CN101821416A - Copper alloy material - Google Patents
Copper alloy material Download PDFInfo
- Publication number
- CN101821416A CN101821416A CN200780100048A CN200780100048A CN101821416A CN 101821416 A CN101821416 A CN 101821416A CN 200780100048 A CN200780100048 A CN 200780100048A CN 200780100048 A CN200780100048 A CN 200780100048A CN 101821416 A CN101821416 A CN 101821416A
- Authority
- CN
- China
- Prior art keywords
- alloy material
- tensile strength
- precipitate
- inclusion
- particle diameter
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Images
Classifications
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
Abstract
A copper alloy material which contains, in terms of mass%, 0.01-2.5% titanium, 0.01-0.5% chromium, and 0.01-1%, excluding 1%, iron, the remainder being copper and impurities. The total number of those precipitates and inclusions present in the alloy material which have a particle diameter of 1 [mu]m or larger (N) and the particle diameter thereof (X) satisfy the equation (1). The relationship between the tensile strength (TS) and conductivity (IACS) of the copper alloy material satisfies the expression (2). The copper alloy material is characterized in that: when it is a plate material having a tensile strength (TS) of 600 MPa or lower, the bendability in a 90 DEG bending test (B90) satisfies the expression (3); when the copper alloy material is a plate material having a tensile strength (TS) exceeding 600 MPa, then the TS and B90 and the plate thickness (t) satisfy the expression (4); and when the copper alloy material is not a plate material, the ductility (E1) and the TS satisfy the expression (5). The material is excellent in strength, conductivity, and processability although it contains no element harmful to the environment.
Description
Technical field
The present invention relates to not use Pb, Cd, Be etc. environment to be produced the Cu alloy material of dysgenic element.
As the purposes of this Cu alloy material, can list electrical and electronic parts, security tool etc.
Electrical and electronic parts as using the Cu alloy material can be listed below.In the electronic applications, can list computer junctor, semiconductor socket, light picker, coaxial connector, IC testing needle (checker pin) etc.In the communications field, can list mobile phone component (junctor, battery terminal, antenna element), submerged repeater housing, exchange board with junctor etc.In the automotive field, can list various parts of electric such as rly., various switch, micromotor, splash pan, various terminal classes.In the medical analysis instrument field, can list medical connector, industrial junctor etc.In field of household appliances, can list household electrical appliances rly., game machine of use light picker, card connectors etc. such as air-conditioning.They are the parts of being made by the strip shaping processing of the about 0.1～0.2mm of thickness mostly.
Except strip, these parts use with the shape of wire rod or block (bulk) usually.As the Electrical and Electronic parts that use the Cu alloy material, in the aerospace field, can list flyer with the injection molded of landing gear, plastics with mould etc.
As fabricated product, can list the welding electrode material from wire rod., for example in the assembling procedure of body of a motor car, use mostly with electrode, spot-wedling electrode as LASER BEAM WELDING.
As security tool, for example have in ammunition depot, colliery etc. and have excavation rod, spanner, chain block (chain block), hammer, screwdriver, pliers, the cutting nippers instruments such as (nipper) that uses in the place of danger of and blast on fire because of spark.
Background technology
At present, as the Cu alloy material that is used for above-mentioned parts, separate out according to the timeliness of Be and to realize that the Cu-Be alloy of strengthening is generally known.This alloy is owing to have excellent tensile strength and electric conductivity concurrently, therefore is widely used as spring with material etc.Yet, in the manufacturing process of Cu-Be alloy and this alloy is processed as in the operation of various parts, generated the Be oxide compound.
Be is the environmentally harmful material that is only second to Pd, Cd.Therefore, in the manufacturing of Cu alloy material, processing, be necessary to be provided with the treatment process of Be oxide compound, thereby manufacturing cost increases, and becomes problem in the process recycling of electrical and electronic parts.In addition, in the welding electrode material, owing in the welding operation, produced the deleterious Be oxide compound of the cardio-pulmonary function to the people of a great deal of, thereby in environmental management, also produced very big cost.Like this, according to environmental problem, the Cu-Be alloy is in-problem material.Therefore, expectation occurs not using environmentally harmful elements such as Pb, Cd, Be, and the two all excellent material of tensile strength and electric conductivity.
Improving tensile strength TS (MPa) and electric conductivity IACS (%) (with respect to the relative value of the electric conductivity of fine copper polycrystalline material) simultaneously is difficult originally.Therefore, user's requirement mostly is an attention specific character wherein.This has also obtained embodiment in the non-patent literature 1 of the various characteristics of stretching the copper product of for example having put down in writing actual manufacturing.
Fig. 1 has put the relation of tensile strength TS (MPa) with the electric conductivity IACS (%) of the Cu alloy material of being put down in writing in the non-patent literature 1 that does not contain harmful element such as Be in order.As shown in Figure 1, the existing Cu alloy material that does not contain harmful elements such as Be, for example in electric conductivity was zone more than 60%, its tensile strength was low to moderate about 250～650MPa, and in the zone more than tensile strength 700MPa, its electric conductivity is low to moderate less than 20%.Like this, it is higher that existing C u alloy material has only a kind of performance in tensile strength (MPa) and the electric conductivity (%) basically.And all not having tensile strength is the above high strength of 1GPa.
For example, in patent documentation 1, what proposed to be referred to as section gloomy (corson) and be makes Ni
2The Cu alloy material that Si separates out.Gloomy in this section is in the alloy, and under the tensile strength of 750～820MPa, electric conductivity is about 40%, in the middle of the alloy that does not contain environmentally harmful elements such as Be, is the balance alloy material preferably of tensile strength and electric conductivity.
Yet all there is limit in this alloy with regard to high strength and high conductivityization, as follows, leaves problem on goods variation range (variation).This alloy has by Ni
2Si separates out the time hardening that is caused.And, lower the content of Ni and Si and when improving electric conductivity, tensile strength significantly reduces.On the other hand, even if in order to increase Ni
2The amount of separating out of Si and increase the amount of Ni and Si, also there is limit in the raising of tensile strength, and electric conductivity obviously reduces.Therefore, the tensile strength that section is gloomy to be alloy in the high zone of the high zone of tensile strength and electric conductivity and the balance variation of electric conductivity, and then the goods variation range narrows down.This ascribes following reason to.
The resistance of alloy (perhaps as its electric conductivity reciprocal) determined by electron scattering, according to the kind of the element of solid solution in the alloy and significantly change.Because the Ni of solid solution significantly raises (electric conductivity is significantly descended) resistance value in the alloy, therefore gloomy in above-mentioned section is in the alloy, and when increasing the amount of Ni, electric conductivity reduces.On the other hand, the tensile strength of Cu alloy material is obtained by the age hardening effect.The amount of precipitate is many more, and in addition, precipitate disperses fine more, and then tensile strength is high more.Gloomy in section is under the situation of alloy, only is Ni owing to separate out particle
2Si, thereby no matter with regard to the amount of separating out, still with regard to the dispersion situation, all there is limit in high strength.
Disclose the material of the balance excellence of a kind of intensity and electroconductibility in the patent documentation 2, this material has improved the problems referred to above.Electrical electronic part is made by the strip bending machining of about 100～200 μ m of thickness mostly.Therefore, except the balance external of above-mentioned intensity and electroconductibility, bendability also is important factor.Usually, the bendability of the strip that rolling processing and ageing treatment are crossed, go up perpendicular to the direction (good way) of rolling direction good, but be parallel on the direction of rolling direction (bad way) relatively poor mostly.This bendability and ductile anisotropy ascribe following reason to: grain structure stretches on rolling direction by rolling, and when bending machining, taking place with the intergranular crack easily is the crackle of starting point.
