CN114150123B - Method for effectively improving alloy strength and conductivity - Google Patents
Method for effectively improving alloy strength and conductivity Download PDFInfo
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- CN114150123B CN114150123B CN202111404375.0A CN202111404375A CN114150123B CN 114150123 B CN114150123 B CN 114150123B CN 202111404375 A CN202111404375 A CN 202111404375A CN 114150123 B CN114150123 B CN 114150123B
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- 239000000956 alloy Substances 0.000 title claims abstract description 141
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 137
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- 238000010791 quenching Methods 0.000 claims abstract description 45
- 230000000171 quenching effect Effects 0.000 claims abstract description 45
- 238000005097 cold rolling Methods 0.000 claims abstract description 42
- 229910017945 Cu—Ti Inorganic materials 0.000 claims abstract description 30
- 238000005098 hot rolling Methods 0.000 claims abstract description 21
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 72
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- 239000000243 solution Substances 0.000 claims description 31
- 238000001816 cooling Methods 0.000 claims description 27
- 239000006104 solid solution Substances 0.000 claims description 24
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 14
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- 238000003723 Smelting Methods 0.000 claims description 11
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- 229910052790 beryllium Inorganic materials 0.000 description 7
- ATBAMAFKBVZNFJ-UHFFFAOYSA-N beryllium atom Chemical compound [Be] ATBAMAFKBVZNFJ-UHFFFAOYSA-N 0.000 description 7
- 239000011159 matrix material Substances 0.000 description 7
- 229910001069 Ti alloy Inorganic materials 0.000 description 6
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- 229910000906 Bronze Inorganic materials 0.000 description 5
- 239000010974 bronze Substances 0.000 description 5
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 5
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Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
-
- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B2003/005—Copper or its alloys
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- Chemical & Material Sciences (AREA)
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- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Conductive Materials (AREA)
Abstract
The invention provides a preparation method for improving alloy strength and conductivity, which is particularly suitable for Cu-Ti alloy, and is characterized in that the alloy is subjected to integral coupling regulation and control of component design, casting, homogenization, low-temperature hot rolling, multiple-cycle ultralow-temperature cold rolling, short-time solution quenching, low-temperature short-time pre-aging treatment, multiple-cycle ultralow-temperature deep cold rolling and isothermal aging treatment, the hardness of the alloy after short-time aging treatment is higher than 340HV, the tensile strength can reach 1110.4MPa, the conductivity is close to 14% IACS, the elastic modulus reaches 127GPa, the hardness is reduced slowly and a secondary peak value 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, and the elastic modulus is 114.2GPa. The preparation method developed by the invention is very suitable for manufacturing the high-strength elastic copper alloy material for typical parts in a plurality of high and new technical fields such as electronic industry, aerospace, instruments and meters, household appliances and the like, and particularly for manufacturing parts with complex shapes and better requirements on strength, elasticity, conductivity and the like.
Description
Technical Field
The invention belongs to the technical field of alloys, and particularly relates to a method for effectively improving alloy strength and conductivity.
Background
With the rapid development of modern electronic industry technology, electronic components are developed to high performance, precision and miniaturization, and thus, higher requirements are placed on the elasticity, strength, conductivity and reliability of the materials used. Although beryllium bronze has excellent elasticity, strength, wear resistance, conductivity and the like, and also has lower stress relaxation characteristics, and is widely applied to a plurality of high and new technical fields of electronic industry, aerospace, instruments and meters, household appliances and the like, the alloy still has the following problems, such as harmful effects of smoke, steam and dust of beryllium and compounds thereof on human health, high production cost, high price and the like, and development of novel elastic copper alloy materials capable of well replacing the beryllium bronze is urgently needed.
