CN113106290A - High-performance tin-phosphor bronze strip and preparation method thereof - Google Patents
High-performance tin-phosphor bronze strip and preparation method thereof Download PDFInfo
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- CN113106290A CN113106290A CN202110309316.9A CN202110309316A CN113106290A CN 113106290 A CN113106290 A CN 113106290A CN 202110309316 A CN202110309316 A CN 202110309316A CN 113106290 A CN113106290 A CN 113106290A
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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
- C22C9/02—Alloys based on copper with tin 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
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
Abstract
The invention discloses a high-performance tin-phosphor bronze strip, which is characterized in that: the tin-phosphor bronze strip comprises the following components in percentage by mass: 6.0-8.0 wt% of Sn, 0.01-0.10 wt% of P, and the balance of Cu and inevitable impurities; the volume fraction of the deformed grain structure in the tin-phosphor bronze strip is 65-80%, and the volume fraction of the recrystallized grain structure is 15-30%. The tin-phosphor bronze strip can realize the yield strength of more than or equal to 700MPa, the elastic modulus of more than or equal to 115GPa and the elongation of more than or equal to 18 percent, when the strip is bent at 90 degrees, the R/t value in the good direction is less than or equal to 0.5, the R/t value in the bad direction is less than or equal to 1.5, the stress relaxation resistance is kept at 150 ℃ for 1000 hours, the residual stress is more than or equal to 63 percent, and the tin-phosphor bronze strip has the high bending and strong resilience performance required by a connector and can be used as a.
Description
Technical Field
The invention belongs to the technical field of copper alloy, and particularly relates to a high-performance tin-phosphor bronze strip and a preparation method thereof.
Background
Along with the rapid development of industries such as 5G communication, consumer electronics, new energy automobiles and the like, electronic products and electronic components gradually develop towards miniaturization and high integration, and for a connector with a complex structure, two troubles exist in a core component contact piece: on the one hand, orange peel and even cracking are easy to occur in the stamping forming process, and on the other hand, the rebound resilience is insufficient after the contact is formed, the clamping effect is unsatisfactory, and reliable electric connection cannot be guaranteed. Therefore, in order to better enable the connector to complete the electrical connection function, the copper alloy strip is required to have good bending performance, namely the R/t in the 90-degree bending failure direction is less than or equal to 1.5, so as to ensure that the punch forming is not cracked, and the formed connector has excellent resilience. Therefore, a bronze alloy for a connector, which is highly demanded, is required to have a yield strength of more than 650MPa and an elastic modulus of more than 115 GPa. In addition, the fatigue strength and the stress relaxation resistance are related to the service life and the stability of the contact element, and because the contact element not only has a certain amount of elastic deformation in the using process but also needs to bear a certain current load, the material has good stress relaxation resistance (the material is required to be insulated for 1000 hours at 150 ℃, and the residual stress is more than or equal to 60 percent). However, the conventional phosphor bronze such as C5191 and C5210 cannot meet the above performance requirements at the same time, and is not sufficient to support the miniaturized and light-weight structure design of the connector.
For example, the invention patent CN105039759A discloses a production method of a high-yield-ratio high-elasticity tin-phosphor bronze alloy, which adopts the control of the contents of alloy elements Sn, P and Ni, and combines with the conventional subsequent processing technology to finally obtain a C5191 bronze product with a higher yield ratio of 0.86-0.95, but the yield strength of the product under the processing technology condition is below 600MPa, and the product cannot meet the performance requirements of miniaturization, lightness, thinness, high integration, intellectualization and multifunction of a future connector.
The invention patent CN105803249B discloses a high-performance tin-phosphor bronze strip process, which produces a high-tin-phosphor bronze strip with tensile strength of more than 850MPa and elongation of more than 17% by strictly controlling the casting, rolling and annealing processes of a tin-phosphor bronze alloy with tin content of 9-11%, but the processing process method cannot simultaneously meet the requirements of high strength and bending and is not beneficial to forming.
Therefore, the method aims at the existing tin-phosphor bronze alloy, needs to be further improved, so that the comprehensive properties of the material, such as yield strength, elastic modulus, stress relaxation resistance and the like, are improved, and the targets of excellent bending property and high contact force of the connector are achieved.
