CN111621657A - Method for simultaneously improving strength plasticity and wear resistance of copper-tin alloy - Google Patents
Method for simultaneously improving strength plasticity and wear resistance of copper-tin alloy Download PDFInfo
- Publication number
- CN111621657A CN111621657A CN202010421581.1A CN202010421581A CN111621657A CN 111621657 A CN111621657 A CN 111621657A CN 202010421581 A CN202010421581 A CN 202010421581A CN 111621657 A CN111621657 A CN 111621657A
- Authority
- CN
- China
- Prior art keywords
- rich phase
- copper
- alloy
- wear resistance
- melt
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 238000000034 method Methods 0.000 title claims abstract description 25
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical class [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 title claims abstract description 24
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 73
- 229910052742 iron Inorganic materials 0.000 claims abstract description 38
- 239000000155 melt Substances 0.000 claims abstract description 28
- 238000001816 cooling Methods 0.000 claims abstract description 24
- 238000010438 heat treatment Methods 0.000 claims abstract description 14
- 230000001276 controlling effect Effects 0.000 claims abstract description 10
- 238000004781 supercooling Methods 0.000 claims abstract description 9
- 230000006698 induction Effects 0.000 claims abstract description 7
- 239000002994 raw material Substances 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 230000001105 regulatory effect Effects 0.000 claims abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- 238000005303 weighing Methods 0.000 claims description 5
- 239000002893 slag Substances 0.000 claims description 3
- 238000007670 refining Methods 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 abstract description 40
- 239000000956 alloy Substances 0.000 abstract description 40
- 238000005266 casting Methods 0.000 abstract description 13
- 238000002360 preparation method Methods 0.000 abstract description 7
- 229910052802 copper Inorganic materials 0.000 abstract description 5
- 239000000463 material Substances 0.000 abstract description 5
- 239000012071 phase Substances 0.000 description 34
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 15
- 238000005204 segregation Methods 0.000 description 12
- 239000010949 copper Substances 0.000 description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical group [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 5
- 229910000906 Bronze Inorganic materials 0.000 description 4
- RIRXDDRGHVUXNJ-UHFFFAOYSA-N [Cu].[P] Chemical compound [Cu].[P] RIRXDDRGHVUXNJ-UHFFFAOYSA-N 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 4
- 239000010974 bronze Substances 0.000 description 4
- IYRDVAUFQZOLSB-UHFFFAOYSA-N copper iron Chemical compound [Fe].[Cu] IYRDVAUFQZOLSB-UHFFFAOYSA-N 0.000 description 4
- 239000007791 liquid phase Substances 0.000 description 4
- 230000006911 nucleation Effects 0.000 description 4
- 238000010899 nucleation Methods 0.000 description 4
- 238000007711 solidification Methods 0.000 description 4
- 230000008023 solidification Effects 0.000 description 4
- 239000000498 cooling water Substances 0.000 description 3
- 239000002002 slurry Substances 0.000 description 3
- 239000007787 solid Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000007872 degassing Methods 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 241001391944 Commicarpus scandens Species 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 238000009750 centrifugal casting Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000005058 metal casting Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000007528 sand casting Methods 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
Images
Classifications
-
- 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
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/02—Alloys based on copper with tin as the next major constituent
Abstract
The invention discloses a method for simultaneously improving the strength plasticity and the wear resistance of a copper-tin alloy, belonging to the technical field of material preparation; the method comprises the following steps of: 8-15%, Fe: 1-8%, P: 0.8-1.2 percent of Cu, and the balance of Cu, placing the raw materials in a medium-frequency induction heating furnace for heating and smelting, then treating the melt by adopting a rapid cooling method, regulating and controlling the proportion of a nanoscale iron-rich phase and an intercrystalline micron-sized iron-rich phase in a primary phase by controlling the cooling rate and the supercooling degree of the melt, improving the wear resistance of the alloy by utilizing the strong plasticity of the nanoscale iron-rich phase reinforced alloy and the intercrystalline micron-sized iron-rich phase, and obtaining the copper-tin alloy with high strength, high plasticity and high wear resistance by controlling the proportion of the nanoscale iron-rich phase and the micron-sized iron-rich phase. The alloy has the advantages of simple components, short preparation process flow, low cost and excellent casting performance, is suitable for the fields of high-speed rails, heavy trucks, aerospace and the like, and has good application prospect.
