TWI351439B - - Google Patents

Description

1351439 IX. Description of the invention: [Technical field of the invention] The present invention relates to a copper alloy excellent in hot workability of a high-strength, high-conductivity electro-mechanical part tool; in particular, for a small-sized, ancient semiconductor machine lead And the copper fittings for the terminal connectors are excellent in strength and ignorant bending workability before being machined. m raw, and has excellent heat [Prior Art] Copper and copper alloys are widely used in connectors, lead parts and flexible circuit boards, and are required for the progress of the emergency. The high performance of the machine and the need for small size and thinning have to be improved. (Strength, · · · · · · · · · · · · · · · · · · · · · · · · · · · · · · · = Increasingly, the lead frame materials for semiconductor devices are often made of heat-dissipating (precipitating alloys such as Cu_Ni_Si, Cu_Fe_p, Cu_Cr_Sn, Cu-Ni p, etc.). The Cu_Ni_P alloy is made of ρ" Finely precipitated and strengthened, and in Patent Document 1, it has been proposed to adjust Ni in the alloy,

The Mg component is reported to have an alloy that combines strength, electrical conductivity, and stress relaxation. [Patent Document 1] Japanese Laid-Open Patent Publication No. 2000-273562. SUMMARY OF THE INVENTION L-hanging, casting in copper mouth gold (for example, in continuous or semi-continuous casting) 1351439

In the middle of the ingot, the heat is dissipated by the mold. In addition to the difficulty in the number of scales, the interior will take some time to solidify. At this time, in the cold at the time of solidification or after solidification, the alloying elements having a content exceeding the limit may be crystallized or precipitated in the crystal or crystal grains. A copper alloy containing 1 or more of Ni and more than 2% of p has advantages of high strength and high electrical conductivity. However, at room temperature, it contains a large amount of Ni in the mother phase CU. -P is the reason why the Ni_p-based compound is precipitated or crystallized at the interface of the granules when the ingot is produced. Since the bright point of the (4)-based compound precipitated or crystallized by the Cu_Ni_p-based alloy is lower than that of the parent phase Cu (four), the solidification of the copper alloy may be uneven, causing internal deformation, and the stress or external force may cause the radiation system. Part of the compound is destroyed and cracks occur during the casting and cooling stages. Further, when the hot milk is heated, the cracking occurs similarly because the chemical compound softens or liquefies earlier than the parent phase. However, in the composition of the Cu_Ni_P-based alloy in Patent Document 1, Ni is 0.01 to 1.0%, and Ρ is 0·01 to 〇2%. Therefore, the above problem is not particularly recognized. An object of the present invention is to provide a Cu-Ni-P-based alloy which is capable of preventing cracking occurring during casting, cooling, and hot working, is excellent in high-temperature ductility, and is excellent in hot workability. In the inventors of the present invention, in order to achieve the above object, it has been found that a Cu-Ni-P-Mg-based alloy which is excellent in hot workability and excellent in strength and electrical conductivity can be obtained by the following configuration. The present invention relates to a copper alloy having excellent hot workability, which is characterized in that it contains Ni·· 1.00% to 2.% by weight (% of the component ratio in the present specification is % by mass). : 0.10%~0.50. /〇, ^^: 0.01〇/〇~0 20%, the ratio of the content of 1351439 to p Ni/P is 4.0~6 s. Humans contain Cr: 〇 〇 3% ~ 0.45 〇 / 〇 or B: 0.005 ~ 0.070%, and the rest are Γ .... U and inevitable impurities. In the above copper alloy, the size and shape of the Nl-p-Mg precipitates in the final cold-rolled milk have an aspect ratio a/b of 2 to 50 when a is a long diameter and u ^ is a short diameter. And the short diameter b is a batch of φ ^ E ^ precipitates (A) of 10 to 25 nm, and the precipitates (A) and the long nine ratio a/b are less than 2 and the long diameter a is such that the precipitates of 20 to 50 nm are recognized. The sum of the areas of (B) accounts for 80% or more of the total area of all the 7 precipitates in the copper alloy. Preferably, the present invention has copper having excellent eight-negative tensile strength of 700 MPa or more and a conductivity of 40% IACS or more, which has excellent hot workability and high strength for conductive electronic equipment. In addition, in the above composition, the total of v1 species of Sn and In is 〇〇1〇/〇 or more, and U0./. With T, the tensile strength is 75 〇Mpa or more, and the conductivity is a characteristic value of 40% IACS or more. The present invention can suppress the Ni_P_Mg compound by adding a specific amount or B to the Cu*Ni-P-Me strip into the a*r Mg糸 alloy. Precipitating or crystallization at the grain boundary, and more preferably by controlling the cooling rate to suppress the formation of coarse Ni_p_Mg-B and Ρ-β compounds. By using _ The high-temperature brittleness of the boundary and the improvement of the hot workability. The copper alloy having excellent hot workability of the present invention exhibits an excellent effect as a high-strength and high-conductivity electronic device. [Embodiment] Next, the composition of the copper alloy is defined in the present invention. The reason for the numerical range is explained along with its effect. UM 439 [Ni amount] Chuan has the effect of ensuring the strength and heat resistance of the alloy, and contributes to the following. It is opened with P: "The precipitation of lanthanide compounds and the improvement of alloy strength." However, if the content is less than 1 · 〇〇 %, the 蛊 method is only J. ", 沄 到 to the desired strength, on the other hand, if Ni contains more than 200%, 目 | 丨, 2 · · 0 /贞!The addition of heat will reduce the product and the electrical conductivity of the product will be significantly reduced. - And 'will make the long-diameter Ni-P-Mg system precipitates the rate of throwing hoarding sheep Increased, it is not good. If the total content of Ni and P (Νι + Ρ) exceeds 2 5〇%, the amount of crystallization of coarse particles will increase, and the precipitation of aging treatment will be better than g, . It is difficult to control the precipitation of fine Ni-P-Mg of 50 nm or less. The amount of Ni contained in the alloy of the present invention is 1.00 to 2.00%, and preferably 1.10 to 1.80% by weight. The [ρ amount] Ρ ′ and Ni are precipitated as a compound w p ^ ^ Gσ to improve the strength and heat resistance of the alloy. If the content of strontium is 0 / 10%, the precipitation of the compound will be insufficient, resulting in the inability to obtain the desired %. On the other hand, ρ contains more than 0.50. /. , Beij heat processing is prepared ^ ^ ^ ^ H ^ B he' and the conductivity is also significantly reduced. Further, since the Ni-p type mountain of the long-term operation is large, the area ratio of the p-out product of the alloy of the present invention is increased, which is not good. 0.20 to 0.40% is preferred.纟The amount is set to G.H)~0.50%’ and in [Mg amount]

The Mg' is precipitated in the form of Ni and p, and the 7575βW W 4 chelate, thereby improving the strength and heat resistance of the alloy. Further, if the shaped precipitates are not added with M to a higher strength. Furthermore, if you lack 姑, you can add 1 to Mg, which will produce Ni-P_Mg-based fiber, which is comparable to Cu-Ni-P alloy.