Disclosure of Invention
The first technical problem to be solved by the invention is to provide a high-performance tin-phosphor bronze strip with excellent comprehensive properties such as yield strength, elastic modulus, stress relaxation resistance and the like.
The technical scheme adopted by the invention for solving the first technical problem is as follows: a high-performance tin-phosphor bronze strip is characterized in that: the tin-phosphor bronze strip comprises the following components in percentage by mass: 6.0-8.0 wt% of Sn, 0.01-0.10 wt% of P, and the balance of Cu and inevitable impurities; the volume fraction of the deformed grain structure in the tin-phosphor bronze strip is 65-80%, and the volume fraction of the recrystallized grain structure is 15-30%.
As for the grain structure of the copper alloy strip, the deformation grains are few, the mechanical property of the material is reduced, and the requirements on strength and elasticity cannot be met; and too many deformed grains are not beneficial to the bending processing performance of the strip, and the connector product is easy to crack in the stamping process. Meanwhile, the recrystallized grain structure directly influences the plasticity of the strip, and once the recrystallized structure is too small, the uniformity of the grain size is poor, so that the bending processing of the strip is not facilitated; too much recrystallized structure may result in insufficient strength and elasticity, which is not favorable for plugging and unplugging the connector. Therefore, in order to balance the requirements on strength and elasticity and bending, the volume fraction of the deformed grain structure in the tin-phosphor bronze strip is controlled to be 65-80%, and the volume fraction of the recrystallized grain structure is controlled to be 15-30%.
Preferably, the alloy further comprises 0.01-0.20 wt% of Ni, 0.001-0.10 wt% of Zn, 0.001-0.20 wt% of Mg and 0.001-0.10 wt% of Ce.
Ni element and P, Sn element can form Ni-P and Ni-Sn compound, which can effectively block dislocation movement and improve the stress relaxation resistance of the alloy. And Zn element can improve the fluidity of the alloy, reduce the crystallization temperature range and reduce the anti-segregation problem of tin bronze.
Mg has the effects of deoxidizing, desulfurizing and improving the stress relaxation resistance of the alloy, has small influence on the conductivity of the alloy, and can improve the work hardening effect of the alloy to a certain extent, but if the content of Mg is too large, the casting performance and the bending processing performance of the alloy are easily reduced, so the content of Mg in the alloy is controlled to be less than 0.2 wt%.
In the process of casting the copper alloy, the Ce element can be used as a nucleation center to improve the nucleation rate of the copper alloy strip, thereby playing a role in refining grains. The cast ingot with fine grains provides an initial structure condition for preparing a finished copper alloy strip with fine grains, and is beneficial to improving the strength and the bending performance of the copper alloy strip. When the content of Ce is less than 0.001 wt%, the grain refining effect is not significant, and when the content is more than 0.2 wt%, the excessive Ce may reduce the conductive performance of the copper alloy strip of the present invention. Therefore, the optimum content range of Ce is 0.001-0.10 wt%.
Preferably, the alloy further comprises 0.0005 to 0.0025 wt% of M, wherein M is at least one selected from V, Cr, Mo, La, Ti, Sb, Zr and Co. The added V, Cr, Mo, La, Sb, Zr and Co elements are the effects of refining grains and enhancing the strength and the bending property of the alloy, when the content of the elements is less than 0.0005 wt%, the effects of refining the grains and improving the property are not obvious, but when the content of the elements is more than 0.0025 wt%, the conductivity of the alloy is not facilitated. Therefore, 0.0005 to 0.0025 wt% of M is added.
Preferably, the volume fraction of the deformed grain structure is D, the volume fraction of the recrystallized grain structure is R, and the ratio of D, R satisfies: D/R is more than or equal to 3.0 and less than or equal to 4.0.
