CN113621850A - High-strength conductive high-temperature softening resistant Cu-Fe alloy and preparation method thereof - Google Patents
High-strength conductive high-temperature softening resistant Cu-Fe alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a high-strength conductive anti-softening Cu-Fe alloy and a preparation method thereof, wherein the alloy comprises Cu, Fe, In, Mg and inevitable impurity elements, Cu is an alloy matrix, and the contents of Fe, In and Mg are as follows: fe content: 3-12 wt%; in content: 0.1-0.5 wt%; mg content: 0.05 to 0.2 wt%. The Cu phase and the Fe phase are main composition phases of the alloy, and the refinement and the uniform distribution of the Fe phase size are realized by adding In and Mg and controlling the cooling rate In the casting process. According to the invention, the high-strength conductive softening-resistant Cu-Fe alloy is prepared by adjusting the alloy proportion and adopting the steps of special smelting casting, homogenization treatment and thermomechanical treatment, the tensile strength, the conductivity and the softening temperature can respectively reach 900-1200 MPa, 55-70% IACS and 450-520 ℃, and the shielding performance of the alloy is excellent.
Description
Technical Field
The invention relates to the field of alloy smelting and processing, in particular to a high-strength conductive high-temperature softening resistant Cu-Fe alloy and a preparation method thereof.
Background
The copper alloy has excellent performance and excellent alloying characteristic, is an economical environment-friendly conductive material at present, and is mainly applied to the fields of lead frames, electric welding electrodes, switch contacts, electric train air conductors and the like. The problems encountered in the high-strength and high-conductivity process of the existing copper alloy are as follows: the strengthening effect of a small amount of alloy elements is not obvious; a large amount of alloy elements can deteriorate the conductivity of the alloy; the conductivity and the strength of the copper conductor in the prior art are difficult to reach high standards at the same time, and the conductivity of the copper conductor is inevitably reduced after the copper alloy is strengthened; in the fields of vacuum switches, welding tips, electric contact wheels and the like, copper alloy is required to have higher high-temperature softening resistance strength besides high strength and high conductivity.
The copper-iron alloy has wide application prospect in the fields of transportation, aerospace, national defense and military industry and the like due to the excellent performances of strength, electric conduction, magnetic shielding and the like and the advantage of low cost, however, because of the characteristics of large Fe phase size and easy segregation in the solidification process of the copper-iron alloy, the series of alloys are difficult to prepare high-quality casting blanks, and the defects of line breakage and peeling are easily caused in the subsequent extrusion, drawing, rolling and other processing processes, so that the difficulty which is difficult to overcome is brought to the preparation of final products. In addition, in the copper alloy processing, processes such as soldering and packaging are required, and in the conventional semiconductor package or electronic component, the requirement for the high temperature softening temperature of the material is generally 380 ℃, so that the copper alloy is required to have good strength and conductivity and good high temperature softening resistance. However, with the complicated shape of the element, a higher demand is placed on the soldering or wire bonding process of copper alloy materials for semiconductor packages, electronic parts, and the like, and the high temperature softening resistance temperature of the materials needs to be increased to a higher level to meet the demand of modern material development. Therefore, the development and design of novel Cu-Fe alloy components are matched with the control of casting, heat treatment and processing processes, the refinement of Fe phase size is realized, the comprehensive performance of the material is further improved, and the preparation of the high-strength conductive high-temperature softening resistant copper-iron alloy has important significance in cost.
Disclosure of Invention
The invention aims to provide a high-strength conductive high-temperature softening resistant Cu-Fe alloy and a preparation method thereof, which can effectively solve the problem that part of the existing alloy is insufficient in performance and improve the high-strength conductivity and high softening resistance of the alloy. In order to realize the purpose of the invention, the following technical scheme is adopted:
the invention relates to a high-strength conductive high-temperature softening resistant Cu-Fe alloy, which comprises the following components of Cu, Fe, In, Mg and inevitable impurity elements, wherein Cu is an alloy matrix, Fe, In and Mg are main alloy elements, and the contents of the main alloy elements are as follows:
fe content: 3-12 wt%;
in content: 0.1-0.5 wt%;
mg content: 0.05-0.2 wt%;
in addition, the alloy optionally contains trace elements such As Cr, P, Mn, Ag, Co, Mo, As, Sb, Al, Hf, Zr, Ni, Ti, Ta, Sn, Zn, Sr and the like, and the total content of the elements is 0.01-0.4 wt%.