The strength of Mg solid-melting in the mother phase 1351439 it has a greater effect in the south, people 曰Α

When Mg 3 is less than %·〇1%, the desired strength and titanium resistance cannot be obtained. & + 旦# *''' 1 On the other hand, if the Mg content exceeds 0.20%', the hot workability is significantly lowered, and the electrical conductivity is remarkably lowered. Moreover, it will produce peaks &&&,,, and the precipitation of the ancestors, and hinder the improvement of strength. Therefore, the alloy of the present invention has a temperature of θ.〇ι〇/0~0.20% to 0.02% 〜0·15°/. It is better. [Ni/P ratio]

Even if the content of N1 and P is within the above range, if the Ni/P ratio of Ni to P deviates from the appropriate stoichiometric composition ratio of the Ni_p-based compound, that is, the solid-solution amount of p may be less than 4.0. Increase, not more than (a) is not good. because

The amount of solid solution of Nl is increased, and the electrical conductivity is remarkably lowered. Therefore, the alloy of the present invention has a Ni/P ratio of 4.0 to 6.5, preferably 4.5 to 6 Torr. [Size and Area Ratio of Ni-P-Mg-Based Precipitates] When the long diameter of the Ni-P-Mg-based precipitate is a-, and the short diameter is b (nm), the aspect ratio a/b is used. In the alloy, there are two kinds of needle-like and fibrous precipitates (A) having a large aspect ratio and a granular precipitate (B) having a degree of a/b=2〇~. By causing the processing deformation before the aging processing to "become less than 0.4 (to be less than full)", needle-like and fibrous precipitates are formed; by processing deformation before the aging processing becomes 0 · 4 or more, granular precipitates are formed. The reason for specifying the size of the precipitate is as follows: The short diameter b before the final cold rolling is a precipitate of less than 10 nm, and if the processing is performed, the precipitate is destroyed and decomposed and then solidified by 1351439. In copper, the conductivity is lowered, and the R is the other side. In the final cold rolling, the short diameter is more than 10 nm, and the precipitates are decomposed. Even if the processing is changed, the rolling process is difficult to rebuild. The π 十 士 士 and u 10 nm or more of the precipitates open > Especially the short diameter b is? The precipitate having n of 20 nm or more has a small change in size after rolling, and is melted by A^^. It is difficult to be destroyed in the 4th car, and the solid solution is more than 5〇nm, and the short diameter exceeds 25nm. (The precipitate 'can be kept in size after rolling, although it is large enough to maintain its size.' The dispersion interval of the precipitates of the precipitates of the large steel alloy t is thermally enhanced by precipitation strengthening and processing strengthening. Further, the long diameter a and the short diameter b are in the dry direction before final cold rolling. The direction is cut at a right angle. The square of the thickness is determined by the flat image analysis device. For all the long diameters...nm, the image is determined by the shadow and the length and the short diameter of all the precipitates are measured. 〇, the plate thickness after drinking is double; in addition, in the case of m „ .,. ~ L < if, the processing of the Go-shaped β system is represented by e = ln(tO / t). The final description of the alloy of the present invention The N "P-Mg system precipitated Ια width ratio 前 before cold-drying is 2 to 5° and the short-diameter and aspect ratio a/b is less than 2 and the long-path a is 2 () (B). The decomposition of 2〇~5〇nm is such that the Ni_p_ before the final cold rolling of the copper alloy of the present invention becomes a heterologous a & g system precipitate..., the aspect ratio a/b is 2 to 50 and the short diameter b is 1〇~2 eve λ τ μ 5nm, at the time The effect is that the good shape π is not full 〇.4 (to the full 〇 为 为 为 妯 n n n n n n n n n n ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± ± Width ratio a/b Λ 翥 曰 欲 欲 欲 欲 欲 长 长 长 长 长 长 长 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 135 The temperature and time during the aging treatment should be appropriately adjusted. However, since it is difficult to make all the precipitates in the preferred range of a and a/b, the above-mentioned ^a/b (8)

And (B) is important in the proportion of all precipitates. Therefore, when the ratio of the total area of the precipitates (8) and (B) in the preferred range of the above-mentioned //b is the ratio of the total area of all the precipitates in the alloy as the area ratio C, the area ratio of the present invention...〇 % or more... "All precipitates" Ni-P-Mg-based precipitates having a long diameter of 3 or more. In the case where the area ratio c is less than 80%, the precipitation of a exceeds 5 〇 and the division b exceeds 25 nm or the long diameter a is not full — or the precipitate of 1 Onm is short. . For example, a precipitate having a diameter of more than 5 〇 nm and a short diameter b °, η Π 1 and a crystallization product generated during casting, or a crystallization product generated during the casting is not subjected to heat treatment or solution treatment. The remaining l〇〇〇nm is in the presence of a large amount of Ν · ^ u ^ 丸 ^ The number of the particles is small, and the analysis of the range of the fine gauge of the milky process has become large, so the desired strength cannot be obtained by =. On the other hand, the long diameter a is less than 20 nm or the short diameter b is the same as that of the precipitated material. Since the precipitate is re-solidified by rolling, the desired conductivity cannot be obtained. For:: Invention of copper alloy before final chilling, aspect ratio

Ni-P, is the precipitate (4), and the length and width of the "A gold...": a is the sum of the precipitates (8) of 20~5〇nm, the sum of the areas of the copper coins, #__, before the aging treatment 1351439 In the case where the processing deformation 77 is 0 to 1.5, the temperature and time during the aging treatment must be appropriately adjusted. [Cr amount] Normally, the cooling rate at the time of solidification of the Cu-Ni-p_Mg-based alloy is slow, for example, the cooling rate from 1100C to 95〇t is less than 30. At (:/min), the Ni-P-Mg-based compound is concentrated, coarsened, and crystallized at the grain boundary, which is not good.