Description
Technical Field
The invention relates to a method for simultaneously improving strength plasticity and wear resistance of a copper-tin alloy, belonging to the technical field of material preparation.
Background
Cast tin bronze has the advantages of high strength, low friction coefficient, good wear resistance and corrosion resistance and the like, is commonly used for manufacturing parts such as bushings, shaft sleeves and the like used under the working condition of rolling wear, but the parts need to bear heavy load, high speed and strong friction, so that the parts are easy to break when working, and how to improve the strong plasticity and wear resistance of the parts is always a research and application hotspot. However, with the rapid development of technologies in the fields of high-speed rails, ships and the like, the traditional tin bronze cannot meet increasingly strict working condition requirements, and the service life is not long due to the fact that parts are prone to surface fatigue failure or fracture caused by element segregation. Therefore, the method has high scientific research and industrial application values for meeting the requirements of parts such as the bushing, the shaft sleeve and the like under high-speed and heavy-load working conditions such as high-speed rails, ships and the like, improving element segregation, disclosing a strengthening and toughening mechanism and developing high-strength, high-toughness and wear-resistant cast tin bronze.
The copper-tin alloy is one of typical solidification segregation alloys, and is easy to generate intergranular segregation and inverse segregation in the solidification process, and the segregation phenomenon is widely generated in series tin bronze continuous casting billets and cast ingots containing 4.7-15% (wt%) tin. As the tin content increases, the degree of segregation of intergranular segregation and inverse segregation also gradually increases. In the solidification process of the copper-tin alloy, because the diffusion speed of tin atoms is obviously faster than that of copper atoms, the solubility of tin elements in the primary alpha-Cu phase is gradually reduced along with the reduction of the temperature, the tin elements are diffused from the primary alpha-Cu phase to a liquid phase, so that the tin elements in the liquid phase are enriched, a low-melting-point phase with high tin content is formed at room temperature, the theoretical tin content of the phase is 32.6% (wt%), and the average value of the tin content in the primary alpha-Cu phase at room temperature is between 1-3% (wt%), so that serious intergranular segregation is formed. Because the temperature difference between the inside and the outside of the casting wall is large, static pressure is generated on the central liquid phase during solidification and shrinkage, and under the combined action of capillary suction force generated by inter-granular tiny pores in a surface shell, the tin-rich liquid phase moves to the surface layer of the casting blank along an inter-dendritic channel to generate inverse segregation.
The tensile strength, plasticity and elongation of the CuSn10P1 alloy in sand casting and metal casting are respectively only 220MPa and 310MPa, 3 percent and 2 percent, 80HBW and 90 HBW.
Disclosure of Invention
The invention aims to provide a method for simultaneously improving the strength plasticity and the wear resistance of a copper-tin alloy, which has the advantages of simple alloy components, short preparation process flow, low cost and excellent casting performance, is suitable for the fields of high-speed rails, heavy trucks, aerospace and the like, has good application prospect, and specifically comprises the following steps:
(1) according to the Sn: 8-15%, Fe: 1-8%, P: weighing raw materials in a proportion of 0.8-1.2% and the balance of Cu (the raw materials are selected according to the mass percentage, such as pure copper, copper-tin intermediate alloy, copper-iron intermediate alloy or pure iron, copper-phosphorus intermediate alloy, and the burning loss content is added), placing the raw materials in a medium-frequency induction heating furnace for heating and smelting, preserving heat for 2-20 min within the range of 1300-1400 ℃, refining, removing slag and standing for 0-5 min when the temperature is reduced to 20-100 ℃ above the liquidus.
(2) And then processing the melt by adopting a rapid cooling method (such as cooling plate processing, stirring processing, ultrasonic processing, gas chilling and the like), regulating and controlling the proportion of the nanoscale iron-rich phase and the intercrystalline micron-sized iron-rich phase in the primary phase by controlling the cooling rate and the supercooling degree of the melt, improving the wear resistance of the alloy by utilizing the strong plasticity of the nanoscale iron-rich phase reinforced alloy and the intercrystalline micron-sized iron-rich phase, and obtaining the copper-tin alloy with high strength, high plasticity and high wear resistance by controlling the proportion of the nanoscale iron-rich phase and the micron-sized iron-rich phase.