In a preferred embodiment of the invention, the high-strength conductive high-temperature softening resistant Cu-Fe alloy comprises the following optimized components:
fe content: 8-10 wt%;
in content: 0.2-0.4 wt%;
mg content: 0.08-0.12 wt%;
in addition, the alloy optionally contains trace elements such As Cr, P, Mn, Ag, Co, Mo, As, Sb, Al, Hf, Zr, Ni, Ti, Ta, Sn, Zn, Sr and the like, and the total content of the elements is 0.1-0.2 wt%.
Through the optimized components, the invention can further improve the alloy performance.
In a preferred embodiment of the invention, the high-strength conductive high-temperature softening resistant Cu-Fe alloy is subjected to multi-pass thermomechanical treatment, the strength of the alloy is 900-1200 MPa, the conductivity of the alloy is 55-70% IACS, and the softening resistant temperature of the alloy is 450-520 ℃.
The invention also relates to a preparation process of the high-strength conductive high-temperature softening resistant Cu-Fe alloy, which comprises the steps of smelting and casting, homogenization treatment and thermomechanical treatment, and specifically comprises the following steps:
1) smelting and casting:
and (3) smelting: adding electrolytic copper, pure iron and a covering agent into a smelting furnace → melting → heating → degassing and adding alloy elements such as In, Mg and the like → sampling analysis → component detection and adjustment, and preparing for casting after the temperature is adjusted.
2) The casting process comprises the following steps: preparing an alloy blank by adopting a continuous casting mode, wherein the specific numerical value of the cooling rate is selected according to different Fe contents: when the Fe content is 3-7, the cooling speed of the casting rod is required to be not lower than 100 ℃/s; when the Fe content is 7-10, the cooling speed of the casting rod is required to be not lower than 300 ℃/s, and when the Fe content is 10-12, the cooling speed of the casting rod is required to be not lower than 500 ℃/s.
3) Homogenizing: the temperature and time of the homogenization procedure are selected according to the iron content, and when the Fe content is 3-7, the homogenization process is carried out for heat preservation at 950 ℃ for 2-6 h; when the Fe content is 7-10, the homogenization process of the Cu-Fe alloy is to preserve heat for 4-10h at 980 ℃; when the Fe content is 10-12, the homogenization process of the Cu-Fe alloy is to preserve heat for 6-12h at 1000 ℃;
4) thermomechanical treatment: primary cold deformation with the strain amount of 3-5, primary annealing-secondary cold deformation, strain amount of 5-7, secondary annealing-tertiary cold deformation, strain amount of 7-8 and aging treatment.
Before adding In, Mg and other elements, introducing argon or nitrogen for 10 minutes to stir the melt for degassing, and then sequentially adding In and Mg, wherein In and Mg can be added In the form of pure metal and master alloy.
In the smelting and casting process, the temperature of a melt before casting is determined according to the content of Fe element, the temperature is 50-100 ℃ above the liquidus line of a Cu-Fe phase diagram, and a crystallizer adopted in the casting process is a non-carbon boron nitride material which has no violent chemical reaction with the main components of the alloy.
In the smelting and casting process, the size of a casting blank is selected according to the content of Fe element, the content of Fe is 3-7, the diameter of a circular casting rod is not more than 30mm at most; Cu-Fe alloy with Fe content of 7-10, the maximum diameter of the round casting rod is not more than 25 mm; the diameter of the round casting rod of the Cu-Fe alloy with the Fe content of 10-12 is not more than 20mm at most, otherwise, the uniform distribution and small size of the primary Fe phase cannot be ensured. The continuous casting mode can also prepare Cu-Fe alloy plates, and the requirement of the same plate thickness of the alloy components is consistent with the diameter of the rod.
In the thermomechanical treatment process in the step 4, the annealing process is selected according to the content of the Fe element, the primary intermediate annealing temperature is higher than the secondary intermediate annealing temperature, the secondary intermediate annealing temperature is higher than the final aging temperature, and otherwise, the high softening resistance temperature cannot be obtained. The three times of intermediate annealing temperatures of the Cu-Fe alloy with the Fe content of 3-7 wt% are respectively 400-450, 350-400 and 200-250 for 1-2 h; Cu-Fe alloy with Fe content of 7-10 wt%, the temperature of the third intermediate annealing is respectively 450-500, 400-450 and 250-300, and the time is 1-2 h; the three times of intermediate annealing temperatures of the Cu-Fe alloy with the Fe content of 10-12 wt% are respectively 500-550, 450-500 and 250-300, and the time is 1-2 h.