Cr can suppress the crystallization or precipitation of the Ni_p_Mg-based compound to the grain boundary during solidification and solidification of the Cu-Ni-P-Mg-based alloy during solidification, thereby improving the hot workability of the alloy. However, if the content is less than 0·03 /〇', the hot workability improvement effect cannot be obtained. On the other hand, if 3 has Cr more than 0.45%, state P Mg-Cr is generated during melting or solidification. a compound such as Cr-P or a crystallization of & Since these Cr-containing compounds and crystallizations are not solid-melted in the mother phase during the melt treatment, the Ni_p_Mg-based compound precipitated during the aging treatment is reduced, and the alloy strength is lowered. Further, a compound such as Ni_p_Mg_Cr or Cr_p, which is in the form of a crystallization or a precipitate of 5 μm or more, remains in the product, and becomes a surface defect of the product, a starting point of cracking during bending processing, or a plating treatment. The starting point of the defect is not good. Therefore, the alloy of the present invention has a content of 0.03% to 45.45% or less, preferably 〇〇5% to 〇鄕. [B amount] B can be suppressed in Cu- When the Ni-P-Mg-based alloy is solidified and cooled after solidification = and during the heating of the hot metal, 4 Ni_p_Mg-based compound precipitates toward the grain boundary crystal, so that the hot workability of the alloy can be improved. However, if the content is 12 1351439 If the content of B is more than 0.070%, the compound containing Ni_p_Mg_B or BP will be produced in the form of decontamination or solidification in the form of less than 0.005 / 〇 '. The compound containing B will be concentrated and coarsened at the grain boundary to crystallize or precipitate, and will not solidify in the Cu matrix during the solution treatment. Therefore, Ni P- precipitated during aging treatment. The reduction of the Mg-based compound leads to a decrease in the strength of the alloy.

Compounds such as Ni P-Mg-B, Β·ρ, etc. will remain in the product in the form of long-diameter 5 from the excess of the claws, which may become the starting point of the product, the starting point of cracking during the bending process, or the plating treatment. The starting point of the defect is not good. Therefore, the B content of the alloy of the present invention is set to be 0.005% to 0.070% or less, preferably 0.007% to 〇_〇6〇%. [Inclusions] 曰, the "miscellaneous matter" of the present invention means that the principal component of the crystal grain interface and/or crystallization or precipitation in the Cu-Ni-P-M "alloy" is a crime.

The crystallization of the Mg-B compound, the B_p compound or the like is not contained in the fine Ni_P_M$, 曰, Zn, etc. which are crystallized or precipitated. The long diameter of the inclusions refers to the average long diameter of the inclusions having a cross-sectional size of 5 mm. If there is a long diameter of more than 50, the abundance of a a*. , ^ inclusions will become a bending process 1 = the starting point of cracking, causing deterioration of the bending workability of the product. Therefore, in the steel alloy of the present invention, the number of inclusions having a long diameter exceeding 50 A" shall be 0 per lmm2. X, if there is a missing matter having a long diameter of 5 ^ containing ^ ^ m, then If there is any impurity h, the enthalpy will increase, so that the crystal which is suppressed can not be obtained: the effect of crystallization at the interface, that is, the addition of two materials cannot be achieved, so that the copper alloy of the present invention has a long diameter. By 1351439 is preferably 100 or less, and more preferably 50 or less. [Sn, In amount]

To borrow less

The amount of Sn and In has the effect of enhancing the strength by solid-solution strengthening without lowering the conductivity of the alloy. Therefore, if it is necessary to add to one of these metals, if the total amount of the metal is less than 〇〇丨%, the effect of improving the strength by solid solution strengthening cannot be obtained. On the other hand, if the total amount is more than 1.0%, the alloy is added. The electrical conductivity and f-mechanism are significantly reduced. Therefore, the amounts of Sn and In which are added alone or in combination of at least two kinds are 0.01% to 1.0%, and the total amount is preferably 0.05% to 8%. Moreover, these elements are deliberately added elements in the present invention, and are not inevitable impurities [quantity]

“It is easy to react with Cr in the alloy. If the alloy is in the shape of an oxide, the effect of Cr addition cannot be obtained. Moreover, p and b are also easily oxidized, especially if P is oxidized, and Ni-P is precipitated. The content of the alloy of the present invention is reduced to 〇〇〇5〇% or less, preferably 〇(9)% or less. [Tensile Strength and Electrical Conductivity] The steel alloy of the present invention is excellent. The hot workability is excellent in electrical conductivity, tensile strength, and bending workability. The tensile strength of the copper alloy of the present invention is preferably 70 〇 MPa or more, and more preferably 75 〇 or more. The degree of conductivity is 950 MPa. Further, the conductivity is preferably 4% IACS, and 45% IACS is more preferable, and the upper limit is usually 65% IAcs. [Cooling speed at the time of solidification and the size of inclusions] satisfying the above invention The Cu-Ni-P-Mg alloy of the requirements can be manufactured by the method used in the industry by the method of ingot casting, hot I melt treatment, intermediate cold rolling, In the aging treatment, final cold rolling, de- ing = annealing, etc., select the appropriate heating temperature, time, cooling Degree, rolling degree, etc.; and in the addition of B: 0.005% to 0.070% of the Cu-Ni-P Mg-B alloy, the solidification speed in the continuous or semi-continuous casting which is usually performed will be adopted due to the solidification stage. The device and the method are different, and in the case of a static injection type or the like which does not use a uniform cold portion mechanism, there is a difference between the outer side and the inner side of the ingot, for example, injecting bright copper into a mold made of iron (φ7〇〇χ1ι 1500 mm). In the case of the static injection type in which it is solidified, the average cooling rate from 丨1〇〇(>c to 95〇<>c is 1 °C/min. The solidification temperature of the copper alloy of the present invention during casting The range is 丨1〇 (rc to 950 C is preferable) If the cooling rate in this cooling temperature range is slow, the Ni_p_Mg_B system and/or the lanthanum-based compound are easily coarsened during the solidification stage, so that the addition of B cannot be obtained. The effect of the ductility is as follows: The number of inclusions in which the main component is a Ni-P-Mg-B system and/or a PB compound has the following correlation with the hot ductility. The cooling rate of 〇°C to 950〇c is 30〇c/min. The casting key is less than 8 5 〇C. After the time, the sample obtained by water cooling is measured, and the result of the inclusion is measured. The number of inclusions in the long diameter of 5 to 5 〇" m is more than one, or the length exceeds (9) When the number of the impurities is one or more per 〇^2, even if it is an alloy to which a certain amount of B is added, the hot rolling at °C may cause cracking. Therefore, the casting and solidification stages are 丨i〇〇(&gt The cooling rate of c to 950 ° C is preferably 3 (rc/min or more. Further, in order to avoid deterioration of the bending workability of the alloy, it is possible to suppress the coarse precipitation of the Ni_P_B-based compound and the p_B-based compound 15 1351439. The solidification stage is self-contained. 〇 to 95〇. The coldness of the crucible is preferably 85 ° C / min or more. Further, if the cold portion speed exceeds 15 〇〇 ec/min, the bright copper cannot be supplied to the solidification shrinkage portion in time, and the defects caused by the pores increase, which is not good. The copper alloy of the present invention to which Cr is added, the solidification temperature ranges from 1100 ° C to 950 ° C during casting, and the cooling rate in the cooling rate range is slower right, then Νι-Ρ and/or Ni_p_Mg The compound is likely to be coarsely formed during the solidification stage, and there is a concern that the effect of addition to improve the hot ductility cannot be obtained. [Examples]

Cu-Ni-P-Mg-Cr alloy (1) Preparation of sample: Electrolytic copper or oxygen-free copper as main raw material, nickel (Ni), I5% p-Cu master alloy (P), 1〇 %Mg-Cu master alloy (Mg), 1〇% CrCu master alloy (cr), tin (tetra), indium (10) as auxiliary materials, melted in a high-frequency melting furnace in a vacuum or in an argon atmosphere. 45x45x9〇mm ingot. The hot rolling test of the cast bond is carried out, and the cast bond which has not cracked under hot rolling is heated at 850 to 90 (heated for 5 to 12 hours under TC, and the core system, Wg crystallization, and solids produced when the scale is formed) After melting, heat-drying is carried out. At the end of hot rolling, the material temperature of the material temperature is 7〇0~85〇°C or more, and after heating for more than 0.5 hours, water cooling is performed to fully blizzle. The money 'sequential aging treatment, intermediate cold rolling, aging treatment, final cold rolling, stress relief annealing' was made into a thickness of 一1 flat. The various sheets were tested by test strips, and the "strength" and "1351439 electric conductivity" were carried out. Evaluation of the hot workability of the ingot: ^ ^ Plus "Sexity" is evaluated by hot rolling. That is, the ingot is cut to t2Μ5·, after heating under (4) for 1 hour, The hot rolling test of the 3rd stage = to 5_. The surface of the sample after hot rolling and the edge of the crucible are visually recognized as cracks. The evaluation is "η ιΑ ^ 'crack"' without cracks on the surface and edges. The evaluation was “no cracks.” Physical property evaluation of the test piece: “Strength” According to the tensile test specified in JIS Z 2241, the tensile strength was measured by breaking the BS test piece. The "electrical conductivity" was measured by the 4-terminal method and the resistance of the test piece was expressed by %1 milk. "Bending workability" It is evaluated by the 90 degree wf curve test. The system is based on CES-M0002-6, using (4) lmm of the coolness, and the 90 degree bending process is carried out with the load of 5 〇 coffee. The evaluation of the bending part is observed by the microscopic mirror. In the case of the surface, the person who has broken the rupture is "X, the bamboo stalker of the grade is "Λ ώ 4- tu it. r has △", and the good one is "〇". The bending direction of the bending axis is a right angle (Good way).

Evaluation of Ni-P-Mg-based precipitates: The alloy strips before the final cold-rolling were cut at right angles parallel to the rolling direction. Using a scanning electron microscope and a penetrating electron microscope cross-section precipitate for 10 fields of view. Observed. In the case where the size of the precipitate is 5 to 5 〇 (10), the image is taken at a magnification of 500,000 to 700,000 times (about 1.4 〇 ι〇ι〇~2() χ 1〇l〇nm2). The size is 100~2000nm. In the case of 439, the picture is taken at 50,000 times to 10,000 times (about i 〇χ ι〇13~2 〇χ ι〇ι; 2). Photograph of photography, using image analysis device (manufactured by Nileco Co., Ltd., trade name: Lujax), the long diameter a is 5 nm, and the precipitates are all #敎敎·^ diameter a, short diameter b and area . From the above, the precipitates are randomly selected from the total of the areas of all the precipitates having a long diameter a of 5 nm or more, and the aspect ratio a/b is 2 to 5 Å and the short diameter b is ι 〇 〜 The ratio of the area of the precipitate (4) of 25(10) to the aspect ratio a/b of less than 2 and the long diameter a of 2〇~5〇(10) is the sum of the areas of the precipitates (B) as the area ratio c (%) ). In addition, it was confirmed that the final cold-rolled (normally processed deformation) or higher, and the Ni p_Mg-based precipitate having a short diameter b of less than 1 〇 nm before the cold rolling was not observed by solid solution. The precipitate having a short diameter b of i〇nm or more retains its long diameter, short diameter, and aspect ratio after the final cold rolling. Further, the area ratio C of the precipitate is similarly unchanged after the final cold rolling. The copper alloy having the composition shown in Table 1 is compared with the comparative example by the embodiment of the high-strength high-conductivity copper alloy excellent in hot workability of the present invention. Further, in Example 1 & In the middle, the processing deformation before the aging treatment is 〇, and the temperature and time during the aging treatment are appropriately adjusted to obtain an alloy in which most of the precipitates are precipitates (A) (standard deviation i5 to 25). In Examples 3 to 5 and Comparative Examples 15'16 and 2, the processing deformation before the aging treatment was 1.4, and the temperature and time during the aging treatment were appropriately adjusted to obtain a large amount of precipitates as precipitates. (Β) alloy (standard deviation 3~W). On the other hand, Comparative Example 17 is called 8 and 19, and the processing changes before the aging treatment are respectively "for the QQ, the temperature for the aging treatment and the 1351439 • time When appropriately adjusted, most of the precipitates are alloys having an average major axis, a flat average short diameter, and an average aspect ratio (standard deviation: 8 nm for Comparative Example 17 and 2 nm for Comparative Example 18 and 23 nm for Comparative Example 19)实施In the alloy example of the present invention, 5' does not crack during hot rolling, and has excellent strength and electrical conductivity. On the other hand, it was reviewed based on the results of (4) 6 to 2Q, and Comparative Examples 6 to 9' were not added. Or the specified amount is not reached, so cracks occur during hot rolling. In the comparative example 1G, the amount of addition of p exceeded 〇_50%. In Comparative Example 11, the amount of addition of more than i 〇〇% in total of In, the amount of addition of Sn in Comparative Example 12 exceeded i 〇〇%, in Comparative Example 13 When the amount of addition was more than 2_00%, and the amount of Mg added in Comparative Example 14 exceeded (4), cracks occurred during hot rolling. The amount of addition of Ni in Comparative Example 15 and the amount of addition of P in Comparative Example 16 were all lower than the range of the present invention, so the strength was low. The ratio of Ni/P in Comparative Example 16 is higher than the specified range. Therefore, the amount of solid solution of Ni increases, resulting in a decrease in electrical conductivity. In Comparative Example 17, since the average long diameter of the precipitate was large, the strength was low. In Comparative Example 18, since the average long diameter of the precipitates was small, the precipitates were solid-melted during cold rolling, so that the electrical conductivity was low and the bending workability was also poor. 7 Comparative Example 1 9 produced fibrous precipitates (length and width) The ratio a/b is 2 to, and the short scale b is a precipitate (A) of 10 to 25 nm), but the short diameter is larger than the predetermined range, so the strength is low. In Comparative Example 20, since the amount of addition of Cr exceeds 0.45 Å/〇, Ni_p_Cr,