Preferably, in the step (2) of the invention, the cooling rate of the melt for rapid cooling is 200-2000 ℃/s, and the supercooling degree of the melt is 20-150 ℃.
Preferably, the nano iron-rich phase is enriched in the primary phase to play a role in strengthening the strong plasticity of the alloy, and the nano iron-rich phase occupies the following area ratio in the microstructure: 0.6-5%; the micron-sized iron-rich phase is mainly distributed among the crystal grains and plays a role in improving the wear resistance of the alloy, and the micron-sized iron-rich phase occupies the following area ratio in a microstructure: 0.4 to 4 percent.
The invention adopts a rapid cooling method (such as cooling plate treatment, centrifugal casting and the like) to treat the melt, regulates and controls the proportion of a nano-scale iron-rich phase and an intercrystalline micron-scale iron-rich phase in a primary phase by controlling the cooling rate and the supercooling degree of the melt, improves the wear resistance of the alloy by utilizing the strong plasticity of the nano-scale iron-rich phase reinforced alloy and the intercrystalline micron-scale iron-rich phase, and obtains the copper-tin alloy with high strength, high plasticity and high wear resistance by controlling the proportion of the nano-scale iron-rich phase and the micron-scale iron-rich phase.
The invention has the beneficial effects that:
(1) the method can effectively refine the microstructure of the alloy and is beneficial to improving the strength and the plasticity of the alloy.
(2) The method can obtain the nano iron-rich phase enriched in the primary phase and the micron iron-rich phase distributed among the microstructure crystal grains, and respectively play roles in strengthening the strong plasticity of the alloy and improving the wear resistance.
(3) The alloy and the method have the advantages of simple components, short preparation process flow, low cost and excellent casting performance, are suitable for the fields of high-speed rails, heavy trucks, aerospace and the like, and have good application prospects.
Drawings
FIG. 1 is a schematic view of the structure regulation for improving the strong plasticity and the wear resistance of the copper-tin alloy.
FIG. 2 is a schematic view of a melt-confined flow induced nucleation apparatus for rapid cooling according to an embodiment of the present invention.
FIG. 3 is a treated microstructure of the CuSn10P1 and CuSn10Fe2P1 alloys of example 1.
Detailed Description
The invention will be described in more detail with reference to the following figures and examples, but the scope of the invention is not limited thereto.
Example 1
The material composition in this embodiment is CuSn10Fe2P1 (wt.%), and the preparation method specifically includes:
(1) weighing about 5kg of pure copper, copper-tin intermediate alloy, copper-iron intermediate alloy and copper-phosphorus intermediate alloy, rapidly heating the alloy to 1350 ℃ by adopting an intermediate frequency induction heating furnace, preserving heat for 10min, then performing air cooling to 1080 ℃ (liquidus to 1028 ℃) to perform degassing and deslagging, and standing for 3min to homogenize the internal temperature field of the alloy melt.
(2) The angle of the melt constrained flow induced nucleation device is adjusted to 60 degrees, the length of the melt constrained channel is 400mm, the flow rate of the up-and-down circulating cooling water is 500L/h, the crucible is collected and preheated to 990 ℃, the cooling rate of the melt in the melt treatment is about 400 ℃/s, and the supercooling degree is about 20 ℃.
(3) And pouring the melt with the homogenized temperature field into a constraint cooling channel for treatment, collecting the semi-solid slurry obtained by treatment by a collection crucible, and then quickly pouring into a wedge-shaped metal mold to obtain a casting. As a comparative sample, CuSn10P1 alloy was processed according to the same procedure and poured into a wedge metal mold to obtain a casting.
The area of the nano iron-rich phase in the microstructure prepared by the method of the embodiment is about 1.2%, and the area ratio of the micron iron-rich phase in the microstructure is about 0.8%, as shown in fig. 3. The nanoscale iron-rich phase is beneficial to improving the segregation and grain refinement of tin element, thereby being beneficial to improving the strong plasticity of the alloy; the micron-sized iron-rich phase is distributed among the grains as a hard phase, so that the hardness and the wear resistance of the alloy are improved.