According to the invention, Cu, Fe, In and Mg are used as materials, and the alloy is prepared by combining various strengthening modes such as casting, homogenization treatment, thermomechanical treatment and the like, so that the alloy performance is obviously improved, the strength of the alloy can reach 900-1500 MPa, the conductivity can reach 55-70% IACS, the softening resistance temperature is 450-520 ℃, the problem of partial insufficient performance In the existing alloy is solved, and the development requirement of modern materials is met.
The beneficial results obtained by the invention are as follows:
1) the method realizes the control of the Fe phase size of the Cu-Fe-In-Mg alloy casting by controlling the cooling rate of Cu-Fe alloys with different Fe contents In the casting process; meanwhile, the requirement is put forward on the size of the casting so as to ensure that the size of the Fe phase does not exceed 4.5 mu m. By setting different thermomechanical treatment systems for Cu-Fe-In-Mg alloys with different Fe contents, Fe atoms are precipitated as far as possible while the sufficient fiberization of the Fe phase is ensured, so that the strength, the conductivity and the high-temperature softening resistance of the alloy are well matched.
2) Further refines the primary Fe phase In the alloy by an alloying method and improves the distribution of the primary Fe phase, and simultaneously improves the casting blank quality of the Cu-Fe-In-Mg alloy. In element can refine Fe phase and make its distribution more dispersed; mg element reacts with impurity elements such as O and the like, plays a role in removing impurities and degassing, and can also effectively improve the strength of the alloy. The high strength of the Cu-Fe system alloy is derived from Fe fibers formed after deformation, and the finer and uniform the Fe fibers, the higher the strength of the Cu-Fe system alloy. Due to the refining effect of the In element on the primary Fe phase, the deformed Cu-Fe-In-Mg alloy has finer and more uniform Fe fibers than the Cu-Fe alloy, thereby having higher tensile strength. In addition, the addition of Mg can promote the desolventizing of Fe atoms from the Cu matrix, so that the conductivity of the alloy is improved; meanwhile, fine and dispersed secondary Fe formed by Fe atom desolventizing has strong pinning effect relative to the movement of dislocation, so that the alloy strength can be further improved.
3) The Cu-Fe-In-Mg alloy has good comprehensive performance, and the tensile strength, the conductivity and the softening temperature can reach 900-1200 MPa, 55-70% IACS and 450-520 ℃ respectively.
Drawings
FIG. 1 is an as-cast structure diagram of example 1.
FIG. 2 is an as-cast structure diagram of comparative example 1.
FIG. 3 is an as-cast structure diagram of example 2.
FIG. 4 is an as-cast structure diagram of example 3.
As can be seen from fig. 1 and 2, the addition of elements such as In and Mg can significantly refine the Fe phase and make the distribution thereof more uniform. As is clear from fig. 1, 3, and 4, In and Mg elements have an effect of refining the Fe phase In both Cu — Fe alloys having Fe contents of 6 to 12 wt.%.
Detailed Description
In order to further understand the present invention, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Unless otherwise specified, the reagents involved in the examples of the present invention are all commercially available products, and all of them are commercially available.
The Cu-Fe alloy plate can be prepared by adopting a continuous casting mode, and the requirement on the thickness of the Cu-Fe plate with the same components is consistent with the diameter of the Cu-Fe rod.
Example 1:
step one, according to alloy components: 6 wt.% Fe, 0.3 wt.% In, 0.1 wt.% Mg, the balance being pure copper. Wherein Fe is 99.95 wt.% pure Fe, In is 99.95 wt.% pure In, and Mg is 99.95 wt.% pure Mg. Putting the prepared copper and iron into a smelting crucible, and putting In and Mg elements on a feeding tray; smelting, namely adding a covering agent, introducing argon for 10 minutes to stir and degas the melt after the temperature reaches 1200-1350 ℃; preserving heat, wherein the heat preservation temperature is 1350 +/-20 ℃, after the heat preservation time is 20min, adding In elements and Mg elements, preserving the heat for 3-5 min, sampling, and detecting and adjusting components; and (3) adopting a boron nitride material as a crystallizer material for continuous casting, wherein when the Fe content is 3-7, the cooling speed of the casting rod is required to be not lower than 100 ℃/s, and the diameter of the round casting rod is 26 mm.
