CN101479396A - Cu-zn alloy with high strength and excellent bendability - Google Patents
Cu-zn alloy with high strength and excellent bendability Download PDFInfo
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- CN101479396A CN101479396A CNA2007800244517A CN200780024451A CN101479396A CN 101479396 A CN101479396 A CN 101479396A CN A2007800244517 A CNA2007800244517 A CN A2007800244517A CN 200780024451 A CN200780024451 A CN 200780024451A CN 101479396 A CN101479396 A CN 101479396A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/04—Alloys based on copper with zinc as the next major constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/004—Copper alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
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- H—ELECTRICITY
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- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
- H01B1/026—Alloys based on copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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Abstract
A Cu-Zn copper alloy which is for use in electronic parts such as terminals and connectors and has high strength and excellent bendability. The Cu-Zn alloy having high strength and excellent bendability comprises 20-40 mass% Zn and, as the remainder, Cu and unavoidable impurities, and has such crystal grain characteristics that the average crystal grain diameter (mGS) is 1-4 [mu]m and the standard deviation (sGS) of the crystal grain diameters is 1/3 mGS or less. In the alloy, the relationship {I(220)+I(111/I(200) between X-ray diffraction intensities in an examination of a rolled plane is 2.0-5.0. The Cu-Zn alloy may further contain any one or more of Ni, Si, Fe, Ti, Co, and Sn in an amount of 0.01-0.3 mass%. The alloy preferably has a sulfur content of 30 ppm or lower and has a surface roughness (Ra) of 0.2 [mu]m or lower.
Description
Technical field
The present invention relates to the high strength of in electronic units such as terminal/junctor, using, the Cu-Zn class copper alloy of excellent in bending workability.
Background technology
In recent years, the development of frivolous/short and smallization of electronic unit is more more remarkable than in the past, and is corresponding therewith, and the copper alloy bar of electronic component-use is also required to adopt thin material.But during the material attenuation, for the contact pressure that keeps junctor etc., the intensity of material itself must be high.On the other hand, in order to realize the miniaturization of electronic unit, for its function of performance in little space, bending machining is also implemented with little bending radius, demanding bendability.Therefore, require material to have the characteristic of high strength and good these the two kinds of mutual contradictions of bendability.
Accompany therewith, high strength copper alloys such as beryllium copper, titanium copper, Corson alloy class are also being used in people exploitation, and copper alloys in the past such as these high strength copper alloys and brass are compared and cost an arm and a leg, and therefore are not suitable for being used in the strict field of cutting down cost.
From this angle,, require its intensity or processibility further to improve for the general copper alloys such as brass that in copper alloy in the past, are considered to have higher mechanical strength.Processibility especially requires bendability good.
At above-mentioned requirements, for example put down in writing the scheme of the crystal grain miniaturization that makes brass in the patent documentation 1, reported in the non-patent literature 1 that the crystal grain miniaturization by alpha brass improves The Characteristic Study.
Patent documentation 1: TOHKEMY 2004-292875 communique
Non-patent literature 1: " copper and copper alloy ", No. 1, the 41st volume, 29-34 page or leaf, 2002 years
Summary of the invention
But the brass of the crystal grain miniaturization of above-mentioned patent documentation 1 and non-patent literature 1 still can't satisfy the quality requirements of the strictness aspect the bendability of high strength and excellence nowadays.The crystal size of 70/30 brass of patent documentation 1 is below the 2 μ m; its purpose is the crystal size that provides even and fine, mixes the mixed grain tissue (with reference to the embodiment result's who shows patent documentation 1 Fig. 2,4-5) that exists with the crystal grain of minor diameter but the crystal behind its final annealing is large diameter crystal grain.In addition; the micronize of non-patent literature 1 record is by metallic substance being applied big strain, by annealing the special methods (ECAP method, ARB method, TorsionMechanical Alloying method etc.) of its recrystallization being carried out; be difficult to make large-scale material; shape is restricted, manufacturing cost very high (non-patent literature 1 29-30 page or leaf).And strain all has big deviation (non-patent literature 1 conclusion (7)) at crystal boundary, intracrystalline, the result, and the distribution and the particle diameter of the recrystallization grain of generation are inhomogeneous, can't realize uniform miniaturization.
