Disclosure of Invention
Aiming at the problems existing in the prior art, the invention provides a method for effectively improving the strength and the conductivity of an alloy, which comprises the following steps:
a method for effectively improving alloy strength and conductivity comprising the steps of:
(1) Vacuum smelting to prepare alloy cast ingots;
(2) Homogenizing heat treatment;
(3) Carrying out low-temperature hot rolling;
(4) Repeatedly cycling ultra-low temperature deep cold rolling deformation;
(5) Short-time solution quenching treatment;
(6) Low-temperature short-time pre-ageing treatment;
(7) Repeatedly cycling ultra-low temperature deep cold rolling deformation;
(8) And (5) isothermal aging treatment.
Specifically, the alloy is a cu—ti alloy.
Specifically, the initial rolling temperature of the low-temperature hot rolling in the step (3) is 700-780 ℃, the heat preservation time is 0.1-2h, and the deformation is 45-90%; the deformation temperature of the multi-cycle ultralow temperature deep cold rolling deformation in the step (4) is between-80 ℃ and-190 ℃, and the total deformation is 40-70%; the solution temperature of the short-time solution quenching treatment in the step (5) is 750-850 ℃, the solution time is 1-3h, and the quenching mode is water quenching; the temperature of the low-temperature short-time pre-ageing treatment in the step (6) is 350-430 ℃, the time is 0.5-3h, and the heating rate is more than 6 ℃/s; the deformation temperature of the multi-cycle ultralow-temperature deep cold rolling deformation in the step (7) is between-80 ℃ and-190 ℃, and the deformation amount is between 60 and 85 percent; the isothermal aging treatment temperature in the step (8) is 350-430 ℃ and the time is 0.5-10h.
Specifically, the homogenizing heat treatment process in the step (2) comprises the following steps: the temperature is 750-850 ℃ and the time is 15-30h.
Specifically, the low-temperature hot rolling process in the step (3) comprises the following steps: the low-temperature hot rolling treatment process comprises the following steps: start rolling temperature: 710-750 ℃, and the heat preservation time is as follows: 0.1-1h, deformation: 45-80%, deformation mode: unidirectional rolling, pass reduction: 3-15%, finishing temperature: greater than 500 ℃.
Specifically, the multi-cycle ultra-low temperature deep cold rolling deformation process in the step (4) comprises the following steps: the low-temperature deformation cycle times are more than 10 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -100 ℃ to-190 ℃, deformation: 5-15%, the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 2-10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-9min, wherein the deformation temperature is as follows: -100 ℃ to-190 ℃, deformation: 5-15%, the deformation mode is as follows: synchronous rolling, pass deformation: 2-10%; repeating the above process to finally lead the total deformation of the alloy plate to reach 40-70%.
Specifically, the short-time solution quenching treatment process in the step (5) comprises the following steps: solid solution temperature: 780-850 ℃, solid solution time: 1.5-3h, heating rate: more than 10 ℃/s, quenching mode: and (3) water quenching, wherein the cooling rate is more than 100 ℃/s.
Specifically, the low-temperature short-time pre-ageing treatment process in the step (6) comprises the following steps: the pre-ageing temperature is 360-430 ℃, the time is 0.7-2.8h, and the heating rate is high: greater than 6.5 ℃/sec.
Specifically, the multi-cycle ultra-low temperature deep cold rolling deformation process in the step (7) comprises the following steps: the low-temperature deformation cycle times are more than 6 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -100 ℃ to-190 ℃, deformation: 8-30%, the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 5-15%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-9min, wherein the deformation temperature is as follows: -100 ℃ to-190 ℃, deformation: 8-30%, the deformation mode is as follows: synchronous rolling, pass deformation: 5-15%; repeating the above process to finally lead the total deformation of the alloy plate to reach 60-85%.
Specifically, the isothermal aging treatment process in the step (8) comprises the following steps: isothermal aging temperature: 360-430 ℃ for the time of: 0.6-5h, and the temperature rising rate is as follows: greater than 6.5 ℃/sec.