Step two, homogenization treatment: homogenizing at 950 deg.C for 4h, and cooling with the furnace; primary drawing: the deformation is changed from large to small according to the pass, and the total strain is 4; primary intermediate annealing treatment: annealing at 400 deg.C for 1h, and air cooling. Secondary drawing: the deformation is changed from large to small according to the pass, and the total strain is 6. Secondary intermediate annealing: annealing at 350 deg.C for 1 hr, and air cooling. Drawing for three times: drawing according to the deformation of the pass from large to small, wherein the total deformation is 8. Aging treatment: and (5) cooling in air at the aging temperature of 200 ℃ for 1 h. The as-cast structure is shown in FIG. 1.
Comparative example 1:
the other conditions were the same as in example 1 except that: the alloy composition is Cu-6 wt.% Fe without the addition of other elements, and the as-cast structure is shown in FIG. 2.
Example 2
Step one, according to alloy components: 9 wt.% Fe, 0.3 wt.% In, 0.1 wt.% Mg, the balance being pure copper. Wherein Fe is 99.95 wt.% pure Fe, In is 99.95 wt.% pure In, and Mg is 99.95 wt.% pure Mg. Putting the prepared copper and iron into a smelting crucible, and putting In and Mg elements on a feeding tray; smelting, namely adding a covering agent, introducing argon gas for 10 minutes to stir and degas the melt when the temperature reaches 1300-1420 ℃; preserving heat, wherein the heat preservation temperature is 1420 +/-20 ℃, after the heat preservation time is 20min, adding In element and Mg element, preserving heat for 3-5 min, sampling, and detecting and adjusting components; and (3) adopting boron nitride as a crystallizer material for continuous casting, wherein when the Fe content is 7-10, the cooling speed of the casting rod is required to be not lower than 300 ℃/s, and the diameter of the round casting rod is 20 mm.
Step two, homogenization treatment: homogenizing at 980 deg.C for 6h, and cooling with the furnace; primary drawing: the deformation is changed from large to small according to the pass, and the total strain is 4; primary intermediate annealing treatment: annealing at 450 deg.c for 1 hr, and air cooling. Secondary drawing: the deformation is changed from large to small according to the pass, and the total strain is 6. Secondary intermediate annealing: annealing at 400 deg.C for 1 hr, and air cooling. Drawing for three times: drawing according to the deformation of the pass from large to small, wherein the total deformation is 8. Aging treatment: and (5) cooling in air at the aging temperature of 250 ℃ for 1 h. The as-cast structure is shown in FIG. 3.
Comparative example 2
According to the alloy components: 9 wt.% Fe, balance copper. Other conditions were the same as in example 2.
Comparative example 3
According to the alloy components: 9 wt.% Fe, 0.3 wt.% In, and the balance copper. Other conditions were the same as in example 2.
Example 3
Step one, according to alloy components: 12 wt.% Fe, 0.3 wt.% In, 0.1 wt.% Mg, and the balance pure copper. Wherein Fe is 99.95 wt.% pure Fe, In is 99.95 wt.% pure In, and Mg is 99.95 wt.% pure Mg. Putting the prepared copper and iron into a smelting crucible, and putting In and Mg elements on a feeding tray; smelting, namely adding a covering agent, introducing argon for 10 minutes to stir and degas the melt when the temperature reaches 1350-1480 ℃; preserving heat, wherein the heat preservation temperature is 1480 +/-20 ℃, after 20min of heat preservation time, adding In element and Mg element, preserving heat for 3-5 min, sampling, and detecting and adjusting components; and (3) adopting boron nitride as a crystallizer material for continuous casting, wherein when the Fe content is 10-12, the cooling speed of the casting rod is required to be not lower than 500 ℃/s, and the diameter of the round casting rod is 16 mm.
Step two, homogenization treatment: homogenizing at 1000 deg.C for 8h, and cooling with the furnace; primary drawing: the deformation is changed from large to small according to the pass, and the total strain is 4; primary intermediate annealing treatment: annealing at 500 deg.C for 1 hr, and air cooling. Secondary drawing: the deformation is changed from large to small according to the pass, and the total strain is 6. Secondary intermediate annealing: annealing at 450 deg.c for 1 hr, and air cooling. Drawing for three times: drawing according to the deformation of the pass from large to small, wherein the total deformation is 8. Aging treatment: and (5) cooling in air at the aging temperature of 250 ℃ for 1 h. The as-cast structure is shown in FIG. 4.
To further test the properties of the alloys, the following methods were used:
(1) tensile strength: and measuring the tensile strength by using an electronic universal tester with the model number of UTM 5105. The tensile sample is a round bar with the length of 12cm, the gauge length is 8cm, the tensile strength value of each sample is measured for 3 times, and the average value is taken.