According to the tin-phosphor bronze strip, the strength and elasticity of the strip are determined by the volume fraction of the deformed grain structure, the clamping contact effect of a connector is directly influenced, and the volume fraction of the recrystallized grain structure has a certain influence on the bending performance of the copper alloy strip. When the volume fraction D/R of the deformed grain structure and the recrystallized grain structure is less than 3.0, the yield strength and elasticity of the strip are poor due to the low volume fraction of the deformed grain structure, and the good rebound effect is difficult to maintain; when the volume fraction D/R of the deformed and recrystallized grain structures is greater than 4.0, the strength and elasticity of the ribbon are excellent, but the volume fraction of the recrystallized grain structures is too small, the bending properties of the ribbon are poor, and it is difficult to satisfy the molding design requirements for miniaturization and high integration of the connector. Therefore, when the volume fraction of the deformed grain structure and the recrystallized grain structure meets the requirement that D/R is more than or equal to 3.0 and less than or equal to 4.0, the copper alloy strip has good bending performance and strong resilience, and ensures that the contact pieces are in close contact.
Preferably, the area fraction a of the cubic texture in the tin-phosphor bronze strip is 10-40%, the area fraction b of the Gaussian texture is 1-15%, and the area fraction c of the S-oriented texture is 1-15%.
The texture directly influences the performance of the material, the texture types in the microstructure of the copper alloy are divided into a deformation texture and a recrystallization texture, the deformation texture comprises a Gaussian texture, an S-oriented texture, a brass texture and the like, and the recrystallization texture is usually a cubic texture. The cubic texture in the strip acts as a recrystallized texture, and its area fraction determines the bending properties of the strip. When the ratio of the cubic texture is high, the bending performance of the strip material is good, and when the ratio of the cubic texture is low, the bending performance of the strip material is poor; the area integral number of the Gaussian texture and the S-oriented texture in the strip material has certain influence on the mechanical property of the strip material. When the area fraction of the deformation texture is higher, the mechanical property of the strip material is relatively higher, and when the area fraction of the deformation texture is lower, the mechanical property of the strip material is relatively lower. Therefore, in order to meet the use requirements of punch forming and clamping at the same time and have high bending and strong resilience, the area fraction a of the copper alloy cubic texture is 10-40%, the area fraction b of the Gaussian texture is 1-15%, and the area fraction c of the S-oriented texture is 1-15%.
Preferably, the area fractions of the cubic texture, the Gaussian texture and the S-oriented texture in the tin-phosphor bronze strip satisfy the following conditions: a/(b + c) is more than or equal to 0.60 and less than or equal to 1.50. When the area fraction a/(b + c) of the cubic texture, the Gaussian texture and the S-oriented texture is less than 0.60, the bending performance is poor due to the low fraction of the cubic texture of the recrystallized texture type; when the texture area fraction a/(b + c) > 1.50, the bending property of the strip is excellent, but the yield strength of the strip is deteriorated if the fraction of deformed texture is too high. Only when the area fractions of the cubic texture, the Gaussian texture and the S-oriented texture meet that a/(b + c) is more than or equal to 0.60 and less than or equal to 1.50, the recrystallization texture and the deformation texture fractions in the texture type of the copper alloy strip material reach the optimal balance, so that the strip material is ensured to have good bending performance and high plugging resistance.
Preferably, the texture grain size of the tin-phosphor bronze strip is less than or equal to 4 microns, and the grain diameter ratio of the minimum grain diameter to the maximum grain diameter is more than or equal to 0.90.
Preferably, the yield strength of the tin-phosphor bronze strip is more than or equal to 700MPa, the elastic modulus is more than or equal to 115GPa, and the elongation is more than or equal to 18%; when the material is bent at 90 degrees, the R/t value in the good direction is less than or equal to 0.5, the R/t value in the bad direction is less than or equal to 1.5, the stress relaxation resistance is kept at 150 ℃ for 1000 hours, and the residual stress is more than or equal to 63 percent.
The second technical problem to be solved by the invention is to provide a preparation method of the high-performance tin-phosphor bronze strip.
The technical scheme adopted by the invention for solving the second technical problem is as follows: a preparation method of a high-performance tin-phosphor bronze strip is characterized in that the preparation process flow of the tin-phosphor bronze strip is as follows: batching → horizontal continuous casting → pre-rolling → homogenizing annealing → milling face → rough rolling → edge shearing → intermediate annealing → washing → intermediate rolling → air cushion furnace annealing → washing → finished product finish rolling → finished product annealing → washing → finished product straightening → shearing; the processing rate of the pre-rolling is 20-40%.
