WO2009096546A1 - 電気電子部品用銅合金材およびその製造方法 - Google Patents
電気電子部品用銅合金材およびその製造方法 Download PDFInfo
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- WO2009096546A1 WO2009096546A1 PCT/JP2009/051623 JP2009051623W WO2009096546A1 WO 2009096546 A1 WO2009096546 A1 WO 2009096546A1 JP 2009051623 W JP2009051623 W JP 2009051623W WO 2009096546 A1 WO2009096546 A1 WO 2009096546A1
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- 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
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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
- C22C9/06—Alloys based on copper with nickel or cobalt as the next major constituent
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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
- C22C9/10—Alloys based on copper with silicon as the next major constituent
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- 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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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L23/00—Details of semiconductor or other solid state devices
- H01L23/48—Arrangements for conducting electric current to or from the solid state body in operation, e.g. leads, terminal arrangements ; Selection of materials therefor
- H01L23/488—Arrangements for conducting electric current to or from the solid state body in operation, e.g. leads, terminal arrangements ; Selection of materials therefor consisting of soldered or bonded constructions
- H01L23/495—Lead-frames or other flat leads
- H01L23/49579—Lead-frames or other flat leads characterised by the materials of the lead frames or layers thereon
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L23/00—Details of semiconductor or other solid state devices
- H01L23/48—Arrangements for conducting electric current to or from the solid state body in operation, e.g. leads, terminal arrangements ; Selection of materials therefor
- H01L23/488—Arrangements for conducting electric current to or from the solid state body in operation, e.g. leads, terminal arrangements ; Selection of materials therefor consisting of soldered or bonded constructions
- H01L23/498—Leads, i.e. metallisations or lead-frames on insulating substrates, e.g. chip carriers
- H01L23/49866—Leads, i.e. metallisations or lead-frames on insulating substrates, e.g. chip carriers characterised by the materials
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L2924/00—Indexing scheme for arrangements or methods for connecting or disconnecting semiconductor or solid-state bodies as covered by H01L24/00
- H01L2924/0001—Technical content checked by a classifier
- H01L2924/0002—Not covered by any one of groups H01L24/00, H01L24/00 and H01L2224/00
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- H—ELECTRICITY
- H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
- H05K—PRINTED CIRCUITS; CASINGS OR CONSTRUCTIONAL DETAILS OF ELECTRIC APPARATUS; MANUFACTURE OF ASSEMBLAGES OF ELECTRICAL COMPONENTS
- H05K1/00—Printed circuits
- H05K1/02—Details
- H05K1/09—Use of materials for the conductive, e.g. metallic pattern
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- H—ELECTRICITY
- H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
- H05K—PRINTED CIRCUITS; CASINGS OR CONSTRUCTIONAL DETAILS OF ELECTRIC APPARATUS; MANUFACTURE OF ASSEMBLAGES OF ELECTRICAL COMPONENTS
- H05K3/00—Apparatus or processes for manufacturing printed circuits
- H05K3/10—Apparatus or processes for manufacturing printed circuits in which conductive material is applied to the insulating support in such a manner as to form the desired conductive pattern
- H05K3/20—Apparatus or processes for manufacturing printed circuits in which conductive material is applied to the insulating support in such a manner as to form the desired conductive pattern by affixing prefabricated conductor pattern
- H05K3/202—Apparatus or processes for manufacturing printed circuits in which conductive material is applied to the insulating support in such a manner as to form the desired conductive pattern by affixing prefabricated conductor pattern using self-supporting metal foil pattern
Definitions
- the present invention is applied to connectors and terminal materials for electrical and electronic equipment, particularly high frequency relays and switches for which high conductivity is desired, or electrical and electronic parts such as connectors, terminal materials and lead frames for automobiles.
- the present invention relates to a copper alloy material and a manufacturing method thereof.
- CXXXX is a type of copper alloy specified by JIS, and% IACS is an abbreviation for international annealed copper standard, and is a unit indicating the conductivity of a material.
- conductivity and strength are contradictory properties, and there are various strengthening methods such as solid solution strengthening, work strengthening, and precipitation strengthening as methods for increasing strength. It is known that it is promising as a method for increasing strength without deteriorating.
- This precipitation strengthening is performed by high-temperature heat treatment of an alloy added with an element that causes precipitation, so that these elements are dissolved in the copper matrix phase, and then heat-treated at a temperature lower than that temperature to precipitate the dissolved element. It is a technique. For example, beryllium copper, Corson alloy, etc. employ the strengthening method.
- alloys containing an intermetallic compound of cobalt (Co) and silicon (Si) in copper are also known.
- copper alloy technology using an intermetallic compound of Co and Si there is a copper alloy (see, for example, Patent Document 1) containing Co, Si, Zn, Mg, and S as essential components, and an alloy containing Co, Si, Mg, Sn, and Zn (eg, , See Patent Document 2), which is a copper alloy that essentially contains Co, Si, Sn, and Zn (see, for example, Patent Document 3).