But if the alloy that has uneven mixed the tissue of crystal particle diameter is implemented plastic workings such as flexural deformation or stretching, then the local deformaton volume production is given birth to difference, concentrates on the position of easy deformation, and partly distortion takes place, and produces be full of cracks and also propagates.That is, contain in the crystalline structure of big particle in the part, big particle becomes the starting point of crackle.Like this, when existing mixed grain to organize, alloy phase ratio, intensity and the bendability variation of the uniform grading identical (neat particle) tissue with median size.In above-mentioned prior art, mainly be to make the crystal grain miniaturization of brass in order to pass and the characteristic that obtains, do not recognize the homogenizing that realizes crystal particle diameter and then obtain excellent intensity and bendability.
And, do not recognize fully in the above-mentioned prior art that the crystalline orientation that can be conceived to brass regulates bendability.
The present invention is directed to above-mentioned condition, provide be applicable to electronic machine, have the suitable intensity and a brass bar of bendability.
The contriver has carried out deep research for the brass of high strength, excellent in bending workability, found that the present invention.The present invention is as follows.
1. the Cu-Zn class alloy of high strength, excellent in bending workability, it is characterized in that: this alloy contains 20-40 quality %Zn, rest part is Cu and unavoidable impurities, have average crystalline particle diameter (mGS) and be the following grain properties of 1/3mGS for the standard deviation (σ GS) of 1-4 μ m and this crystal particle diameter, { I (220)+I (111) }/I (200) is 2.0-5.0 from the relational expression of the X-ray diffraction intensity of rolling surface.
2. the Cu-Zn class alloy of high strength, excellent in bending workability, it is characterized in that: this alloy is with the cold rolling acquisition of following Cu-Zn class alloy, described Cu-Zn class alloy contains 20-40 quality %Zn, rest part is Cu and unavoidable impurities, have average crystalline particle diameter (mGS) and be the following grain properties of 1/3mGS for the standard deviation (σ GS) of 1-4 μ m and this crystal particle diameter, { I (220)+I (111) }/I (200) is 2.0-5.0 from the relational expression of the X-ray diffraction intensity of rolling surface.
3. the Cu-Zn class alloy of high strength, excellent in bending workability, it is characterized in that: this alloy contains more than any one of 20-40 quality %Zn, 0.01-0.3 quality %Ni, Si, Fe, Ti, Co, Sn, rest part is Cu and unavoidable impurities, have average crystalline particle diameter (mGS) and be the following grain properties of 1/3mGS for the standard deviation (σ GS) of 1-4 μ m and this crystal particle diameter, { I (220)+I (111) }/I (200) is 2.0-5.0 from the relational expression of the X-ray diffraction intensity of rolling surface.
4. the Cu-Zn class alloy of high strength, excellent in bending workability, it is characterized in that: this alloy is with the cold rolling acquisition of following Cu-Zn class alloy, described Cu-Zn class alloy contains more than any one of 20-40 quality %Zn, 0.01-0.3 quality %Ni, Si, Fe, Ti, Co, Sn, rest part is Cu and unavoidable impurities, and having average crystalline particle diameter (mGS) is 1-4
The standard deviation of μ m and this crystal particle diameter (σ GS) is the following grain properties of 1/3mGS, and { I (220)+I (111) }/I (200) is 2.0-5.0 from the relational expression of the X-ray diffraction intensity of rolling surface.
5. the Cu-Zn class alloy of each described high strength, excellent in bending workability among the above-mentioned 1-4, this alloy is to contain S below the 30ppm.
6. the Cu-Zn class alloy of each described high strength, excellent in bending workability among the above-mentioned 1-5, the surface roughness Ra of this alloy is below the 0.2 μ m.