Other block materials or wire rod for example also utilize as mould for plastics, welding electrode material or security tool, except the balance of intensity and electroconductibility, also usually require the processibility in their manufacturing procedure.In addition, require to be used for to prevent to ftracture and the ductility of breach in their use.
In addition, the inventor waits the copper alloy that has proposed intensity and excellent electric conductivity in patent documentation 3.Yet, when the copper alloy that proposes is rolled,, therefore be unsuitable for mass production owing to there is the problem of thickization of precipitate about 900 ℃ in the document.
Patent documentation 1: Japanese kokai publication sho 61-250134 communique
Patent documentation 2: Japanese kokai publication hei 2-170932 communique
Patent documentation 3: TOHKEMY 2005-281850 communique
Non-patent literature 1: stretch Copper product デ one タ Block Star Network (stretching copper product databook), on August 1st, 1997, the distribution of copper association, 328～355 pages are stretched by Japan.
Summary of the invention
The problem that invention will solve
The present invention makes in order to address the above problem, and its purpose is to provide a kind of and does not use harmful element with environmental problem and the Cu alloy material of intensity, electroconductibility and excellent in workability.Especially be to provide a kind of Cu alloy material, the electric conductivity that it had and the balance of tensile strength are for being alloy same degree or the high level more than it with Be being added to the above-mentioned Cu-Be that forms among the Cu.Further, the invention provides can solution heat treatment and high temperature under rolling copper alloy.
Wherein, " balance of electric conductivity and tensile strength for Cu-Be be alloy same degree or the high level more than it ", be meant that particularly the Cu alloy material has in Fig. 1 tensile strength TS in the zone that is expressed as " balance is good " and the physics value of electric conductivity IACS, this means the state that satisfies following formula (2).Below, this state is called " the extraordinary state of the balance of tensile strength and electric conductivity ".
TS≥648.06+985.48×exp(-0.0513×IACS)…(2)
Wherein, TS represents tensile strength (MPa), and IACS represents electric conductivity (%).
For the Cu alloy material, except the characteristic of above-mentioned tensile strength and electric conductivity, also require the hot strength of regulation.This is because for example employed connector material is exposed in the environment more than 200 ℃ sometimes in automobile and the computer.Fine copper is when being heated to more than 200 ℃, and room temperature strength significantly reduces, and can not keep desired spring characteristic, but above-mentioned Cu-Be be alloy or section gloomy be in the alloy, even be heated to after 400 ℃, room temperature strength does not almost reduce yet.
Therefore, as hot strength, with Cu-Be be that the equal level of alloy is a target.Particularly, be that 50% Heating temperature is defined as heat resisting temperature with the hardness rate of descent before and after the heat test, heat resisting temperature is to be considered as the hot strength excellence more than 400 ℃.Preferred heat resisting temperature is more than 500 ℃.
About bendability, being to be target more than the equal level of alloy with Cu-Be.
Particularly, bendability when being sheet materials such as strip about the Cu alloy material, to being that the sample that mode was cut out on the long limit of sample carries out 90 ° of pliability tests with various radius-of-curvature with direction (bad way) perpendicular to rolling direction, measure the minimum profile curvature radius R (mm) that crackle does not take place, can be with (the bendability B in=90 ° of pliability tests R/t) obtaining of the ratio by calculating this minimum profile curvature radius R and thickness of slab t (mm)
90Estimate the bendability of sheet material.
The scope that the bendability of sheet material described here is good is meant in tensile strength TS is sheet material below the 600MPa and satisfies following formula (3), and, surpass at tensile strength TS and to be meant in the sheet material of 600MPa and to satisfy following formula (4):
B
90≤2.0…(3)
B
90≤25.093-54.82×exp[-{(TS+583.61)/1254}
2]+1.25×t…(4)
Wherein, B
90Represent the bendability B in 90 ℃ of pliability tests
90, TS represents tensile strength (MPa), and t represents thickness of slab (mm).
Wherein, surpass in the sheet material of 600MPa, preferably satisfy following formula (4 ') at this tensile strength TS:
B
90≤24.238-43.087×exp[-{(TS+383.46)/1199.4}
2]+1.25×t…(4’)
Wherein, in this tensile strength TS surpasses the sheet material of 600MPa, further preferably satisfy following formula (4 "):
B
90≤-33.0949-55.0551×exp[-{(TS+1898.3)/1949.91}
2]+1.25×t…(4”)
And, be sheet material material in addition about the Cu alloy material, for example, the processibility when the Cu alloy material is wire rod can be estimated by the relation of ductility El (%) and tensile strength TS (MPa).The good scope of processibility about wire rod described here is meant and satisfies following formula (5):
El≥24.138-24.6076×exp[-{(TS-1816.36)/2213.52}
2]…(5)
Wherein El represents ductility (%), and TS represents tensile strength (MPa).
In addition, in the material beyond the sheet material, preferably satisfy following formula (5 '):
El≥59.0438-61.9662×exp[-{(TS-2359.36)/4047.4}
2]…(5′)
In addition, in the material beyond the sheet material, ductility El (%) further preferably satisfies following formula (5 "):
El≥89.6632-168.32×exp[-{(TS-10630.2)/11614.9}
2]…(5″)
For Cu alloy material, except the characteristic of above-mentioned tensile strength TS, electric conductivity IACS and processibility, also require wear resistant as security tool.Therefore, for wear resistant, with the equal level of tool steel be target.Particularly, the hardness under the room temperature counts 250 when above by Vickers' hardness, the wear resistant excellence.
In addition, by Ti-Cr binary system phasor shown in Figure 2 as can be known, Ti-Cr compound and metal Ti etc. have been generated in the high-temperature zone of the process of cooling of Cu alloy material of the present invention after solidifying.That is, in the present invention, described precipitate is Cu for example
4Ti, Metal Cr, metal A g etc., and described inclusion is for example Cr-Ti compound, metal oxide, metallic carbide, metal nitride etc.
The scheme that is used to deal with problems
The main idea of Cu alloy material of the present invention is following (1) to (4) any one:
(1) a kind of Cu alloy material, it is characterized in that, this Cu alloy material contains 0.01～2.5%Ti by quality %, 0.01～0.5%Cr and 0.01% above and be lower than 1%Fe, surplus is made of Cu and impurity, in the middle of the precipitate and inclusion that exists in the alloy material, particle diameter is that the above precipitate of 1 μ m and the total number N of inclusion satisfy following formula (1), and the relation of tensile strength TS and electric conductivity IACS satisfies following formula (2), at the Cu alloy material is that tensile strength TS is when being sheet material below the 600MPa, satisfy following formula (3), at the Cu alloy material is that tensile strength TS is when surpassing the sheet material of 600MPa, satisfy following formula (4), and, when the Cu alloy material is material beyond the sheet material, satisfy following formula (5):
logN≤0.4742+17.629×exp(-0.1133×X)…(1)
TS≥648.06+985.48×exp(-0.0513×IACS)…(2)
B
90≤2.0…(3)
B
90≤25.093-54.82×exp[-{(TS+583.61)/1254}
2]+1.25×t…(4)
El≥24.138-24.6076×exp[-{(TS-1816.36)/2213.52}
2]…(5)
Wherein, the implication of the symbol in the formula is as described below respectively:
N: the precipitate that the particle diameter 1 μ m of per unit area is above and the total number (mm of inclusion
-2),
X: particle diameter is the above precipitate of 1 μ m and the particle diameter (μ m) of inclusion,
TS: tensile strength (MPa),
IACS: electric conductivity (%),
B
90: the bendability in 90 ° of pliability tests,
T: thickness of slab (mm),
El: ductility (%).
Wherein, B
90, TS and El all be meant the value of the vertical sample of rolling direction of the long limit of taking sample and plate.
(2) according to above-mentioned (1) described Cu alloy material, it is characterized in that,, also contain 0.005～1%Ag by quality %.