- Patent Documents 2 to 3 describe Co and Si precipitates as Co 2 Si compounds.
- Patent Document 4 There is also a document describing a Cu—Co—Si based alloy as a copper alloy for use in lead frames.
- the improvement objective in this patent document 1 is hot workability, there is no description about the precipitate of Co and Si, and there is no description of how the size etc. were controlled. Moreover, even if it sees an Example, the result of having evaluated the intensity
- the Patent Document 2 is described with the Co 2 Si compound for precipitates of Co and Si, wherein a is not unknown for its size and its control method, only the annealing for one hour at 500 ° C. or 450 ° C. And no recrystallization treatment was performed. That is, the crystal grain size is unclear because of the strong rolled material.
- Patent Document 3 as in Patent Document 2, although the precipitates of Co and Si is described with Co 2 Si compound, similar size and a control method in Patent Document 2 is not known, 1 400 ⁇ 500 ° C. Time annealing is performed. Before that, solution treatment and cold rolling are performed at 950 ° C. The description of this document shows that the Sn addition amount is as high as 1 mass% or more, and therefore, the conductivity is relatively low, ie, 30% IACS or less in the examples.
- Patent Document 4 is a copper alloy for use in a lead frame and is described as a precipitation strengthening type alloy, but does not show a specific compound or its size. Furthermore, only a heat treatment at 500 ° C. for 1 hour, followed by cold rolling and a strain relief annealing at 300 ° C. for 1 hour, no recrystallization treatment is performed. Therefore, it is estimated that the crystal grain size is unclear.
- the object of the present invention is to provide a copper alloy suitable for electrical and electronic parts such as connectors, terminal materials, and relays, which have high conductivity, high strength, and excellent bending workability. It is in providing a material and its manufacturing method.
- the inventors of the present invention have studied copper alloys suitable for electric / electronic component applications, and have a conductivity of 50% IACS or higher, a tensile strength of 500 MPa or higher, and a bending workability of R / t ⁇ 2 at the same time. It turns out that is important.
- R / t R is a bending radius
- t is a plate thickness. The lower this value, the better the workability. Therefore, in order to achieve both strength and bending workability, the present invention has a specific component composition, and finds the optimum relationship between the crystal grain size limitation and the precipitate size, and further studies are made. This led to the completion of the invention.
- Co includes 0.2 to 2 mass%
- Si includes 0.05 to 0.5 mass%
- the balance is made of Cu and inevitable impurities
- the crystal grain size is 3 to 35 ⁇ m
- both Co and Si are mixed.
- a copper alloy material for electrical and electronic parts characterized in that the size of the precipitate containing 5 to 50 nm, (2) The copper alloy material for electrical and electronic parts according to (1), further comprising 0.01 to 0.5 mass% of one or more selected from the group consisting of Fe, Ni, Cr and P , (3) The copper alloy material for electrical and electronic parts according to (1), further comprising 0.01 to 0.5 mass% of one or more selected from the group consisting of Sn, Zn, Mg and Mn , (4) The copper alloy material for electrical and electronic parts according to (2), further comprising 0.01 to 0.5 mass% of one or more selected from the group consisting of Sn, Zn, Mg and Mn , (5) Any one of (1) to (4), wherein the electrical conductivity is 50% IACS or more, the tensile strength is 500 MPa or more, and the bending workability (R / t) is 2 or less.
- the copper alloy material for electrical and electronic parts described above, and (6) a copper alloy containing 0.2 to 2 mass% Co and 0.05 to 0.5 mass% Si, with the balance being Cu and inevitable impurities at 700 ° C. or higher
- “high conductivity” means that the conductivity is 50% IACS or more.
- the present invention is an alloy having a specific composition of Cu—Co—Si.
- a copper alloy material having three characteristics, and a copper alloy material suitable for parts for electrical and electronic equipment can be obtained.
- Fe, Ni, Cr, P and Sn, Zn, Mg, Mn as alloy components, a copper alloy material having more excellent characteristics can be obtained.
- solution recrystallization heat treatment at a specific temperature and limiting the cooling rate, the crystal grain size and the size of the precipitate can be controlled, and a copper alloy material having excellent characteristics can be obtained.
- the copper alloy material of the present invention is a copper alloy material having a specific shape, for example, a plate material, a strip material, a wire material, a rod material, a foil, and the like, and can be used for any electric / electronic component. Is not particularly limited, for example, suitable for connectors, terminal materials, etc., particularly high frequency relays and switches for which high conductivity is desired, or connectors, terminal materials and lead frames for automobiles Used.
- Co and Si are essential components. Co and Si in the copper alloy mainly form precipitates of Co 2 Si intermetallic compounds to improve strength and conductivity.