The mechanical properties of the castings prepared by the method in the embodiment are shown in table 1, and it can be seen from table 1 that the strength, plasticity and hardness of the CuSn10Fe2P1 prepared by the embodiment are obviously improved.
TABLE 1
| Tensile strength/Mpa | Elongation/percent | hardness/HBW | |
| CuSn10P1 | 396 | 9.53 | 106 |
| CuSn10Fe2P1 | 458 | 12.68 | 132 |
Example 2
The material component described in this embodiment is cus8fe1p0.8 (wt.%), and the specific preparation method is as follows:
(1) weighing about 6kg of pure copper, copper-tin intermediate alloy, copper-iron intermediate alloy and copper-phosphorus intermediate alloy, rapidly heating the alloy to 1380 ℃ by adopting an intermediate frequency induction heating furnace, preserving heat for 20min, then air-cooling to 1100 ℃ (liquidus to 1028 ℃) to remove gas and slag, and standing for 5min to homogenize the internal temperature field of the alloy melt.
(2) The angle of the melt constrained flow induced nucleation device is adjusted to be 45 degrees, the length of the melt constrained channel is 300mm, the flow rate of the up-and-down circulating cooling water is 600L/h, the crucible is collected and preheated to 980 ℃, the cooling rate of the melt in the melt treatment is about 2000 ℃/s and the supercooling degree is about 50 ℃.
(3) And pouring the melt with the homogenized temperature field into a constraint cooling channel for treatment, collecting the semi-solid slurry obtained by treatment by a collection crucible, and then quickly pouring into a wedge-shaped metal mold to obtain a casting. As a comparison sample, CuSn8P0.8 alloy is processed according to the same steps and poured into a wedge-shaped metal mold to obtain a casting. Obtaining the high-strength and high-toughness copper-tin alloy with the performance cooperatively regulated by the nanoscale iron-rich phase and the micron-sized iron-rich phase.
The mechanical properties of the castings prepared by the method in the embodiment are shown in table 2, and it can be seen from table 2 that the strength, plasticity and hardness of the cus8fe1p0.8 prepared by the embodiment are obviously improved.
TABLE 2
Tensile strength/MPa elongation/% hardness/HBW
CuSn8P0.83686.8108
CuSn8Fe1P0.842910.5126
Example 3
The component of the material in this example is cusn14fe6p1.2 (wt.%), and the specific implementation steps are as follows:
(1) weighing about 8kg of pure copper, copper-tin intermediate alloy, copper-iron intermediate alloy and copper-phosphorus intermediate alloy, rapidly heating the alloy to 1300 ℃ by adopting an intermediate frequency induction heating furnace, preserving heat for 3min, then air-cooling to 1050 ℃ (liquidus 1028 ℃) for degassing and deslagging, and standing for 1min to homogenize the internal temperature field of the alloy melt;
(2) the angle of the melt constrained flow induced nucleation device is adjusted to be 50 degrees, the length of the melt constrained channel is 350mm, the flow rate of the up-and-down circulating cooling water is 550L/h, the crucible is collected and preheated to 970 ℃, the cooling rate of the melt in the melt treatment is about 800 ℃/s, and the supercooling degree is about 100 ℃.
(3) And pouring the melt with the homogenized temperature field into a constraint cooling channel for treatment, collecting the semi-solid slurry obtained by treatment by a collection crucible, and then quickly pouring into a wedge-shaped metal mold to obtain a casting. As a comparative sample, a cusn14p1.2 alloy was processed according to the same procedure to obtain a centrifugal cast article.
The mechanical properties of the castings prepared by the method in the embodiment are shown in Table 3, and the CuSn14Fe6P1.2 prepared by the embodiment has obviously improved strength, plasticity and hardness as shown in Table 3.