The present invention is that the relational expression of the X-ray diffraction intensity of particular value and rolling surface { I (220)+I (111) }/I (200) is the Cu-Zn class alloy of 2.0-5.0 by the standard deviation (σ GS) of preparation average crystalline particle diameter (mGS), this crystal particle diameter, can realize high strength and excellent bendability simultaneously.Therefore the Cu-Zn class alloy of high strength of the present invention, excellent in bending workability can be widely used as the copper alloy bar of electronic component-use to provide than lower costs of high strength copper alloy such as in the past beryllium copper, titanium copper, Corson alloy classes.
The best mode that carries out an invention
(1) composition of copper alloy
(a) copper alloy as object of the present invention is a Cu-Zn class alloy, promptly so-called brass.Specifically, be contain 20-40 quality %Zn, rest part is the Cu-Zn class alloy of Cu and unavoidable impurities, is object for 2 kinds with a kind of brass, the brass of stipulating among the JIS for example.
In addition, in the Cu-Zn class alloy of above-mentioned (a) record, add any one of Ni, Si, Fe, Ti, Co, Sn when above, also be equivalent to Cu-Zn class alloy of the present invention with 0.01-0.3 quality %.
(b) add in the Cu-Zn class alloy for solution strengthening more than any one of Ni, Si, Fe, Ti, Co, Sn.The preferred 0.01-0.3 quality of addition %, further preferred 0.05-0.25 quality %, less than 0.01 quality %, then can't obtain desirable strength, and surpass 0.3 quality %, then hot workability, cold-forming property, stampability, Young's modulus, cost aspect etc. are unfavorable, not preferred.
(c) in the impurity, wish that S is few as far as possible.Even this is that distortion of materials can also can significantly reduce during hot rolling owing to contain S on a small quantity.When particularly electrolytic copper etc. being directly used in cast raw material, though contain more S, by limiting this value, the crackle in the time of can preventing hot rolling.And, if the solid solution capacity of S increases, embrittlement then takes place, toughness is impaired, and therefore the sulphur composition that may contain as unavoidable impurities is preferably below the 30 quality ppm, further below the preferred 15 quality ppm.Therefore, employed raw material in the time of also will taking into full account preparation Cu-Zn class alloy of the present invention when using useless raw material, should suppress sneaking into of S as far as possible according to ordinary method.In addition and since with the contacted charcoal of molten metal, carbon raw material etc. in also contain S, therefore having a mind to control S also is effective from sneaking into of these raw materials.
(2) standard deviation of average crystalline particle diameter (mGS) and crystal particle diameter thereof (σ GS)
Find in one embodiment of the invention: cold rolling in the middle of carrying out continuously, process annealing, finally in the preparation process of cold rolling, final annealing, the recrystallization behavior is relevant with the characteristic of the copper alloy the finished product (annealing) that possess intensity and bendability simultaneously in final final annealing after cold rolling.Promptly, the invention provides the copper alloy that has both excellent bendability, this excellent bendability standard deviation (σ GS) following for 1-4 μ m by average crystalline particle diameter (mGS) and this crystal particle diameter obtains for the following grain properties of 1/3mGS, and this grain properties obtains by recrystallization in final final annealing after cold rolling.Usually, when average crystalline particle diameter (mGS) is less than 1 μ m behind final annealing, if the annealing of the low temperature that crystal particle diameter can not increase, short period of time, the part of not re-crystallization can residually be arranged then.Therefore, when implementing final annealing, need the cost time enough, and need carry out temperature treatment, be difficult to industrial applications in order to obtain to be lower than the crystal grain of 1 μ m and not residual not re-crystallization part.On the other hand, the average crystalline particle diameter above 4 μ m can't obtain enough intensity.Considered by above situation, wish that the average crystalline particle diameter is 1-4 μ m, preferred 1.5-4 μ m is further about preferred 2 μ m.