- Co is 0.2 to 2 mass%, preferably 0.5 to 1.5 mass%, more preferably 0.8 to 1.4 mass%
- Si is 0.05 to 0.5 mass%, preferably 0.1 to 0. .45 mass%, more preferably 0.18 to 0.35 mass%.
- these mainly form precipitates of intermetallic compounds of Co 2 Si and contribute to precipitation strengthening. If the amount of Co is too small, the precipitation strengthening amount is small, and if it is too large, the effect is saturated.
- the optimum addition ratio based on the stoichiometric ratio of this compound is Co / Si ⁇ 4.2. However, with this value as the center, Co / Si is 3.0 to 6.0, more preferably 3.8.
- the temperature at which solution recrystallization is performed is preferably in the range of 700 to 800 ° C.
- the addition amount of Co is 0.5 to 1.2 mass%.
- the temperature for performing the solution recrystallization treatment is preferably in the range of 800 to 900 ° C.
- the temperature for performing the solution recrystallization treatment is 900 to 900 ° C.
- a range of less than 950 ° C is preferred.
- the temperature at which the solution recrystallization treatment is performed is not limited to the above temperature range, but the above temperature range is a desirable range based on the crystal grain size described later.
- Fe, Ni, Cr and P to the copper alloy of the present invention, and the amount thereof is 0.01 to 0.5 mass%, preferably 0.2 to 0.4 mass%.
- Precipitates containing both Co and Si include "Co and Si precipitates” as well as “Co and Si, and any one or more of Fe, Ni, Cr and P" (Including precipitates containing the element). If the amount added is too small, the effect of the addition is small, and if it is too large, conversely, it dissolves in the copper matrix and forms other compounds that have no strengthening action (inconsistent precipitates). This is to inhibit conductivity.
- the copper alloy of the present invention it is preferable to add one or more of Sn, Zn, Mg and Mn to the copper alloy of the present invention, and the amount thereof is 0.01 to 0.5 mass%, preferably 0.08. ⁇ 0.3 mass%. These have the effect of strengthening the copper alloy by dissolving in the copper matrix. Therefore, if the amount is too small, the effect is not obtained. If the amount is too large, the conductivity is hindered. Zn has an effect of improving solder adhesion, and Mg and Mn have an effect of improving hot workability. Of course, even if Fe, Ni, Cr, P and Sn, Zn, Mg, Mn are added in a limited range, individual characteristics are not inhibited as long as they are within the specified range.
- the crystal grain size and the size of the precipitate containing both Co and Si are strictly defined.
- the crystal grain size is 3 to 35 ⁇ m, preferably 5 to 20 ⁇ m. The reason for this is that if the crystal grain size is too small, recrystallization is sufficient, and mixed grains including unrecrystallized grains where insufficient recrystallized portions are observed tend to be poor in bending workability. On the other hand, if the crystal grain size is too large, the grain boundary density is low due to the coarse grain size, and it is assumed that the workability deteriorates because the bending stress cannot be sufficiently absorbed.
- the “crystal grain size” is a value measured based on JIS-H0501 (cutting method) described later. Further, in the copper alloy material of the present invention, the size of the precipitate of the compound mainly containing both Co and Si is set to 5 to 50 nm. Since this compound strengthens by precipitation in conformity with the copper matrix, if this size is too small, a sufficient amount of precipitation strengthening cannot be obtained, and if it is too large, it loses its consistency and conversely decreases strength. Therefore, it was limited to this range. Desirably, the size of the precipitate is 10-30 nm. The “size of the precipitate” here is an average size of the precipitate determined by the method described later.
- a material having an electrical conductivity of 50% IACS or more, a tensile strength of 500 MPa or more, and a bending workability (R / t) of 2 or less is preferable.
- the reason is based on satisfying the minimum electrical conductivity, tensile strength and bending workability required for electric and electronic parts required by the market as electric and electronic equipment demands miniaturization and high performance.
- the conductivity is more preferably 55% IACS or more, and even more preferably 60% IACS or more, and the higher the better, but the upper limit is usually about 70% IACS.
- the tensile strength is more preferably 550 MPa or more, and even more preferably 600 MPa or more, and the higher the better, the upper limit is usually about 850 MPa.
- the bending workability (R / t) is more preferably 1.5 or less, still more preferably 1 or less, and the smaller the better. In practice, the lower limit is zero.
- a preferred method for producing a copper alloy material according to the present invention is, for example, as follows.
- the outline of the main manufacturing process of the copper alloy material according to the present invention is as follows: melting ⁇ casting ⁇ hot rolling ⁇ facing ⁇ cold rolling ⁇ solution recrystallization heat treatment ⁇ rapid cooling ⁇ aging heat treatment ⁇ final cold rolling ⁇ low temperature annealing It is. Aging heat treatment and final cold rolling may be performed in reverse order. The final low-temperature annealing may be omitted.
