CN114908270A - High-tin-phosphor bronze strip and preparation method thereof - Google Patents
High-tin-phosphor bronze strip and preparation method thereof Download PDFInfo
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- CN114908270A CN114908270A CN202210554842.6A CN202210554842A CN114908270A CN 114908270 A CN114908270 A CN 114908270A CN 202210554842 A CN202210554842 A CN 202210554842A CN 114908270 A CN114908270 A CN 114908270A
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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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/045—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds for horizontal casting
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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 tin-phosphor bronze strip, which is characterized in that: the high tin-phosphor bronze comprises the following components in percentage by mass: 9.0-12.0 wt%, P: 0.03-0.4 wt%, Fe: 0.05-0.15 wt%, Zn: 0.1 to 0.25 wt%, the balance being Cu and unavoidable impurities; the ratio of a/(b + c) of the internal texture of the strip material is more than or equal to 0.04 and less than or equal to 0.3, wherein a is the area rate of the cubic texture, b is the area rate of the Copper texture, and c is the area rate of the S-shaped texture. By adding 0.1-0.25 wt% of Zn element, the anti-segregation of the high-tin-content phosphor bronze strip is improved, and the content difference of the tin element in the strip crystal and in the crystal boundary is less than or equal to 0.3 wt%; the ratio of the cubic texture area rate (a), the Copper texture area rate (b) and the S-shaped texture area rate (c) is controlled to be more than or equal to 0.04 and less than or equal to a/(b + c) and less than or equal to 0.3, so that the yield strength of the strip material is more than or equal to 690MPa, the R/t in the good direction is less than or equal to 1.0 and the R/t in the bad direction is less than or equal to 1.5 under the condition of 180-degree bending, the uniformity of residual stress in the strip material is improved, the warping of the strip material after etching is less than or equal to 1mm, and the stability of the base material when the base material is processed into a plate-to-plate connector is ensured.
Description
Technical Field
The invention relates to the technical field of copper alloy, in particular to a high-tin phosphor bronze strip and a preparation method thereof.
Background
The board-to-board connector is one of various connector products with the strongest transmission capability, and is an important part of various electronic communication products such as mobile phones and the like. Along with the development trends of more complex working modules, more abundant use functions and thinner appearance volume of connecting components in the fields of 5G communication equipment, intelligent household appliances, new energy automobiles and the like, the number of the plate-to-plate connectors in the current 5G mobile phone is increased from about 15 sets to 30-45 sets in the 4G mobile phone, and in order to ensure the volume, the pin size of the connector is smaller, the structural design is more complex, and higher requirements are provided for base materials.
On one hand, in order to ensure reasonable layout of the internal structure of the mobile phone, the material is suitable for various large-angle bending processing in the processing process of the connector pin, and the material has Good bending performance in a Good direction (Good Way) and a Bad direction (Bad Way). On the other hand, in order to ensure stable and efficient signal transmission during the use of the connector, the terminals and the contacts must have tight bonding force, so that the substrate material not only has high strength, but also has good stress relaxation resistance. Among various copper alloys, high tin-phosphor bronze (tin content is more than or equal to 9.0%) is gradually replacing titanium-copper with good comprehensive performance and low price, and becomes an important base material of products in the field, but the following problems still need to be improved. Firstly, with the increase of the tin content in the strip, the segregation of tin element can occur due to the large difference of melting points of tin element and copper element, and finally the strip is cracked during cold rolling or bending. Secondly, the yield strength of the common bronze strip cannot meet the performance requirement of the board-to-board connector, and the strip is easy to deform and warp after etching processing, so that the connector has poor contact after being used for a period of time and the signal transmission is unstable.
Therefore, in view of the above problems, further improvements in high tin bronze alloy strip are needed to meet the use requirements of board-to-board connectors.
Disclosure of Invention
The invention aims to solve the first technical problem of providing a high tin-phosphor bronze strip with good bending performance and no warpage after etching.
