.3mass% of Ni ， 佶 兮 # p The value of the total content of the side temple and Co divided by the content of Si (Fe + Ni + Co) / Si is set to 0.02 to 15. 16 · As for the scope of patent application] [9]. 4 丄 Tule 12 copper alloy of high strength, wherein the alloy composition further contains 0.005 ~ 0.3mass% Fe and / or 0.005 ~ 0.3maSS% i N !, so that the total of these and c0 contains The value divided by the content (Fe + Ni + Co) / Si becomes 0.02 to 15. 17 · If the scope of patent application is the first! Workers, 2nd, 3rd, 4th, 5th, 6th, 7th, 8th, 9th, i0, 11th, 12th, 13th , Item 丨 4, item 丨 5, or i 6 The local strength copper alloy according to the above item, wherein the alloy composition further contains 0.003 to 0.3 mass% of each selected from P, Sb, As, Sr, Mg, Y, Cr, La, Ti, Mn, Zr, In, and An element of at least one of Hf. 18 · — A high-strength copper alloy, characterized in that the alloy composition contains 66 to 76 mass% of Cu and 21 to 33 mass% of Zn and 0.5 to 2 mass% of Si (these contents have Cu-5.Si = 62 ~ 67mass% and Zη + 6 · Si (32 ~ 38mass%)), showing a crystalline structure with an average crystal grain size d of 0.3 / D $ 3 · 5 // m, in the state of recrystallization. 2% safety limit stress 66 593703 is 250N / mm2 or more. · 19. The high-strength copper alloy according to item 18 of the scope of the patent application, wherein the alloy composition further contains 0.005 ~ 3 mass% 2 C0, and the value of the content of c0 divided by the content of si C0 / Si becomes 0.005 to 0.4. 20. The high-strength copper alloy according to item 18 of the scope of the patent application, wherein the alloy composition further contains 0.03 to lmass%, so that the value of the Si content divided by the Sn content becomes Si or more than 1 . 21. The high-strength copper alloy according to item 19 of the scope of application, wherein the alloy composition further contains 0.03 to lmass% 2 Sn, and the Si content is divided by the value of the Sn content Si / Sn to be 1 or more. 22. The high-strength copper alloy according to item 18 of the scope of patent application, wherein the alloy composition further contains 0.005 ~ 0.3mass% Fe and / or 0.005 ~ 0.3mass% of Ni, so that the total content thereof is divided The value of the Si content (Fe + Ni) / Si is 0.0005 to 0.4. 23. The high-strength copper alloy according to item 20 of the patent application scope, wherein the alloy composition further contains 0.005 to 0.3 mass% Fe and / or 0.005 to 0.3 mass% Ni, so that the total content is divided The value (Fe + Ni) / Si based on the Si content is set to 0.05 to 0.4. 24. The high-strength copper alloy according to item 19 of the patent application scope, wherein the alloy composition further contains 0.05 mass% Fe and / or 0.005 to 0.3maSS% Ni ′, so that the The value obtained by dividing the total content by the Si content ϊ (Fe + Ni + Co) / Si becomes 0.05 to 0.4. 25. The high-strength copper alloy according to item 21 of the patent application scope, wherein the alloy composition further contains 0. 005. 3mass% Fe and / or 67 593703 0. 5 ~ 0. 3mass 0 / 〇 of Ni Let the total content of these years &gt; and C0 be divided by the value of si (Fe + Ni + Co) / Si to be the value of (Fe + Ni + Co) / Si to 〇005 ~ 〇4.丨. For example, the scope of patent application for item 18's, item 19, item 20, item predicate, town crest, knot. 26. High-strength copper 1 &amp; of Leiy item, young item, 91st reading, 22 item, 23 item, ~ 21 Beyon 24 item or 25 item, among which, the total is detailed into 仫 &amp; 1 ▲ Bei Yu's zt) item how strong copper &gt; gold, where the alloy composition is ~ &gt; Mouth, step contains P, Sb and As content of 0.005 ~ 0.2maSS% respectively And ^ 〇〇03〜〇 · 3mass% of Sr, Mg, γ, Γ υ · w χ La, Ti, Μη and at least one of the elements, in the case of containing at least one of P, sb, As, the Wait until the content becomes 0.05% ~ 0.25% and delete 3%. 27. If the scope of the patent application is No. 1, No. 2, No. 3, No. 4, No. 5, No. 6, No. 7, No. 8 &amp; δ, No. 9, No. 1 Item, 顼, item 12, item 13, 箓 π Η brother item 14, item 15, item 16, item 18, item 19, item 20 kg 0 item, item 21, item 22, The high-sounding voice of the first, 24th, or 25th item is Renren /, Α &amp; copper alloy, which is obtained by plastic working (including processing rate of 30% or more; person 1, order processing) Plasticity is added to the material and recrystallized. J ,,,, and 0 are only available on the day. The high-strength copper alloy such as the 27th in the scope of patent application, will be = force :: material to complete, . . The recrystallized material is formed by heat treatment at a temperature of 1 ~ 1_ seconds. 2 9 · If the recrystallized material in item 27 of the patent application scope, * I. Difficulty copper alloy, it is cold rolled or cold drawn. The formed cold-worked material 30. For example, the high-order processing # U nr degree copper alloy of item 29 of the patent application scope, the material of the material is from 150 ~ 600 ° c, 1 second to 4 hours. The content and content of the heat treatment are Zr, In # I1 顼 23 顼 sexual force workers 68 593703. 31. If the high-strength copper alloy in item 29 of the scope of patent application is applied, it is a processed product made of cold-worked material into a predetermined product shape. 32. If the high-strength copper alloy according to item 31 of the patent application scope is obtained by subjecting the processed material to heat treatment at 150 to 600 ° C for 1 second to 4 hours. 33. If the scope of application for patents is 1, 2, 3, 4, 4, 5, 6, 7, 8, 9, 9, 10, High-strength copper alloys according to item 12, item 13, item 14, item 15 or item 16 Φ, which are rolled materials or processed products processed into a predetermined product shape. 34. If you apply for a high-strength copper alloy with the scope of items 18, 19, 20, 21, 22, 23, 24, or 25, it is a wire rod or Product processing material processed into a predetermined product shape. First, schema: None 69