The method solves the traditional segregation problem of the tin-phosphor bronze by a pre-rolling mode, applies certain cold rolling processing deformation to a casting blank, performs homogenization annealing after the pre-rolling thinning process, and can completely remove a surface segregation layer by a surface milling process. Meanwhile, the pre-rolling is favorable for forming deformed grains with proper volume fraction, and the recrystallization is generated near a crystal grain boundary during the re-homogenizing annealing, so that the formation of recrystallized grains after the subsequent intermediate annealing is facilitated, and good organization conditions are provided for the subsequent formation of specific deformed grains, recrystallized grain types and volume fraction in the copper alloy strip. The pre-rolling processing rate of the invention is 20-40%. When the rolling processing rate is lower than 20%, the cold deformation degree is too small, the dislocation density and the energy are insufficient, enough deformed grains are difficult to form, and the alloy is not beneficial to keeping more than 65-80% of deformed grain structures in the subsequent processing; when the processing rate is more than 40 percent, a large amount of dislocation is aggregated to form a cellular substructure, the number of cellular pressure structures is gradually increased along with the increase of the deformation degree, and the material is in an unstable state at the moment and is not beneficial to forming a sufficient amount of recrystallized grain structures in the subsequent annealing process.
Preferably, the homogenizing annealing temperature is 700-850 ℃, and the heat preservation time is 6-12 h. The homogenizing annealing process is an important step for forming a large-angle grain boundary, the homogenizing annealing temperature is 700-850 ℃, firstly, atoms are ensured to be fully diffused to eliminate segregation, crack defects caused by segregation in the subsequent processing process are reduced, secondly, recrystallized grains with proper volume fractions are ensured to be formed after the strip is subjected to homogenizing annealing treatment, and basic conditions are provided for finally forming deformed grains and recrystallized grains with optimal volume fractions. When the annealing temperature is lower than 700 ℃, the atom diffusion driving force is insufficient, the homogenizing annealing effect is not ideal, the segregation of tin-phosphor bronze cannot be completely eliminated, and meanwhile, the recrystallized grain structure is insufficient, so that the processing plasticity is influenced; when the annealing temperature is higher than 850 ℃, secondary recrystallization and abnormal growth of crystal grains are easy to occur, so that the recrystallized crystal grains are too large and thick, and the strength and resilience of the material cannot be ensured finally. The heat preservation time is 6-12 h, so that atoms have sufficient diffusion time in the annealing process, and segregation is eliminated. The holding time is less than 6h, which can cause insufficient diffusion of solute atoms; the holding time of more than 12h can cause excessively coarse grains and influence the bending performance of the finished strip.
The rough rolling processing rate of the invention reaches 75-90%. Because good plasticity conditions are provided by the previous pre-rolling, homogenizing annealing and complete face milling processes, the rough rolling and high-processing-rate rolling not only fully utilizes the plasticity of the material and the rolling capacity of rolling mill equipment, creates favorable conditions for reducing the processes and shortening the delivery period of subsequent processing, but also is most beneficial to fully crushing and refining the structure grains, realizes the synchronous improvement of the strength and the plasticity of the material and achieves the purpose of fine grain strengthening. Moreover, the method ensures that the structure crystal grains of the product are fine, can also improve the bending performance of the strip, and can also avoid the problem of rough surface caused by coarse structure crystal grains. Meanwhile, the large-machining-rate rough rolling can form deformation textures with the total area fraction of more than 65% in the copper alloy strip, including Gaussian textures and S-oriented textures, so that preparation is made for forming specific textures and area fractions in subsequent finished strips.
The intermediate annealing adopts step type heat preservation annealing: firstly, preserving heat at low temperature of 280-350 ℃ for 1-6 h; and then high-temperature annealing is adopted, the temperature is 380-450 ℃, the heat preservation time is 2-10 hours, the grain size of the annealed structure is less than 8 mu m, and the area fraction of the cubic texture in the copper alloy strip subjected to intermediate annealing is more than 50%. The material enters a recovery state from a fibrous structure by adopting low-temperature heat preservation, the capability generated by rolling is eliminated, and then high-temperature annealing is carried out, so that the structure enters a recrystallization stage, a critical recrystallization structure is obtained, the complete growth of the structure is inhibited, and the small crystal grains of the structure are controlled. Meanwhile, the texture of the alloy is transformed along with the process progress during the processing.