Aiming at the problems that the existing Cu-Ti series alloy is not excellent enough in strength, conductivity and other performances, the invention provides a preparation method for effectively improving the strength and conductivity of the Cu-Ti series alloy, which can not only not increase the production cost of the alloy, but also has excellent comprehensive performance, and is suitable for being applied to various technical fields, in particular to various high and new technical fields with certain requirements on the strength, conductivity, elasticity, processability, production cost and the like of the copper alloy, the industries of production and manufacture of civil products and the like, and manufacturers for producing similar copper alloy products.
In the invention, in addition to proper homogenization heat treatment and hot rolling deformation in the hot processing multi-process regulation, a certain amount of ultralow-temperature deep cold rolling deformation treatment is carried out before solid solution, so that the rapid dissolution of the precipitated phase can be effectively promoted, and the residual quantity of the CuTi precipitated phase in the alloy matrix can be obviously reduced. Besides, in the research process, except that the multi-process coupling regulation and control of the thermal processing process enables the alloy structure to meet specific requirements, the common characteristic of the Cu-Ti alloy is that the Cu-Ti alloy can continuously grow from a mother phase to form a new phase through concentration fluctuation in consideration of amplitude modulation decomposition precipitation behavior, a nucleation process is not needed, a microstructure with a fine component periodically changing is formed in the whole grain range after desolventizing and decomposition, and an elastic strain field generated by keeping co-operation of different two phases of the component can strongly prevent dislocation movement so as to generate a strengthening effect. The preaging regulation and control ensures that the alloy is subjected to slight amplitude modulation decomposition, and then is subjected to ultra-low temperature deep cold rolling deformation, so that micro areas with slight amplitude modulation decomposition are broken, dislocation movement can be effectively blocked due to amplitude modulation decomposition tissues generated by the preaging regulation and control, and dislocation distribution formed in the ultra-low temperature deep cold rolling deformation process is more uniformly dispersed. In addition, the amplitude-modulated decomposed tissue crushed by ultra-low temperature deep cold rolling deformation can be used as nucleation points for further aging precipitation in the subsequent aging process, so that the precipitation rate and the precipitation quantity of alloy precipitates are obviously increased. Significant increases in alloy strength and conductivity must be obtained due to the rapid progression of amplitude-modulated decomposition. Finally, the alloy can have the characteristics of high strength and high conductivity by the regulation and control of the process.
Detailed Description
The invention will be described in detail below with reference to the drawings and the detailed description. The embodiments shown below do not limit the inventive content described in the claims in any way. The whole contents of the constitution shown in the following examples are not limited to the solution of the invention described in the claims.
As shown in fig. 1, the preparation method of the present invention comprises the steps of: the method comprises the steps of preparing alloy ingots by vacuum melting, homogenizing heat treatment, low-temperature hot rolling, multiple times of circulating ultra-low temperature deep cold rolling deformation, short-time solid solution quenching treatment, low-temperature short-time pre-aging treatment, multiple times of circulating ultra-low temperature deep cold rolling deformation and isothermal aging treatment, so that the grain structure of the copper alloy can be controlled, the quantity and density of alloy peak aging state precipitation can be obviously induced, and finally, the copper alloy has high strength and high conductivity.
The raw materials respectively adopt 99.9wt percent of electrolytic high-purity Cu, sponge Ti, other intermediate alloys, pure metals and the like. Firstly, alloy is smelted by using a vacuum intermediate frequency induction furnace. The specific chemical compositions of the alloys used in the examples are shown in Table 1.
Then carrying out homogenization heat treatment (the temperature is 750-850 ℃ and the time is 15-30 h) on the alloy cast ingot, and carrying out heat processing multi-process coupling regulation and control, wherein the specific treatment process is as follows: firstly, carrying out low-temperature hot rolling deformation on the cast ingot after homogenization treatment, wherein the starting rolling temperature is as follows: 700-780 ℃, and the heat preservation time is as follows: 0.1-2h, deformation: 45-90%; and then carrying out repeated circulation ultra-low temperature deep cold rolling deformation on the hot rolled plate, wherein the deformation temperature is as follows: -80 ℃ to-190 ℃, total deformation: 40-70%; then carrying out short-time solution quenching treatment on the ultra-low temperature deep cold-rolled sheet, wherein the solution temperature is as follows: 750-850 ℃, solid solution time: 1-3h, quenching mode: water quenching; then firstly carrying out low-temperature short-time pre-ageing treatment on the solution quenched alloy plate at the treatment temperature of 350-430 ℃ for 0.5-3h, and increasing the temperature rate: greater than 6 ℃/sec; and then carrying out multiple-cycle ultra-low temperature deep cold rolling deformation on the pre-ageing alloy plate, wherein the deformation temperature is as follows: -80 ℃ to-190 ℃, deformation amount: 60-85%; and finally, carrying out isothermal aging treatment on the ultralow-temperature deep cold-rolled sheet, wherein the aging temperature is as follows: 350-430 ℃ for the time of: 0.5-10h. And finally, carrying out microhardness, conductivity and tensile property measurement on the alloy in different states, and carrying out tissue characterization on the alloy in a typical state.