(3) according to above-mentioned (1) or (2) described Cu alloy material, it is characterized in that, by quality %, also contain and respectively be 0.01～1% and add up to more than one the element among Sn, Mn, Co, Al, Si, Nb, Ta, Mo, V, W, Au, Zn, Ni, Te, Se and the Ge of being selected from below 1.0%.
(4) according to each above-mentioned (1)～(3) described Cu alloy material, it is characterized in that,, also contain and add up to 0.001～0.1% more than one the element in Zr, Mg, Li, Ca and the rare earth element of being selected from by quality %.
The effect of invention
According to the present invention, can provide and not use harmful element, the Cu alloy material of intensity, electroconductibility and excellent in workability with environmental problem.
Description of drawings
Fig. 1 is the figure that has put in the non-patent literature 1 relation of the tensile strength of the Cu alloy material that does not contain harmful element such as Be of record and electric conductivity in order.
Fig. 2 is a Ti-Cr binary system phasor.
Fig. 3 is the tensile strength TS that draws at multiple thickness of slab of Cu sheet alloy of example of the present invention and the bendability B in 90 ° of pliability tests
90Graph of a relation.
Fig. 4 is the graph of a relation of ductility El (%) and tensile strength TS of the Cu alloy wire of example of the present invention.
Embodiment
Below, embodiments of the present invention are described.In addition in the following description, " % " about the content of each element is meant " quality % ".
(A) about the chemical constitution of Cu alloy material of the present invention
One of Cu alloy material of the present invention has following chemical constitution: contain 0.01～2.5%Ti, 0.01～0.5%Cr and 0.01% above and be lower than 1%Fe, surplus is made of Cu and impurity.
Ti：0.01～2.5％
Ti guarantees the necessary element of the strength of materials.That is, when ageing treatment, Ti can be used as Cu
4Ti separates out, and can improve intensity by its precipitation-hardening.Content at Ti is lower than at 0.01% o'clock, can not obtain full intensity.And, surpass at 2.5% o'clock at its content, though intensity raises electroconductibility deterioration, bendability variation in addition.Therefore, the content with Ti is set at 0.01～2.5%.In addition, preferred range is 0.01～2.0%.In addition, be used to guarantee that the preferred content of intensity is more than 0.1%.
Cr：0.01～0.5％
As mentioned above, Ti is effectively for improving intensity, but when residuing in the Cu matrix not separating out, forms solid solution Ti, its electroconductibility of obvious damage.In contrast, Cr damages electroconductibility under solid solution condition degree is low, by interacting with solid solution Ti intensive, with the fixing solid solution Ti of the form of Cr-Ti.As a result, the solid solution Ti of matrix reduces, and electroconductibility improves.This effect can be 0.01% to obtain when above at Cr content.Yet Cr content surpasses at 0.5% o'clock, and ductility such as bendability are impaired.Therefore, Cr content is set at 0.01～0.5%.
Fe:0.01% is above and be lower than 1%
Fe is a balance of not damaging intensity and electroconductibility basically, and can improve the element of processibility.In addition, even Fe contains simultaneously with above-mentioned Ti and Cr, also can in solidifying neutralization cooling, not generate the element of unnecessary intermetallic compound etc.Be lower than at 0.01% o'clock at content, the raising effect of unpredictable processibility.On the other hand, containing 1% when above, not only its effect reaches capacity, and the electroconductibility deterioration.Therefore, be set at the content of Fe more than 0.01% and be lower than 1%.Preferred Fe content is 0.05～0.5%, and further preferred Fe content is 0.05～0.3%.
In the Cu alloy material of the present invention, except above-mentioned chemical ingredients, can also contain 0.005～0.1% Ag.
Ag：0.005～0.1％
Ag can contain as required.Even Ag is the element that also is difficult to make the electroconductibility deterioration under the state of solid solution in Cu matrix.In addition, metal A g can improve intensity by fine separating out.Therefore, especially, can contain 0.005～0.1% Ag wanting to show under the situation of this effect.This effect becomes when above significantly 0.005%, and is reaching capacity surpassing at 1% o'clock, even therefore contain the above Ag of this amount, also can only cause the cost rising of alloy.Preferred Ag content is 0.1～1%.
In addition, in the Cu alloy material of the present invention, respectively do for oneself 0.01～1.0% and add up to more than one the element among Sn, Mn, Co, Al, Si, Nb, Ta, Mo, V, W, Au, Zn, Ni, Te, Se and the Ge of being selected from below 1.0% in order to improve erosion resistance and thermotolerance, can to contain.
Sn, Mn, Co, Al, Si, Nb, Ta, Mo, V, W, Au, Zn, Ni, Te, Se and Ge: respectively do for oneself 0.01～1.0%
These elements are in the balance of keeping intensity and electric conductivity, have the element that improves erosion resistance and thermotolerance effect, therefore can contain these elements as required.
This effect is usually brought into play by the above-mentioned unit of containing separately more than 0.01%.Yet when their content was superfluous, electric conductivity reduced.Therefore, when containing Sn, Mn, Co, Al, Si, Nb, Ta, Mo, V, W, Au, Zn, Ni, Te, Se and Ge, the upper limit of content is defined as 1.0%.
In addition, even the content of these elements in above-mentioned scope, surpasses at 1.0% o'clock, the electroconductibility variation in their total amount.Therefore, when containing these elements, the upper limit of this total amount need be limited in below 1.0%.Preferred total content range is 0.1～0.5%.
In addition, in the Cu alloy material of the present invention,, can also contain and add up to 0.001～0.5% in Zr, Mg, Li, Ca and the rare earth element (REM) more than one of being selected from order to improve hot strength.
Zr, Mg, Li, Ca and rare earth element: respectively do for oneself 0.001～0.1%
Therefore these elements can contain these elements as required owing to being to combine with Sauerstoffatom in the Cu matrix to generate the element that fine oxide improves hot strength.This effect is 0.001% to become remarkable when above at the total content of these elements.Yet, surpassing at 0.1% o'clock at this content, above-mentioned effect not only reaches capacity, and has problem such as bendability deterioration.Therefore, containing when being selected from Zr, Mg, Li, Ca and the rare earth element more than one, the total content ideal is 0.001～0.1%.Preferred content is 0.005～0.05%.In addition, rare earth element is meant Sc, Y and lanthanon, can contain the simple substance of each element, in addition, also can contain norium (misch metal).
(B) about the precipitate that exists in the Cu alloy material of the present invention and the total number of inclusion
In Cu alloy material of the present invention, in the precipitate and inclusion that exists in the alloy, the precipitate that particle diameter 1 μ m is above and the total number N of inclusion need satisfy following formula (1):
logN≤0.4742+17.629×exp(-0.1133×X)…(1)
Wherein, N is the above precipitate of the particle diameter 1 μ m of per unit area and the total number (mm of inclusion
-2), and X is that particle diameter is the above precipitate of 1 μ m and the particle diameter (μ m) of inclusion.
In addition, the total number of precipitate and inclusion preferably satisfies following formula (1 '):
logN≤0.4742+7.9749×exp(-0.1133×X)…(1’)
Wherein, N is the above precipitate of the particle diameter 1 μ m of per unit area and the total number (mm of inclusion
-2), and X is that particle diameter is the above precipitate of 1 μ m and the particle diameter (μ m) of inclusion.
And, the total number of precipitate and inclusion, further preferably satisfy following formula (1 "):
logN≤0.4742+6.3579×exp(-0.1133×X)…(1”)
Wherein, N is the above precipitate of the particle diameter 1 μ m of per unit area and the total number (mm of inclusion
-2), and X is that particle diameter is the above precipitate of 1 μ m and the particle diameter (μ m) of inclusion.