- the solution recrystallization heat treatment before the final cold rolling be 700 ° C. or more and less than 950 ° C.
- the reason specified in this way is that the above-mentioned element such as Co is sufficiently solution-treated and 700 ° C. or higher is necessary for the recrystallization treatment.
- This is not an industrially preferable temperature because problems such as partial melting of the material and shape deformation occur.
- it is a temperature at which the solution treatment and the recrystallization treatment can be sufficiently performed at 800 ° C. or more and less than 950 ° C., and can be stably produced industrially.
- the crystal grain size in the copper alloy material is determined by solution recrystallization heat treatment at this temperature.
- rapid cooling at a cooling rate of 50 ° C./sec or more from the solution recrystallization heat treatment temperature is preferred. If this rapid cooling cannot be obtained, the element dissolved at the high temperature may cause precipitation.
- the particles (compounds) that have precipitated during cooling are non-coherent precipitates that do not contribute to strength, and nucleation occurs when coherent precipitates are formed in the next aging heat treatment step. It contributes as a site and promotes the precipitation of that portion, which adversely affects the properties.
- the cooling rate is preferably 80 ° C./sec or more, more preferably 100 ° C./sec or more. A quenching rate as fast as possible is desirable, but the practical upper limit is usually about 200 ° C./sec.
- This cooling rate means an average rate from the high-temperature solution recrystallization heat treatment temperature to 300 ° C. Since a large tissue change does not occur at a temperature of 300 ° C. or lower, the cooling rate to this temperature may be appropriately controlled.
- the aging heat treatment is preferably performed at 450 ° C. to 600 ° C., more preferably 500 ° C. to 575 ° C.
- the aging heat treatment is preferably performed for 1 to 4 hours, more preferably 2 to 3 hours. When the aging heat treatment is performed before the final cold rolling, it is more preferable to perform the aging heat treatment at 525 to 575 ° C.
- the aging heat treatment is more preferably performed at 450 to 550 ° C, and further preferably 475 ° C to 525 ° C. This is because the precipitation temperature zone is shifted to the low temperature side by the cold rolling treatment.
- Processing rate in final cold rolling that is, (H ⁇ H 1 ) ⁇ H ⁇ 100, where H represents the thickness before final cold rolling, and H 1 represents the thickness after final cold rolling.
- H represents the thickness before final cold rolling
- H 1 represents the thickness after final cold rolling.
- low-temperature annealing strain relief annealing
- it can be carried out by a conventional method, but is preferably 300 ° C. to 450 ° C., more preferably 350 ° C. to 400 ° C., preferably 5 seconds to 120 seconds, more preferably 10 to 30 seconds.
- Process A Solution recrystallization heat treatment ⁇ Rapid cooling ⁇ Aging heat treatment (at a temperature of 500 to 600 ° C. for 0.5 to 6 hours) ⁇ Final cold rolling (working rate 5 to 25%) ⁇ Final copper alloy material Accordingly, strain relief annealing was performed at a temperature of 300 to 400 ° C. for 1 to 2 hours after the final cold rolling to remove strain due to the final cold rolling.
- Step B Solution recrystallization heat treatment ⁇ Rapid cooling ⁇ Final cold rolling (working rate 5 to 25%) ⁇ Aging heat treatment (at a temperature of 450 to 550 ° C. for 0.5 to 5 hours) ⁇ Final copper alloy material Tables 1 and 2 show the solution recrystallization heat treatment temperature employed in the comparative examples, the cooling rate during the rapid cooling treatment, the aging heat treatment temperature, the aging heat treatment time, and the final cold rolling rate.
- SEM scanning electron microscope
- the “mixed grain” in the table is a structure in which both recrystallization and non-recrystallized (rolling residue) are mixed.
- the particle size was not measured. It is said that bending workability deteriorates when unrecrystallized exists. Therefore, mixed grains are undesirable structures.
- Precipitate Size The precipitate size was evaluated using a transmission electron microscope. Since the final copper alloy material becomes difficult to observe due to the influence of processing strain (particularly in the case of the step A), the structure of the material after aging heat treatment was observed. This is because the size and density of the precipitate do not change in strain relief annealing or cold rolling, and the size of the precipitate after the aging heat treatment matches the size of the precipitate of the final copper alloy material.
- a specimen for TEM is cut out from an arbitrary place on the aging heat treatment material, and electropolished with a methanol solution of nitric acid (20%) at a temperature of ⁇ 20 to ⁇ 25 ° C. (twin jet: made by Struers). Was completed. Thereafter, observation was carried out at an acceleration voltage of 300 kV, and three photographs with a magnification of 100,000 were arbitrarily taken with the incident direction of the electron beam being set to the vicinity of (001). Using the photograph, the average size of the precipitates (about 100) was determined.
- the cooling rate was adjusted by changing the kind of the cooling liquid for quenching and the amount of the cooling liquid.