The specific implementation mode is as follows:
TABLE 1 implementation of the inventive alloy chemistry
Comparative example 1
According to the component design value of alloy No. 1, firstly smelting alloy by using a vacuum intermediate frequency induction furnace; then carrying out homogenization heat treatment (the temperature is 750-850 ℃ and the time is 15-30 h) on the alloy cast ingot, and carrying out heat processing multi-process coupling regulation and control, wherein the specific treatment process is as follows: firstly, carrying out low-temperature hot rolling deformation on the cast ingot after homogenization treatment, wherein the starting rolling temperature is as follows: 700-780 ℃, and the heat preservation time is as follows: 0.1-2h, deformation: 45-90%; and then carrying out cold rolling deformation at room temperature on the hot rolled plate, wherein the total deformation is as follows: 40-70%, pass reduction: 4-15%; then carrying out solution quenching treatment on the cold-rolled sheet, wherein the solution temperature is as follows: 750-850 ℃, solid solution time: 1-5h, quenching mode: water quenching; then firstly, cold rolling and deforming the solid solution quenched alloy plate at room temperature, wherein the deformation is as follows: 60-85%, pass reduction: 5-17%; finally, carrying out isothermal aging treatment on the room-temperature cold-rolled sheet at 350, 400 and 450 ℃ for the aging time: 0.5-10h. Finally, microhardness, conductivity, tensile properties were measured for the different state alloys as shown in fig. 2 and table 2, and the structure characterization of the typical state alloys (as shown in fig. 3).
Comparative example 2
According to the component design value of alloy No. 2, firstly smelting alloy by using a vacuum intermediate frequency induction furnace; then carrying out homogenization heat treatment (the temperature is 750-850 ℃ and the time is 15-30 h) on the alloy cast ingot, and carrying out heat processing multi-process coupling regulation and control, wherein the specific treatment process is as follows: firstly, carrying out low-temperature hot rolling deformation on the cast ingot after homogenization treatment, wherein the starting rolling temperature is as follows: 700-780 ℃, and the heat preservation time is as follows: 0.1-2h, deformation: 45-90%; and then carrying out cold rolling deformation at room temperature on the hot rolled plate, wherein the total deformation is as follows: 40-70%, pass reduction: 4-15%; then carrying out solution quenching treatment on the cold-rolled sheet, wherein the solution temperature is as follows: 750-850 ℃, solid solution time: 1-5h, quenching mode: water quenching; then firstly, cold rolling and deforming the solid solution quenched alloy plate at room temperature, wherein the deformation is as follows: 60-85%, pass reduction: 5-17%; finally, carrying out isothermal aging treatment on the room-temperature cold-rolled sheet at 350, 400 and 450 ℃ for the aging time: 0.5-10h. Finally, microhardness, conductivity and tensile properties of the alloys in different states were measured as shown in fig. 4 and table 2.