The Cu-Ti alloy belongs to an aging strengthening alloy, and has higher strength, elasticity and good high-temperature stress relaxation resistance, heat resistance and heat resistanceAbrasion resistance and fatigue resistance. A great deal of researches show that the Cu-Ti alloy with the Ti content of 2.5% -5% has good performance for replacing beryllium bronze, and the Cu-Ti alloy which is strengthened by amplitude modulation decomposition and precipitation can reach the strength and elasticity equivalent to the beryllium bronze through proper heat treatment and heat processing treatment, but is generally low in conductivity. Therefore, how to enable the cu—ti alloy to have high strength, high elasticity, and high and thus, a large number of researchers improve the performance of the cu—ti alloy by adding alloying elements such as Cr, zr, al, cd, mg, ni, sn, co and the like as trace addition elements. The performance of the alloy is good and balanced after Cr, zr and Cd are added, however, cd is taken as a toxic element, and the environment-friendly requirement is not met. Although the study shows that Cr element can effectively improve the performance of Cu-Ti alloy, the related action mechanism is not revealed. In addition, the Cu-3Ti-4Al alloy added with Al has the conductivity improved by 6% IACS after aging at 450 ℃ compared with Cu-3Ti, but the peak hardness is reduced from 280HV to 180HV. Structural characterization has found that Cu4Ti is the main strengthening phase in the alloy, and is formed based on nucleation and growth principles rather than amplitude modulation decomposition, and the precipitated phase grows along the c direction, which reduces lattice mismatch strain energy between the matrix and the precipitated phase, and AlCu is also formed 2 Ti(DO 3 ) The principal plane of inertia of the precipitated phase approaches 110 of the face-centered cubic matrix. Eventually, the formation of these phases reduces the solid solubility of Ti in the Cu matrix, resulting in an increase in conductivity. In addition, after a certain amount of Ni element is added into the Cu-3Ti alloy, the microstructure of the as-cast alloy can be converted from dendrite to equiaxed form, and annealing twinning can also occur in the interior of the residual NiTi phase in the aging process. The change in structure ultimately results in an increase in the electrical conductivity of the alloy, but a decrease in strength.
Considering that the key to influence the properties of alloy strength, elasticity, conductivity and the like is still the composition and process, if the as-cast structure of the alloy can be regulated and controlled by proper microalloying and then proper process regulation and control are carried out, so that the alloy matrix can be as much as possible to separate out solute element Ti, and the Cu-Ti alloy can show excellent comprehensive properties. Therefore, it is very necessary to develop a high-strength conductive Cu-Ti alloy material which does not increase the production cost of the alloy and has excellent comprehensive properties, and a preparation technology thereof, so that the urgent requirements of the high and new technical fields on the material are better met. In addition, the preparation process of the novel Cu-Ti alloy material can play an important role in inspiring and pushing the development of other novel metal materials. Conductivity is the key to further enabling wide application of the material.
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.
Drawings
FIG. 1 is a flow chart of an alloy preparation process;
FIG. 2 shows the change of hardness and conductivity of Cu-Ti alloy in comparative example 1;
FIG. 3 is a metallographic structure corresponding to the final cold rolling state of the Cu-Ti alloy in the implementation process of comparative example 1;
FIG. 4 shows the change of hardness and conductivity of Cu-Ti-La alloy in the implementation process of comparative example 2;
FIG. 5 is a comparison of the hardness and conductivity change rules of the Cu-Ti alloy during the implementation of comparative example 1 and example 1;
FIG. 6 is a metallographic structure of a Cu-Ti alloy in a final ultralow temperature deep cold rolled state in the implementation process of the embodiment 1;
FIG. 7 is a comparison of the hardness and conductivity change rules of the Cu-Ti-La alloys in the implementation of comparative example 2 and example 2.
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.
Claims (5)
1. A method for effectively improving the strength and conductivity of an alloy is characterized in that the alloy is Cu-Ti, and the alloy does not contain other elements; the method comprises the following steps:
(1) Vacuum smelting to prepare alloy cast ingots;
(2) Homogenizing heat treatment: the temperature is 750-850 ℃ and the time is 15-30h;
(3) Low temperature hot rolling: the initial rolling temperature is 700-780 ℃, the heat preservation time is 0.1-2h, and the deformation is 45-90%;
(4) Multiple circulation ultra-low temperature deep cold rolling deformation: 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%;
(5) Short-time solution quenching treatment: the solid solution temperature is 750-850 ℃, the solid solution time is 1-3h, and the quenching mode is water quenching;
(6) Low-temperature short-time pre-ageing treatment: the temperature is 350-430 ℃, the time is 0.7-3h, and the heating rate is more than 6 ℃/s;
(7) Multiple circulation ultra-low temperature deep cold rolling deformation: 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 ensure that the total deformation of the alloy plate reaches 60-85 percent;
(8) Isothermal aging treatment: the temperature is 350-430 ℃ and the time is 0.5-10h.
2. The method for effectively improving the strength and the electrical conductivity of an alloy according to claim 1, wherein the low-temperature hot rolling process of the step (3) is as follows: 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 ℃.
3. The method for effectively improving the strength and the electrical conductivity of an alloy according to claim 1, wherein the short-time solution quenching treatment process in the step (5) is as follows: 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.
4. The method for effectively improving the strength and the electrical conductivity of an alloy according to claim 1, wherein the low-temperature short-time pre-aging treatment process in the step (6) is as follows: 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.
5. The method for effectively increasing the strength and the electrical conductivity of an alloy according to claim 1, wherein the isothermal aging process of step (8) is as follows: 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.
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