The compound such as Cr_P or Cr is crystallized or precipitated upon solidification, and the average long diameter a of the precipitate and the crystallization is deviated from the range of the present invention, and the area ratio C of the precipitate is low, so the strength and the electrical conductivity are both low and curved. Poor workability. 19 1351439

[1<] Perception rate 1% IACS Bub·5 »r> fS oj : 45.0 I oo VO 〇\ 00 r*· <> *T) Inch ri cs wS <〇mm S. Packing 4一•Ο 0C Ό (Ν 00 s 00 o 卜o Vi 00 % •o <N v〇ο «η UJ 3 •o */> 卜 v> § •n Bending workability〇〇〇〇〇※ ※ 〇〇〇<〇<1 Ni-P type precipitate area ratio c (%) 5; 00 Os 〇\ OS 5; ※ ※ ※ 00 σ\ 〇oo U-) Aspect ratio a/b 〇 ( N ν~) (Ν ΓΟ fS ※ ※ ※ <Ν 2 o 00 Average short diameter b (nm) 00 TJ- oo m 00 οο (N ΓΛ m σί o SO m | average long diameter! a(nm) 沄τί * Ο ν〇00 CN fO 卜ro ※ ※ m iN CN fS o Wi \〇Hot work processing no cracks no cracks no cracks no cracks no cracks I cracks cracks 1 cracks 1 cracks 1 cracks I Cracks have cracks, cracks, cracks, cracks, no cracks, no cracks, no cracks, no cracks, no cracks, no cracks, chemical composition (mass. /〇) Sn+ln 1 1 1 «〇»r> ogd 1 1 1 (N 〇1 <Ν m V-> « η 1 1 1 1 1 1 1 1 Ni/P 00 <τΐ \〇rt v-> 〇(Ν Ό vS Ο vS (Ν wS 〇»nv〇23.6 CN vS ΓΟ <τΐ — oo — 5 1 The remaining 1 I remaining I 1 remaining 1 1 remaining I 1 remaining | 1 remaining 1 1 remaining I 1 remaining I 1 remaining I 1 remaining I 1 remaining 1 1 remaining 1 1 remaining I 1 remaining I 1 remaining 1 1 remaining ι 1 remaining I 1 rest ι 1 rest I 1 rest I 1 I 1 1 〇 \ ΓΟ o 1 1 1 〇 \ 〇 1 fS VO o 1 1 1 1 I 1 I 1 1 1 ! 1 • nomd 1 1 1 m Ο 1 oo * η 1 1 1 1 1 ι 1 1 u 00 (N Ο mso 00 o ON <so 1 1 〇s ο is d 00 fS o w-> ο 00 rs 〇(N <N 〇00 ο in ο 〇\ CM 〇O «η fs o P os ο S Ο S ososo S 〇〇S 〇ο 艺 do S ο S 〇ro Ο s ο g ο osogo | 0.09 1 CL (Ν (Ν Ο CN 〇ΡΊ Ν 〇 o » 〇(N 〇00(N 〇00 (N 〇ο Ό ο fN omm ο 卜τΤ 〇fN Ο <- g ο (N 〇 oo (N oo <Ν 00 ON Ό ΓΛ •η (Ν 00 < N Ό ν〇!〇CS νΊ ΓΟ W-) 〇v-> VO <7n <NA ° ;〇d — (N ΓΛ <n VO 卜 00 ΟΝ ο aίΝ mv〇卜00 〇\ This example compares the example. ^^^^^咮鹖咮鹖碟长嵴"※":^^燃名痪<长<"丨"·-fr-啭 1351439

Cu-Ni-P-Mg-B series Inventive Examples 1 to 6 and Comparative Examples 7 to 20 (Table 2) Production of Samples (a): Electrolytic copper or oxygen-free copper as a main raw material, nickel (Ni) ), 1 5% P-Cu master alloy (P), 10% Mg-Cu master alloy (Mg), 2% B-Cu master alloy (B), tin

(Sn) and indium (In) were used as the auxiliary materials. The high-frequency melting furnace was melted in a vacuum or an argon atmosphere, and a 45x45x9 mm ingot was cast using a casting mold of cast iron. The hot rolling test of the ingot is carried out, and the ingot which has not cracked under the hot rolling is sequentially subjected to hot rolling, melt treatment, aging treatment, intermediate cold rolling, aging treatment, final cold rolling, stress relief annealing, and the like. A plate with a thickness of 15 mm. Test pieces were taken for each of the obtained sheets, and the evaluations of "strength", "conductivity" and "bending workability" were performed. Hot workability evaluation of wheel keys (a): , , ,, and processability are evaluated by heat drying. Material, will bond: Cut into 45x45x25mm, add at 850 °C! This is from the h" h L Bu heating for 1 hour, with 3 P are: and = 5_ hot rolling test. For the hot-rolled sample table, = edge visually recognizable cracks are evaluated as "have The crack has no crack on the edge and is smooth. It is evaluated as “no crack”. Physical property evaluation of 1 ° type test piece (a):

"Strength" is based on the tensile test of the dry test of the T-B test in JIS Z 2241, using the test piece. The tensile strength β π J "conductivity" is determined by the 4-terminal method. Representation" /〇lAc bending workability"

It is evaluated by a 90 degree W bending test. 21 1351439 The test is based on CES-M0002-6, using R=〇 lm

a,,,,,,,,,,,,,,,,,,,,,,,,,,,,, Bending section Micromirror observes the condition of the raised surface of the central part, and breaks it: the second is =: = = "△", and the good one is "〇". Bend 2 The direction of the milk is right angle (Good way).

