CN116083749A - Tellurium copper alloy strip and preparation method thereof - Google Patents
Tellurium copper alloy strip and preparation method thereof Download PDFInfo
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- CN116083749A CN116083749A CN202310053303.9A CN202310053303A CN116083749A CN 116083749 A CN116083749 A CN 116083749A CN 202310053303 A CN202310053303 A CN 202310053303A CN 116083749 A CN116083749 A CN 116083749A
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- 229910052714 tellurium Inorganic materials 0.000 title claims abstract description 37
- PORWMNRCUJJQNO-UHFFFAOYSA-N tellurium atom Chemical compound [Te] PORWMNRCUJJQNO-UHFFFAOYSA-N 0.000 title claims abstract description 36
- 229910000881 Cu alloy Inorganic materials 0.000 title claims abstract description 31
- 238000002360 preparation method Methods 0.000 title description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 34
- 239000010949 copper Substances 0.000 claims abstract description 34
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical group [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 31
- 238000005452 bending Methods 0.000 claims abstract description 27
- 238000012545 processing Methods 0.000 claims abstract description 18
- 239000011159 matrix material Substances 0.000 claims abstract description 15
- 239000002245 particle Substances 0.000 claims abstract description 15
- 238000005096 rolling process Methods 0.000 claims abstract description 11
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 238000000137 annealing Methods 0.000 claims description 25
- 239000000956 alloy Substances 0.000 claims description 17
- 229910045601 alloy Inorganic materials 0.000 claims description 16
- 238000004321 preservation Methods 0.000 claims description 11
- 238000005098 hot rolling Methods 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 10
- 238000003723 Smelting Methods 0.000 claims description 8
- 238000010438 heat treatment Methods 0.000 claims description 7
- 238000005482 strain hardening Methods 0.000 claims description 5
- QZCHKAUWIRYEGK-UHFFFAOYSA-N tellanylidenecopper Chemical compound [Te]=[Cu] QZCHKAUWIRYEGK-UHFFFAOYSA-N 0.000 claims description 4
- RIRXDDRGHVUXNJ-UHFFFAOYSA-N [Cu].[P] Chemical compound [Cu].[P] RIRXDDRGHVUXNJ-UHFFFAOYSA-N 0.000 claims description 3
- 238000009749 continuous casting Methods 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims 1
- 239000000463 material Substances 0.000 abstract description 16
- 229910052761 rare earth metal Inorganic materials 0.000 abstract description 11
- 230000000052 comparative effect Effects 0.000 description 21
- 238000012360 testing method Methods 0.000 description 11
- 239000013078 crystal Substances 0.000 description 5
- 238000010998 test method Methods 0.000 description 5
- 238000009826 distribution Methods 0.000 description 4
- 238000005266 casting Methods 0.000 description 3
- 238000001514 detection method Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910001369 Brass Inorganic materials 0.000 description 2
- 238000005054 agglomeration Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 239000010951 brass Substances 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 238000003801 milling Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000011056 performance test Methods 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 238000007545 Vickers hardness test Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000011112 process operation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/003—Rolling non-ferrous metals immediately subsequent to continuous casting, i.e. in-line rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- 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
-
- 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
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B13/00—Apparatus or processes specially adapted for manufacturing conductors or cables
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B13/00—Apparatus or processes specially adapted for manufacturing conductors or cables
- H01B13/0016—Apparatus or processes specially adapted for manufacturing conductors or cables for heat treatment
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B2003/005—Copper or its alloys
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Abstract
The invention discloses a tellurium copper alloy strip, which is characterized in that: the tellurium copper alloy comprises the following components in percentage by mass: 0.1 to 0.3 weight percent, P:0.008 to 0.012wt percent, RE:0.01 to 0.05wt% RE is selected from Ce and/or La, and the balance is copper and unavoidable impurities. Rare earth elements are added into the red copper matrix, and the rare earth elements are enriched at the grain boundary so as to refine grains; by adding Te element and utilizing the second phase particles to strengthen the copper matrix, the plastic reduction of the strip processed at a large processing rate is avoided, the hardness of the tellurium copper alloy strip is finally 90-120 HV1, the tensile strength is more than or equal to 280MPa, the elongation is more than or equal to 15%, the conductivity is more than or equal to 97% IACS, and the high-temperature softening resistance temperature is more than or equal to 400 ℃; under the condition of 90-degree bending, the R/t of the strip material is smaller than or equal to 1.0 in the direction perpendicular to the rolling direction, and the R/t of the strip material is smaller than or equal to 1.0 in the direction parallel to the rolling direction.