The technical scheme adopted by the invention for solving the first technical problem is as follows: a high tin-phosphor bronze strip is characterized in that: the high tin-phosphor bronze comprises the following components in percentage by mass: 9.0-12.0 wt%, P: 0.03-0.4 wt%, Fe: 0.05-0.15 wt%, Zn: 0.1 to 0.25 wt%, the balance being Cu and unavoidable impurities; the ratio of a/(b + c) of the internal texture of the strip material is more than or equal to 0.04 and less than or equal to 0.3, wherein a is the area rate of the cubic texture, b is the area rate of the Copper texture, and c is the area rate of the S-shaped texture.
When the high-tin phosphor bronze alloy is subjected to non-vacuum horizontal continuous casting, a part of oxygen is dissolved in copper water in the smelting process, and if the oxygen is not removed, the oxygen exists in a casting blank in a cuprous oxide form when the copper water is solidified, so that surface defects such as peeling and the like are formed in the subsequent processing process. The invention selects P element as degasifier to remove oxygen dissolved in copper water, and simultaneously prevents the formation of hard and brittle Cu caused by adding excessive P element 3 And P phase, which influences the cold processing property of the material. The content of the P element is controlled to be 0.03-0.4 wt%.
The high-tin phosphor bronze alloy strip is easy to generate inverse segregation in the smelting process, because the melting point of tin element in the tin phosphor bronze alloy is low, the solid-liquid two-phase temperature interval of the alloy is large, and macroscopic inverse segregation and microscopic segregation are easy to generate in the casting solidification process, but the content of the tin element in the casting blank is more than or equal to 9.0 wt%, and the formation of segregation is further aggravated. According to the invention, by adding 0.05-0.15 wt% of Zn element, the fluidity of the alloy is obviously improved, the crystallization temperature interval is reduced, the anti-segregation condition of the Sn element in the high-tin phosphor bronze alloy casting blank is further lightened, the growth of the casting structure is controlled to a certain extent, the uniformity of the crystal grains of the casting structure is improved, a foundation is laid for reducing the microsegregation in the crystal grains and at the crystal grain boundary, the uniformity of residual stress in the strip is improved, and the warping height of the strip after etching is reduced.
The microstructure of the material is the key for determining the performance of the material, and the invention controls the internal texture proportion of the alloy strip so that the internal texture proportion of the strip meets the requirement that a/(b + c) is more than or equal to 0.04 and less than or equal to 0.3, wherein a is the area rate of the cubic texture, b is the area rate of the Copper texture, and c is the area rate of the S-shaped texture. Among various textures of the Copper alloy, the cubic texture is a recrystallized texture, and the Copper texture and the S texture are processed textures. In order to ensure the high strength of the material, the content of the processing texture is increased, but when the processing texture is excessive, the bending property of the material is obviously reduced, the bending requirement in the processing process of the plate-to-plate connector is not met, when the area ratio of the texture meets the proportion, the bending property of the strip is obviously improved, and meanwhile, the strength and hardness value of the strip are not reduced too much.
Preferably, the content difference of Sn in the high-tin phosphor bronze crystal and at the crystal boundary is less than or equal to 0.3 wt%.
Preferably, the yield strength of the high tin-phosphor bronze strip reaches more than 690MPa, and under the 180-degree bending condition, the R/t in the good direction is less than or equal to 1.0, and the R/t in the bad direction is less than or equal to 1.5; wherein, the good direction is a direction parallel to the rolling direction, and the bad direction is a direction vertical to the rolling direction; after the high tin-phosphor bronze strip is etched, the warping height is less than or equal to 1 mm.
The second technical problem to be solved by the invention is to provide a preparation method of the high tin-phosphor bronze strip.
The technical scheme adopted by the invention for solving the second technical problem is as follows: the preparation method of the high tin-phosphor bronze strip is characterized by comprising the following process flows of: horizontal continuous casting → stepped homogenizing annealing → primary cold working → primary intermediate annealing → secondary cold working → secondary intermediate annealing → finished product cold working → tension annealing; the homogenizing annealing is carried out in two stages, wherein the first stage is heating to 550-.