- water water temperature: 20-30 ° C.
- silicon oil liquid temperature: 20-30 ° C.
- salt bath liquid temperature: 300 ° C., using nitrate
- FIG. 1 shows an example of the cooling rate of the coolant in each bottle. This data is a result of measurement with a thermocouple attached to a test piece (50 ⁇ 150 ⁇ 0.2 mm).
- No. shown in the comparative example. 1 to 13 are outside the scope of the embodiment described in the above item (1), and do not satisfy at least one of the conditions of strength, conductivity and bending workability.
- No. Nos. 11 to 15 are comparative examples relating to the embodiment described in the above item (2), and are outside the range of the composition defined in the above item (2).
- Reference numerals 16 to 18 are comparative examples relating to the embodiment described in the above item (3), which are outside the range of the composition defined in the above item (3), and satisfy at least one of the conditions of strength, conductivity, and bending workability. Not done.
- No. 19 and 20 are comparative examples relating to the embodiment described in the above section (5), and are outside the scope of the embodiment defined in the above section (5), and thus are within the scope of the embodiment described in the above section (5).
- Invention Examples 1 to 4 particularly Invention Examples 2 to 3
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Abstract
Description
近年、これらが使用される電子・電気機器で使用される電流の周波数が高くなり、表皮効果により実質的な導電率が低下するため、材料にも高導電性が要求されるようになっている。そこで、元々、黄銅やリン青銅は導電性が低く、コルソン銅合金はコネクタ材として、中導電性(EC≒40~50%IACS)を示すが、さらに高導電性が求められている。また、ベリリウム銅は中導電性を有するが高価であり、さらにはベリリウムが環境負荷物質であるために他の銅合金等への置き換えが検討されていることも周知である。一方、高導電性である純銅(C1100)やSn入銅(C14410)などは強度が低い欠点がある。そこで、従来のコルソン銅を越える導電性と、同等の引張強度、曲げ加工性を備えた銅合金が所望されている。
上記CXXXXとは、JISで規定された銅合金の種類であり、%IACSとはinternational annealed copper standardの略で、材料の導電性を示す単位である。
その公知例を挙げると、CoとSiと、Zn、Mg、Sを必須成分として含む銅合金(例えば、特許文献1参照)があり、CoとSiと、Mg、Sn,Znを含む合金(例えば、特許文献2参照)があり、CoとSiと、Sn、Znを必須に含む銅合金(例えば、特許文献3参照)である。特許文献2~3にはCoとSiの析出物についてCo2Si化合物との記載がある。また、リードフレーム用途の銅合金としてのCu-Co-Si系合金が記載されている文献もある(例えば、特許文献4参照)。
特許文献2にはCoとSiの析出物についてCo2Si化合物との記載があるが、そのサイズやその制御方法に関しては記載が無く不明であり、500℃または450℃で1時間の焼鈍のみを行い、再結晶処理を行っていない。つまり、強圧延材のため結晶粒径は不明確である。
特許文献3には、特許文献2と同様、CoとSiの析出物についてCo2Si化合物との記載があるが、特許文献2と同様サイズやその制御方法は不明で、400~500℃で1時間の焼鈍を行っている。また、その前に950℃で溶体化処理と冷間圧延を行っている。この文献の記載はSn添加量が1mass%以上と高いため、実施例を見ると導電率は30%IACS以下と比較的低い導電性が示されている。