(2) Conductivity: the conductivity adopts SB-2230 type DC digital resistance instrument and bridge fixture to measure resistance. In the process of measuring the conductivity of the wire, firstly, a vernier caliper is used for measuring the diameter of the wire, an electric bridge clamp is used for selecting a proper effective measurement length on a sample, the resistance value of the sample is recorded after measurement, and the conductivity of the alloy is calculated according to the formula (1).
Wherein σ is the conductivity of the alloy, unit: % IACS; r is the resistance value of the sample, unit: m omega; k is copper alloyResistance-converted temperature coefficient of gold; s is the cross-sectional area of the wire sample, unit: mm is2(ii) a L is the effective measurement length of the sample, unit: mm.
(3) Softening temperature: and (4) taking the sample after the final annealing, and respectively carrying out heat preservation for 1h at different temperatures in an SX 2-18-13 type box type resistance furnace for isochronal annealing treatment. The strength of the sample after the isochronal annealing was measured, and when the strength was 80% of the strength before the isochronal annealing, the temperature was the softening temperature of the final annealed sample.
TABLE 1 final mechanical, conductivity and temperature resistance test results for the example and comparative alloys
Through the experiment, the Fe phase can be refined by adding the alloy elements under the condition of the same Fe content, the refining effect of Fe is improved by adding trace alloy elements, and the strength can be greatly improved under the condition of not substantially influencing the conductivity of the alloy.
The foregoing describes preferred embodiments of the present invention, but is not intended to limit the invention thereto. Modifications and variations of the embodiments disclosed herein may be made by those skilled in the art without departing from the scope and spirit of the invention.
Claims (9)
1. A Cu-Fe alloy comprises Cu, Fe, In, Mg and inevitable impurity elements, wherein Cu is an alloy matrix, Fe, In and Mg are main alloy elements, and the content of the main alloy elements is as follows:
fe content: 3-12 wt%;
in content: 0.1-0.5 wt%;
mg content: 0.05-0.2 wt%;
optionally, the alloy also contains trace Cr, P, Mn, Ag, Co, Mo, As, Sb, Al, Hf, Zr, Ti, Ni, Ta, Sn, Zn and Sr elements, and the total content of the elements is 0.01-0.4 wt%.
2. The Cu-Fe alloy according to claim 1, having the following composition of alloying elements:
fe content: 8-10 wt%;
in content: 0.2-0.4 wt%;
mg content: 0.08-0.12 wt%;
optionally, the alloy also contains trace elements of Cr, P, Mn, Ag, Co, Mo, As, Sb, Al, Hf, Zr, Ti, Ni, Ta, Sn, Zn and Sr, the total content of the elements is 0.1-0.2 wt%, and the balance is copper.
3. The Cu-Fe alloy according to claim 1 or 2, wherein the alloy has a strength of 900-1200 MPa, an electrical conductivity of 55-70% IACS and a softening resistance temperature of 450-520 ℃ after multi-pass thermomechanical treatment.
4. The method for preparing a Cu-Fe alloy according to any one of claims 1 to 3, comprising the steps of melt casting-homogenization treatment-thermomechanical treatment, in particular as follows:
1) smelting and casting:
and (3) smelting: adding electrolytic copper, pure iron and a covering agent into a smelting furnace → melting → heating → degassing and adding In, Mg and optional other alloy elements → sampling analysis → component detection and adjustment, and preparing for casting after the temperature is adjusted;
2) the casting process comprises the following steps: preparing an alloy blank by adopting a continuous casting mode, wherein the specific numerical value of the cooling rate is selected according to different Fe contents: when the Fe content is 3-7, the cooling speed of the casting rod is required to be not lower than 100 ℃/s; when the Fe content is 7-10, the cooling speed of the casting rod is required to be not lower than 300 ℃/s, and when the Fe content is 10-12, the cooling speed of the casting rod is required to be not lower than 500 ℃/s;
3) homogenizing: the temperature and time of the homogenization procedure are selected according to the iron content, and when the Fe content is 3-7, the homogenization process is carried out for heat preservation at 950 ℃ for 2-6 h; when the Fe content is 7-10, the homogenization process of the Cu-Fe alloy is to preserve heat for 4-10h at 980 ℃; when the Fe content is 10-12, the homogenization process of the Cu-Fe alloy is to preserve heat for 6-12h at 1000 ℃;
4) thermomechanical treatment: primary cold deformation with the strain amount of 3-5, primary annealing-secondary cold deformation, strain amount of 5-7, secondary annealing-tertiary cold deformation, strain amount of 7-8 and aging treatment.