Evaluation of Ni-P-Mg system precipitates (a):

The alloy strips before the final cold rolling were cut thickly in parallel with the dry direction, and were observed using a scanning electron microscope and a penetrating electron microscope = cross-section precipitate for 10 fields of view. In the case where the size of the precipitate is 5 to 5 〇 (10), the field of view is 500,000 to 700,000 times (about i 4 X 1〇1.

1〇10·2) Performing photography 'When the size of the precipitate is (10) to 2_nm, the image is taken at 50,000 times to 100,000 times (about i 〇χ ι〇η~2〇X). The length of the precipitates with a long diameter a of 5 nm or more were measured by the image analysis device (product name: Lukekes), and the lengths a and the area were measured one by one. 1 选取 is selected to be a precipitate having an aspect ratio a/b of 2 to 5 Å and a short diameter b of 1 〇 to 25 nm with respect to the sum of the areas of all the precipitates having a long diameter a of 5 nm or more (A) The area and aspect ratio a/b is less than 2 and the long diameter 3 is 2〇~5, such as the sum of the area of the precipitate (B) of the claw, and the ratio is taken as the area ratio, and it is confirmed that: By the final cold rolling (normal processing deformation 々 = 2 or more), the Ni p_Mg-based precipitate having a short diameter b of less than 1 〇 nm before the cold rolling is not observed by solid solution, and the short diameter b is l. The precipitates above 〇nm retain their long diameter, short diameter and aspect ratio after the final cold milk. The area ratio C of the precipitates is also almost unchanged after the final cold rolling. 51439

[s conductivity%IACS «ο ΓΛ cK r- «Λϊ «r> * ※ v〇〆fO trj •r» 3 ro v〇PO m to m cn CO V*) Tensile strength (MPa) 1 GO r- s 〇s 〇\ ΟΟ 00 r- 5: % (N 〇*nv〇Os v〇«Ν ν〇*Tt m 00 Ό !bend 1 processability 1 〇〇〇〇〇〇X 〇〇X 〇〇〇 Ni-P system precipitates * U彡« 00 ON «〇ON OS 〇\ 00 σ\ σ\ σ> % % % % oo *r^ On Ss 00 00 cs O ON Aspect ratio a/b rn o ( N ρ rf ※ Concentration 00 (N m to xn if鄣io 呀 mo (N o 00 fN •TJ CN «/> m % % ※ ※ <N <N v〇«η <N 00 rn inclusions Number of objects (pieces/mm2) over 50 β mo 〇o 〇Ο or^) VO 〇 O O O 〇ο o O o Ο c IT» C l it ΓΛ CS o (N s (N < Ν m § § I Ο 卜 inch p· P; m «Ν 2 hot rolling process without cracks no cracks 1 no cracks I no cracks 1 no cracks ι no cracks 1 cracks ι cracks cracks 1 cracks 1 cracks 1 Crack I 1 has cracks 1 no cracks no cracks no cracks no cracks no cracks no cracks no Trace 1100~950°C Cooling rate fc/min) ο oo 〇ο o ο s 〇〇〇〇〇ο ο o Ο Ο ο ο o 〇ο ΓΛ Alloy composition (% by mass) Sn+In 1 1 1 3 〇ο <N ΓΟ o I 1 〇1 JQ 〇ι 1 1 1 I 1 1 1 Ni/P ο wS V) r^i »n vS vS •r> »n cs irj *ri \〇vS ON (N *n Inch - »η叶ννΐ ir! 00 Tt — rn 00 ο »η 5 1 remaining 1 1 remaining II remaining 1 1 remaining 1 1 remaining I 1 remaining Ί 1 remaining I 1 remaining I 1 remaining I 1 remaining 1 1 Rest I 1 remaining 1 1 remaining 1 1 remaining ι 1 remaining I 1 remaining ι 1 remaining ι 1 remaining I l remaining ι rest ι c 1 1 i ο ο <N mo 1 1 1 1 00 VO 〇II 1 1 I 1 I 1 ζΛ 1 1 1 ο I 1 1 1 〇1 in 〇ι ι 1 I ι 1 ι 1 CQ 1 0.035 1 | 0.042 1 | 0.051 I 1 0.025 1 1 0.035 1 | 0.045 | 1 | 0.003 1 1 0.050 1 1 0.057 1 I 0.052 1 0.065 1 0.042 1 1 0.033 1 | 0.030 I 1 0.03〇n | 0.135 | | 0.060 1 | 0.057 | 1 0.009 by ο oodg ο ο o Art ο s ο ο m rj o 〇go 1 ooogd 0- (N 〇沄or^imd «η fS ο ο m 〇艺ο ON (N Ο 〇8 〇沄ο 0 0 (Ν Ο so <N 〇ίΝ (N o ίΝ (Ν ο ro o QJ oogd u-> v〇jn CM g ίΝ ίΝ \〇*η CN ΝΝ <N »r><N*r> ΓΊ Os 00 oo ό — <N rf V) 00 σ Ο & - < Ν ΙΛ ΙΛ » 00 00 Os Comparison of inventions. ¢κ*瘅3⁄4c¢铋 碟 长 长 长 " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " " An example of a high-strength conductive copper alloy having excellent hot workability will be described in comparison with a comparative example. In Examples 1 to 6 of the alloy of the present invention, cracks did not occur during hot rolling, and excellent strength and electrical conductivity were obtained. On the other hand, Comparative Examples 7 to 20 are alloys in which the composition deviates from the alloy composition range or the Ni/P ratio and the precipitate size of the present invention. In Comparative Examples 7 to 8, since B was not added or a predetermined amount was not obtained, cracks occurred during hot rolling. Since the amount of addition of Ni in Comparative Example 9 exceeded 2.0%, the amount of addition of p in Comparative Example 1 exceeded 〇_5〇% and the ratio of Ni/P deviated, and the amount of addition of Sn in Comparative Example u exceeded 丄〇%, and Sn in Comparative Example 12 Since the total amount of addition with In exceeds 丨〇%, cracks occur during hot rolling. In Comparative Example 13, since the amount of Mg added exceeded 0.20%, cracks occurred during hot rolling. In Comparative Example 14, since the long diameter of the precipitate was small (12 nm) and the area ratio C was 0, the precipitate was solid-melted at the time of cold rolling, and the electrical conductivity was low and the bending workability was also poor. In Comparative Example 15, since the precipitate was too large, the area ratio C was 〇 ', so the tensile strength was low. In Comparative Example 16, since it was not added, the tensile strength was low. In Comparative Example i7, since the amount of B added exceeds 〇070%, the compounds such as Ni-P_Mg_B and B_P are crystallized or precipitated during solidification, resulting in a decrease in the amount of precipitates of the Ni-P-Mg system, resulting in a decrease in strength and electrical conductivity. , bending workability is deteriorated. In Comparative Example 18, since the Ni/p ratio was lower than the appropriate composition ratio, the solid solution amount of p was increased, and the electrical conductivity was lowered. Comparing W 19, since the 沁/P ratio is higher than the appropriate composition ratio, the amount of solid solution is increased, and the conductivity is lowered. In Comparative Example 20', since the addition amount of Ni and p was lower than the range specified in the present invention, the strength was low. 24 1351439 Inventive Examples 21 to 26 and Comparative Examples 27 to 38 (Table 3) Preparation of Samples (b): Electrolytic copper or oxygen-free copper as main raw material, nickel (Ni), 1 5% P-Cu master alloy (P), l〇%Mg-Cu master alloy (Mg), 2% B-Cu master alloy (B), tin (Sn), indium (in) as auxiliary materials, using high frequency melting furnace in vacuum or argon environment In the atmosphere, 'cast 45x45x90mm or (|) 50x90mm cast key. Since the cooling rate during casting and solidification is changed, the material of the mold is iron,