Example 1
According to the component design value of alloy No. 1, firstly smelting alloy by using a vacuum intermediate frequency induction furnace; then carrying out homogenization heat treatment (the temperature is 750-850 ℃ and the time is 15-30 h) on the alloy cast ingot, and carrying out heat processing multi-process coupling regulation and control, wherein the specific treatment process is as follows: firstly, carrying out low-temperature hot rolling deformation on the cast ingot after homogenization treatment, wherein the starting rolling temperature is as follows: 710-750 ℃, and the heat preservation time is as follows: 0.1-1h, deformation: 45-80%, deformation mode: unidirectional rolling, pass reduction: 3-15%, finishing temperature: greater than 500 ℃; then carrying out multiple-cycle ultralow-temperature deep cold rolling deformation treatment on the hot rolled plate, wherein the low-temperature deformation cycle times are more than 10 times, firstly placing the hot rolled plate in a liquid nitrogen tank for more than 30min, and then carrying out ultralow-temperature deformation at the deformation temperature: -100 ℃ to-190 ℃, deformation: 5% -15%, the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 2-10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-9min, wherein the deformation temperature is as follows: -100 ℃ to-190 ℃, deformation: 5% -15%, the deformation mode is as follows: synchronous rolling, pass deformation: 2-10%; repeating the above process to finally lead the total deformation of the alloy plate to reach 40-70%; then carrying out short-time solution quenching treatment on the multi-cycle ultralow-temperature deep cold-rolled sheet, wherein the solution temperature is as follows: 780-850 ℃, solid solution time: 1.5-3h, heating rate: more than 10 ℃/s, quenching mode: water quenching, wherein the cooling rate is more than 100 ℃/s; then firstly, carrying out low-temperature short-time pre-ageing treatment on the solution quenched alloy plate, wherein the pre-ageing temperature is 360-430 ℃, the time is 0.7-2.8h, and the temperature rising rate is high: greater than 6.5 ℃/sec; and then carrying out multiple-cycle ultralow-temperature deep cold rolling deformation treatment on the low-temperature pre-ageing alloy plate, wherein the low-temperature deformation cycle times are more than 6 times, firstly placing the alloy plate in a liquid nitrogen tank for more than 30min, and then carrying out ultralow-temperature deformation at the deformation temperature: -100 ℃ to-190 ℃, deformation: 8% -30%, the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 5-15%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-9min, wherein the deformation temperature is as follows: -100 ℃ to-190 ℃, deformation: 8% -30%, the deformation mode is as follows: synchronous rolling, pass deformation: 5-15%; repeating the above process to finally ensure that the total deformation of the alloy plate reaches 60-85 percent; and finally, carrying out isothermal aging treatment on the ultralow-temperature cold-rolled sheet, wherein the isothermal aging temperature is as follows: 360-430 ℃ for the time of: 0.6-10h, and the temperature rising rate is as follows: greater than 6.5 ℃/sec. Microhardness, electrical conductivity, tensile properties measurements were then performed on the different state alloys as shown in fig. 5 and table 2, and the texture characterization of the typical state alloys (as shown in fig. 6).
Example 2
According to the component design value of the alloy No. 2, firstly smelting the alloy by using a vacuum intermediate frequency induction furnace; then carrying out homogenization heat treatment (the temperature is 750-850 ℃ and the time is 15-30 h) on the alloy cast ingot, and carrying out heat processing multi-process coupling regulation and control, wherein the specific treatment process is as follows: firstly, carrying out low-temperature hot rolling deformation on the cast ingot after homogenization treatment, wherein the starting rolling temperature is as follows: 710-750 ℃, and the heat preservation time is as follows: 0.1-1h, deformation: 45-80%, deformation mode: unidirectional rolling, pass reduction: 3-15%, finishing temperature: greater than 500 ℃; then carrying out multiple-cycle ultralow-temperature deep cold rolling deformation treatment on the hot rolled plate, wherein the low-temperature deformation cycle times are more than 10 times, firstly placing the hot rolled plate in a liquid nitrogen tank for more than 30min, and then carrying out ultralow-temperature deformation at the deformation