And, even the average crystalline particle diameter below 4 μ m, if its standard deviation (σ GS) surpasses 1/3mGS, then bendability to improve effect little, can't realize target capabilities.Therefore, the dispersiveness of crystal particle diameter of the present invention is expressed as below the 1/3mGS with the standard deviation of crystal particle diameter, below the preferred 1/5mGS.
Among the present invention, the mensuration of crystal particle diameter is undertaken by the process of chopping of JIS H0501.Specifically, number goes out to be prescribed the crystal grain numbers of the complete crosscut of straight line line segment of length, with the mean value of this cutting length as crystal particle diameter.Standard deviation as its deviation index is not the standard deviation of cutting length, but the standard deviation of this crystal particle diameter.
In another embodiment of the present invention, the preparation process of cold rolling in the middle of carry out continuously, final annealing, final rolling intact goods after cold rolling is also included within this embodiment.Promptly, even carry out finally rolling to the copper alloy that has both excellent bendability, the copper alloy of intensity and excellent in bending workability also can be provided, the bendability of wherein said excellence obtains for the following grain properties of 1/3mGS by final cold rolling preceding average crystalline particle diameter (mGS) standard deviation (σ GS) following for 1-4 μ m and this crystal particle diameter, and this grain properties obtains by recrystallization in final annealing.In the finished product that strengthened by final cold working dislocation, can't determine clear and definite intergranular, can't measure correct crystal particle diameter, therefore final average crystalline particle diameter and standard deviation before cold rolling be stipulated, effective for the adjusting of the finished product character.(3) relational expression of X-ray diffraction intensity
For the effective crystal face of bendability orientation is (100), and deleterious crystal face orientation is (111) and (220).The contriver finds to satisfy the relational expression of following X-ray diffraction intensity in order to improve the bendability of brass bar in the past.That is, { I (220)+I (111) }/I (200) is 2.0-5.0.{ I (220)+I (111) }/I (200) can't obtain enough intensity less than 2.0 o'clock, surpassed at 5.0 o'clock, the bendability variation.Preferably the scope of { I (220)+I (111) }/I (200) is at 2.0-4.0.
The integrated value of the diffracted intensity of (hk1) face when here, I (hk1) is to use Co pipe ball that rolling surface is carried out X-ray diffraction.
(4) control of crystal particle diameter and crystalline orientation (relational expression of X-ray diffraction intensity)
The brass of the invention described above can carry out cold working repeatedly and anneal preparing by casting, hot-work, the cold working rate of limit adjusting afterwards limit that common those skilled in the art adopt in the routine preparation of brass.Among the present invention, can select suitable Heating temperature, time, speed of cooling, rolling working modulus etc.
Carry out following control, then can obtain average crystalline particle diameter (mGS) for 1-4 μ m is following, the standard deviation (σ GS) of this crystal particle diameter is the following crystal grain of 1/3mGS, can make { I (220)+I (111) }/I (200) is 2.0-5.0.By the vertical continuous casting method brass raw material of the present invention is cast ingot bar, then it is carried out hot rolling, implement cold working rate then and be cold rolling more than 75%.Then 600 ℃-800 ℃ down annealing, implement cold working rate again and be cold rolling 70% or more, anneal down at 400 ℃-700 ℃ again.And the cooling after the at this moment last thermal treatment is preferably with 20 ℃/second-60 ℃/second enforcements, and this is to be effective below the 1/3mGS for the standard deviation that makes crystal particle diameter (σ GS).
(5) surfaceness (Ra)
Problem of the present invention provides the material of excellent in bending workability, but when the bending machining that to carry out that crooked curvature is little, angle of bend is big etc. harsh, also be easy to generate wrinkle even in fact do not break, be considered as crackle sometimes when producing wrinkle by mistake, become the obstacle of quality evaluation.
Therefore, even people are desirable to provide the material that also is difficult to produce wrinkle when carrying out harsh bending machining.Therefore, the present invention provides the material that is difficult to produce wrinkle, excellent in bending workability by the surfaceness (Ra) of prescribed material.That is, Ra is below the 0.2 μ m, below the preferred 0.15 μ m.