Preferably, the medium rolling step adopts a high-processing-rate mode for rolling, and the total processing rate is 65-75%. If the processing rate of the medium rolling is lower than 65%, enough internal energy cannot be reserved for next annealing, and recrystallization recovery in the annealing process is insufficient, so that the bending performance of the finished copper alloy strip is poor; if the processing rate of the medium rolling is more than 75%, most of the cubic texture formed in the step annealing process is converted into a deformation texture, and the strip is easy to crack under the action of stress due to the excessive deformation texture, so that the rolling crack of the strip is caused.
Preferably, the annealing temperature of the air cushion furnace is 700-900 ℃, the time of passing through the heating zone in the air cushion furnace is 5-15 s, the grain size of the copper alloy after annealing in the air cushion furnace is controlled below 5 mu m, and the area fraction of the cubic texture in the strip material is above 50%.
The annealing temperature of the air cushion furnace is 700-900 ℃, so that the copper alloy can obtain uniform and fine structure grains on one hand, and a cubic texture with the area fraction of more than 50% is formed on the other hand, and the cubic texture, the Gaussian texture and the S-oriented texture with specific area ratio are ensured to be formed in the copper alloy strip after the subsequent thermomechanical treatment, so that the copper alloy strip has the advantages of yield strength, elastic modulus and stress relaxation resistance, and meanwhile, the bending performance is excellent. When the annealing temperature is lower than 700 ℃, the driving force for recovery recrystallization of the alloy is insufficient, the transformation from the deformation texture to the cubic texture is slow, the cubic texture with the area fraction of more than 50 percent can not be formed, and the final bending performance of a finished product is not facilitated; when the annealing temperature is higher than 900 ℃, enough internal energy exists in the recovery recrystallization process, secondary recrystallization and abnormal growth of crystal grains are easy to occur, and the uniformity of structure crystal grains is not facilitated. The time of passing through the heating zone in the air cushion furnace is 5-15 s, so that the time of recovery recrystallization and grain growth is controlled, and fine and uniform equiaxial grains are obtained. When the time of passing through the heating zone in the furnace is less than 5s, the recovery recrystallization of the alloy is insufficient, and the growth speed of equiaxed grains is slow; when the time of passing through a heating zone in the furnace is more than 15s, the texture crystal grains have enough activity, the crystal grains start to be swallowed, the size of the texture crystal grains cannot be controlled below 5 mu m, and the elasticity and the connection stability of a finished product are directly influenced.
Preferably, the finish rolling reduction rate of the finished product is 20 to 40 percent.
Preferably, the annealing temperature of the finished product annealing is 150-350 ℃, and the heat preservation time is 1-6 h.
Compared with the prior art, the invention has the advantages that: the volume fraction of the deformed grain structure of the tin-phosphorus bronze strip is 65-80% and the volume fraction of the recrystallized grain structure of the tin-phosphorus bronze strip is 15-30%, so that the yield strength of the tin-phosphorus bronze strip is not less than 700MPa, the elastic modulus is not less than 115GPa, the elongation is not less than 18%, the R/t value in the good direction is not more than 0.5 and the R/t value in the bad direction is not more than 1.5 when the tin-phosphorus bronze strip is bent at 90 degrees, the stress relaxation resistance is kept at 150 ℃ for 1000 hours, the residual stress is not less than 63%, the tin-phosphorus bronze strip has high bending and strong resilience performance required by a connector, and can be used as an.
Detailed Description
The present invention will be described in further detail with reference to examples.
Selecting 14 example alloys to prepare the tin-phosphor bronze strip according to the preparation method of the invention, wherein the specific components are shown in Table 1, and the preparation process flow is as follows: batching → horizontal continuous casting → pre-rolling → homogenizing annealing → milling face → rough rolling → edge shearing → intermediate annealing → cleaning → intermediate rolling → air cushion furnace annealing → cleaning → finished product finish rolling → finished product annealing → cleaning → finished product straightening → shearing, and the specific process parameter control is shown in table 2.