temperature: -100 ℃ to-190 ℃, deformation: 5% -15%, the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 2-10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-9min, wherein the deformation temperature is as follows: -100 ℃ to-190 ℃, deformation: 5% -15%, the deformation mode is as follows: synchronous rolling, pass deformation: 2-10%; repeating the above process to finally lead the total deformation of the alloy plate to reach 40-70%; then carrying out short-time solution quenching treatment on the multi-cycle ultralow-temperature deep cold-rolled sheet, wherein the solution temperature is as follows: 780-850 ℃, solid solution time: 1.5-3h, heating rate: more than 10 ℃/s, quenching mode: water quenching, wherein the cooling rate is more than 100 ℃/s; then firstly, carrying out low-temperature short-time pre-ageing treatment on the solution quenched alloy plate, wherein the pre-ageing temperature is 360-430 ℃, the time is 0.7-2.8h, and the temperature rising rate is high: greater than 6.5 ℃/sec; and then carrying out multiple-cycle ultralow-temperature deep cold rolling deformation treatment on the low-temperature pre-ageing alloy plate, wherein the low-temperature deformation cycle times are more than 6 times, firstly placing the alloy plate in a liquid nitrogen tank for more than 30min, and then carrying out ultralow-temperature deformation at the deformation temperature: -100 ℃ to-190 ℃, deformation: 8% -30%, the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 5-15%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-9min, wherein the deformation temperature is as follows: -100 ℃ to-190 ℃, deformation: 8% -30%, the deformation mode is as follows: synchronous rolling, pass deformation: 5-15%; repeating the above process to finally ensure that the total deformation of the alloy plate reaches 60-85 percent; and finally, carrying out isothermal aging treatment on the ultralow-temperature cold-rolled sheet, wherein the isothermal aging temperature is as follows: 360-430 ℃ for the time of: 0.6-10h, and the temperature rising rate is as follows: greater than 6.5 ℃/sec. Microhardness, conductivity, tensile properties measurements were then performed on the different state alloys as shown in fig. 7 and table 2.
TABLE 2 mechanical Properties of several Cu-Ti alloys in different states
Example 3
The embodiment adopts common Cu-Ti alloy as a processing object, and the specific operation steps and technological parameters are as follows:
(1) Firstly smelting Cu-Ti alloy by using a vacuum intermediate frequency induction furnace;
(2) Homogenizing heat treatment, wherein the temperature is as follows: 750 ℃, time: 15h;
(3) Low-temperature hot rolling, and initial rolling temperature: 700 ℃, and the heat preservation time is as follows: 0.1h, deformation: 45%, deformation mode: unidirectional rolling, pass reduction: 3%, finishing temperature: greater than 500 ℃. The method comprises the steps of carrying out a first treatment on the surface of the
(4) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 10 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -80 ℃, deformation: 5, deformation mode: synchronous rolling, wherein the pass deformation is 2%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2min, wherein the deformation temperature is as follows: -80 ℃, deformation: 5, deformation mode: synchronous rolling, pass deformation: 2%; repeating the above process to finally enable the total deformation of the alloy plate to reach 40%;
(5) Short-time solution quenching treatment, solution temperature: 750 ℃, solid solution time: 1h, heating rate: more than 10 ℃/s, quenching mode: water quenching, wherein the cooling rate is more than 100 ℃/s;
(6) Low-temperature short-time pre-ageing treatment, wherein the pre-ageing temperature is 350 ℃, the time is 0.5h, and the heating rate is as follows: greater than 6 ℃/sec. The method comprises the steps of carrying out a first treatment on the surface of the
(7) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 6 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -80 ℃, deformation: 8, deformation mode: synchronous rolling, wherein the pass deformation is 5%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2min, wherein the deformation temperature is as follows: -80 ℃, deformation: 8, deformation mode: synchronous rolling, pass deformation: 5%; repeating the above process to finally ensure that the total deformation of the alloy plate reaches 60 percent;
(8) Isothermal aging treatment, isothermal aging temperature: 350 ℃, time: 0.5h, heating rate: greater than 6.5 ℃/sec.