The adjusting of the surfaceness of material can be by managing final milling train the surfaceness of working roll carry out, the material surface that has duplicated the roller surface forms required surfaceness.In addition, in the annealing steps behind regulation rolling,, also can obtain the required surfaceness of the finished product by in order to remove mechanical mill that de-sludging etc. carries out or chemical grinding etc.
(6) tensile strength, bendability and electric conductivity
Brass intensity height of the present invention, excellent in bending workability, and have excellent electroconductibility concurrently.The tensile strength of copper alloy of the present invention is in the material of having annealed more than the preferred 450MPa, in rolling intact material more than the preferred 540M Pa.Its upper limit is generally about 680MPa.
The bendability of brass of the present invention is a test film of getting 10mmw * 100mml with rolling direction with meeting at right angles, carry out W pliability test (JIS H 3110), can obtain the above good surface appearance of metewand C grade that the technological standard JBTA T307:1999 of copper association stretches in Japan.Among the present invention, be evaluated as good if the material of having annealed is more than the C grade.On the other hand, for the cold rolling rolling intact material of last enforcement, with the bending radius of minimum than (r (bending radius)/t (test film thickness)) as metewand, preferred r/t ≦ 2, further preferred r/t ≦ 1, further preferred r/t=0.
Embodiment
The preparation method of embodiments of the invention 1 and embodiment 2 below is shown.
(1) embodiment 1
The copper alloy of forming shown in the table 1 is fused in Ajax-Wyatt furnace, be cast in the mold of thickness 180mm by the vertical continuous casting method then, make ingot bar.Be hot-rolled down to 9mm then.Carry out the cold rolling of cold working rate 83% then, make 1.5mm, anneal again, cold rolling, implement final annealing.The preparation condition of each step is illustrated in the table 1 as embodiment 1.
The measuring method of correlation properties value of the present invention is as follows.
(a) tensile strength (TS:MPa), 0.2% endurance (YS:MPa) are to get 13B test film (JIS Z 2201) abreast with rolling direction, obtain by tension test (JIS Z2241).
(b) crystal particle diameter is by the process of chopping (JIS H 0501), the crystal grain number that several line segments that go out to be prescribed length cut off fully, as crystal particle diameter, the standard deviation of crystal particle diameter (σ GS) is the standard deviation of this crystal particle diameter with the mean value of this cutting length.Promptly, to be amplified to 4000 times with the rectangular section structure of rolling direction by sweep electron microscope image (SEM image), in the line segment of 50 μ m length, with the number of line segment divided by the intersection point of line and crystal boundary, with income value as crystal particle diameter, 10 lines are measured, with each crystal particle diameter of gained on average as the application's average crystalline particle diameter (mGS), with the standard deviation of each crystal particle diameter standard deviation (σ GS) as the application.
(c) crystalline orientation is in rolling surface, measures the integrated value of the diffracted intensity of (111), (220) and (200) each face by X-ray diffraction, obtains 1={1 (220)+1 (111) } 71 (200) value.This measure to use Co pipe ball, and the measurement range of each face is (111): 2 θ=47.0 °-52.0 °, (220): 2 θ=84.0 °-89.0 °, (200): 2 θ=55.5 °-60.5 ° (θ represents angle of diffraction).
(d) bendability (r/t) is a test film of getting 10mmw * 100mml with rolling direction with meeting at right angles, carry out W pliability test (JIS H3110) with various bending radius, obtain Japan and stretch the above good surface appearance of metewand C grade of the technological standard JBTA T307:1999 of copper association, obtain do not crack, the bending radius of the minimum of uneven surface is than (r (bending radius)/t (test film thickness)).Metewand is divided into five grades, grade A: do not have wrinkle, grade B: wrinkle are little, grade C: wrinkle are big, grade D: crackle is little, grade E: crackle is big.Non-defective unit is meant the test film that is evaluated as grade A, B, C.Here, " wrinkle " expression can be by observation by light microscope to because the height that occurs of bending machining caves in or the state of striped, " crackle " be meant can't from directly over observe the end of crackle, but the state that splits along zone of fracture.The bending axis of W pliability test and rolling direction are parallel direction.
(e) surfaceness (Ra) is measured according to JIS-B0601 (1994).
The result of the effect of embodiment 1 is as shown in table 1.
[table 1]
Unit in the table " % ", " ppm " expression " quality % ", " quality ppm ", element is not added in "-" expression.
Among the example 1-8, therefore the relational expression of the standard deviation of average crystalline particle diameter (mGS), this crystal particle diameter (σ GS), X-ray diffraction intensity { I (220)+I (111) }/I (200) has obtained the Cu-Zn class alloy of high strength, excellent in bending workability in the scope that satisfies claim 1 or claim 3.
In the comparative example 9,11, the average crystalline particle diameter is less than 1 μ m, the residual part that not re-crystallization is arranged of part.Therefore, curved part produces the crack.In the comparative example 10,12, the average crystalline particle diameter surpasses 4 μ m, does not therefore obtain enough intensity.In the comparative example 13, the average crystalline particle diameter is 1-4 μ m, but standard deviation surpasses 1/3 of average crystalline particle diameter, and therefore,, standard deviation identical with the average crystalline particle diameter is that the example below 1/3 1 of average crystalline particle diameter is compared, and bendability is poor.
In the comparative example 14, the relational expression of X-ray diffraction intensity { I (220)+I (111) }/I (200) does not therefore obtain enough intensity less than 2.0, greater than 5.0, has therefore produced crackle in the bendability test in the comparative example 15.
In the example 7, S concentration surpasses 30 quality ppm, so bendability is poorer than other example.In the example 8, surface roughness Ra surpasses 0.2 μ m, and therefore wrinkle are more obvious than other example in the bendability test.
(2) embodiment 2
Among the embodiment 2, each material that the final annealing of embodiment 1 is intact carries out finally rolling with working modulus 0-40%.For example, it is example 16 (rolling intact) that the material (annealing) of example 1 has been carried out final cold rolling embodiment, and it is comparative example 24 (rolling finishing) that the material (annealing) of comparative example 9 has been carried out final cold rolling embodiment.Example 17-23, comparative example 25-30 are too.Its preparation condition is as shown in table 2, and the result of the effect of embodiment 2 is as shown in table 2.
[table 2]
Among the example 16-23, therefore the standard deviation (σ GS) of final average crystalline particle diameter (mGS), this crystal particle diameter before cold rolling, relational expression { I (220)+I (111) }/I (200) of X-ray diffraction intensity obtained the Cu-Zn class alloy of high strength, excellent in bending workability in the scope that satisfies claim 2 or claim 4.
In the comparative example 24,26, final cold rolling preceding average crystalline particle diameter is less than 1 μ m, and therefore the residual part that not re-crystallization is arranged of part, still produces the crack at final cold rolling back bend.In the comparative example 25,27, final cold rolling preceding average crystalline particle diameter surpasses 4 μ m, so does not also obtain enough intensity after finally cold rolling.In the comparative example 28, final cold rolling preceding average crystalline particle diameter is 1-4 μ m, but standard deviation surpasses 1/3 of average crystalline particle diameter, therefore,, standard deviation identical with the average crystalline particle diameter is that the example below 1/3 16 of average crystalline particle diameter is compared, and final bendability after cold rolling is poor.
In the comparative example 29, relational expression { I (220)+I (111) }/I (200) of the X-ray diffraction intensity before finally cold rolling is less than 2.0, therefore also do not obtain enough intensity after finally cold rolling, therefore comparative example 30 has produced crackle greater than 5.0 in the bendability test.
In the example 22, S concentration surpasses 30 quality ppm, so bendability is poorer than other example.In the example 23, surface roughness Ra surpasses 0.2 μ m, and therefore wrinkle are more obvious than other example in the bendability test.
Claims (6)
1. the Cu-Zn class alloy of high strength, excellent in bending workability, it is characterized in that: this alloy contains 20-40 quality %Zn, rest part is Cu and unavoidable impurities, have average crystalline particle diameter (mGS) and be the following grain properties of 1/3mGS for the standard deviation (σ GS) of 1-4 μ m and this crystal particle diameter, { I (220)+I (111) }/I (200) is 2.0-5.0 from the relational expression of the X-ray diffraction intensity of rolling surface.
2. the Cu-Zn class alloy of high strength, excellent in bending workability, it is characterized in that: this alloy is with the cold rolling acquisition of following Cu-Zn class alloy, described Cu-Zn class alloy contains 20-40 quality %Zn, rest part is Cu and unavoidable impurities, have average crystalline particle diameter (mGS) and be the following grain properties of 1/3mGS for the standard deviation (σ GS) of 1-4 μ m and this crystal particle diameter, { I (220)+I (111) }/I (200) is 2.0-5.0 from the relational expression of the X-ray diffraction intensity of rolling surface.
3. the Cu-Zn class alloy of high strength, excellent in bending workability, it is characterized in that: this alloy contains more than any one of 20-40 quality %Zn, 0.01-0.3 quality %Ni, Si, Fe, Ti, Co, Sn, rest part is Cu and unavoidable impurities, have average crystalline particle diameter (mGS) and be the following grain properties of 1/3mGS for the standard deviation (σ GS) of 1-4 μ m and this crystal particle diameter, { I (220)+I (111) }/I (200) is 2.0-5.0 from the relational expression of the X-ray diffraction intensity of rolling surface.
4. high strength, the Cu-Zn class alloy of excellent in bending workability, it is characterized in that: this alloy is with the cold rolling acquisition of following Cu-Zn class alloy, described Cu-Zn class alloy contains 20-40 quality %Zn, 0.01-0.3 quality %Ni, Si, Fe, Ti, Co, more than any one of Sn, rest part is Cu and unavoidable impurities, having average crystalline particle diameter (mGS) is 1-4 μ m, and the standard deviation of this crystal particle diameter (σ GS) is the following grain properties of 1/3mGS, and { I (220)+I (111) }/I (200) is 2.0-5.0 from the relational expression of the X-ray diffraction intensity of rolling surface.
5. the Cu-Zn class alloy of each described high strength, excellent in bending workability among the claim 1-4, this alloy is to contain S below the 30ppm.
6. the Cu-Zn class alloy of each described high strength, excellent in bending workability among the claim 1-5, the surface roughness Ra of this alloy is below the 0.2 μ m.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP181516/2006 | 2006-06-30 | ||
| JP2006181516A JP5247010B2 (en) | 2006-06-30 | 2006-06-30 | Cu-Zn alloy with high strength and excellent bending workability |
| PCT/JP2007/063012 WO2008001852A1 (en) | 2006-06-30 | 2007-06-28 | Cu-Zn ALLOY WITH HIGH STRENGTH AND EXCELLENT BENDABILITY |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101479396A true CN101479396A (en) | 2009-07-08 |
| CN101479396B CN101479396B (en) | 2011-07-06 |
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Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2007800244517A Expired - Fee Related CN101479396B (en) | 2006-06-30 | 2007-06-28 | Cu-zn alloy with high strength and excellent bendability |
Country Status (4)
| Country | Link |
|---|---|
| JP (1) | JP5247010B2 (en) |
| KR (1) | KR101088666B1 (en) |
| CN (1) | CN101479396B (en) |