特許文献4は、リードフレーム用途の銅合金であり、析出強化型合金と記載されているが具体的な化合物やそのサイズを示していない。更に、500℃で1時間の熱処理、その後に冷間圧延と300℃で1時間のひずみ取り焼鈍を行っているだけで再結晶処理を行っていない。よって、結晶粒径は不明確であると推定される。
一方、合金組織において、結晶粒径が粗大であると曲げ加工性が悪いことが知られているが、特許文献3の溶体化温度は950℃と非常に高温であり、高温ほど結晶粒径が粗大化するためこの材料の曲げ加工性は悪いと判断される。また、950℃は銅合金の融点近傍であり、材料形状が安定せず、また、高温ほど熱処理炉の耐火材に特殊な材料を使用する必要があるため工業的には不利な条件である。
そこで上記のような問題点に鑑み、本発明の課題は、高導電性で強度が高く、曲げ加工性の三者が共に優れたコネクタ、端子材、リレーなどの電気電子部品に適した銅合金材およびその製造方法を提供することにある。
ここで、R/tにおけるRは曲げ半径、tは板厚であり、この値が低いほど良好な曲げ加工性を示す指針となる。
そこで、本発明は高導電性であると共に強度、曲げ加工性の両立を図るため、特定の成分組成を有し、結晶粒径の限定と析出物のサイズとの最適な関係を見出し、さらに検討を重ね発明を完成させるに至った。
(1)Coを0.2~2mass%、Siを0.05~0.5mass%を含み、残部がCuおよび不可避不純物からなり、その結晶粒径が3~35μmで、CoとSiの両方を含む析出物のサイズが5~50nmであることを特徴とする電気電子部品用銅合金材、
(2)更にFe、Ni、CrおよびPからなる群から選ばれる1種または2種以上を0.01~0.5mass%含むことを特徴とする(1)記載の電気電子部品用銅合金材、
(3)更にSn、Zn、MgおよびMnからなる群から選ばれる1種または2種以上を0.01~0.5mass%含むことを特徴とする(1)記載の電気電子部品用銅合金材、
(4)更にSn、Zn、MgおよびMnからなる群から選ばれる1種または2種以上を0.01~0.5mass%含むことを特徴とする(2)記載の電気電子部品用銅合金材、
(5)導電率が50%IACS以上、かつ、引張強度が500MPa以上で、曲げ加工性(R/t)が2以下であることを特徴とする(1)~(4)のいずれか1項記載の電気電子部品用銅合金材、および
(6)Coを0.2~2mass%、Siを0.05~0.5mass%を含み、残部がCuおよび不可避不純物からなる銅合金を700℃以上950℃未満で溶体化再結晶熱処理を行う工程aと、前記工程a後に、前記溶体化再結晶熱処理時の温度から300℃までの平均冷却速度を50℃/sec以上とする冷却処理を行う工程bとを有する、結晶粒径が3~35μmで、CoとSiの両方を含む析出物のサイズが5~50nmである銅合金材を得ることを特徴とする電気電子部品用銅合金材の製造方法。
なお、ここで「高導電性」は、導電率が50%IACS以上であることを意味する。
さらに、特定の温度で溶体化再結晶熱処理を行い、その冷却速度を限定することで、結晶粒径と析出物のサイズが制御でき、優れた特性を持つ銅合金材を得ることができる。
本発明の上記及び他の特徴及び利点は、適宜添付の図面を参照して、下記の記載からより明らかになるであろう。
本発明の銅合金組成では、CoとSiが必須成分である。銅合金中のCoとSiは、主としてCo2Si金属間化合物の析出物を形成して強度および導電率を向上する。
Coを0.2~2mass%、好ましくは0.5~1.5mass%、さらに好ましくは0.8~1.4mass%、Siを0.05~0.5mass%、好ましくは0.1~0.45mass%、さらに好ましくは0.18~0.35mass%である。このように規定する理由は、前記したようにこれらは主としてCo2Siの金属間化合物の析出物を形成し、析出強化に寄与する。Co量が少なすぎると析出強化量が小さく、多すぎるとその効果が飽和してしまう。また、この化合物の化学量論比から最適な添加比は、Co/Si≒4.2であるが、この値を中心にCo/Siを3.0~6.0、より好ましくは3.8~4.6の範囲内になるように調整することが好ましい。
また、Coの添加量と溶体化再結晶処理を行う温度との関係では、好ましい範囲がある。例えば、Coの添加量が0.2~0.8mass%の場合には溶体化再結晶処理を行う温度は700~800℃の範囲が好ましく、Coの添加量が0.5~1.2mass%の場合には溶体化再結晶処理を行う温度は800~900℃の範囲が好ましく、Coの添加量が1.0~2.0mass%の場合には溶体化再結晶処理を行う温度は900~950℃未満の範囲が好ましい。もちろん、溶体化再結晶処理を行う温度は上記温度範囲に限定されるものではないが、上記温度範囲は、後に記載する結晶粒径に基づく望ましい範囲である。
もちろん、Fe、Ni、Cr、PとSn、Zn、Mg、Mnを制限された範囲で複合添加しても、上記規定した範囲内であれば、個々の特性を阻害することはない。
また、更に本発明の銅合金材では主にCoとSiの両方を含む化合物の析出物のサイズを5~50nmとしている。この化合物は銅母相と整合に析出をして強化するため、このサイズが小さすぎると十分な析出強化量を得ることができず、大きすぎるとその整合性を失って逆に、強度の低下を招くためこの範囲に限定した。望ましい、析出物のサイズは10~30nmである。