The comparative example is C5210, and the specific composition is shown in Table 1.
The prepared alloys of 14 examples are subjected to performance detection such as room temperature tensile mechanical property, elastic modulus, 90-degree bending and the like, and microstructure detection such as structure grain type, volume fraction, texture type, area fraction and the like.
Tensile test at room temperature according to GB/T228.1-2010 Metal Material tensile test part 1: room temperature test method, a test was conducted on an electronic universal mechanical property tester using a 20mm wide tape head specimen with a drawing speed of 5 mm/min.
Elastic modulus test the elastic modulus of copper alloys was tested according to GB/T22315-.
And (3) metallographic structure grain size test according to JIS H0501: the product finding method in 1986 stretched copper product crystal size test method tests the grain size in a 500-time metallographic microscope photograph. The sample had a width of 10mm and a length of 10 mm.
And (4) carrying out a texture grain uniformity test, selecting grains with the minimum diameter and the maximum diameter on a gold phase picture, and measuring the diameter size of the grains. The uniformity of the crystal grains is expressed by the ratio of the minimum crystal grain diameter to the maximum crystal grain diameter of the structure.
The tapes of the examples were analyzed for texture grain type and volume fraction, grain boundary type and volume fraction, texture type and area fraction using EBSD.
The bending performance test is carried out on a universal testing machine through a corresponding bending die according to GB/T232-2010 metal material bending test method, and the sample width is 10mm and the length is 50 mm.
The stress relaxation resistance test is to test the stress relaxation resistance rate of the copper alloy at the temperature of 150 ℃ according to the test method specified in GB/T10120-2013 'Metal material tensile stress relaxation test method'.
The fatigue strength test is carried out according to GB/T4337-2008 'rotating bending method for fatigue test of metal materials', the test is carried out on a fatigue strength testing machine, and in order to accurately measure the data, the test is carried out by selecting three samples to measure each data and then taking the average value of the data.
As can be seen from Table 4, the yield strength of the copper alloy strip for the connector is more than or equal to 700MPa, the elastic modulus is more than or equal to 115GPa, the elongation is more than or equal to 18%, the 90-degree bending processability of the copper alloy strip is that the R/t value in the good direction (parallel to the rolling direction) is less than or equal to 0.5, the R/t value in the bad direction (perpendicular to the rolling direction) is less than or equal to 1.5, the stress relaxation resistance is kept at 150 ℃ for 1000 hours, the residual stress is more than or equal to 63%, the fatigue strength can also keep more than 54% of the original strength, and the above performances meet the requirements of high bending and strong resilience of the connector.
TABLE 1 Components of inventive and comparative examples
Table 2 key process parameter control for embodiments of the invention
TABLE 3 microstructures of examples of the invention
TABLE 4 Properties of inventive and comparative examples
Claims (10)
1. A high-performance tin-phosphor bronze strip is characterized in that: the tin-phosphor bronze strip comprises the following components in percentage by mass: 6.0-8.0 wt% of Sn, 0.01-0.10 wt% of P, and the balance of Cu and inevitable impurities; the volume fraction of the deformed grain structure in the tin-phosphor bronze strip is 65-80%, and the volume fraction of the recrystallized grain structure is 15-30%.
2. A high performance tin-phosphor bronze strip according to claim 1, characterized in that: also comprises 0.01 to 0.20 wt% of Ni, 0.001 to 0.10 wt% of Zn, 0.001 to 0.20 wt% of Mg and 0.001 to 0.10 wt% of Ce.
3. A high performance tin-phosphor bronze strip according to claim 1, characterized in that: and 0.0005 to 0.0025 wt% of M, wherein M is at least one selected from V, Cr, Mo, La, Ti, Sb, Zr and Co.
4. A high performance tin-phosphor bronze strip according to claim 1, characterized in that: the volume fraction of the deformed grain structure is recorded as D, the volume fraction of the recrystallized grain structure is recorded as R, and the D, R ratio satisfies the following conditions: D/R is more than or equal to 3.0 and less than or equal to 4.0.