In the Cu alloy material of the present invention, by separating out Cu imperceptibly
4Ti, Metal Cr and metal A g can not reduce electric conductivity ground and improve intensity.They improve intensity by precipitation-hardening.Owing to the Cr of solid solution combines the purity that improves matrix with Ti, therefore, electroconductibility is near the electroconductibility of fine copper.
Yet, work as Cu
4It is thick to 10 μ m and when separating out that the particle diameter of Ti, Metal Cr, metal A g or Cr-Ti compound becomes, and ductility reduces, and is easy to generate crackle or breach when bending machining when for example being processed into junctor or Punching Technology.In addition, sometimes fatigue characteristic and shock-resistant characteristic are produced detrimentally affect in use.Especially, when generating thick Ti-Cr compound during cooling after solidifying, be easy to generate crackle or breach in the manufacturing procedure after this.In addition, because hardness excessively increases in the ageing treatment process, therefore, hindered Cu
4Ti, Metal Cr and the fine of metal A g are separated out, thereby can not realize the high strength of Cu alloy material.In the precipitate and inclusion that exists in alloy, when the precipitate that particle diameter 1 μ m is above and the particle diameter of inclusion and total number discontented foot formula (1), it is remarkable that this problem becomes.
Therefore, among the present invention,, stipulated that the precipitate more than the particle diameter 1 μ m and the total number N of inclusion satisfy above-mentioned formula (1) in the precipitate that exists and the inclusion in alloy as prerequisite.Sometimes preferably satisfy above-mentioned formula (1 '), further preferably satisfy above-mentioned formula (1 ") sometimes.
In addition, the precipitate that the particle diameter 1 μ m that exists in the Cu alloy material of per unit area is above and the total number (mm of inclusion
-2) measuring method as described below.
The total number of＜precipitate and inclusion 〉
To carrying out mirror ultrafinish with the vertical and parallel section of the rolling surface of Cu alloy material with rolling direction, ammoniacal liquor and aqueous hydrogen peroxide solution are mixed and the corrosive fluid that obtains carries out etching in order to volume ratio 9: 1, observe the visual field of 1mm * 1mm then with opticmicroscope with the multiplying power of 100 times or 500 times.After this, measure precipitate and inclusion major diameter (with under the condition that does not contact crystal boundary in the way in the longest collinear length that intragranular draws) in those major diameters more than the 1 μ m, the value defined that is obtained is a particle diameter.
In addition, round up below the radix point with the particle diameter (μ m) that obtains like this, according to 1 μ m, 2 μ m ... the particle diameter of α μ m (α is a natural number) is decided to be 1/2 with the frame line person of intersection in 1mm * 1mm visual field, be positioned at frame line person and be decided to be 1, calculate the total number n
1, with number the N (=n in optional 10 visuals field
1+ n
2+ ... + n
10) mean value (N/10) be defined as the precipitate of each particle diameter of this sample and the total number of inclusion.
Therefore, for at 1 μ m, 2 μ m ... each particle diameter of α μ m (α is a natural number) is calculated the numerical value on the right of above-mentioned formula (1), formula (1 ') and formula (1 "); in the particle size determination value of precipitate and inclusion is during more than the 1.0 μ m and less than 1.5 μ m; substitution X=1; and be that (α-0.5) μ m is above and during less than (α+0.5) μ m; substitution X=α (in this case, α is the natural number more than 2) gets final product.
Like this, at 1 μ m, 2 μ m ... each particle diameter of α μ m (α is a natural number) calculate the right numerical value, only satisfy in the situation of all particle diameters under the situation of above-mentioned formula (1), formula (1 ') or formula (1 "), the total number N that is defined as above precipitate of particle diameter 1 μ m in the precipitate that exists in the Cu alloy material and the inclusion and inclusion satisfies above-mentioned formula (1), formula (1 ') or formula (1 ").
(C) about the manufacturing of Cu alloy material of the present invention
Below, manufacture method of the present invention is described.
Melt preferably vacuum melting, if but when using fusing assistant (flux) etc. to be the atmosphere of non-oxidizable or reductibility, also can be air melting.This be because, when the solid solution oxygen in melting copper increases, in subsequent handling, generate water vapor, bubbling has caused so-called hydrogen disease etc.In addition, generate the solid solution element of easy oxidation such as the thick oxide compound of Ti, Cr etc., it when residual, significantly reduces ductility and fatigue characteristic in end article.
From the viewpoint of speed of cooling and productivity, the method that obtains the casting sheet is preferably continuous casting.Preferably, cool off in the humidity province of the casting sheet temperature to 600 after casting at least just ℃ with the above average cooling rate of 0.5 ℃/s, preferred average cooling rate be 5 ℃/more than the s.If the speed of cooling after the casting is slow, it is thick that precipitate becomes.For with the solid solution fully again of thick precipitate, need through the thermal treatments more than tens of hours under 800～900 ℃.Yet, when carrying out the long thermal treatment of this high temperature, produce the problem of surface oxidation, shape defect.On the other hand, because the precipitate of residual not solid solution in the thermal treatment of short period of time, thereby handle the back precipitate as nuclear heat and become thick, might damage ductility and bendability, in addition, owing to help the solid solution element of precipitation-hardening to reduce, thereby can not obtain the full intensity rising.Copper alloy of the present invention is the composition system of solid solution fully again, because the solid solution fully again of the thick precipitate of temporarily separating out as previously mentioned is difficult, is therefore preferably just carrying out quenching after the casting.
As long as can obtain the above speed of cooling of 0.5 ℃/s to casting process, then be not particularly limited, for example can be ingot casting method (ingot).In the casting in the atmosphere, because being involved in of oxide compound etc., the problem on the quality of casting sheet has taken place, the casting of tilt pouring method is reined in the therefore preferred Devi of adopting.
Gained casting sheet can carry out removing of surface dressing or rising head (riser) portion as required.Because the casting plate shape when not needing roughing near the end article shape, can directly carry out cold working or in the warm processing of 200～300 ℃ humidity province, but in order to adjust size shape, can be with heat forged and the combination of hot rolling system.Heating temperature during to hot-work also is not particularly limited, and is preferably 700～950 ℃.As required, after solution heat treatment is carried out in 700～950 ℃ humidity provinces, preferably carry out cold working or warm processing, and transfer to the timeliness operation with the degree of finish more than 20%.Aging condition also is not particularly limited, preferably, in non-oxidizable or reducing atmosphere, carries out 350～450 ℃ of thermal treatments of 2～24 hours down.The combination of cold working or warm processing and ageing treatment can be carried out repeatedly.
Working method is not particularly limited.For example, be shaped as strip etc. when tabular at end article, can adopt rolling, and, be not under the tabular situation, if wire rod, can adopt wire drawing or extrude, in addition, if block shape can adopt and forge or punching press.
(D) about the rerum natura of Cu alloy material of the present invention
To Cu alloy material of the present invention, measure the bendability B in tensile strength TS (MPa), ductility El (%), electric conductivity IACS (%) and the 90 ° of pliability tests
90Below describe the evaluation of their measuring method and their physics value in detail.
＜tensile strength TS (MPa) 〉
The 13B sample that obtains from the Cu alloy material that draw direction and rolling direction are vertical, stipulates among the JISZ2201 according to the method for stipulating among the JIS Z2241, is obtained the tensile strength TS (MPa) under the room temperature (25 ℃).
＜electric conductivity IACS (%) 〉
Take vertically sample with vertical, the wide 10mm of rolling direction * long 60mm from the Cu alloy material, galvanization on sample vertical, the potential difference at the two ends of mensuration sample is obtained resistance by 4 terminal methods.Then, calculate the resistance (resistivity) of per unit volume, obtain electric conductivity IACS (%) by its ratio with the resistivity 1.72 μ Ω cm of the standard test specimen that the annealing of polycrystalline fine copper is obtained by the volume of the sample of measuring with micrometer.