Example 4
The embodiment adopts common Cu-Ti alloy as a processing object, and the specific operation steps and technological parameters are as follows:
(1) Firstly smelting Cu-Ti alloy by using a vacuum intermediate frequency induction furnace;
(2) Homogenizing heat treatment, wherein the temperature is as follows: 850 ℃, time: 30h;
(3) Low-temperature hot rolling, and initial rolling temperature: 780 ℃, the heat preservation time is as follows: 2h, deformation: 90%, deformation mode: unidirectional rolling, pass reduction: 15% of finishing temperature: greater than 500 ℃. The method comprises the steps of carrying out a first treatment on the surface of the
(4) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 10 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -190 ℃, deformation: 15%, deformation mode: synchronous rolling, wherein the pass deformation is 10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 9min, wherein the deformation temperature is as follows: -190 ℃, deformation: 15%, deformation mode: synchronous rolling, pass deformation: 10%; repeating the above process to finally ensure that the total deformation of the alloy plate reaches 70%;
(5) Short-time solution quenching treatment, solution temperature: 850 ℃, solid solution time: 3h, heating rate: more than 10 ℃/s, quenching mode: water quenching, wherein the cooling rate is more than 100 ℃/s;
(6) Low-temperature short-time pre-ageing treatment, wherein the pre-ageing temperature is 430 ℃, the time is 3h, and the heating rate is as follows: greater than 6.5 ℃/sec;
(7) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 6 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -190 ℃, deformation: 30%, deformation mode: synchronous rolling, wherein the pass deformation is 15%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 9min, wherein the deformation temperature is as follows: -190 ℃, deformation: 30%, deformation mode: synchronous rolling, pass deformation: 15%; repeating the above process to finally enable the total deformation of the alloy plate to reach 85%;
(8) Isothermal aging treatment, isothermal aging temperature: 430 ℃, time: 3h, heating rate: greater than 6.5 ℃/sec.
Example 5
In the embodiment, cu-Ti alloy is adopted as a processing object, and the specific operation steps and the technological parameters are as follows:
(1) Firstly smelting Cu-Ti alloy by using a vacuum intermediate frequency induction furnace;
(2) Homogenizing heat treatment, wherein the temperature is as follows: 800 ℃ for the time of: 20h;
(3) Low-temperature hot rolling, and initial rolling temperature: 710 ℃, heat preservation time: 1h, deformation: 80%, deformation mode: unidirectional rolling, pass reduction: 5%, finishing temperature: greater than 500 ℃. The method comprises the steps of carrying out a first treatment on the surface of the
(4) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 10 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -100 ℃, deformation: 10%, deformation mode: synchronous rolling, wherein the pass deformation is 8%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 7min, wherein the deformation temperature is as follows: -100 ℃, deformation: 10%, deformation mode: synchronous rolling, pass deformation: 8%; repeating the above process to finally enable the total deformation of the alloy plate to reach 50%;
(5) Short-time solution quenching treatment, solution temperature: 780 ℃, solid solution time: 1.5h, heating rate: more than 10 ℃/s, quenching mode: water quenching, wherein the cooling rate is more than 100 ℃/s;
(6) Low-temperature short-time pre-ageing treatment, wherein the pre-ageing temperature is 360 ℃, the time is 0.7h, and the temperature rising rate is as follows: greater than 6 ℃/sec;
(7) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 6 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -100 ℃, deformation: 20%, deformation mode: synchronous rolling, wherein the pass deformation is 10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 7min, wherein the deformation temperature is as follows: -100 ℃, deformation: 12%, deformation mode: synchronous rolling, pass deformation: 10%; repeating the above process, and finally enabling the total deformation of the alloy plate to reach 65%;
(8) Isothermal aging treatment, isothermal aging temperature: 360 ℃ and the time is as follows: 0.6h, heating rate: greater than 6.5 ℃/sec.
Example 6
In the embodiment, cu-Ti alloy is adopted as a processing object, and the specific operation steps and the technological parameters are as follows:
(1) Firstly smelting Cu-Ti alloy by using a vacuum intermediate frequency induction furnace;
(2) Homogenizing heat treatment, wherein the temperature is as follows: 800 ℃ for the time of: 20h;
(3) Low-temperature hot rolling, and initial rolling temperature: 750 ℃, and the heat preservation time is as follows: 0.5h, deformation: 55%, deformation mode: unidirectional rolling, pass reduction: 5%, finishing temperature: greater than 500 ℃. The method comprises the steps of carrying out a first treatment on the surface of the
(4) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 10 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -110 ℃, deformation: 10%, deformation mode: synchronous rolling, wherein the pass deformation is 8%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 7min, wherein the deformation temperature is as follows: -110 ℃, deformation: 10%, deformation mode: synchronous rolling, pass deformation: 8%; repeating the above process to finally enable the total deformation of the alloy plate to reach 50%;
(5) Short-time solution quenching treatment, solution temperature: 800 ℃, solid solution time: 2h, heating rate: more than 10 ℃/s, quenching mode: water quenching, wherein the cooling rate is more than 100 ℃/s;
(6) Low-temperature short-time pre-ageing treatment, wherein the pre-ageing temperature is 400 ℃, the time is 2.8h, and the heating rate is as follows: greater than 6.5 ℃/sec;
(7) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 6 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -110 ℃, deformation: 20%, deformation mode: synchronous rolling, wherein the pass deformation is 10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 7min, wherein the deformation temperature is as follows: -110 ℃, deformation: 12%, deformation mode: synchronous rolling, pass deformation: 10%; repeating the above process, and finally enabling the total deformation of the alloy plate to reach 65%;
(8) Isothermal aging treatment, isothermal aging temperature: 400 ℃ and time: 5h, heating rate: greater than 6.5 ℃/sec.