Description
Technical Field
The invention belongs to the technical field of copper alloy, and particularly relates to a tellurium copper alloy strip and a preparation method thereof.
Background
The electromagnetic relay is an important element in an automobile control circuit, and is mainly used for realizing the on-off of a high-current switch through small current, so that the contact of the switch is not ablated in the processes of on-off and on-off. Among the various influences on the working stability of the working contact, the base material of the conductive contact is one of the biggest influencing factors, and the contact materials commonly used at present are red copper and brass alloys. The red copper has good electrical conductivity and thermal conductivity, but has poor strength and wear resistance, and low softening temperature resistance at high temperature, and can generate thermal deformation in the long-term use process. Brass has good processability and low price, but has poor electric conductivity and heat conductivity.
After the study of red copper by scholars at home and abroad, it is found that the strength of the material can be obviously improved by adding a certain tellurium (Te) element into red copper, and a tellurium copper alloy product represented by C14500 is developed based on the strength. The series of products have good electric conductivity and heat conductivity, simultaneously strengthen the strength of a copper matrix and improve the cutting processing capability of the material. However, the current C14500 alloy is not applied on a large scale, on the one hand, the conductivity of the C14500 alloy is generally 80-90% IACS, and when the C14500 alloy is subjected to high-current operation for a long time, the temperature of an electric contact is obviously increased, and finally the electric contact is invalid; on the other hand, the addition of tellurium element can form a hard and brittle tellurium copper composite second phase in the copper alloy, so that the bending performance of the strip is seriously affected, and the processing of an electric contact is not facilitated.
In order to solve the problems, the invention regulates and controls the grain size and the distribution of tellurium copper composite phases through the design of alloy components and technological parameters, and prepares a high-performance tellurium copper alloy material with high conductivity and good bending performance.
Disclosure of Invention
The first technical problem to be solved by the invention is to provide a tellurium copper alloy strip with high conductivity, good bending performance and high-temperature softening resistance.
The second technical problem to be solved by the invention is to provide a preparation method of a tellurium copper alloy strip.
The invention solves the first technical problem by adopting the technical scheme that: a tellurium copper alloy strip, characterized in that: the tellurium copper alloy comprises the following components in percentage by mass: 0.1 to 0.3 weight percent, P:0.008 to 0.012wt percent, RE:0.01 to 0.05wt% RE is selected from Ce and/or La, and the balance is copper and unavoidable impurities.
According to the invention, a certain amount of Te element is added into red copper, so that a dispersed tellurium-containing second phase (copper tellurium compound particles) is formed in a copper matrix, and the strength and hardness of the copper matrix are further improved. Because of the existence of the second phase, the pinning effect is formed on the dislocation movement, the driving force required by the growth of the crystal grains of the strip is larger, and finally the bending performance and the high-temperature softening resistance of the strip are improved. When the Te element is added in excessive amount, the second phase can generate obvious agglomeration phenomenon, and the second phase is difficult to eliminate by annealing; when the Te element is added in an excessively small amount, the density per unit area of the second phase particles is less than 1.0X10 4 Individual/mm 2 The strip material has little strengthening effect of the second phase, so that the mass percent of Te element is 0.1 to 0.3 weight percent.
And when a certain amount of Ce and/or La is added, rare earth elements are more easily enriched at the grain boundary, and the rare earth elements at the grain boundary can prevent the recrystallization and growth of crystal grains during hot rolling, so that the purpose of grain refinement is realized. After grain refinement, when the strip is bent, the deformation becomes more uniform, and the strip is not easy to crack.
Preferably, the phase structure of the tellurium copper alloy comprises an alpha matrix phase and a tellurium-containing second phase dispersed on the matrix phase, the second phase being in the form of particles having a size of 200 to 600nm and a unit area density of the second phase particles of 1.0 to 2.0X10 4 Individual/mm 2 . When the size of the second phase particles is smaller than 200nm, although the structure of the second phase is finer, the grains are more easily recrystallized and grown during homogenizing annealing, and the grain size of the strip is larger, so that the bending property of the strip is affected. When the density per unit area of the second phase particles is less than 1.0X10 4 Individual/mm 2 The ribbon has little reinforcing effect of the second phase when the second phase particles have a density per unit area of more than 2.0X10 4 Individual/mm 2 When the material is used, the material is easy to form a segregation phase, and the bending performance of the material is affected.
Preferably, the tellurium copper alloy strip has the hardness of 90-120 HV1, the tensile strength of more than or equal to 280MPa, the elongation of more than or equal to 15%, the conductivity of more than or equal to 97% IACS and the high-temperature softening resistance temperature of more than or equal to 400 ℃; under the condition of 90-degree bending, R/t is less than or equal to 1.0 in the direction perpendicular to the rolling direction, R/t is less than or equal to 1.0 in the direction parallel to the rolling direction, wherein R is the bending radius, and t is the thickness of the strip.
The invention solves the second technical problem by adopting the technical proposal that: the preparation method of the tellurium copper alloy strip is characterized by comprising the following steps of: smelting, semi-continuous casting, hot rolling, homogenizing annealing, cold working and stress relief annealing; the heating temperature of the hot rolled cast ingot is 850-950 ℃, the heat preservation time is 3-4 hours, and the total processing rate of hot rolling is more than 90%; the homogenizing annealing temperature is 750-850 ℃, and the heat preservation time is 4-8 h.
The heating temperature of the hot rolled cast ingot is 850-950 ℃, and the cooling speed is high due to the high copper content of tellurium copper, so that the heat preservation temperature is required to be selected to be higher than that of red copper, thereby ensuring the final rolling temperature of hot rolling to be higher than 650 ℃. Because the solid solubility of Te element in the copper matrix is extremely low, the Te element can be prevented from forming strip-shaped or block-shaped agglomeration distribution in the copper matrix by adopting higher finishing temperature, so that the tellurium-containing second phase is dispersed and distributed in the copper matrix, and the uniformity of strip components and tissues is improved. Meanwhile, a foundation is laid for obtaining a second phase matrix with a specific size by subsequent homogenizing annealing.
The homogenizing annealing temperature is 750-850 ℃, the heat preservation time is 4-8 h, and under the homogenizing annealing condition, coarse second-phase particles after hot rolling can be spheroidized to form finer dispersed particles. Meanwhile, because rare earth elements are enriched in crystal boundaries, crystal grains are not excessively grown, and the subsequent processing cracking of the strip is caused.
Preferably, the smelting charging sequence is as follows: firstly adding an electrolytic copper plate, after the electrolytic copper plate is completely melted, adding copper-tellurium intermediate alloy required by the required components, heating to 1130-1180 ℃, and finally adding phosphorus-copper intermediate alloy and rare earth-copper intermediate alloy required by the required components. By adopting the feeding sequence, the uniformity of the components of the cast ingot is ensured, the final addition of the P element plays a role in degassing, meanwhile, rare earth elements cannot be burnt seriously, and the rare earth elements can be enriched at a grain boundary during solidification.
Preferably, the cold working has a working rate of 60 to 75%. In the range of the processing rate, the homogenized recrystallized grains are ensured to be crushed to a certain extent, and the purpose of refining the grains is achieved. Meanwhile, partial recrystallization structure is reserved, so that the remarkable reduction of the plasticity of the strip after the recrystallization structure is changed into a processing structure is avoided, and the strip is ensured to have higher elongation and good bending performance.
Preferably, the temperature of the stress relief annealing is 280-350 ℃, and the heat preservation time is 2-6 h. When the annealing temperature is low, larger processing stress generated by cold processing on the strip cannot be effectively eliminated; when the annealing temperature is higher, the crystal grains are obviously grown, and the bending deformation processing of the strip is not facilitated.
Compared with the prior art, the invention has the advantages that: rare earth elements are added into the red copper matrix, and the rare earth elements are enriched at the grain boundary so as to refine grains; by adding Te element and utilizing the second phase particles to strengthen the copper matrix, the plastic reduction of the strip processed at a large processing rate is avoided, the hardness of the tellurium copper alloy strip is finally 90-120 HV1, the tensile strength is more than or equal to 280MPa, the elongation is more than or equal to 15%, the conductivity is more than or equal to 97% IACS, and the high-temperature softening resistance temperature is more than or equal to 400 ℃; under the condition of 90-degree bending, R/t is less than or equal to 1.0 in the direction perpendicular to the rolling direction, R/t is less than or equal to 1.0 in the direction parallel to the rolling direction, wherein R is the bending radius, and t is the thickness of the strip. The high-voltage direct-current relay is suitable for high-voltage direct-current relays, connectors and the like which need bending or stamping processing.
Drawings
Fig. 1 is a scanning electron microscope photograph of example 1 of the present invention.
Detailed Description
The invention is described in further detail below with reference to the embodiments of the drawings.
The invention is illustrated by selecting 10 examples and 8 comparative examples, and the mass percentages of the chemical components of each example and comparative example are shown in table 1.
The preparation of the examples comprises the following preparation steps:
1) Smelting: the materials are mixed according to the required components, and the smelting feeding sequence is as follows: firstly adding an electrolytic copper plate, after the electrolytic copper plate is completely melted, adding copper-tellurium intermediate alloy required by the required components, heating to 1130-1180 ℃, and finally adding phosphorus-copper intermediate alloy and rare earth-copper intermediate alloy required by the required components. In the whole smelting process, argon gas is always blown into the furnace, the air flow is 5LPM, and the smelting temperature is 1150-1200 ℃.
2) Semi-continuous casting: the casting temperature is 1130-1180 ℃, the casting speed is 40-60 mm/min, and the thickness of the cast ingot is 180mm.
3) And (3) hot rolling: and hot rolling the cast ingot, wherein the heating temperature of the cast ingot is 850-950 ℃, the heat preservation time is 3-4 h, and the total processing rate of hot rolling is more than 90%.
4) Milling: the thickness of milling surfaces of the upper surface and the lower surface of the hot rolled blank is 0.5-1.0 mm respectively, so that oxide inclusions on the surfaces and cold insulation during casting solidification are removed.
5) Homogenizing and annealing: the temperature is 750-850 ℃, and the heat preservation time is 4-8 h.
6) Cold working: the processing rate is 60-75%.
7) Stress relief annealing: the temperature is 280-350 ℃, and the heat preservation time is 2-6 h.
The details of key process operation parameters of the invention are shown in table 2, and the details of performance test data of the alloy strip are shown in table 3.
Comparative example 1 differs from example 1 in that: rare earth elements are not added;
comparative example 2 differs from example 1 in that: the content of Te element is 0.8wt%;
comparative example 3 differs from example 1 in that: no homogenizing annealing is performed;
comparative example 4 differs from example 1 in that: the homogenizing annealing temperature is 700 ℃;
comparative example 5 differs from example 1 in that: the homogenizing annealing temperature is 900 ℃;
comparative example 6 differs from example 1 in that: the cold rolling reduction ratio is 55%;
comparative example 7 differs from example 1 in that: the cold rolling reduction ratio is 80%;
comparative example 8 differs from example 1 in that: no stress relief anneal is performed.
The above examples and comparative examples were analyzed for conductivity, hardness, tensile strength, grain size, bending properties, softening temperature, and morphology and distribution of second phase particles.
And (3) conductivity detection: the test is carried out according to the requirements of GB/T32791-2016 copper and copper alloy conductivity vortex test method, and the size of the test strip is 100mm multiplied by 100mm.
And (3) hardness detection: according to GB/T4340.0-2009 Vickers hardness test section 1: test method requires that the test strip be 30mm by 30mm in size.
Tensile strength detection: room temperature tensile test according to GB/T228.1-2010 metal material tensile test part 1: the room temperature test method is carried out on an electronic universal mechanical property tester, the test sample is dumbbell-shaped, the width of the tensile sample is 20mm, and the tensile speed is 5mm/min.
And (3) testing the size of metallographic structure grains, and testing the size of grains in a photograph acquired by a metallographic microscope, wherein the metallographic structure grains are 100 times as large as the size of grains in the photograph, according to the intercept point method in GB/T6394-2007 method for measuring average grain size of metals. The test strip dimensions were 10mm by 10mm.
Bending performance test according to GB/T232-2010 metal material bending test method, bending tests with bending angles of 90 degrees in the directions parallel to the rolling direction and perpendicular to the rolling direction are respectively carried out, and the width of the test strip is 10mm and the length of the test strip is 50mm.
The high temperature softening resistance test is carried out according to the requirements of GB/T33370-2016 copper and copper alloy softening temperature test method, and the sample length is 40mm and the sample width is 40mm.