According to the present invention, at intensity and electroconductibility, seek a kind of Cu alloy material, the electric conductivity that it had and the balance of tensile strength for Cu-Be be alloy same degree or the high level more than it.
Therefore, the relation of tensile strength and electric conductivity (balance) satisfies following formula (2) and then is evaluated as " zero ", does not satisfy then being evaluated as " * ".
TS≥648.06+985.48×exp(-0.0513×IACS)…(2)
Wherein, TS represents tensile strength (MPa), and IACS represents electric conductivity (%).
＜bendability 〉
The bendability of sheet material is according to the bendability B in tensile strength TS, thickness of slab t and the 90 ° of pliability tests
90Relation (balance) estimate.Take the sample of a plurality of wide 10mm * long 60mm from the strip of Cu alloy material, making becomes the long limit of sample with the vertical direction of rolling direction (bad way), and the radius-of-curvature (internal diameter) of change bend is implemented 90 ° of pliability tests.Use opticmicroscope, the bend of the sample after the outside diameter viewing test.And, be R with the minimum profile curvature radius that crackle does not take place, the ratio by calculating this minimum profile curvature radius and the thickness t of sample (=R/t), obtain 90 ° of bendability B in the pliability test
90For a part of sample, take wherein parallel direction (good way) to become the sample on the long limit of sample with rolling direction, carry out pliability test, all shown good value, be not the industrial level that becomes problem.
" evaluation " on bendability hurdle is as follows: when tensile strength TS is sheet material below the 600MPa, and the bendability B in 90 ° of pliability tests among the bad way
90Satisfy following formula (3) and then be evaluated as " zero ", and, when tensile strength TS surpasses the sheet material of 600MPa, the bendability B in 90 ° of pliability tests
90Satisfy following formula (4) and then be evaluated as " zero ".In contrast, discontented foot formula (3) and following formula (4) then are evaluated as " * ".
B
90≤2.0…(3)
B
90≤25.093-54.82×exp[-{(TS+583.61)/1254}
2]+1.25×t…(4)
Wherein, B
90Represent the bendability in 90 ° of pliability tests, TS represents tensile strength (MPa), and t represents thickness of slab (mm).
The Cu alloy material that Figure 3 shows that aftermentioned example of the present invention when thickness of slab t=2mm tensile strength TS and the bendability B in 90 ° of pliability tests
90The figure of relation.All show and satisfy above-mentioned formula (4).
Then, be sheet material material in addition about the Cu alloy material, the processibility when for example being wire rod is estimated with the relation of tensile strength TS (MPa) by ductility El (%).El (%) satisfies following formula (5) with tensile strength TS (MPa) and then is evaluated as " zero ", does not satisfy then being evaluated as " * ".
El≥24.138-24.6076×exp[-{(TS-1816.36)/2213.52}
2]…(5)
Wherein, in formula (5), El represents ductility (%), and TS represents tensile strength (MPa).
Figure 4 shows that the figure of relation of ductility El (%) and tensile strength TS (MPa) of the Cu alloy wire of aftermentioned example of the present invention.All show and satisfy above-mentioned formula (5).
Embodiment 1
To have Cu alloy vacuum melting in high frequency melting furnace of the chemical constitution shown in the table 1, be cast in the mold of steel, obtain the ingot bar of thick 50mm, wide 100mm, high 200mm.As rare earth element, add the simple substance or the norium of each element.For a part of sample, by being installed in the thermopair of mold inwall, measure the temperature variation in the process of cooling after the casting, by with analysis of Heat Transfer and usefulness, obtain the cooling curve of casting sheet central part, the average cooling rates before being cooled to 600 ℃ are 2 ℃/s.In addition, in comparative example 36, be cast in the sand mo(u)ld mold, reduce the test of speed of cooling.Under this situation, being cooled to 600 ℃ of average cooling rates before is 0.2 ℃/s.
About test number 1～35, cut off and remove and emit notch portion, be heated to after 900 ℃ then, heat forged to thickness is 20mm.Further, be heated to after 900 ℃, it is 5mm that heat is rolling to thickness.In order to remove descaling (scale), grinding skin is heated to 250 ℃ then, and carries out warm rollingly, is 1mm until thickness.In addition, carry out 850 ℃ * 10 minutes solution heat treatment, cold rolling is 0.4mm until thickness.And, carry out the ageing treatment of 450 ℃ * 2h, further carry out 50% cold rolling, be 0.2mm until thickness, carry out the ageing treatment of 400 ℃ * 2h, obtain strip.For a part, in order to get all the cold rolling rate before the final timeliness ready, cold rolling carries out the thermal treatment of 450 ℃ * 2h then to 0.6mm or 0.2mm, and cold rolling similarly carries out the ageing treatment of 400 ℃ * 8h to 0.3mm or 0.1mm respectively, obtains strip.
For test number 36, also attempt trial-production, but when reaching thickness 0.4mm rolling, crackle is serious, is difficult to continue test with same operation.After investigating the precipitate and inclusion in each operation, though also residual a large amount of thick precipitate and inclusion when having confirmed cold rolling, even and the precipitate and the inclusion that generate when solidifying do not eliminate through solution heat treatment yet.
(table 1)
To the strip of such making,, obtain the particle diameter of precipitate and inclusion and the total number N (mm of per unit area according to aforementioned measuring method
-2), the bendability B in tensile strength TS (MPa), ductility El (%), electric conductivity IACS (%) and the 90 ° of pliability tests
90Further obtain balance (TS/El) and the bendability B of balance (TS/IACS), tensile strength TS and the ductility El of tensile strength TS and electric conductivity IACS respectively by these values
90Balance (B with tensile strength TS
90/ TS).These results are together shown in the table 1.In addition, add up to symbol ◎, zero, △ in the number hurdle to represent to satisfy formula (1 "), formula (1 ') and formula (1) respectively.
In the test number 1～28 of example of the present invention, the total number N of the particle diameter of precipitate and inclusion and per unit area all satisfies formula (1), the balance (TS/IACS) and the bendability B of tensile strength TS and electric conductivity (IACS)
90Balance (B with tensile strength TS
90/ TS) the two is all excellent.
In contrast, in the test number 29～35 of comparative example, balance (TS/IACS) and the bendability B of tensile strength TS and electric conductivity IACS
90Balance (B with tensile strength TS
90/ TS) all be inferior.In addition, in the test number 36 of comparative example, be in the stage of 0.2mm to thickness attempting 50% cold rolling, investigated the dispersion situation of precipitate and inclusion, as a result, be dispersed with a large amount of particle diameters 1 μ m above precipitate and inclusion in the Cu alloy material, do not satisfy above-mentioned formula (1).
Fig. 3 has summed up the bendability B shown in the table 1
90Balance (B with tensile strength TS
90/ TS).The present invention's example is represented with zero, and comparative example is represented with ■.Use the bendability B of formula (4), formula (4 ') and formula (4 ") expression when showing sample thickness t=0.2mm simultaneously in the figure respectively
90Relation with tensile strength TS.
Have the Cu alloy of the chemical constitution shown in the table 2 (three kinds) with high frequency melting furnace vacuum melting, be directly connected in the continuous casting of the graphite casting die that keeps stove, obtain the casting sheet of thickness 30mm, width 100mm by use.
(table 2)
After this, the processing thermal treatment of three kinds of different methods A, B shown in each Cu alloy carry out table 3 respectively and C obtains the strip of test number 41～49.
(table 3)
To the strip of such making,, obtain the particle diameter of precipitate and inclusion and the total number N (mm of per unit area according to aforementioned measuring method
-2), the bendability B in tensile strength TS (MPa), ductility El (%), electric conductivity IACS (%) and the 90 ° of pliability tests
90Further obtain balance (TS/El) and the bendability B of balance (TS/IACS), tensile strength TS and the ductility El of tensile strength TS and electric conductivity IACS respectively by these values
90Balance (B with tensile strength TS
90/ TS).These results are together shown in the table 2.In addition, add up to symbol zero expression in the number hurdle to satisfy formula (1 ').