Example 7
In the embodiment, cu-Ti alloy is adopted as a processing object, and the specific operation steps and the technological parameters are as follows:
(1) Firstly smelting Cu-Ti alloy by using a vacuum intermediate frequency induction furnace;
(2) Homogenizing heat treatment, wherein the temperature is as follows: 800 ℃ for the time of: 20h;
(3) Low-temperature hot rolling, and initial rolling temperature: 720 ℃, and the heat preservation time is as follows: 0.5h, deformation: 55%, deformation mode: unidirectional rolling, pass reduction: 5%, finishing temperature: greater than 500 ℃. The method comprises the steps of carrying out a first treatment on the surface of the
(4) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 10 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -110 ℃, deformation: 10%, deformation mode: synchronous rolling, wherein the pass deformation is 8%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 7min, wherein the deformation temperature is as follows: -110 ℃, deformation: 10%, deformation mode: synchronous rolling, pass deformation: 8%; repeating the above process to finally enable the total deformation of the alloy plate to reach 50%;
(5) Short-time solution quenching treatment, solution temperature: 800 ℃, solid solution time: 2h, heating rate: more than 10 ℃/s, quenching mode: water quenching, wherein the cooling rate is more than 100 ℃/s;
(6) Low-temperature short-time pre-ageing treatment, wherein the pre-ageing temperature is 400 ℃, the time is 2h, and the heating rate is as follows: greater than 6.5 ℃/sec;
(7) Repeatedly cycling ultra-low temperature deep cold rolling deformation, and the deformation temperature is as follows: the low-temperature deformation cycle times are more than 6 times, firstly, the low-temperature deformation is carried out after the low-temperature deformation is carried out for more than 30 minutes in a liquid nitrogen tank, and the deformation temperature is as follows: -110 ℃, deformation: 20%, deformation mode: synchronous rolling, wherein the pass deformation is 10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 7min, wherein the deformation temperature is as follows: -110 ℃, deformation: 12%, deformation mode: synchronous rolling, pass deformation: 10%; repeating the above process, and finally enabling the total deformation of the alloy plate to reach 65%;
(8) Isothermal aging treatment, isothermal aging temperature: 400 ℃ and time: 2h, heating rate: greater than 6.5 ℃/sec.