Oxidation and oxidation. A thermocouple was inserted into the center of the mold, and the lioot: to 95 缚 was measured for solidification and solidification. (: The cooling rate is 340 ° C / min for the cast iron scale mold, 85 minutes for the alumina mold, and 33 c / min for the yttrium oxide mold. For the ingots with a cooling rate of 20 t: / min or less, In the direction solidification, the ingot was prepared at a cold heading speed of 2〇t:/min, 15〇c/min and 1〇t/min. The hot rolling test of the ingot was carried out, and no crack occurred under hot rolling. The ingot is sequentially subjected to hot rolling, melt treatment, aging treatment, intermediate cold rolling, aging treatment, final cold rolling, and stress relief annealing to prepare a flat plate having a thickness of 0.10 mm. Test pieces are taken for various sheets obtained. Evaluation of "strength", "conductivity" and "bending workability": Evaluation of hot workability of helium (b): The ingot was cut into 45x45x45mm or φ50χ45ππη at 85〇χ:_ after heating for 1 hour In the four-stage, the thickness test is carried out from the thickness of 45_ to 12% of the coffee, and the inclusion of the same type of test piece of the same type as the thermal evaluation of the ingot described above (b): The evaluation of the inclusions in the sample application is carried out as follows: 25 1351439 rows of hot rolling, 15 Body treatment, aging treatment, intermediate cold rolling, aging treatment, final cold rolling, stress relief annealing 'for thickness 〇 1. mirror-grinding of dry parallel sections of t-plate samples' by electron microscopy in _ times pairs 5, the observation of 5 fields or more of small inclusions (about 0.3WO, calculate the number of impurities per W. On the other hand, the crack in the hot workability evaluation of the tungsten bond in the ingot) After 8 hours of adding the machine, the water is cooled, and the obtained sample is evaluated for (4). The mirror is ground by the sample, and the inclusions are observed with the mirror to calculate the position of the board. The number of inclusions in the electron microscopy of the mother lmm. The alloy with good workability, the 4 mt, ·,,, the plate pattern and the water cooling after the ingot is added at 85 ° C for an hour. The comparison of the number of inclusions in the soil, the ', and the 'models' is roughly the same. The evaluation of the physical properties of the test piece (b): The "strength" is based on JIS Z 2241 Φ 丄 - 丄 ^ R ^ ^ Η ^ The tensile test of the standard, using 13 : B§ =: Determination of tensile strength, conductivity The resistance of the η ge) test piece is expressed in % IACS. The "bending workability" is evaluated by bending the M0002 6 * # p by 90 degree W. The test is based on CES-M0002-6, using R= 〇lmm fixture degree f-curve processing. Evaluation of the bending section "What is the negative 90 H: ^ A ® ^ fl* The condition of the central raised surface is observed by an optical microscope, and the crack is "△", which is good as " 〇^ X"' occurs in a good way ^ (Good way) 〇" 胄 crankshaft is perpendicular to the rolling direction 26 1351439

Ts t-rate%IACS 1_____ 52.2 51.5 51.8 47.6 46.7 45.8 w 38.7 36.2 5 w-> Tensile strength (MPa) 00 ro CO 830 l〇v〇00 870 875 V) 卜r- 5 CN (N v〇〆 ·, /·, Bending workability 〇〇<1 〇〇<3 % % 〇X 〇Inclusions (number/mm2) More than 50 amo ο oooo 〇\ τΐ- <N two s〇〇ο 〇 5-50 βη\卜卜(N m tN VO 00 § ΓΊ VD (N 卜 。 mos 热 热 热 热 热 热 热 热 mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos mos Crack I has cracks | cracks cracks cracks cracks cracks no cracks no cracks no cracks 1100~950° (: cooling rate (°C / min) 340 00 ro 340 00 m Ο 340 340 j 340 340 340 340 340 340 340 340 Alloy composition (% by mass) Sn+In 1 1 1 0.67 ] 0.65 | 0.63 I 1 1 1 0.61 | 1 1 °·54 1 1 1 1 1 !-35 1 1 1 1 Ni/P Wj VO vS m Ιτί CN 卜m >〇m uS in 卜卜々· m »ri V~1 (N ON r- Tt Tt m σ&lt ; (N vS wS remaining rest remaining 1 rest | remaining | remaining | remaining 1 1 remaining 1 remaining rest | remaining | remaining 1 remaining 1 remaining | remaining | remaining rest remaining | remaining I remaining = 1 1 1 1 0.35 I 0.32 0.31 1 1 1 0.30 1 0.29 1 1 1 1 0.70 1 1 1 1 1 1 0.32 1 0.33 0.32 1 1 1 1 0.25 1 1 1 o CO 0.65 1 1 1 CQ 0.038 ;0.035 ! 0.034 | 0.029 ] 0.031 0.033 0.038 1 0.035 1 1 0.039 1 0.033 | 0.003 0.002 0.055 0.056 0.057 0.044 0.040 0.025 0.135 0.050 i 0.06 0.07 0.06 0.06 0.07 0.07 0.07 1 0.06 1 0.06 0.07 | 0.05 0.04 0.07 0.08 0.29 0.05 0.06 0.05 0.04 0.05 Cu 0.23 0.22 0.23 (4) 0.25 0.26 0.22 1 0.22 1 1 0.23 1 0.25 0.32 0.31 0.44 0.61 0.27 0.26 0.27 0.12 0.26 0.13 2 1.25 ro CN (N Ν 〇〇 1.35 1.35 w-><N (N (N LL2LI 1.35 1.51 1.46 2.33 (N »r> 1.33 fN (N σ \二1 1.35 0.71 6 CM (N < N < N < N 09 a 〇CN m Ό r- 00 Os o Comparative Example of the inventive example. ^^^,^^^^^^^^"※匕:_'v"集矣痪<长<"-"*-6-啭1351439 A copper alloy composed of the components shown in Table 3, An example of the high-strength conductive copper alloy excellent in hot workability of the present invention will be described in comparison with a comparative example. In Examples 21 to 26 of the alloy of the present invention, cracks were not generated during hot rolling, and excellent strength and electrical conductivity were obtained. Since Examples 23 and 26 of the present invention have a slow cooling rate of 33 t /min at the time of casting, compared with the other invention examples, the number of inclusions is large and the bending workability is slightly inferior. The other aspects were reviewed in Comparative Examples 27 to 38, Comparative Examples 27 to 29, since U00 ° C to 950. (: The cooling rate is slow, so the number of inclusions is large, and cracks occur during hot rolling. Comparative Examples 3 to 38 are alloys whose composition deviates from the alloy composition range of the present invention or the Ni/P ratio. Comparative Example 3 1~ 32, since no addition of B or a predetermined amount was observed, cracking occurred during hot rolling. Since the amount of Ni added in Comparative Example 33 exceeded 2. 〇0/〇, the amount of p added in Comparative Example 34 exceeded 〇·5〇%. In Comparative Example 35, the amount of addition of Mg exceeded 0.20%, and the total amount of addition of Sn and in in Comparative Examples 36 to 37 exceeded 1% by weight, so that cracks occurred during hot rolling, respectively. Comparative Example 38 'Because the Ni/P ratio is lower than appropriate In the composition ratio, the amount of solid solution of p is increased to decrease the conductivity. In Comparative Example 39, since the amount of B added exceeds 0.070%, the compound such as Ni_p_Mg_B system or B_p system is crystallized or precipitated during solidification, resulting in Ni_P_Mg system. The amount of precipitates was reduced, the tensile strength and electrical conductivity were low, and the bending workability was also poor. In Comparative Example 4, since the amount of Ni added was low, the tensile strength was low. [Simplified illustration] 28 1351439