In the test number 41～49 of example of the present invention, the total number N of the particle diameter of precipitate and inclusion and per unit area all satisfies formula (1), balance (TS/IACS) and the bendability B of tensile strength TS and electric conductivity IACS
90Balance (B with tensile strength TS
90/ TS) the two is all excellent.Can confirm,, also can obtain good result even change the processing heat-treat condition.
Embodiment 3
To have Cu alloy vacuum melting in high frequency melting furnace of the chemical constitution shown in the table 4, be cast in the mold of steel, obtain the ingot bar of diameter 70mm and high 170mm.As rare earth element, add the simple substance or the norium of each element.
(table 4)
Table 4
Cut off and remove and emit notch portion, be heated to after 900 ℃ then, heat forged to diameter is 30mm.In order to remove descaling, grinding skin is being heated to 250 ℃ then, and is carrying out warm rolling.In addition, carry out 850 ℃ * 10 minutes solution heat treatment, cold rolling is 15mm until diameter.And, carry out the ageing treatment of 400 ℃ * 8h, obtain wire rod.
For the wire rod of such making,, obtain the particle diameter of precipitate and inclusion and the total number N (mm of per unit area according to aforementioned measuring method
-2), tensile strength TS (MPa), ductility El (%) and electric conductivity IACS (%).These results are together shown in the table 4.In addition, add up to symbol ◎, zero, △ in the number hurdle to represent to satisfy formula (1 "), formula (1 ') and formula (1) respectively.
In the test number 61～71 of example of the present invention, the total number N of the particle diameter of precipitate and inclusion and per unit area all satisfies formula (1), and the two is all excellent for the balance (TS/IACS) of tensile strength TS and electric conductivity IACS and the balance (TS/El) of tensile strength TS and ductility El.
In contrast, in the test number 72～78 of comparative example, the balance (TS/IACS) of tensile strength TS and electric conductivity IACS and the balance (TS/El) of tensile strength TS and ductility El all are inferior.
Fig. 4 has summed up the relation of ductility El shown in table 1 and the table 4 and tensile strength TS.Zero is the example of the present invention in the strip shown in the table 1, ● be the example of the present invention in the wire rod shown in the table 4.△ is the comparative example in the strip shown in the table 1, ▲ be the comparative example in the wire rod of table 4.Show the ductility El that uses formula (5), formula (5 ') and formula (5 ") expression respectively and the relation of tensile strength TS in the figure simultaneously.
Utilizability on the industry
According to the present invention, do not use the harmful element with environmental problem fully, the Cu alloy material of intensity, electric conductivity and excellent in workability can be provided.
Claims (4)
1. Cu alloy material, it is characterized in that, this Cu alloy material contains 0.01～2.5%Ti by quality %, 0.01～0.5%Cr and 0.01% above and be lower than 1%Fe, surplus is made of Cu and impurity, in the middle of the precipitate and inclusion that exists in the alloy material, particle diameter is that the above precipitate of 1 μ m and the total number N of inclusion satisfy following formula (1), and the relation of tensile strength TS and electric conductivity IACS satisfies following formula (2), at the Cu alloy material is that tensile strength TS is when being sheet material below the 600MPa, satisfy following formula (3), at the Cu alloy material is that tensile strength TS is when surpassing the sheet material of 600MPa, satisfy following formula (4), and, when the Cu alloy material is material beyond the sheet material, satisfy following formula (5);
logN≤0.4742+17.629×exp(-0.1133×X)…(1)
TS≥648.06+985.48×exp(-0.0513×IACS)…(2)
B
90≤2.0…(3)
B
90≤25.093-54.82×exp[-{(TS+583.61)/1254}
2]+1.25×t…(4)
E1≥24.138-24.6076×exp[-{(TS-1816.36)/2213.52}
2]…(5)
Wherein, the implication of the symbol in the formula is as described below respectively:
N: the particle diameter of per unit area is the above precipitate of 1 μ m and the total number (mm of inclusion
-2);
X: particle diameter is the above precipitate of 1 μ m and the particle diameter (μ m) of inclusion;
TS: tensile strength (MPa);
IACS: electric conductivity (%);
B
90: the bendability in 90 ° of pliability tests;
T: thickness of slab (mm);
E1: ductility (%);
Wherein, B
90, TS and E1 all be meant the value of the vertical sample of rolling direction of the long limit of taking sample and plate.
2. Cu alloy material according to claim 1 is characterized in that, by quality %, also contains 0.005～1%Ag.
3. Cu alloy material according to claim 1 and 2, it is characterized in that, by quality %, also contain and respectively be 0.01～1.0% and add up to more than one the element among Sn, Mn, Co, Al, Si, Nb, Ta, Mo, V, W, Au, Zn, Ni, Te, Se and the Ge of being selected from below 1.0%.
4. according to each described Cu alloy material of claim 1～3, it is characterized in that,, also contain and add up to 0.001～0.1% more than one the element in Zr, Mg, Li, Ca and the rare earth element of being selected from by quality %.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/JP2007/064813 WO2009016706A1 (en) | 2007-07-27 | 2007-07-27 | Copper alloy material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN101821416A true CN101821416A (en) | 2010-09-01 |
Family
ID=39758336
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200780100048A Pending CN101821416A (en) | 2007-07-27 | 2007-07-27 | Copper alloy material |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US20100189593A1 (en) |
| EP (1) | EP2180071A1 (en) |
| JP (1) | JP4134279B1 (en) |
| CN (1) | CN101821416A (en) |
| WO (1) | WO2009016706A1 (en) |
Cited By (28)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103429771A (en) * | 2011-03-16 | 2013-12-04 | Jx日矿日石金属株式会社 | Cu-Ni-Si alloy wire having excellent bendability |
| CN104409136A (en) * | 2014-12-22 | 2015-03-11 | 孙华桥 | Compound conducting bar |
| CN104630556A (en) * | 2015-02-06 | 2015-05-20 | 中南大学 | Ultrahigh-strength high-toughness high corrosion-resisting CuNiSiNbSn elastic copper alloy and preparation method thereof |
| CN104745860A (en) * | 2015-04-10 | 2015-07-01 | 苏州靖羽新材料有限公司 | Copper alloy for electronic and electrical equipment |
| CN104862521A (en) * | 2015-06-02 | 2015-08-26 | 余锦芳 | Shaft sleeve with good lubricity |
| CN104911391A (en) * | 2015-07-03 | 2015-09-16 | 苏州科茂电子材料科技有限公司 | Copper-based alloy material for coaxial cables and preparation method of copper-based alloy material |
| CN105112720A (en) * | 2015-09-08 | 2015-12-02 | 周欢 | Copper alloy used for wire |
| CN105714146A (en) * | 2016-02-29 | 2016-06-29 | 欧士玺 | Copper alloy valve |