The Cu-Ti alloy precipitation is characterized by amplitude modulation decomposition precipitation behavior, and is mainly characterized in that a new phase can be formed by continuously growing from the fluctuation of the concentration of a mother phase in the precipitation process, a nucleation process is not needed, a microstructure with periodically changed fine components is formed in the whole grain range after desolventizing and decomposing, and the elastic strain field generated by the two phases with different components kept together can strongly prevent dislocation movement, so that the strengthening effect is generated. Therefore, the method firstly carries out multi-process coupling regulation and control before solid solution, including low-temperature hot rolling and multi-cycle ultra-low temperature deep cold rolling deformation, the process coupling regulation and control not only can lead the residual CuTi in an alloy matrix to obtain more uniform dispersion distribution, but also can obviously reduce the size, the strain energy storage around a precipitation phase can also obviously increase, finally compared with the traditional hot processing technology, the method can better remelt the CuTi precipitation into the alloy matrix through short-time solid solution treatment, and provides a guarantee for improving the strength of the alloy with the subsequent maximum potential. The invention also particularly designs and develops a preparation process for coupling pre-aging and ultralow temperature deformation after solid solution to regulate and control amplitude modulation decomposition and dislocation distribution characteristics according to the precipitation characteristics of the alloy, namely amplitude modulation decomposition behavior. The preaging regulation and control ensures that the alloy is subjected to slight amplitude modulation decomposition, and then is subjected to ultra-low temperature deep cold rolling deformation, so that micro areas with slight amplitude modulation decomposition are broken, dislocation movement can be effectively blocked due to amplitude modulation decomposition tissues generated by the preaging regulation and control, and dislocation distribution formed in the ultra-low temperature deep cold rolling deformation process is more uniformly dispersed. In addition, the amplitude-modulated decomposed tissue crushed by ultra-low temperature deep cold rolling deformation can be used as nucleation points for further aging precipitation in the subsequent aging process, so that the precipitation rate and the precipitation quantity of alloy precipitates are obviously increased. Significant increases in alloy strength and conductivity must be obtained due to the rapid progression of amplitude-modulated decomposition. Finally, the alloy can have the characteristics of high strength and high conductivity by the regulation and control of the process. Example 1 after the developed process control, the aging precipitation rate of the alloy in the isothermal aging process is obviously accelerated, and the corresponding aging hardness peak value is also obviously increased, and a double peak phenomenon (mainly caused by the pre-aging control) occurs. According to the performance test results, the hardness of the alloy after short-time aging treatment is higher than 340HV, the tensile strength can reach 1110.4MPa, the elastic modulus reaches 127GPa, the conductivity is close to 14% IACS, the hardness is slowly reduced and a secondary peak appears after further aging, the peak hardness is close to 340HV, the tensile strength can still reach 1091.3MPa, the conductivity is higher than 15% IACS, the elastic modulus is 114.2GPa, and the comprehensive performance is obviously superior to that of the Cu-Ti alloy plate and strip prepared by the traditional process (as shown in Table 2, FIG. 2 and FIG. 5). The above-mentioned remarkable improvement of the comprehensive performance is achieved, and the main reason is that as described above, the positive influence of the multi-cycle ultra-low temperature deep cold rolling deformation on the alloy structure before solid solution is achieved, and the precipitation can be remarkably refined compared with the conventional process (as shown in fig. 3 and 6).
In addition, a great deal of researches show that the structure and the performance of the Cu-Ti alloy can be effectively improved by adding proper microalloying elements, and the invention also compares and researches the performance change condition of the Cu-Ti and Cu-Ti-La alloy after being regulated and controlled by a new designed and developed process. From comparative example 2 and example 2, it can be seen that a proper amount of microalloyed La does have a certain effect on the combination of Jin Yingdu and conductivity, but the effect is not more remarkable than the effect of the multi-process coupling regulation process. After the alloy is subjected to the multi-process coupling regulation, the final comprehensive performance of the alloy is also very excellent. The precipitation rate is remarkably accelerated, and the conductivity is greatly improved (as shown in fig. 7).
In conclusion, the Cu-3.0wt% Ti- (La) alloy is subjected to multi-process coupling regulation and control, so that the amplitude modulation decomposition characteristics corresponding to the alloy are obviously changed, the aging precipitation rate is obviously accelerated, and the peak hardness, the strength and the conductivity are obviously improved. The preparation method capable of effectively improving the strength and the conductivity of the Cu-Ti alloy can well meet the urgent requirements of manufacturing typical parts in a plurality of high-new technical fields such as electronic industry, aerospace, instruments and meters, household appliances and the like on high-strength, high-elasticity and high-conductivity copper alloy. Therefore, the preparation method of the invention is not only very suitable for being applied to a plurality of high and new technical fields, especially the fields with special requirements on high-strength, high-elasticity and high-conductivity novel copper alloy, but also is especially suitable for being applied and popularized to the industries with more sensitivity such as harmful effects of smoke, steam and dust of beryllium and compounds thereof on human health in the process of applying beryllium bronze. In addition, the preparation technology has a certain guiding significance for further development, processing and application of high-strength conductive copper alloy and other similar metal materials in other fields, and is worthy of copper alloy processing enterprises to pay attention to the alloy and the preparation process thereof, so that the alloy can be popularized and applied as soon as possible.
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.