None [Main component symbol description] Benefit $ »*> 29

Claims (1)

1351439 X. Patent application scope: " i A copper alloy with excellent hot workability, characterized in that it contains Ni in a mass ratio of Ni: 1 ·〇〇〇/. ~2.00%, P: 0.10%~〇.5〇. /0, Mg: 0.01% to 〇.2〇%, the ratio of the content of Ni to P, Ni/P is 4.0 to 6.5, and contains Cr: 0.03% to 0.45 °/. The rest is composed of Cu and unavoidable impurities. 2. A copper alloy having excellent hot workability, characterized by containing Ni in a mass ratio: 1.00% to 2.00%, P: 0.10% to 05%, and Mg: 0. 〇1% ～0.20%, Ni/P ratio of Ni and P is 4.0 to 6.5, and contains Cr. 0.03% to 0.45%, and at least one of Sn and In is 0.01% to 1. 〇0% or less. The rest is composed of Cu and unavoidable impurities. 3. A copper alloy having excellent hot workability, characterized by containing Ni: L0~2.〇%, P: 〇1〇~〇5〇%, Mg: 〇_〇1% by mass ratio ~0.20% 'The ratio of Ni to P is Ni/p is 4 〇~6 5, and contains B: 〇.〇ι〇〇/0~〇070〇/〇, 苴余为• , ,你冯Lu和It is composed of inevitable impurities. 4. A copper alloy having excellent hot workability, characterized by having Ni: i in a mass ratio. ~2.〇%, p: 〇1〇~〇5〇%, Mg: 〇·(4)~〇·鸠, the ratio of the content of Nip is 4, 65, and contains Β: 0·005%~〇.〇 7〇% 'and contains "and in the middle" = 〇 〇 〇 1% or more, the following is recognized, and the rest is composed of Cu impurities. 5. Avoiding the charge 5. If the patent application scope is 3 or 4, the excellent hot workability of 30 1351439 copper gold, of which the length of the long diameter 5~5〇//m is (10) or less. And the number of lost objects exceeding 50"m is (10) per one. 6. A copper alloy having excellent hot workability according to the i or 2 of the patent application 'in which the size and shape of the Ni-P_Mg-based precipitate before the final cold rolling' is a short diameter of a... When there is at least an aspect ratio ^: 2:50 and a short " 10~2511〇1 precipitate (a), the precipitate (4), the aspect ratio a/b is less than 2 and the long diameter is 4 2〇~ The sum of the areas of the precipitates (8) is more than or equal to the sum of the areas of all the precipitates in the copper alloy. 7. If the copper alloy having excellent hot workability in the third or fourth aspect of the patent application is applied, the size of the mMg precipitate before the cold milk is 'the size of the long diameter and the short diameter of 卩b. There is at least a precipitate (A) having an aspect ratio 2 of 2 to 5 Å and a short diameter U 10 to 25 _, and the precipitate (4) has an aspect ratio a/b of less than 2 and a county a Α 9η is not two and long. It is more than the sum of the area of the surface of the product (Β) of the surface of the product (Β) of the sho. 8. The copper alloy with excellent thermal reinforcement according to item 5 of the patent application has a tensile strength of 700 MPa or more and a conductivity of 4% or more of iacs or more for users of high-conductivity conductive electronic equipment. 9. The copper alloy with excellent thermal reinforcement according to item 6 of the patent application has a tensile strength of 700 MPa or more and a conductivity of 4 〇% iacs or more for users of high-strength and high-conductivity electronic equipment. 10. A copper alloy having excellent hot workability according to item 7 of the patent application, which has a tensile strength of 700 MPa or more and a conductivity of 40% IACS 31 1351439 or more for users of high-strength and high-conductivity electronic equipment. 11. A method for producing a copper alloy having excellent hot workability, which is used for producing a steel alloy having excellent hot workability according to item 5 of the patent application; characterized in that it is self-twisting (9) to 95 (at the time of casting) The average cooling rate of rCi is 30 °C/min or more. I2. A method for producing copper alloy with excellent hot workability, which is used to manufacture the excellent heat of the fifth application patent. : The characteristic is: self-help in the praying to ~ the average is 85 ° c / min or more. »»>, schema: 32