| CN105950907A (en) * | 2016-06-13 | 2016-09-21 | 芜湖卓越线束***有限公司 | High-strength abrasion-resistant alloy material for wiring harness terminal and preparation method of high-strength abrasion-resistant alloy material for wiring harness terminal |
| WO2017198128A1 (en) * | 2016-05-16 | 2017-11-23 | 浙江大学 | Super-strong high-conductivity copper alloy used as material for contact line of high-speed railway allowing speed higher than 400 kilometers per hour |
| WO2017198127A1 (en) * | 2016-05-16 | 2017-11-23 | 浙江大学 | High-strength and high-conductivity copper alloy and applications of alloy as material of contact line of high-speed railway allowing speed higher than 400 kilometers per hour |
| CN107460367A (en) * | 2017-08-29 | 2017-12-12 | 河南科技大学 | A kind of copper alloy of the resistance to abrasion of seawater corrosion containing sand and preparation method thereof |
| CN107805731A (en) * | 2017-10-23 | 2018-03-16 | 江苏都盛科技发展有限公司 | A kind of new alloy material for electric heater |
| CN108004428A (en) * | 2017-12-25 | 2018-05-08 | 浙江力博实业股份有限公司 | A kind of continuously extruded method for preparing cupraloy bar |
| CN108018440A (en) * | 2017-12-25 | 2018-05-11 | 浙江力博实业股份有限公司 | A kind of preparation method of copper alloy with high strength and high conductivity silk material |
| CN108018441A (en) * | 2017-12-25 | 2018-05-11 | 浙江力博实业股份有限公司 | A kind of preparation method of high property copper alloy silk material |
| CN108118179A (en) * | 2017-12-25 | 2018-06-05 | 浙江力博实业股份有限公司 | A kind of preparation method of high-performance cupraloy band |
| CN108118180A (en) * | 2017-12-25 | 2018-06-05 | 浙江力博实业股份有限公司 | A kind of preparation method of Cu-Cr-Zr alloy band used for lead frame |
| CN108179305A (en) * | 2017-12-25 | 2018-06-19 | 浙江力博实业股份有限公司 | A kind of continuously extruded method for preparing Cu-Cr-Zr alloy bar |
| CN108893646A (en) * | 2018-07-10 | 2018-11-27 | 浙江力博实业股份有限公司 | A kind of preparation method of electrode material copper chromium zirconium-niobium alloy |
| CN109022892A (en) * | 2018-07-10 | 2018-12-18 | 浙江力博实业股份有限公司 | A kind of preparation method of electrode material copper chromium almag |
| CN109055810A (en) * | 2018-07-10 | 2018-12-21 | 浙江力博实业股份有限公司 | A kind of preparation method of electrode material copper cobalt chrome-silicon alloy |
| CN110218899A (en) * | 2019-06-21 | 2019-09-10 | 灵宝金源朝辉铜业有限公司 | A kind of high strength anti-corrosion Cu-Ti system alloy foil and preparation method thereof |
| CN110885937A (en) * | 2019-12-19 | 2020-03-17 | 福州大学 | Cu-Ti-Ge-Ni-X copper alloy material and preparation method thereof |
| CN111118335A (en) * | 2020-01-17 | 2020-05-08 | 河北中泊防爆工具集团股份有限公司 | Titanium bronze alloy material and preparation method and application thereof |
| CN111534714A (en) * | 2020-06-24 | 2020-08-14 | 宁波博威合金板带有限公司 | Nb and Al-containing titanium bronze alloy strip and preparation method thereof |
| CN112143933A (en) * | 2020-08-18 | 2020-12-29 | 北京金鹏宝志科技有限公司 | Creep-resistant high-conductivity copper alloy in high-temperature environment |
| CN115418521A (en) * | 2022-07-11 | 2022-12-02 | 大连理工大学 | High-temperature-resistant copper alloy and preparation method thereof |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5490439B2 (en) * | 2009-04-30 | 2014-05-14 | Ｊｘ日鉱日石金属株式会社 | Manufacturing method of titanium copper for electronic parts |
| JP5873618B2 (en) * | 2009-08-18 | 2016-03-01 | 新日鐵住金株式会社 | Method for producing copper alloy |
| JP2015086452A (en) * | 2013-11-01 | 2015-05-07 | 株式会社オートネットワーク技術研究所 | Copper alloy wire, copper alloy twisted wire, coated cable, wire harness and manufacturing method of copper alloy wire |
| JP6354275B2 (en) * | 2014-04-14 | 2018-07-11 | 株式会社オートネットワーク技術研究所 | Copper alloy wire, copper alloy stranded wire and automotive electric wire |
| KR101693814B1 (en) * | 2014-12-26 | 2017-01-09 | 한국기계연구원 | Ti included oxide dispersion strengthened copper alloy and method for manufacturing dispersed copper |
| CN107805732A (en) * | 2017-10-23 | 2018-03-16 | 江苏都盛科技发展有限公司 | A kind of new alloy material for electric heater |
| TW202246536A (en) * | 2021-05-26 | 2022-12-01 | 國立清華大學 | High strength and wear resistant multi-element copper alloy and use thereof |
Family Cites Families (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4594221A (en) | 1985-04-26 | 1986-06-10 | Olin Corporation | Multipurpose copper alloys with moderate conductivity and high strength |
| US4822560A (en) * | 1985-10-10 | 1989-04-18 | The Furukawa Electric Co., Ltd. | Copper alloy and method of manufacturing the same |
| JP2714561B2 (en) | 1988-12-24 | 1998-02-16 | 日鉱金属株式会社 | Copper alloy with good direct bonding properties |
| JPH03188246A (en) * | 1989-12-14 | 1991-08-16 | Nippon Mining Co Ltd | Production of high strength and high conductivity copper alloy |
| JPH03199356A (en) * | 1989-12-27 | 1991-08-30 | Nippon Mining Co Ltd | Manufacture of high strength and high conductivity copper alloy for electronic equipment |
| JPH03199351A (en) * | 1989-12-27 | 1991-08-30 | Nippon Mining Co Ltd | Manufacture of high strength and high conductivity copper alloy for electronic equipment having good stress relaxation property and bendability |
| JP2891021B2 (en) * | 1993-03-05 | 1999-05-17 | 住友金属工業株式会社 | High strength copper alloy wire |
| JP3479470B2 (en) * | 1999-03-31 | 2003-12-15 | 日鉱金属株式会社 | Copper alloy foil for hard disk drive suspension and method of manufacturing the same |
| JP3731600B2 (en) | 2003-09-19 | 2006-01-05 | 住友金属工業株式会社 | Copper alloy and manufacturing method thereof |
| JP2005290543A (en) * | 2004-03-12 | 2005-10-20 | Sumitomo Metal Ind Ltd | Copper alloy and its production method |
-
2007
- 2007-07-27 JP JP2008513833A patent/JP4134279B1/en not_active Expired - Fee Related
- 2007-07-27 EP EP07791507A patent/EP2180071A1/en not_active Withdrawn
- 2007-07-27 WO PCT/JP2007/064813 patent/WO2009016706A1/en active Application Filing
- 2007-07-27 CN CN200780100048A patent/CN101821416A/en active Pending
-
2010
- 2010-01-26 US US12/693,696 patent/US20100189593A1/en not_active Abandoned
Cited By (37)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103429771B (en) * | 2011-03-16 | 2015-08-26 | Jx日矿日石金属株式会社 | The Cu-Ni-Si alloy bar of excellent in bending workability |
| CN103429771A (en) * | 2011-03-16 | 2013-12-04 | Jx日矿日石金属株式会社 | Cu-Ni-Si alloy wire having excellent bendability |
| CN104409136A (en) * | 2014-12-22 | 2015-03-11 | 孙华桥 | Compound conducting bar |
| CN104409136B (en) * | 2014-12-22 | 2016-09-07 | 孙华桥 | A kind of preparation method of compound conductive bar |
| CN104630556A (en) * | 2015-02-06 | 2015-05-20 | 中南大学 | Ultrahigh-strength high-toughness high corrosion-resisting CuNiSiNbSn elastic copper alloy and preparation method thereof |
| CN104745860A (en) * | 2015-04-10 | 2015-07-01 | 苏州靖羽新材料有限公司 | Copper alloy for electronic and electrical equipment |
| CN104862521A (en) * | 2015-06-02 | 2015-08-26 | 余锦芳 | Shaft sleeve with good lubricity |
| CN106090014A (en) * | 2015-06-02 | 2016-11-09 | 余锦芳 | A kind of axle sleeve good for the lubricity of bearing |