5. A high performance tin-phosphor bronze strip according to claim 1, characterized in that: the area fraction a of the cubic texture in the tin-phosphor bronze strip is 10-40%, the area fraction b of the Gaussian texture is 1-15%, and the area fraction c of the S-oriented texture is 1-15%.
6. A high performance tin-phosphor bronze strip according to claim 5, characterized in that: the area fractions of the cubic texture, the Gaussian texture and the S-oriented texture in the tin-phosphor bronze strip meet the following conditions: a/(b + c) is more than or equal to 0.60 and less than or equal to 1.50.
7. A high performance tin-phosphor bronze strip according to claim 1, characterized in that: the yield strength of the tin-phosphor bronze strip is more than or equal to 700MPa, the elastic modulus is more than or equal to 115GPa, and the elongation is more than or equal to 18%; when the bending is carried out at 90 degrees, the R/t value in the good direction is less than or equal to 0.5, and the R/t value in the bad direction is less than or equal to 1.5; the stress relaxation resistance is kept at 150 ℃ for 1000 hours, and the residual stress is more than or equal to 63 percent.
8. A method for preparing a high-performance tin-phosphor bronze strip according to any one of claims 1 to 7, characterized in that the process flow for preparing the tin-phosphor bronze strip is as follows: batching → horizontal continuous casting → pre-rolling → homogenizing annealing → milling face → rough rolling → edge shearing → intermediate annealing → washing → intermediate rolling → air cushion furnace annealing → washing → finished product finish rolling → finished product annealing → washing → finished product straightening → shearing; the processing rate of the pre-rolling is 20-40%.
9. The method for producing a high-performance tin-phosphor bronze strip according to claim 8, wherein: the homogenizing annealing temperature is 700-850 ℃, and the heat preservation time is 6-12 h.
10. The method for producing a high-performance tin-phosphor bronze strip according to claim 8, wherein: the annealing temperature of the air cushion furnace is 700-900 ℃, the time of passing through the heating zone in the air cushion furnace is 5-15 s, the grain size of the copper alloy after annealing in the air cushion furnace is controlled below 5 mu m, and the area fraction of the cubic texture in the strip material is above 50%.
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| CN114107727A (en) * | 2021-11-22 | 2022-03-01 | 宁波金田铜业(集团)股份有限公司 | Preparation method of low-plate type I value tin-phosphor bronze strip |
| CN114438368A (en) * | 2022-01-13 | 2022-05-06 | 宁波金田铜业(集团)股份有限公司 | Leadless free-cutting tin-phosphor bronze alloy and preparation method thereof |
| CN114908270A (en) * | 2022-05-19 | 2022-08-16 | 宁波金田铜业(集团)股份有限公司 | High-tin-phosphor bronze strip and preparation method thereof |
| CN116875842A (en) * | 2023-07-19 | 2023-10-13 | 中国科学院金属研究所 | Rare earth copper-tin-phosphorus alloy material and preparation method thereof |
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Cited By (5)
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| CN114107727A (en) * | 2021-11-22 | 2022-03-01 | 宁波金田铜业(集团)股份有限公司 | Preparation method of low-plate type I value tin-phosphor bronze strip |
| CN114438368A (en) * | 2022-01-13 | 2022-05-06 | 宁波金田铜业(集团)股份有限公司 | Leadless free-cutting tin-phosphor bronze alloy and preparation method thereof |
| CN114438368B (en) * | 2022-01-13 | 2023-02-10 | 宁波金田铜业(集团)股份有限公司 | Lead-free-cutting tin-phosphor bronze alloy and preparation method thereof |
| CN114908270A (en) * | 2022-05-19 | 2022-08-16 | 宁波金田铜业(集团)股份有限公司 | High-tin-phosphor bronze strip and preparation method thereof |
| CN116875842A (en) * | 2023-07-19 | 2023-10-13 | 中国科学院金属研究所 | Rare earth copper-tin-phosphorus alloy material and preparation method thereof |
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| CN113106290B (en) | 2022-04-26 |
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