| WO (1) | WO2008001852A1 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104737329A (en) * | 2013-05-08 | 2015-06-24 | 住友电气工业株式会社 | Lead conductor and electrical energy storage device |
| CN105063416A (en) * | 2015-07-22 | 2015-11-18 | 芜湖楚江合金铜材有限公司 | Environmental-friendly economical copper alloy wire and processing method thereof |
| CN110050079A (en) * | 2017-11-15 | 2019-07-23 | Ｊｘ金属株式会社 | Corrosion resistance CuZn alloy |
| CN110117735A (en) * | 2019-05-07 | 2019-08-13 | 浙江天河铜业股份有限公司 | A kind of low-cost high-strength copper strips and its manufacturing method |
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| JP5191725B2 (en) * | 2007-08-13 | 2013-05-08 | Ｄｏｗａメタルテック株式会社 | Cu-Zn-Sn based copper alloy sheet, manufacturing method thereof, and connector |
| EP2319947A4 (en) * | 2008-07-31 | 2011-11-23 | Furukawa Electric Co Ltd | Copper alloy material for electrical and electronic components, and manufacturing method therefor |
| JP5619389B2 (en) * | 2008-08-05 | 2014-11-05 | 古河電気工業株式会社 | Copper alloy material |
| JP5889698B2 (en) * | 2012-03-30 | 2016-03-22 | 株式会社神戸製鋼所 | Cu-Zn alloy plate excellent in stress relaxation resistance and method for producing the same |
| CN105018782B (en) * | 2015-07-23 | 2017-09-26 | 宁波博威合金板带有限公司 | A kind of copper alloy of the silicon containing cobalt |
| JP6803457B2 (en) | 2017-03-24 | 2020-12-23 | 株式会社Ihi | Abrasion resistant copper-zinc alloy and machinery using it |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02170953A (en) * | 1988-12-22 | 1990-07-02 | Nippon Mining Co Ltd | Production of copper alloy having good bendability |
| JPH02173230A (en) * | 1988-12-24 | 1990-07-04 | Nippon Mining Co Ltd | Copper alloy having good direct bonding properties |
| JP2001335865A (en) * | 2000-03-22 | 2001-12-04 | Nippon Mining & Metals Co Ltd | Brass strip excellent in deep drawability and its production method |
| KR100513947B1 (en) * | 2002-03-29 | 2005-09-09 | 닛코 킨조쿠 가부시키가이샤 | A copper alloy having good pressing workability and manufacturing method therefor |
| JP4012845B2 (en) * | 2003-03-26 | 2007-11-21 | 住友金属鉱山伸銅株式会社 | 70/30 brass with refined crystal grains and method for producing the same |
| JP5032011B2 (en) * | 2005-08-09 | 2012-09-26 | 三井住友金属鉱山伸銅株式会社 | Hard α brass and method for producing the hard α brass |
-
2006
- 2006-06-30 JP JP2006181516A patent/JP5247010B2/en active Active
-
2007
- 2007-06-28 WO PCT/JP2007/063012 patent/WO2008001852A1/en active Application Filing
- 2007-06-28 KR KR1020087030585A patent/KR101088666B1/en not_active IP Right Cessation
- 2007-06-28 CN CN2007800244517A patent/CN101479396B/en not_active Expired - Fee Related
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104737329A (en) * | 2013-05-08 | 2015-06-24 | 住友电气工业株式会社 | Lead conductor and electrical energy storage device |
| CN105063416A (en) * | 2015-07-22 | 2015-11-18 | 芜湖楚江合金铜材有限公司 | Environmental-friendly economical copper alloy wire and processing method thereof |
| CN110050079A (en) * | 2017-11-15 | 2019-07-23 | Ｊｘ金属株式会社 | Corrosion resistance CuZn alloy |
| CN110050079B (en) * | 2017-11-15 | 2021-09-10 | Ｊｘ金属株式会社 | Corrosion resistant CuZn alloy |
| CN110117735A (en) * | 2019-05-07 | 2019-08-13 | 浙江天河铜业股份有限公司 | A kind of low-cost high-strength copper strips and its manufacturing method |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20090028526A (en) | 2009-03-18 |
| JP2008007839A (en) | 2008-01-17 |
| CN101479396B (en) | 2011-07-06 |
| KR101088666B1 (en) | 2011-12-01 |
| JP5247010B2 (en) | 2013-07-24 |
| WO2008001852A1 (en) | 2008-01-03 |
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