| CN104862521B (en) * | 2015-06-02 | 2016-11-16 | 江苏华夏重工有限公司 | The axle sleeve that a kind of lubricity is good |
| CN104911391A (en) * | 2015-07-03 | 2015-09-16 | 苏州科茂电子材料科技有限公司 | Copper-based alloy material for coaxial cables and preparation method of copper-based alloy material |
| CN104911391B (en) * | 2015-07-03 | 2016-12-21 | 江毓锋 | A kind of coaxial cable copper-based alloy material and preparation method thereof |
| CN105112720A (en) * | 2015-09-08 | 2015-12-02 | 周欢 | Copper alloy used for wire |
| CN105714146A (en) * | 2016-02-29 | 2016-06-29 | 欧士玺 | Copper alloy valve |
| WO2017198127A1 (en) * | 2016-05-16 | 2017-11-23 | 浙江大学 | High-strength and high-conductivity copper alloy and applications of alloy as material of contact line of high-speed railway allowing speed higher than 400 kilometers per hour |
| WO2017198128A1 (en) * | 2016-05-16 | 2017-11-23 | 浙江大学 | Super-strong high-conductivity copper alloy used as material for contact line of high-speed railway allowing speed higher than 400 kilometers per hour |
| US10781508B2 (en) | 2016-05-16 | 2020-09-22 | Zhejiang University | High-strength and high-conductivity copper alloy and applications of alloy as material of contact line of high-speed railway allowing speed higher than 400 kilometers per hour |
| US10801087B2 (en) | 2016-05-16 | 2020-10-13 | Zhejiang University | High-strength and high-conductivity copper alloy and applications of alloy as material of contact line of high-speed railway allowing speed higher than 400 kilometers per hour |
| CN105950907A (en) * | 2016-06-13 | 2016-09-21 | 芜湖卓越线束***有限公司 | High-strength abrasion-resistant alloy material for wiring harness terminal and preparation method of high-strength abrasion-resistant alloy material for wiring harness terminal |
| CN107460367A (en) * | 2017-08-29 | 2017-12-12 | 河南科技大学 | A kind of copper alloy of the resistance to abrasion of seawater corrosion containing sand and preparation method thereof |
| CN107805731A (en) * | 2017-10-23 | 2018-03-16 | 江苏都盛科技发展有限公司 | A kind of new alloy material for electric heater |
| CN108004428A (en) * | 2017-12-25 | 2018-05-08 | 浙江力博实业股份有限公司 | A kind of continuously extruded method for preparing cupraloy bar |
| CN108018441A (en) * | 2017-12-25 | 2018-05-11 | 浙江力博实业股份有限公司 | A kind of preparation method of high property copper alloy silk material |
| CN108118180A (en) * | 2017-12-25 | 2018-06-05 | 浙江力博实业股份有限公司 | A kind of preparation method of Cu-Cr-Zr alloy band used for lead frame |
| CN108179305A (en) * | 2017-12-25 | 2018-06-19 | 浙江力博实业股份有限公司 | A kind of continuously extruded method for preparing Cu-Cr-Zr alloy bar |
| CN108118179A (en) * | 2017-12-25 | 2018-06-05 | 浙江力博实业股份有限公司 | A kind of preparation method of high-performance cupraloy band |
| CN108018440A (en) * | 2017-12-25 | 2018-05-11 | 浙江力博实业股份有限公司 | A kind of preparation method of copper alloy with high strength and high conductivity silk material |
| CN108893646A (en) * | 2018-07-10 | 2018-11-27 | 浙江力博实业股份有限公司 | A kind of preparation method of electrode material copper chromium zirconium-niobium alloy |
| CN109022892A (en) * | 2018-07-10 | 2018-12-18 | 浙江力博实业股份有限公司 | A kind of preparation method of electrode material copper chromium almag |
| CN109055810A (en) * | 2018-07-10 | 2018-12-21 | 浙江力博实业股份有限公司 | A kind of preparation method of electrode material copper cobalt chrome-silicon alloy |
| CN110218899A (en) * | 2019-06-21 | 2019-09-10 | 灵宝金源朝辉铜业有限公司 | A kind of high strength anti-corrosion Cu-Ti system alloy foil and preparation method thereof |
| CN110885937A (en) * | 2019-12-19 | 2020-03-17 | 福州大学 | Cu-Ti-Ge-Ni-X copper alloy material and preparation method thereof |
| CN111118335A (en) * | 2020-01-17 | 2020-05-08 | 河北中泊防爆工具集团股份有限公司 | Titanium bronze alloy material and preparation method and application thereof |
| CN111118335B (en) * | 2020-01-17 | 2022-04-08 | 河北中泊防爆工具集团股份有限公司 | Titanium bronze alloy material and preparation method and application thereof |
| CN111534714A (en) * | 2020-06-24 | 2020-08-14 | 宁波博威合金板带有限公司 | Nb and Al-containing titanium bronze alloy strip and preparation method thereof |
| CN111534714B (en) * | 2020-06-24 | 2021-08-31 | 宁波博威合金板带有限公司 | Nb and Al-containing titanium bronze alloy strip and preparation method thereof |
| CN112143933A (en) * | 2020-08-18 | 2020-12-29 | 北京金鹏宝志科技有限公司 | Creep-resistant high-conductivity copper alloy in high-temperature environment |
| CN115418521A (en) * | 2022-07-11 | 2022-12-02 | 大连理工大学 | High-temperature-resistant copper alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| EP2180071A1 (en) | 2010-04-28 |
| US20100189593A1 (en) | 2010-07-29 |
| JPWO2009016706A1 (en) | 2010-10-07 |
| JP4134279B1 (en) | 2008-08-20 |
| WO2009016706A1 (en) | 2009-02-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101821416A (en) | Copper alloy material | |
| CN1856588B (en) | Copper alloy and method for production thereof | |
| JP4809935B2 (en) | Copper alloy sheet having low Young's modulus and method for producing the same | |
| CN100567531C (en) | Copper base alloy and manufacture method thereof | |
| CN101646791B (en) | Cu-ni-si-co-based copper alloy for electronic material, and method for production thereof | |
| EP2426225B1 (en) | Copper alloy with high strength, high electrical conductivity, and excellent bendability | |
| JP5050226B2 (en) | Manufacturing method of copper alloy material | |
| JP3961529B2 (en) | High strength copper alloy | |
| CN102112641B (en) | Copper alloy material for electrical/electronic component | |
| JP5320642B2 (en) | Copper alloy manufacturing method and copper alloy | |
| TWI465591B (en) | Cu-Ni-Si alloy and its manufacturing method | |
| WO2006109801A1 (en) | Copper alloy and process for producing the same | |
| WO2006104152A1 (en) | Copper alloy and process for producing the same | |
| JP5880670B2 (en) | Method for determining melting temperature of copper alloy slabs | |
| JP5873618B2 (en) | Method for producing copper alloy | |
| CN100584975C (en) | Copper-base alloy and preparation method thereof | |
| CN101146920A (en) | Copper alloy for electronic material | |
| CN109609801A (en) | High property copper alloy and preparation method thereof | |
| CN103703154A (en) | Copper alloy | |
| JP4887851B2 (en) | Ni-Sn-P copper alloy | |
| JP2004149874A (en) | Easily-workable high-strength high-electric conductive copper alloy | |
| JP2005113259A (en) | Cu ALLOY AND MANUFACTURING METHOD THEREFOR | |
| CN103140591A (en) | Cu-co-si-based alloy for electronic material and method of manufacturing the same | |
| CN103052728A (en) | Copper-cobalt-silicon alloy for electrode material | |
| WO2015075990A1 (en) | Copper alloy plate, and electronic component for large current applications and electronic component for heat dissipation applications each provided with same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C02 | Deemed withdrawal of patent application after publication (patent law 2001) | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Open date: 20100901 |