The Sn content of the high-tin-phosphor bronze alloy is 9.0-12.0 wt%, and the degree of inverse segregation in the casting blank is increased sharply along with the increase of the Sn content, so that more energy is needed to complete the long-range diffusion, and the uniform distribution of components and tissues is realized. Therefore, the invention adopts 850-950 ℃ as the homogenizing annealing temperature, thereby improving the diffusion efficiency of the Sn element and achieving the purpose of reducing the inverse segregation. In addition, in order to comply with the trend of light weight and miniaturization of board-to-board connectors, the tin-phosphorus strip material used as the base material needs to have good dimensional tolerance to ensure the reliability of the assembly and use of the connector. At present, domestic and foreign researches show that casting stress has important influence on the plate type I value and the dimensional tolerance of the strip, so that the method adopts a step-by-step homogenization annealing process, firstly preserves heat at 550 ℃ and 650 ℃ for 3-10h to eliminate part of casting stress in the casting blank, and then preserves heat at 850 ℃ and 950 ℃ for 3-10h to realize improvement on casting blank anti-segregation.
Preferably, the temperature difference between the middle part and the two sides of the casting blank is controlled within 50 ℃, the outlet temperature of the casting blank is ensured to be 200-250 ℃, the solidification process of the casting blank is regulated, and finally the macrosegregation of Sn elements on the surface layer and the inner part of the casting blank and the middle part and the two sides of the casting blank is effectively controlled. Meanwhile, the grain size of the casting structure grains in the casting blank is basically kept consistent through controlling the temperature difference of the casting blank, the average grain size is within the range of 2-8mm, the grain size difference caused by uneven cooling is avoided, and the consistency and the stability of the structure and the performance in the subsequent processing of the strip are ensured.
Preferably, the processing rate of the primary cold working is more than 70%, the primary intermediate annealing adopts bell jar furnace annealing, the annealing temperature is 500-580 ℃, the annealing time is 5-10h, the processing rate of the secondary cold working is 55-65%, the secondary intermediate annealing adopts expanding air cushion furnace annealing, the annealing temperature is 600-700 ℃, and the speed is 35-65 m/min. In order to ensure the high strength of the material, rolling is usually carried out at a large working rate of more than 70% in one cold working process, the area ratio of the cubic texture in the strip is gradually reduced, the area ratio of the Copper texture is obviously improved, and the S-shaped texture is also increased. However, when the processing texture is too much, the bending property of the material is obviously reduced, the bending requirement in the processing process of the plate-to-plate connector is not met, the area rate of the cubic texture of the strip is increased by the subsequent annealing treatment, the bending property of the strip is obviously improved, and meanwhile, the alloy strip also has enough Copper texture and S-shaped texture to ensure that the strength and the hardness value of the strip are not reduced too much. Therefore, the method synergistically regulates the texture of the strip through multi-step annealing and cold processing.
Preferably, the cold machining rate of the finished product is controlled to be 20-35%.
Preferably, the annealing temperature of the tension annealing is 280-350 ℃, and the tension is controlled to be 20-100N/mm 2 . In the cold working of the finished product, due to the low cold working rate, plastic elongation usually occurs only on the surface of the alloy strip in most cases, and the internal area of the alloy strip has low elongation or even no elongation. While the strip itself is a whole, this non-uniformity of plastic elongation creates residual stresses. The generation of residual stress not only affects the plate shape and the dimensional tolerance of the material, but also seriously affects the stress relaxation resistance of the alloy material, so that the phenomenon of poor contact of a plate-to-plate connector prepared by using the material as a matrix after being used for a period of time occurs. The research of the invention shows that a small number of crystal grains in the strip are recrystallized through the annealing treatment (stress relief annealing) of external tension, and meanwhile, the crystal grains are deflected at a large angle to eliminate the position difference brought in the rolling process, so that the residual stress is uniformly released, the performance of each part of the strip tends to be consistent, and the strip after etching is prevented from being obviously warped. The annealing temperature of the tension annealing of the strip is 280-350 ℃, and the tension is controlled to be 20-100N/mm 2 During the process, the residual stress in the strip material is mostly eliminated, and the surface warpage of the subsequent strip material is less than or equal to 1mm after the subsequent strip material is etched.
Compared with the prior art, the invention has the advantages that: by adding 0.1-0.25 wt% of Zn element, the anti-segregation of the high-tin-content phosphor bronze strip is improved, and the content difference of the tin element in the strip crystal and in the crystal boundary is less than or equal to 0.3 wt%; the ratio of the cubic texture area rate (a), the Copper texture area rate (b) and the S-shaped texture area rate (c) is controlled to be more than or equal to 0.04 and less than or equal to a/(b + c) and less than or equal to 0.3, so that the yield strength of the strip material is more than or equal to 690MPa, the R/t in the good direction is less than or equal to 1.0 and the R/t in the bad direction is less than or equal to 1.5 under the condition of 180-degree bending, the uniformity of residual stress in the strip material is improved, the warping of the strip material after etching is less than or equal to 1mm, and the stability of the base material when the base material is processed into a plate-to-plate connector is ensured. The high-tin phosphor bronze alloy strip with good comprehensive performance prepared by the invention can be used as a board-to-board connector material of electronic equipment such as a 5G mobile phone, a portable computer and the like after being etched.
Detailed Description
The present invention will be described in further detail with reference to examples.
10 examples and 5 comparative examples were selected, and the specific components are shown in Table 1. The 10 embodiments are prepared according to the process flow of the high tin-phosphor bronze strip, and the process flow comprises the following steps: horizontal continuous casting → step type homogenizing annealing → surface milling → primary cold working → primary intermediate annealing → secondary cold working → secondary intermediate annealing → finished product cold working → tension annealing; the preparation method specifically comprises the following steps:
(1) horizontal continuous casting: feeding materials according to the sequence of firstly adding copper, then adding tin and finally adding zinc, adding a phosphorus-copper intermediate alloy after the metals are completely melted for removing gas in the solution, then performing a spectrum test, and horizontally and continuously casting the molten metal in a smelting furnace from a molten metal converter to a holding furnace after the test is qualified, wherein the casting parameters are selected as follows: the casting temperature is 1150-; the temperature difference between the middle part and the two sides of the casting blank is controlled within 50 ℃, and the outlet temperature of the casting blank is ensured to be 200-250 ℃.
(2) Step-type homogenizing annealing: firstly, 550-650 ℃ is used as the annealing temperature, the heat preservation time is selected to be 3-10h, and then the heat preservation is carried out for 3-10h at 850-950 ℃.
(3) Milling a surface: the thickness of each milling surface on the upper surface and the lower surface is 0.6-1.0 mm, and a surface skinning area and an inverse segregation layer can be removed simultaneously;
(4) primary cold processing: cold-processing the milled strip material to 0.7-1.5 mm;
(5) primary annealing: annealing in a bell-jar furnace at 500-580 deg.c for 5-10 hr;
(6) secondary cold processing: the secondary cold working rate is 55-65%, and the thickness of the strip is 0.25-0.5 mm;
(7) secondary annealing: carrying out continuous annealing by using an air cushion furnace, wherein the heating temperature range is 600-700 ℃, and the speed of the strip passing through the air cushion furnace is 35-65 m/min;
(8) and (3) processing a finished product: cold working the strip to 0.15-0.4 mm;
(9) and (3) tension annealing: the annealing temperature is 280-350 ℃, and the tension is controlled to be 20-100N/mm 2 。
The details of the parameters of the stepped homogenizing annealing process, the content difference of the casting structure crystal grains and the Sn element are shown in a table 1, the details of the key process parameter control texture occupation ratio are shown in a table 2, and the details of the strip performance analysis are shown in a table 3.
Comparative example 1 differs from the present example in that: the content of Zn element in the casting blank is lower than 0.1 wt%;
comparative example 2 differs from the present example in that: the temperature difference between the middle part and the two sides of the casting blank is not within 50 ℃, and the outlet temperature of the casting blank is 300-350 ℃.
Comparative example 3 differs from the present example in that: step-type homogenizing annealing is not adopted;
comparative examples 4 and 5 differ from the present example in that: the area ratio of the cubic texture, the Copper texture and the S-type texture was not controlled.
For 10 prepared examples and 5 prepared comparative examples, grain size of cast structure, EDS analysis of Sn element distribution, EBSD analysis, yield strength, bending property and surface warpage test were performed, respectively.
And (3) testing the grain size, namely testing the grain size in a metallographic microscope acquisition photo with the magnification of 100 times according to a comparison method in GB/T6394-2007 metal average grain size determination method. The sample had a width of 10mm and a length of 10 mm.
Sn element distribution and texture analysis is tested by using an FEI Verios G4 field emission scanning electron microscope carrying an Oxford Symmetry EBSD probe and an EDS probe, wherein EBSD analyzes and calculates the test result by means of Channel 5 software.
And (3) detecting yield strength, wherein a room-temperature tensile test is carried out according to GB/T228.1-2010 metal material tensile test part 1: room temperature test method the test was carried out on an electronic universal mechanical property tester, using a 20mm wide tape head specimen with a tensile speed of 5 mm/min.
And (3) testing the bending performance, namely performing bending on a universal testing machine on a corresponding bending die according to GB/T232-.
And surface warpage detection, namely, combining the detection and verification of geometric tolerance of the GB/T1958 and 2017 product geometric technical specification (GPS), the detection and verification of the outer dimension and the allowable deviation of the strip material of the copper and copper alloy plate processed by GB/T17793 and 2010 and the detection of the dimension of a smooth workpiece of the GB/T3177-2009 product geometric technical specification (GPS), wherein the width of the sample is 100mm, and the length of the sample is 100 mm.
As can be seen from comparison between the comparative example 1 and the example, when the Zn content is low, the casting structure crystal grains of the strip are small, and the content difference of the Sn element in the crystal grain interior and the crystal grain boundary is high, which proves that the addition of the Zn element is not only beneficial to the control of the casting structure crystal grains, but also beneficial to the diffusion of the Sn element.
As can be seen from comparison between comparative example 2 and the examples, when the temperature difference between the middle and both sides of the cast slab is not within 50 ℃, the outlet temperature of the cast slab is 300-350 ℃. The casting blank has the problems that crystal grains on two sides are smaller and crystal grains in the middle are larger, the average grain size is more than 10mm, the casting structure is not beneficial to the diffusion of Sn element, the segregation of the Sn element is caused, and the larger casting structure is not beneficial to the refining of the subsequent rolling processing crystal grains and the regulation and control of the structure distribution.
Comparing comparative example 3 with the examples, it can be seen that the step-type homogenization annealing is more advantageous to solve the problem of micro segregation inside the strip compared with the step-type homogenization annealing.
Comparing the comparative example 4 with the example, it can be seen that when the recrystallized texture in the strip is less and the Copper texture and the S-shaped texture are more, the strength of the alloy strip is higher, but the bending performance is obviously reduced, when the strip is bent at 180 degrees, the R/t in the good direction is less than or equal to 1.5, and the R/t in the bad direction is less than or equal to 2.5; on the contrary, as can be seen by comparing comparative example 5 with the examples, the yield strength of the strip is significantly reduced again when the recrystallized structure is more.
Table 1 example and comparative example ingredients and key process parameter control
TABLE 2 comparative example and working Process and texture ratio comparison
TABLE 3 Properties of examples and comparative examples
Claims (8)
1. A high tin-phosphor bronze strip characterized by: the high tin-phosphor bronze comprises the following components in percentage by mass: 9.0-12.0 wt%, P: 0.03-0.4 wt%, Fe: 0.05-0.15 wt%, Zn: 0.1 to 0.25 wt%, the balance being Cu and unavoidable impurities; the internal texture proportion of the strip material satisfies a/(b + c) which is more than or equal to 0.04 and less than or equal to 0.3, wherein a is the area rate of the cubic texture, b is the area rate of the Copper texture, and c is the area rate of the S-shaped texture.
2. The high tin-phosphor bronze strip according to claim 1, characterized in that: the Sn content difference between the grain interior and the grain boundary of the high-tin phosphor bronze is less than or equal to 0.3 wt%.
3. The high tin-phosphor bronze strip according to claim 1, characterized in that: the yield strength of the high tin-phosphor bronze strip reaches more than 690MPa, and under the condition of 180-degree bending, the R/t in the good direction is less than or equal to 1.0, and the R/t in the bad direction is less than or equal to 1.5; wherein, the good direction is a direction parallel to the rolling direction, and the bad direction is a direction vertical to the rolling direction; after the high tin-phosphor bronze strip is etched, the warping height is less than or equal to 1 mm.
4. A method for preparing a high tin-phosphor bronze strip according to any of claims 1 to 3, characterized in that the process flow of the high tin-phosphor bronze strip comprises: horizontal continuous casting → stepped homogenizing annealing → primary cold working → primary intermediate annealing → secondary cold working → secondary intermediate annealing → finished product cold working → tension annealing; the homogenizing annealing is carried out in two stages, wherein the first stage is heating to 550-.
5. The method of manufacturing a high tin-phosphor bronze strip according to claim 4, characterized in that: the temperature difference between the middle part and the two sides of the casting blank is controlled within 50 ℃, and the outlet temperature of the casting blank is ensured to be 200-250 ℃.
6. The method of manufacturing a high tin-phosphor bronze strip according to claim 4, characterized in that: the processing rate of the primary cold working is more than 70%, the primary intermediate annealing adopts bell jar furnace annealing, the annealing temperature is 500-580 ℃, the annealing time is 5-10h, the processing rate of the secondary cold working is 55-65%, the secondary intermediate annealing adopts expansion air cushion furnace annealing, the annealing temperature is 600-700 ℃, and the speed is 35-65 m/min.
7. The method of manufacturing a high tin-phosphor bronze strip according to claim 4, characterized in that: and the cold machining rate of the finished product is controlled to be 20-35%.
8. The method of manufacturing a high tin-phosphor bronze strip according to claim 4, characterized in that: the annealing temperature of the tension annealing is 280-350 ℃, and the tension is controlled to be 20-100N/mm 2 。
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116287851A (en) * | 2022-09-09 | 2023-06-23 | 昆明冶金研究院有限公司北京分公司 | Tin phosphor bronze strip, preparation method and application thereof |
| CN116770124A (en) * | 2023-06-08 | 2023-09-19 | 中铝科学技术研究院有限公司 | Modified tin-phosphor bronze alloy and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105803249A (en) * | 2016-05-09 | 2016-07-27 | 安徽鑫科新材料股份有限公司 | High-performance tin-phosphor bronze strip and production method thereof |
| CN113106291A (en) * | 2021-03-23 | 2021-07-13 | 宁波金田铜业(集团)股份有限公司 | Tin-phosphor bronze strip with excellent comprehensive performance and preparation method thereof |
| CN113106290A (en) * | 2021-03-23 | 2021-07-13 | 宁波金田铜业(集团)股份有限公司 | High-performance tin-phosphor bronze strip and preparation method thereof |
| CN113215424A (en) * | 2021-04-29 | 2021-08-06 | 中铜华中铜业有限公司 | Preparation process of high-uniformity tin-phosphor bronze strip |
-
2022
- 2022-05-19 CN CN202210554842.6A patent/CN114908270B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105803249A (en) * | 2016-05-09 | 2016-07-27 | 安徽鑫科新材料股份有限公司 | High-performance tin-phosphor bronze strip and production method thereof |
| CN113106291A (en) * | 2021-03-23 | 2021-07-13 | 宁波金田铜业(集团)股份有限公司 | Tin-phosphor bronze strip with excellent comprehensive performance and preparation method thereof |
| CN113106290A (en) * | 2021-03-23 | 2021-07-13 | 宁波金田铜业(集团)股份有限公司 | High-performance tin-phosphor bronze strip and preparation method thereof |
| CN113215424A (en) * | 2021-04-29 | 2021-08-06 | 中铜华中铜业有限公司 | Preparation process of high-uniformity tin-phosphor bronze strip |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116287851A (en) * | 2022-09-09 | 2023-06-23 | 昆明冶金研究院有限公司北京分公司 | Tin phosphor bronze strip, preparation method and application thereof |
| CN116770124A (en) * | 2023-06-08 | 2023-09-19 | 中铝科学技术研究院有限公司 | Modified tin-phosphor bronze alloy and preparation method thereof |
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