ここでいう「析出物のサイズ」は、後述する方法で求めた析出物の平均サイズである。
本発明においては、最終冷間圧延前の溶体化再結晶熱処理を700℃以上950℃未満とするのが好ましい。このように規定した理由は、上記のCoなどの元素を十分に溶体化処理する目的と再結晶処理するためには700℃以上が必要であり、また、950℃以上になると銅の融点近傍となり材料の部分溶融や形状変形問題が発生するため工業的に好ましい温度ではない。好ましくは、800℃以上950℃未満であれば十分に溶体化処理と再結晶処理ができ、かつ、工業的に安定的に製造できうる温度である。この温度の溶体化再結晶熱処理によって銅合金材中の結晶粒径が決定する。
冷却速度は、80℃/sec以上が好ましく、さらに好ましくは100℃/sec以上であり、できる限り早い焼入れ速度が望ましいが、その実際的な上限は通常200℃/sec程度である。
なお、この冷却速度は高温の溶体化再結晶熱処理温度から300℃までの平均速度を意味する。300℃以下の温度では大きな組織変化は起きないため、この温度までの冷却速度を適切に制御すればよい。
本発明では、溶体化再結晶熱処理後に、またはその後の最終冷間圧延後に、時効熱処理を行うことが好ましい。時効熱処理は450℃~600℃で行うことが好ましく、より好ましくは500℃~575℃である。また、時効熱処理は、1~4時間行うことが好ましく、より好ましくは2~3時間である。
最終冷間圧延前に時効熱処理を行う場合には、525~575℃で時効熱処理を行うことがより好ましい。
最終冷間圧延後に時効熱処理を行う場合には、450~550℃で時効熱処理を行うことがより好ましく、さらに好ましくは475℃~525℃である。冷間圧延処理により析出温度帯が低温側にシフトするためである。
最終冷間圧延での加工率(即ち、(H-H1)÷H×100、ここでHは最終冷間圧延前の板厚を表し、H1は最終冷間圧延後の板厚を表す)は、5~25%が好ましく、より好ましくは5~10%である。
低温焼鈍(ひずみ取り焼鈍)を行う場合には常法により行うことができるが、好ましくは300℃~450℃、より好ましくは350℃~400℃で、好ましくは5秒~120秒、より好ましくは10秒~30秒である。
本発明の実施例および比較例に用いた銅合金は、表1、表2に示した成分を含有し、残部がCuと不可避不純物から成る合金(本発明例No.1~30、比較例No.1~20)である。これらの各合金を高周波溶解炉により溶解し、これらを10~30℃/秒の冷却速度で鋳造して厚さ30mm、幅100mm、長さ150mmの鋳塊を得た。
得られた鋳塊を930~970℃の温度で0.5~1.0時間保持後、熱間圧延を行い板厚t=12mmの熱延板を作製し、その両面を各1mm面削してt=10mmとし、次いで冷間圧延によりt=0.3mmに仕上げ、700~950℃の温度で溶体化再結晶熱処理を行った。この溶体化再結晶熱処理をした材料を次の2工程のいずれかの処理を施して最終銅合金材を作成した。
工程A:溶体化再結晶熱処理→急速冷却→時効熱処理(500~600℃の温度で0.5~6時間)→最終冷間圧延(加工率5~25%)→最終銅合金材
なお、必要に応じて、最終冷間圧延後300~400℃の温度で1~2時間のひずみ取り焼鈍を実施し、最終冷間圧延による歪を取り除いた。
工程B:溶体化再結晶熱処理→急速冷却→最終冷間圧延(加工率5~25%)→時効熱処理(450~550℃の温度で0.5~5時間)→最終銅合金材
本発明例および比較例で採用した溶体化再結晶熱処理温度、急速冷却処理時の冷却速度、時効熱処理温度、時効熱処理時間、最終冷間圧延加工率を表1および表2に示す。
a.結晶粒径:
供試材からの試験片の圧延方向に垂直な断面を湿式研磨、バフ研磨により鏡面に仕上げた後、クロム酸:水=1:1の液で数秒研磨面を腐食した後、光学顕微鏡で200~400倍の倍率か、走査型電子顕微鏡(SEM)の二次電子像を用いて500~2000倍の倍率で写真をとり、断面粒径をJIS H0501の切断法に準じて結晶粒径を測定した。
なお、表中の「混粒」とは、再結晶と未再結晶(圧延加工残留)の両方が混在した組織で、混粒の場合には粒径は測定しなかった。未再結晶が存在すると曲げ加工性が劣化すると言われている。そのため、混粒は望ましくない組織である。
b.析出物のサイズ
析出物のサイズは透過電子顕微鏡を用いて評価を行った。最終銅合金材では加工歪みの影響で観察しにくくなるため(特にA工程の場合)時効熱処理後の材料の組織観察を実施した。ひずみ取り焼鈍や冷間圧延では析出物のサイズや密度は変わらず、時効熱処理後の析出物のサイズと最終銅合金材の析出物のサイズが一致するためである。時効熱処理材の任意の場所からTEM用試験片を切り出し、硝酸(20%)のメタノール溶液で温度-20~-25℃で電解研磨(ツインジェット:ストルアス社製)を行って観察用の試験片を完成させた。
その後、加速電圧:300kVで観察を行って、電子線の入射方位を(001)近傍に合わせて、10万倍の倍率の写真を任意に3枚撮影した。その写真を用いて析出物(約100個)の平均サイズを求めた。
各供試材の圧延平行方向から切り出したJIS Z2201-13B号の試験片を引張り速度10mm/分、ゲージ長50mmの条件で、JIS Z2241に準じて3本測定しその平均値を求めた。
d.導電率測定:
四端子法を用いて、20℃(±1℃)に管理された恒温槽中で、各供試材の各試験片の2本について導電率を測定し、その平均値(%IACS)を求めた。このとき端子間距離は100mmとした。
e.曲げ加工性:
各供試材(厚さ0.15~0.25mm)を圧延方向に垂直に幅10mm、長さ35mmに切出し、これを曲げの軸が圧延方向に平行となるように90°W曲げ(Bad-way曲げ)し、曲げ部における割れの有無を50倍の光学顕微鏡で目視観察および走査型電子顕微鏡(SEM)によりその曲げ加工部位を観察し割れの有無を調査した。曲げ半径Rは、R=0~0.5(mm)の8水準(0、0.1、0.15、0.2、0.25、0.3、0.4、0.5)とした。
なお、評価結果はR/t(Rは曲げ半径、tは板厚)で表記し、割れが発生する限界のRを採用してR/tを算出した。仮に、R=0.15(mm)で割れが発生せず、R=0.1で割れが発生した場合は、板厚(t)=0.15mmならR/t=0.15/0.15=1と表記した。
この例は全て冷却液が約5L(リットル)の場合であり、水>シリコンオイル>塩浴の順に冷却速度が速くなる。なお、今回の試験とは冷却液の条件を変化させた場合についても試験を行ったところ、冷却液の量を減らすと冷却速度のカーブがなだらかとなるが、冷却液量を増やしても顕著に冷却速度の向上は見られなかった。
これに対し、比較例に示すNo.1~13は前記(1)項に記載の態様の範囲外のものがあり、強度、導電性、曲げ加工性の条件の少なくとも1つを満足していない。また、No.11~15は前記(2)項に記載の態様に関する比較例であり、前記(2)項で規定する組成の範囲外であり、No.16~18は前記(3)項に記載の態様に関する比較例であり、前記(3)項で規定する組成の範囲外であり、強度、導電性、曲げ加工性の条件の少なくとも1つを満足していない。
そしてNo.19,20は前記(5)項に記載の態様に関する比較例であり、前記(5)項で規定する態様の範囲外であるので、前記(5)項に記載の態様の範囲内である本発明例1~4(特に本発明例2~3)と比較して、引張強度、曲げ加工性が劣る傾向がみられる。
Claims (6)
- Coを0.2~2mass%、Siを0.05~0.5mass%を含み、残部がCuおよび不可避不純物からなり、その結晶粒径が3~35μmで、CoとSiの両方を含む析出物のサイズが5~50nmであることを特徴とする電気電子部品用銅合金材。
- 更にFe、Ni、CrおよびPからなる群から選ばれる1種または2種以上を0.01~0.5mass%含むことを特徴とする請求項1記載の電気電子部品用銅合金材。
- 更にSn、Zn、MgおよびMnからなる群から選ばれる1種または2種以上を0.01~0.5mass%含むことを特徴とする請求項1記載の電気電子部品用銅合金材。
- 更にSn、Zn、MgおよびMnからなる群から選ばれる1種または2種以上を0.01~0.5mass%含むことを特徴とする請求項2記載の電気電子部品用銅合金材。
- 導電率が50%IACS以上、かつ、引張強度が500MPa以上で、曲げ加工性(R/t)が2以下であることを特徴とする請求項1~4のいずれか1項記載の電気電子部品用銅合金材。
- Coを0.2~2mass%、Siを0.05~0.5mass%を含み、残部がCuおよび不可避不純物からなる銅合金を700℃以上950℃未満で溶体化再結晶熱処理を行う工程aと、前記工程a後に、前記溶体化再結晶熱処理時の温度から300℃までの平均冷却速度を50℃/sec以上とする冷却処理を行う工程bとを有する、結晶粒径が3~35μmで、CoとSiの両方を含む析出物のサイズが5~50nmである銅合金材を得ることを特徴とする電気電子部品用銅合金材の製造方法。
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JP2011038151A (ja) * | 2009-08-12 | 2011-02-24 | Furukawa Electric Co Ltd:The | 銅合金材およびその製造方法 |
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WO2011122490A1 (ja) | 2010-03-30 | 2011-10-06 | Jx日鉱日石金属株式会社 | Cu-Co-Si合金材 |
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Also Published As
Publication number | Publication date |
---|---|
JPWO2009096546A1 (ja) | 2011-05-26 |
EP2248921A1 (en) | 2010-11-10 |
EP2248921A4 (en) | 2011-03-16 |
CN101952465A (zh) | 2011-01-19 |
JP4615616B2 (ja) | 2011-01-19 |
CN101952465B (zh) | 2012-09-19 |
JP2011032583A (ja) | 2011-02-17 |
JP5391169B2 (ja) | 2014-01-15 |
US20100326573A1 (en) | 2010-12-30 |
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