The second phase particles in the alloy are analyzed by a field emission scanning electron microscope JSM-IT700HR and an electron microscope photo is taken, and the distribution situation of the second phase is shown in figure 1.
From a comparison of the examples and comparative examples, it can be demonstrated that the chemical composition and the processing according to the invention have a significant effect on the properties of the strip. As is clear from comparative example 1, when the rare earth element was not added, the average grain size of the strip was larger, and the bending property was lowered. As is clear from comparative example 2, the second phase of the strip was distributed in a lath shape, and the bending property of the strip was significantly lowered, as the length reached 600. Mu.m, due to the excessive addition amount of Te element, despite the homogenization annealing treatment. As is clear from comparative examples 3 and 4, when the homogenizing annealing is not performed or the homogenizing annealing temperature is low, the second phase particles are also distributed in a lath shape, resulting in poor bending property of the strip and low conductivity. As is clear from comparative example 5, when the homogenizing annealing temperature is high, the grain growth of the strip is remarkable, and the bending property of the strip is also lowered. As is evident from comparative example 6, when the processing rate of the strip material is small, the hardness and strength of the strip material are low, and the use requirement of the strip material is not satisfied. As is clear from comparative example 7, when the processing rate of the strip material is large, the elongation of the strip material is remarkably reduced, and the bending performance is also reduced. As is clear from comparative example 8, when the stress relief annealing is not performed, the working stress in the strip is large, the bending property of the strip is poor, and the softening temperature is lowered to 350 ℃.
TABLE 1 chemical composition/wt% of examples and comparative examples
Table 2 key process parameter control for the examples
Table 3 properties of examples and comparative examples
Claims (7)
1. A tellurium copper alloy strip, characterized in that: the tellurium copper alloy comprises the following components in percentage by mass: 0.1 to 0.3 weight percent, P:0.008 to 0.012wt percent, RE:0.01 to 0.05wt% RE is selected from Ce and/or La, and the balance is copper and unavoidable impurities.
2. The tellurium copper alloy strip of claim 1, wherein: the phase structure of the tellurium copper alloy comprises an alpha matrix phase and a tellurium-containing second phase dispersed on the matrix phase, wherein the second phase is granular and has a size of 200-600 nm, and the density of the second phase particles per unit area is 1.0-2.0X10 4 Individual/mm 2 。
3. The tellurium copper alloy strip of claim 1 or 2, wherein: the tellurium copper alloy strip has the hardness of 90-120 HV1, the tensile strength of more than or equal to 280MPa, the elongation of more than or equal to 15%, the conductivity of more than or equal to 97% IACS and the high-temperature softening resistance temperature of more than or equal to 400 ℃; under the condition of 90-degree bending, R/t is less than or equal to 1.0 in the direction perpendicular to the rolling direction, R/t is less than or equal to 1.0 in the direction parallel to the rolling direction, wherein R is the bending radius, and t is the thickness of the strip.
4. A method for producing a tellurium copper alloy strip as claimed in any one of claims 1 to 3, wherein the process flow of the tellurium copper alloy strip comprises: smelting, semi-continuous casting, hot rolling, homogenizing annealing, cold working and stress relief annealing; the heating temperature of the hot rolled cast ingot is 850-950 ℃, the heat preservation time is 3-4 hours, and the total processing rate of hot rolling is more than 90%; the homogenizing annealing temperature is 750-850 ℃, and the heat preservation time is 4-8 h.
5. The method for preparing the tellurium copper alloy strip of claim 4, wherein: the feeding sequence of smelting is as follows: firstly adding an electrolytic copper plate, after the electrolytic copper plate is completely melted, adding copper-tellurium intermediate alloy required by the required components, heating to 1130-1180 ℃, and finally adding phosphorus-copper intermediate alloy and rare earth-copper intermediate alloy required by the required components.
6. The method for preparing the tellurium copper alloy strip of claim 4, wherein: the cold working rate is 60-75%.
7. The method for preparing the tellurium copper alloy strip of claim 4, wherein: the temperature of the stress relief annealing is 280-350 ℃, and the heat preservation time is 2-6 h.
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| CN202310053303.9A CN116083749A (en) | 2023-01-31 | 2023-01-31 | Tellurium copper alloy strip and preparation method thereof |
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| CN202310053303.9A CN116083749A (en) | 2023-01-31 | 2023-01-31 | Tellurium copper alloy strip and preparation method thereof |
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