5. The preparation method of claim 4, wherein the melt is degassed by stirring with argon or nitrogen for 5-20 min before adding In and Mg, and then the In and Mg elements are added sequentially, wherein the In and Mg can be added In the form of pure metal and master alloy.
6. The method as claimed in claim 4, wherein the melt temperature before casting is 1300-1400 ℃ during the melting and casting process.
7. The method of claim 4, wherein: the crystallizer adopted in the casting process is a boron nitride material which is non-carbon and has no violent chemical reaction with the main components of the alloy.
8. The preparation method according to claim 4, wherein in the smelting and casting process, the size of a casting blank is selected according to the Fe element content, the Fe content is 3-7 wt% of Cu-Fe alloy, and the diameter of a circular casting rod is not more than 30mm at most; a Cu-Fe alloy having an Fe content of 7 to 10 wt%, the circular cast rod having a diameter of not more than 25mm at the maximum; Cu-Fe alloy with Fe content of 10-12 wt% and circular casting rod with diameter not more than 20 mm.
9. The method according to claim 4, wherein in the thermomechanical treatment process in step 4, the annealing process is selected according to the content of Fe element, and the primary intermediate annealing temperature is higher than the secondary intermediate annealing temperature which is higher than the final aging temperature; the three times of intermediate annealing temperatures of the Cu-Fe alloy with the Fe content of 3-7 are respectively 400-450, 350-400 and 200-250, and the time is 1-2 h; the temperature of the third intermediate annealing is respectively 500-450 ℃, 400-450 ℃ and 250-300 ℃ for 2-4 h; the three times of intermediate annealing temperatures of the Cu-Fe alloy with the Fe content of 10-12 are respectively 500-550, 450-500 and 250-300, and the time is 2-4 h.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114807669A (en) * | 2022-05-12 | 2022-07-29 | 江西理工大学 | Preparation method of Cu-Fe-Mg-RE alloy with ultrahigh strength, high conductivity, heat resistance and electromagnetic shielding |
| CN115927975A (en) * | 2022-12-28 | 2023-04-07 | 中南大学 | Fe-Cu alloy and preparation method and application thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02111829A (en) * | 1988-10-20 | 1990-04-24 | Sumitomo Metal Mining Co Ltd | Copper alloy for lead frame |
| JPH05331572A (en) * | 1992-03-31 | 1993-12-14 | Toshiba Corp | Copper-iron alloy |
| JPH0718355A (en) * | 1993-06-30 | 1995-01-20 | Mitsubishi Electric Corp | Copper alloy for electronic appliance and its production |
| CN107400796A (en) * | 2017-06-22 | 2017-11-28 | 安徽晋源铜业有限公司 | A kind of high-temperature-resistant high is without beryllium copper wire and preparation method thereof |
| CN112111670A (en) * | 2020-09-21 | 2020-12-22 | 江西理工大学 | Cu-Fe-Cr-Mg electromagnetic shielding material and preparation method thereof |
-
2021
- 2021-08-16 CN CN202110937928.2A patent/CN113621850A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02111829A (en) * | 1988-10-20 | 1990-04-24 | Sumitomo Metal Mining Co Ltd | Copper alloy for lead frame |
| JPH05331572A (en) * | 1992-03-31 | 1993-12-14 | Toshiba Corp | Copper-iron alloy |
| JPH0718355A (en) * | 1993-06-30 | 1995-01-20 | Mitsubishi Electric Corp | Copper alloy for electronic appliance and its production |
| CN107400796A (en) * | 2017-06-22 | 2017-11-28 | 安徽晋源铜业有限公司 | A kind of high-temperature-resistant high is without beryllium copper wire and preparation method thereof |
| CN112111670A (en) * | 2020-09-21 | 2020-12-22 | 江西理工大学 | Cu-Fe-Cr-Mg electromagnetic shielding material and preparation method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114807669A (en) * | 2022-05-12 | 2022-07-29 | 江西理工大学 | Preparation method of Cu-Fe-Mg-RE alloy with ultrahigh strength, high conductivity, heat resistance and electromagnetic shielding |
| CN115927975A (en) * | 2022-12-28 | 2023-04-07 | 中南大学 | Fe-Cu alloy and preparation method and application thereof |
| CN115927975B (en) * | 2022-12-28 | 2024-03-22 | 中南大学 | Fe-Cu alloy and preparation method and application thereof |
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