TABLE 3
| Tensile strength/Mpa | Elongation/percent | hardness/HBW | |
| CuSn14P1.2 | 394 | 8.5 | 117 |
| CuSn14Fe6P1.2 | 482 | 13.8 | 153 |
Claims (4)
1. A method for simultaneously improving strength plasticity and wear resistance of a copper-tin alloy is characterized by comprising the following steps:
(1) according to the Sn: 8-15%, Fe: 1-8%, P: weighing 0.8-1.2% of raw materials and the balance of Cu, and putting the raw materials into a medium-frequency induction heating furnace for heating and smelting to obtain a melt;
(2) and then treating the melt by adopting a rapid cooling method, and regulating and controlling the proportion of the nanoscale iron-rich phase in the primary phase and the intergranular micron-sized iron-rich phase by controlling the cooling rate and the supercooling degree of the melt.
2. The method for simultaneously improving the strength plasticity and the wear resistance of the copper-tin alloy according to claim 1, wherein the method comprises the following steps: the conditions of heating and smelting in the medium-frequency induction heating furnace in the step (1) are as follows: keeping the temperature within 1300-1400 ℃ for 2-20 min, refining, removing slag and standing for 0-5 min when the temperature is reduced to 20-100 ℃ above the liquidus.
3. The method for simultaneously improving the strength plasticity and the wear resistance of the copper-tin alloy according to claim 1, wherein the method comprises the following steps: in the step (2), the cooling rate of the melt for rapidly cooling is 200-2000 ℃/s, and the supercooling degree of the melt is 20-150 ℃.
4. The method for simultaneously improving the strength plasticity and the wear resistance of the copper-tin alloy according to claim 1, wherein the method comprises the following steps: the occupied area ratio of the nano iron-rich phase in the microstructure is as follows: 0.6-5%; the area ratio of the micron-sized iron-rich phase in the microstructure is as follows: 0.4 to 4 percent.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010421581.1A CN111621657B (en) | 2020-05-18 | 2020-05-18 | Method for simultaneously improving strength plasticity and wear resistance of copper-tin alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010421581.1A CN111621657B (en) | 2020-05-18 | 2020-05-18 | Method for simultaneously improving strength plasticity and wear resistance of copper-tin alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111621657A true CN111621657A (en) | 2020-09-04 |
| CN111621657B CN111621657B (en) | 2021-08-10 |
Family
ID=72257097
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010421581.1A Active CN111621657B (en) | 2020-05-18 | 2020-05-18 | Method for simultaneously improving strength plasticity and wear resistance of copper-tin alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111621657B (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114393197A (en) * | 2021-12-21 | 2022-04-26 | 西安理工大学 | Directional solidification preparation method of high-tin-content high-plasticity copper-tin alloy |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4116686A (en) * | 1976-05-13 | 1978-09-26 | Olin Corporation | Copper base alloys possessing improved processability |
| JPS63266049A (en) * | 1987-04-24 | 1988-11-02 | Furukawa Electric Co Ltd:The | Production of high tensile copper based alloy |
| CN102257170A (en) * | 2008-12-19 | 2011-11-23 | 古河电气工业株式会社 | Copper alloy material for electrical/electronic components, and method for producing same |
| JP2012097327A (en) * | 2010-11-02 | 2012-05-24 | Hitachi Cable Ltd | Copper alloy improved in hot and cold workability, method for production thereof, and copper alloy strip or alloy foil obtained from copper alloy |
| JP2013199699A (en) * | 2012-03-26 | 2013-10-03 | Furukawa Electric Co Ltd:The | Nonlead free-cutting phosphor bronze wrought product, copper alloy part, and method of manufacturing nonlead free-cutting phosphor bronze wrought product |
| CN109926564A (en) * | 2019-03-14 | 2019-06-25 | 昆明理工大学 | A kind of moulding integrated device and method of slurrying of ZCuSn10P1 alloy semi-solid slurry |
| CN110000344A (en) * | 2019-03-14 | 2019-07-12 | 昆明理工大学 | A kind of device and method for continuously preparing semi solid slurry inhibiting ZCuSn10P1 alloy tin element segregation |
| CN110218902A (en) * | 2019-06-24 | 2019-09-10 | 北京科技大学 | A method of decrease even is eliminated at copper alloy grain boundaries and is segregated |
-
2020
- 2020-05-18 CN CN202010421581.1A patent/CN111621657B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4116686A (en) * | 1976-05-13 | 1978-09-26 | Olin Corporation | Copper base alloys possessing improved processability |
| JPS63266049A (en) * | 1987-04-24 | 1988-11-02 | Furukawa Electric Co Ltd:The | Production of high tensile copper based alloy |
| CN102257170A (en) * | 2008-12-19 | 2011-11-23 | 古河电气工业株式会社 | Copper alloy material for electrical/electronic components, and method for producing same |
| JP2012097327A (en) * | 2010-11-02 | 2012-05-24 | Hitachi Cable Ltd | Copper alloy improved in hot and cold workability, method for production thereof, and copper alloy strip or alloy foil obtained from copper alloy |
| JP2013199699A (en) * | 2012-03-26 | 2013-10-03 | Furukawa Electric Co Ltd:The | Nonlead free-cutting phosphor bronze wrought product, copper alloy part, and method of manufacturing nonlead free-cutting phosphor bronze wrought product |
| CN109926564A (en) * | 2019-03-14 | 2019-06-25 | 昆明理工大学 | A kind of moulding integrated device and method of slurrying of ZCuSn10P1 alloy semi-solid slurry |
| CN110000344A (en) * | 2019-03-14 | 2019-07-12 | 昆明理工大学 | A kind of device and method for continuously preparing semi solid slurry inhibiting ZCuSn10P1 alloy tin element segregation |
| CN110218902A (en) * | 2019-06-24 | 2019-09-10 | 北京科技大学 | A method of decrease even is eliminated at copper alloy grain boundaries and is segregated |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114393197A (en) * | 2021-12-21 | 2022-04-26 | 西安理工大学 | Directional solidification preparation method of high-tin-content high-plasticity copper-tin alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111621657B (en) | 2021-08-10 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| WO2021114536A1 (en) | Steel for ball screw bearing and manufacturing method therefor | |
| CN109338035B (en) | Steel for wind driven generator gear box bearing and production method thereof | |
| CN100566873C (en) | A kind of straightening of kinked rail cast iron roll collar and preparation method thereof | |
| CN110000362B (en) | High-tungsten-vanadium high-speed steel wear-resistant roller and manufacturing method thereof | |
| WO2015043060A1 (en) | Non-quenched and tempered steel and manufacturing method therefor | |
| WO2015043059A1 (en) | Non-quenched and tempered steel and manufacturing method therefor | |
| CN111945053B (en) | Method for preparing high-speed steel roller by composite modification treatment | |
| CN110106393B (en) | High-manganese wear-resistant aluminum bronze alloy and preparation method thereof | |
| Zhiqiang et al. | Microstructures and mechanical characteristics of electromagnetic casting and direct-chill casting 2024 aluminum alloys | |
| WO2015043058A1 (en) | Production process for non-quenched and tempered steel | |
| WO2015043057A1 (en) | Non-quenched and tempered steel and manufacturing method therefor | |
| CN111621657B (en) | Method for simultaneously improving strength plasticity and wear resistance of copper-tin alloy | |
| CN106702252B (en) | A kind of heat resistant and wear resistant alloy steel material and preparation method | |
| CN109112391B (en) | Hot work die steel and preparation method thereof | |
| Wan | Si phase morphology and mechanical properties of ZL107 Al alloy improved by La modification and heat treatment | |
| CN111575511A (en) | Method for improving micro-macro segregation of copper-tin alloy | |
| CN115612920B (en) | Steel for flexible bearing of robot harmonic reducer and production method of steel | |
| CN108015255B (en) | Preparation method of high-speed tool steel | |
| CN105420629B (en) | Suitable for the high-ductility hard material collars and manufacture method of high-speed wire rolling | |
| CN111961955B (en) | High-toughness nodular cast iron and preparation method thereof | |
| CN112877564B (en) | Copper-steel solid-liquid composite bimetallic material for hot extrusion die and preparation method thereof | |
| JP5282546B2 (en) | High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance | |
| CN107287491A (en) | A kind of production method of utilization continuous casting billet milling Limit specifications special heavy plate | |
| CN111424208A (en) | Casting process of cylinder body casting | |
| JP2007327083A (en) | Spheroidal graphite cast iron and its production method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |