Ultrahigh-strength TiB2 / Al-Mg-Si conductor material and preparation method thereof

Abstract

The application discloses an ultrahigh-strength TiB2 / Al-Mg-Si conductor material and a preparation method thereof. According to mass percentage, the conductor material comprises Ti 1.1-1.6%, B 0.4-0.9%, Mg 0.6-0.9%, Si 0.6-0.9%, Fe impurity content less than 0.2%, other impurity content less than 0.1%, and the balance of Al. The preparation method of the conductor material comprises the following steps: step 1, melting: remelting and diluting Al-TiB2 precursors to prepare TiB2 / Al-Mg-Si porcelain aluminum alloy ingot; step 2, homogenizing annealing; step 3, hot extrusion deformation to obtain an extruded rod; step 4, solid solution treatment; step 5, artificial aging; step 6, room temperature drawing; and step 7, low-temperature artificial aging to obtain the ultrahigh-strength TiB2 / Al-Mg-Si conductor material. The preparation method is closely combined with the traditional aluminum conductor material preparation process, is easy to popularize and can be mass-produced. The ultrahigh-strength TiB2 / Al-Mg-Si conductor material has excellent mechanical properties and electrical conductivity, the elastic modulus is 73.0-73.3 GPa, the tensile strength is 404.2-409.4 MPa, and the conductivity is 56.3-56.5% IACS.

Description

TECHNICAL FIELD

[0001] The present application discloses a kind of super high-strength TiB2 / Al-Mg-Si conductor material and preparation method thereof. BACKGROUND

[0002] Large capacity, long distance, large span overhead transmission conductor is the main carrier of long distance power transmission, and high-performance aluminum conductor material has become an urgent need for large span overhead transmission line construction. Overhead transmission conductor not only needs high enough conductivity to reduce line loss, but also needs enough strength to withstand self weight and resist severe service conditions, such as wind load, icing and atmospheric environmental corrosion, which seriously threaten the safe operation of power system.

[0003] Full aluminum alloy strand generally uses Al-Mg-Si alloy as conductor material, Al-Mg-Si alloy wire not only has good conductivity and high tensile strength, but also has good corrosion resistance and welding performance, with a series of advantages such as large capacity, light weight and good sag performance. Large-scale production and application of Al-Mg-Si alloy wire puts very high requirements on continuous casting and rolling, drawing, heat treatment and artificial aging process equipment. Its mechanical properties and conductivity are very sensitive to work hardening, solid solution and aging, so the production process window of high-performance Al-Mg-Si aluminum alloy wire is very narrow.

[0004] In summary, it is an urgent problem to develop a production process of high-performance Al-Mg-Si aluminum alloy wire. SUMMARY

[0005] Therefore, the present application provides a kind of super high-strength TiB2 / Al-Mg-Si conductor material and preparation method thereof, to obtain a kind of super high-strength TiB2 / Al-Mg-Si conductor material with higher elastic modulus, strength and conductivity.

[0006] The technical scheme provided by the present application is specifically a kind of super high-strength TiB2 / Al-Mg-Si conductor material, according to mass percentage content, comprising:

[0007] Ti 1.1-1.6%, B 0.4-0.9%, Mg 0.6-0.9%, Si 0.6-0.9%, Fe impurity content is less than 0.2%, and the content of each other impurity is less than 0.1%, and the balance is Al.

[0008] The present application also provides a preparation method of the above-mentioned conductor material, comprising:

[0009] Step 1: smelting: using Al-TiB2 precursor, pure aluminum, Al-Mg intermediate alloy and Al-Si intermediate alloy for batching, remelting and diluting the Al-TiB2 precursor to prepare TiB2 / Al-Mg-Si duralumin alloy ingot;

[0010] Step 2: homogenizing annealing of the TiB2 / Al-Mg-Si duralumin alloy ingot;

[0011] Step 3: hot extrusion deformation of the annealed TiB2 / Al-Mg-Si duralumin alloy ingot to obtain an extruded rod;

[0012] Step 4: solid solution treatment of the extruded rod;

[0013] Step 5: artificial aging of the aluminum rod after solid solution treatment;

[0014] Step 6: room temperature drawing of the aluminum rod after artificial aging;

[0015] Step 7: low-temperature artificial aging or natural aging of the room temperature drawn aluminum wire to obtain an ultra-high strength TiB2 / Al-Mg-Si conductor material.

[0016] Preferably, in step 1, using Al-TiB2 precursor, pure aluminum, Al-Mg intermediate alloy and Al-Si intermediate alloy for batching, including: the mass fraction of TiB2 particles in the Al-TiB2 precursor is 5-7%, the B / Ti stoichiometric ratio is 2.0-2.1; the mass fractions of the Al-Mg intermediate alloy and the Al-Si intermediate alloy are 7-9% and 5-6%, respectively; the mass fraction of Mg element in the Al-Mg intermediate alloy is 9-11%, and the mass fraction of Si element in the Al-Si intermediate alloy is 11-13%.

[0017] Preferably, in step 1, the step 1 remelts and dilutes the Al-TiB2 precursor to prepare a TiB2 / Al-Mg-Si duralumin alloy ingot:

[0018] a, melt and heat the Al-TiB2 precursor and pure aluminum to 720-750℃, stir to fully mix and react, add Al-Mg intermediate alloy and Al-Si intermediate alloy for alloying to obtain a melt;

[0019] b, using high-purity argon to refine the melt;

[0020] c, pouring the melt into a steel mold to obtain a TiB2 / Al-Mg-Si duralumin alloy ingot at a pouring temperature of 720-750℃.

[0021] Preferably, in step 2, the TiB2 / Al-Mg-Si duralumin alloy is subjected to homogenization annealing, including: 540-570℃ for 12-24h, cooling to 250-300℃, air cooling.

[0022] Preferably, in step 3, the ingot is preheated to 350-380℃ before being subjected to hot extrusion deformation, the extrusion speed is 0.2-0.5m / min, and the extrusion ratio is 1:18-25.

[0023] Preferably, in step 4, the extruded rod is subjected to solid solution treatment, the solid solution temperature is 550-570℃, the solid solution time is 30-60min, and the room temperature water quenching is performed.

[0024] Preferably, in step 5, the artificial aging temperature is 170-190℃, and the aging time is 1-8h.

[0025] Preferably, the aluminum rod after artificial aging is subjected to room temperature drawing, the deformation amount is 60-99%, and the drawing speed is 10-20m / min.

[0026] Preferably, the aluminum conductor drawn at room temperature is subjected to low-temperature artificial aging, the aging temperature is 130-150℃, and the aging time is 1-8h.

[0027] The super-high-strength TiB2 / Al-Mg-Si conductor material and the preparation method thereof provided by the application have simple process, are easy to popularize, and can be mass-produced. TiB2 / Al-Mg-Si composite material is prepared by adding TiB2 hard ceramic particles to Al-Mg-Si aluminum alloy, the elastic modulus of the material is improved, the structural stiffness of the conductor is improved, and more excellent sag characteristics are obtained. The TiB2 particles can further improve the strength of the Al-Mg-Si aluminum alloy from the perspective of the reinforcing phase, and appropriate composition control can make the addition of TiB2 ceramic particles hardly damage the electrical conductivity of the conductor.

[0028] The super-high-strength TiB2 / Al-Mg-Si conductor material (GB / T 23308-2009) prepared by the method has more excellent physical and chemical properties, higher elastic modulus, strength and electrical conductivity, wherein the elastic modulus is 73.0-73.3GPa, the tensile strength is 404.2-409.4MPa, and the electrical conductivity is 56.3-56.5% IACS.

[0029] The super-high-strength TiB2 / Al-Mg-Si conductor material provided by the application can be used in overhead transmission conductor, conductor material of high-strength and high-conductivity all-aluminum alloy stranded wire, and core material of aluminum alloy core stranded wire. The specific application scenarios can be new long-distance power transmission energy-saving lines, power transmission lines in heavy pollution and coastal areas, icing areas and other special geographical conditions, ultra-high voltage AC / DC lines and large-span power transmission lines.

[0030] It is to be understood that both the foregoing general description and the following detailed description are exemplary and explanatory only and are not restrictive of the disclosure. BRIEF DESCRIPTION OF DRAWINGS

[0031] The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the present application and serve to explain the principles of the present application, in which, like reference numerals designate corresponding parts throughout the several views.

[0032] In order to more clearly illustrate the technical solutions of the embodiments of the present application or the prior art, the accompanying drawings needed to be used in the embodiments or prior art description will be briefly introduced as follows. Obviously, for those skilled in the field, under the premise of no creative labor, other drawings can also be obtained based on these drawings.

[0033] Fig. 1 Schematic diagram of TiB2 / Al-Mg-Si conductor material prepared by different process paths in the embodiments of the present application;

[0034] Fig. 2 Strength and electrical conductivity of TiB2 / Al-Mg-Si conductor material prepared by different process paths in the embodiments of the present application;

[0035] Fig. 3 Dislocation configuration, precipitate distribution and size statistical results of TiB2 / Al-Mg-Si conductor material prepared by different process paths in Example 1 of the present application, wherein (a) is Comparative Example 1, (b) is Comparative Example 2, (c) is Comparative Example 3, (d) is Comparative Example 4, (e) is Example 1, and (f) is Example 2. DETAILED DESCRIPTION

[0036] The exemplary embodiments will be described in detail herein with reference to the attached drawings. In the following description, unless otherwise indicated, like numbers in the attached drawings refer to the same or similar elements. The embodiments described in the following exemplary embodiments are not meant to represent all embodiments consistent with the present application. Rather, they are merely examples of methods consistent with some aspects of the present application as detailed in the appended claims.

[0037] It should be noted that:

[0038] Unless otherwise specified, the units used in the present specification are international standard units, and the numerical values and numerical value ranges appearing in the present application should be understood as including systematic errors that are inevitable in industrial production.

[0039] In the present specification, the numerical value range represented by "numerical value A ~ numerical value B" refers to a range including the end point numerical values A and B.

[0040] In the present specification, the numerical range indicated using "above" or "below" means a numerical range including the number.

[0041] In the present specification, the meaning indicated using "may" includes both the meaning of performing a certain process and the meaning of not performing a certain process.

[0042] In the present specification, when "room temperature" is used, the temperature can be 15-25℃.

[0043] In the present specification, when the manufacturer of a reagent or an apparatus is not indicated, it is a general product that can be obtained through commercial purchase.

[0044] In view of the problems that the production process of the Al-Mg-Si aluminum alloy conductor is complex, and the market has higher and higher requirements for the sag characteristics, strength and electrical conductivity of the conductor, the present embodiment provides an ultrahigh-strength TiB2 / Al-Mg-Si conductor material, the composition of the TiB2 / Al-Mg-Si conductor material is 1.37% Ti, 0.63% B, 0.75% Mg, 0.75% Si, the content of Fe impurities is less than 0.1%, the content of each other impurity is less than 0.1%, and the balance is aluminum.

[0045] The present embodiment also provides a preparation method of the above material, step 1: smelting: using Al-TiB2 precursor, pure aluminum, Al-Mg intermediate alloy and Al-Si intermediate alloy for batching, remelting and diluting the Al-TiB2 precursor to prepare a TiB2 / Al-Mg-Si ceramic aluminum alloy ingot;

[0046] The TiB2 hard ceramic phase is introduced by smelting to improve the solidification structure, which specifically includes the following steps: melting and heating the Al-TiB2 precursor and pure aluminum to 720-750℃ in a crucible smelting furnace, stirring to fully mix and react, adding Al-Mg intermediate alloy and Al-Si intermediate alloy for alloying; b, using high-purity argon to refine the melt; c, pouring into a steel mold, the pouring temperature is 720-750℃;

[0047] The mass fraction of TiB2 particles in the Al-TiB2 precursor is 5-7%, and the stoichiometric ratio of B / Ti is 2.0-2.1.

[0048] The mass fraction of Mg element in the Al-Mg intermediate alloy is 9-11%, preferably 10%(Al-10%Mg).

[0049] The mass fraction of Si element in the Al-Si intermediate alloy is 11-13%, preferably 12%(Al-12%Mg).

[0050] The mass fraction of the Al-Mg intermediate alloy and the Al-Si intermediate alloy is 7-9% and 5-6%, respectively.

[0051] Step 2: homogenization annealing of the TiB2 / Al-Mg-Si ceramic duralumin alloy ingot; macrosegregation is eliminated through homogenization annealing;

[0052] Specifically, the homogenization annealing: the ingot is subjected to homogenization annealing, 540-570℃ for 12-24h, furnace cooling to 250-300℃, and air cooling; further preferably, the homogenization annealing: the ingot is subjected to homogenization annealing in a muffle furnace, 560-570℃ for 12-15h, furnace cooling to 270-300℃, and air cooling;

[0053] Step 3: hot extrusion deformation of the annealed TiB2 / Al-Mg-Si ceramic duralumin alloy ingot to obtain an extruded rod; the extrusion texture is regulated by the ceramic phase through hot extrusion;

[0054] Specifically, the hot extrusion deformation: the ingot is preheated to 350-380℃ and then subjected to hot extrusion deformation to form an aluminum rod, the extrusion speed is 0.2-0.5m / min, and the extrusion ratio is 1:18-25;

[0055] Step 4: solid solution treatment of the extruded rod; high-temperature short-time solid solution treatment is combined with the ceramic phase to avoid deterioration of the structure;

[0056] Step 5: artificial aging of the aluminum rod after solid solution treatment; a dispersed precipitate phase is formed through artificial aging;

[0057] Specifically, the extruded rod is subjected to solid solution treatment, the solid solution temperature is 550-570℃, the solid solution time is 30-60min, and the room temperature water quenching is performed; preferably, the solid solution temperature is 555-565℃, and the solid solution time is 30-45min;

[0058] The artificial aging: the aluminum rod after solid solution treatment is subjected to artificial aging, the aging temperature is 170-190℃, and the aging time is 1-8h; preferably, the artificial aging, the aging temperature is 170-180℃, and the aging time is 6-8h;

[0059] Step 6: room temperature drawing of the aluminum rod after artificial aging; the interaction of the precipitate phase, the ceramic phase and dislocations significantly improves the strength; the aluminum rod after artificial aging is subjected to room temperature drawing, the deformation amount is 60-99%, and the drawing speed is 10-20m / min; preferably, the deformation amount is 90-99%, and the drawing speed is 15-20m / min;

[0060] Step 7: low-temperature artificial aging or natural aging of the room-temperature drawn aluminum wire to obtain the ultra-high-strength TiB2 / Al-Mg-Si conductor material. The low-temperature artificial aging treatment uses high-density uniformly distributed dislocations to accelerate the desorption of residual solid solution atoms and thereby improve the electrical conductivity;

[0061] wherein the low-temperature artificial aging has an aging temperature of 130-150℃ and an aging time of 1-5h. Preferably, the aging temperature is 140-150℃ and the aging time is 3-5h, and the aging temperature and aging time of the low-temperature artificial aging need to be strictly controlled to prevent serious recovery of dislocations and serious coarsening of precipitated phases.

[0062] The application will be further explained and described in conjunction with specific examples, but is not used to limit the protection scope of the application.

[0063] Example 1

[0064] The preparation method of the ultra-high-strength TiB2 / Al-Mg-Si conductor material (optimized T9+3h) comprises the following steps:

[0065] Step 1: batching 1) Al-6%TiB2 precursor (aluminum base matrix containing TiB2 particles with a mass fraction of 6%), the contents of Ti element and B element are 4.14% and 1.88% respectively, and the mass fraction of the precursor added is 33.3%;

[0066] 2) Al-10%Mg intermediate alloy, the added mass fraction is 8.88%;

[0067] 3) Al-12%Si intermediate alloy, the added mass fraction is 5.03%;

[0068] 4) industrial pure aluminum (purity >99.7%), the mass fraction is 52.79%;

[0069] 5) the composition of the TiB2 / Al-Mg-Si conductor material is 1.37%Ti, 0.63%B, 0.75%Mg, 0.75%Si, the Fe impurity content is less than 0.1%, and the content of each other impurity is less than 0.1%.

[0070] melting: 1) melt and heat the Al-6%TiB2 precursor and the industrial pure aluminum to 730℃ in a crucible melting furnace, and stir to fully mix and react them;

[0071] 2) add Al-10%Mg and Al-12%Si intermediate alloys for alloying;

[0072] 3) use high-purity argon to refine the melt for 5min;

[0073] 4) pour the melt into a steel mold, and the pouring temperature is 720℃.

[0074] Step 2: homogenization annealing: homogenization annealing of the ingot was performed using a muffle furnace, 570 °C for 12 h, furnace cooling to 300 °C, air cooling;

[0075] Step 3: hot extrusion deformation: the ingot was preheated to 380 °C using a muffle furnace and then subjected to hot extrusion deformation, extrusion speed 0.2 m / min, extrusion ratio 1:20;

[0076] Step 4: solution treatment: solution treatment of the extruded rod was performed using a muffle furnace, solution temperature 560 °C, solution time 30 min, water quenching at room temperature;

[0077] Step 5: artificial aging: artificial aging of the aluminum rod of step (5) was performed using an aging furnace, aging temperature 170 °C, aging time 7 h;

[0078] Step 6: room temperature drawing: room temperature drawing of the aluminum rod of step (6) was performed using a drawing machine, deformation 90%, drawing speed 10 m / min;

[0079] Step 7: low-temperature artificial aging: low-temperature artificial aging of the aluminum conductor material wire of step (7) was performed using an aging furnace, aging temperature 150 °C, aging time 3 h.

[0080] Example 2

[0081] This comparative example discloses a TiB2 / Al-Mg-Si conductor material (T9+8h), comprising the following steps:

[0082] Step 1: batching: 1) Al-6% TiB2 precursor (aluminum base matrix containing TiB2 particles with a mass fraction of 6%), the contents of Ti element and B element are 4.14% and 1.88% respectively, the mass fraction of the precursor added is 33.3%; 2) Al-10% Mg intermediate alloy, the mass fraction added is 8.88%; 3) Al-12% Si intermediate alloy, the mass fraction added is 5.03%; 4) industrial pure aluminum (purity > 99.7%), the mass fraction is 52.79%; 5) the composition of the TiB2 / Al-Mg-Si conductor material is 1.37% Ti, 0.63% B, 0.75% Mg, 0.75% Si, the content of Fe impurities is less than 0.1%, and the content of each other impurity is less than 0.1%.

[0083] Melting: 1) the Al-6% TiB2 precursor and the industrial pure aluminum were melted and heated to 730 °C in a crucible melting furnace, and stirred to fully mix and react; 2) Al-10% Mg and Al-12% Si intermediate alloys were added for alloying; 3) high-purity argon was used to refine the melt for 5 min; 4) the melt was poured into a steel mold, and the pouring temperature was 720 °C.

[0084] Step 2: homogenization annealing: homogenization annealing of the ingot was carried out using a muffle furnace, 570℃ for 12h, furnace cooling to 300℃, air cooling;

[0085] Step 3: hot extrusion deformation: the ingot was preheated to 380℃ using a muffle furnace and then hot extrusion deformation was carried out, the extrusion speed was 0.2m / min, and the extrusion ratio was 1:20;

[0086] Step 4: solution treatment: solution treatment of the extruded rod was carried out using a muffle furnace, the solution temperature was 560℃, the solution time was 30min, and water quenching at room temperature;

[0087] Step 5: artificial aging: artificial aging of the aluminum rod of step (5) was carried out using an aging furnace, the aging temperature was 170℃, and the aging time was 7h;

[0088] Step 6: room temperature drawing: room temperature drawing of the aluminum rod of step (6) was carried out using a drawing machine, the deformation was 90%, and the drawing speed was 10m / min;

[0089] Step 7: low-temperature artificial aging: low-temperature artificial aging of the aluminum conductor material wire of step (7) was carried out using an aging furnace, the aging temperature was 150℃, and the aging time was 8h.

[0090] Comparative Example 1

[0091] This comparative example discloses a preparation method of TiB2 / Al-Mg-Si conductor material (T6), comprising the following steps:

[0092] Step (1) batching: 1) Al-6%TiB2 precursor (aluminum base matrix containing 6% mass fraction of TiB2 particles), the contents of Ti element and B element are 4.14% and 1.88% respectively, and the mass fraction of the precursor added is 33.3%;

[0093] 2) Al-10%Mg intermediate alloy, the mass fraction added is 8.88%;

[0094] 3) Al-12%Si intermediate alloy, the mass fraction added is 5.03%;

[0095] 4) industrial pure aluminum (purity >99.7%), mass fraction is 52.79%;

[0096] 5) the composition of the TiB2 / Al-Mg-Si conductor material is 1.37%Ti, 0.63%B, 0.75%Mg, 0.75%Si, the content of Fe impurities is less than 0.1%, and the content of each other impurity is less than 0.1%.

[0097] Step (2) Melting: 1) Al-6%TiB2 precursor and commercial pure aluminum were melted and heated to 730℃ in a crucible melting furnace, and stirred to fully mix and react;

[0098] 2) Al-10%Mg and Al-12%Si intermediate alloy were added for alloying;

[0099] 3) High purity argon was used to refine the melt for 5 min;

[0100] 4) The melt was poured into a steel mold at a pouring temperature of 720℃.

[0101] Step (3) Homogenization annealing: The ingot was homogenization annealed in a muffle furnace at 570℃ for 12 h, furnace cooled to 300℃, and air cooled;

[0102] Step (4) Hot extrusion deformation: The ingot was preheated to 380℃ in a muffle furnace and then hot extruded, with an extrusion speed of 0.2 m / min and an extrusion ratio of 1:20;

[0103] Step (5) Solution treatment: The extruded rod was solution treated in a muffle furnace at a solution temperature of 560℃ for 30 min, and then water quenched at room temperature;

[0104] Step (6) Artificial aging: The aluminum rod of step (5) was artificially aged in an aging furnace at an aging temperature of 170℃ for 7 h.

[0105] Comparative Example 2

[0106] This comparative example discloses a preparation method of TiB2 / Al-Mg-Si conductor material (T3), comprising the following steps:

[0107] Steps (1)-(5) are exactly the same as Comparative Example 1;

[0108] Step (6) Room temperature drawing: The aluminum rod of step (5) was drawn at room temperature using a drawing machine, with a deformation of 90% and a drawing speed of 10 m / min;

[0109] Step (7) Natural aging: The aluminum conductor wire of step (6) was placed in room temperature for natural aging for 7 days.

[0110] Comparative Example 3

[0111] This comparative example 3 discloses a preparation method of TiB2 / Al-Mg-Si conductor material (T8), comprising the following steps:

[0112] Steps (1)-(6) are exactly the same as Comparative Example 2;

[0113] Step (7) Artificial aging: The aluminum conductor material of step (6) was artificially aged in an aging furnace, the aging temperature was 170 °C, and the aging time was 4 h.

[0114] Comparative Example 4

[0115] This comparative example discloses the preparation method of TiB2 / Al-Mg-Si conductor material (T9), including the following steps:

[0116] Steps (1)-(5) are exactly the same as Comparative Example 1;

[0117] Step (6) Artificial aging: The aluminum rod of step (5) was artificially aged in an aging furnace, the aging temperature was 170 °C, and the aging time was 7 h;

[0118] Step (7) Room temperature drawing: The aluminum rod of step (6) was drawn at room temperature by a drawing machine, the deformation was 90%, and the drawing speed was 10 m / min;

[0119] Step (8) Natural aging: The aluminum conductor material of step (7) was placed in room temperature for natural aging for 7 days.

[0120] In combination with Comparative Examples 1-4 and Examples 1 and 2, the process flow simplified schematic diagram, tensile strength and electrical conductivity, and microstructure characterization are shown in Table 1. Figs. 1-3

[0121] Fig. 1 is a schematic diagram of TiB2 / Al-Mg-Si conductor material prepared by different process paths.

[0122] Fig. 2 is the strength and electrical conductivity of TiB2 / Al-Mg-Si conductor material prepared by different process paths. Comparative Example 2 T3 state and Comparative Example 3 T8 state are respectively natural aging and artificial aging after room temperature deformation of the supersaturated solid solution.

[0123] The tensile strength obtained by T3 state is 354.5 MPa, and the electrical conductivity is 43.9% IACS.

[0124] The tensile strength obtained by T8 state is 335.0 MPa, and the electrical conductivity is 50.3% IACS.

[0125] The room temperature deformation on the basis of Comparative Example 1 T6 state greatly improves the strength of the material, wherein the tensile strength obtained by only natural aging after room temperature deformation, i.e. T9 process, is increased from 350.5 MPa of T6 state to 454.9 MPa, increased by 29.8%. The obtained electrical conductivity is increased from 46.1% IACS of T6 state to 50.7% IACS.

[0126] ​In Example 1, after 3 hours of low-temperature artificial aging, the tensile strength decreased from 454.9 MPa in the T9 state to 427.4 MPa. The electrical conductivity, however, was significantly improved, increasing from 50.7% IACS to 55.5% IACS.

[0127] In Example 2, after 8 hours of low-temperature artificial aging, the tensile strength decreased from 427.4 MPa after 3 hours to 406.8 MPa, while the conductivity increased from 55.5% IACS after 3 hours to 56.4% IACS.

[0128] Compared to the T8 process for preparing traditional Al-Mg-Si aluminum alloy conductors, the TiB2 / Al-Mg-Si conductor material prepared by the process in Example 2 exhibits significantly improved tensile strength and excellent conductivity.

[0129] Fig. 3 These are the dislocation configurations, precipitate distributions, and size statistics of TiB2 / Al-Mg-Si conductor materials prepared using different process routes. Transmission electron microscopy analysis shows that the tilt axis is the

[001] zone axis of the matrix. Fig. 3 (a) shows the bright-field image and precipitate size statistics of the T6 state in Control Example 1. Only sporadic dislocation lines exist in the matrix, and the dislocation density is low. Along <100> The needle-like precipitates are uniformly and diffusely distributed in the matrix, with a precipitate size of approximately 3.3 nm.

[0130] Fig. 3 Images (b) and (c) correspond to the bright-field images of the T3 and T8 states of Control Example 2 and Control Example 3, respectively. The results show that after solution treatment and room-temperature deformation, dislocations multiply under the interaction with the solid-solution atoms, entanglement occurs between dislocations to form dislocation walls, and subgrains are formed. Natural aging alone after room-temperature deformation of the supersaturated solid solution cannot fully exfoliate the solid-solution atoms; therefore, no precipitated phase was observed in the matrix. When the supersaturated solid solution is artificially aged after room-temperature deformation, the solid-solution atoms fully exfoliate under the promoting effect of dislocations, and severe dislocation recovery occurs, resulting in a significant decrease in dislocation density. Due to the accelerating effect of dislocations during artificial aging precipitation, the resulting precipitated phase is unevenly distributed, large in size (approximately 5.3 nm), and exhibits an uneven size distribution.

[0131] Fig. 3 (d) shows the bright-field image and precipitate size statistics of the T9 state in Comparative Example 4. After room temperature deformation based on the T6 state, the dislocation density of the T9 state was greatly increased through the strong interaction between the precipitate and the dislocation, while the precipitate size remained unchanged at approximately 3.0 nm.

[0132] contrast Fig. 3From (c) and (d), compared with the T8 process which deforms the supersaturated solid solution at room temperature, the T9 process deforms the matrix of dispersed precipitates at room temperature, the precipitates strongly pin the dislocations, so that the dislocations cannot slide over a large range, and the entanglement of dislocations to form dislocation walls is rare, so that the distribution of dislocations is more uniform, and the dislocation density is higher.

[0133] Fig. 3 (e) and (f) are the bright field images and the size statistics of precipitates of the T9 / 3h and T9 / 8h processes, respectively. After the low-temperature artificial aging for 3h, the distribution of dislocations, the dislocation density and the size of precipitates of Example 1 do not change significantly, and the uniform distribution of dislocations, the high dislocation density and the dispersed fine precipitates are still maintained. The dislocations do not significantly recover, and the precipitates do not significantly coarsen, so that the mechanical properties of the T9 state do not significantly decrease. However, the electrical conductivity is significantly improved, which means that the solid solution atoms remaining in the matrix in the T6 state are fully precipitated during the low-temperature artificial aging, reducing the scattering of free moving electrons.

[0134] After the low-temperature artificial aging for 8h, the dislocations of Example 2 significantly recover. However, compared with the T8 state, the matrix still retains a high density of dislocations. The precipitates also coarsen to a certain extent, about 5.0nm, and the distribution of the precipitates changes from dispersed to uneven.

[0135] Other embodiments of the application will be apparent to those skilled in the art from consideration of the specification and practice of the application disclosed herein. It is intended that the specification and examples be considered as exemplary only, with the true scope and spirit of the application being indicated by the following claims.

[0136] It should be understood that the application is not limited to the embodiments described above, and various modifications and changes can be made without departing from the scope of the application. The scope of the application is only limited by the appended claims.

Claims

1. A method for preparing an ultra-high strength TiB2 / Al-Mg-Si conductor material, characterized in that, The ultra-high strength TiB2 / Al-Mg-Si conductor material comprises, by weight percentage: Ti 1.1~1.6%, B 0.4~0.9%, Mg 0.6~0.9%, Si 0.6~0.9%, Fe impurity content less than 0.2%, each of the other impurities content less than 0.1%, balance Al; The preparation method of the ultra-high strength TiB2 / Al-Mg-Si conductor material includes: Step 1: Melting: Using Al-TiB2 precursor, pure aluminum, Al-Mg master alloy and Al-Si master alloy as raw materials, the Al-TiB2 precursor is remelted and diluted to prepare TiB2 / Al-Mg-Si ceramic-coated aluminum alloy ingots. Step 2: Homogenize the TiB2 / Al-Mg-Si ceramic-aluminum alloy ingot; Step 3: The annealed TiB2 / Al-Mg-Si ceramic-aluminum alloy ingot is hot-extruded to obtain an extrusion bar; Step 4: Solution treatment of the extrusion rod; Step 5: Artificially age the solution-treated aluminum rod; the artificial aging temperature is 170~190℃, and the aging time is 1~8 h; Step 6: Perform room temperature drawing on the artificially aged aluminum rod; Step 7: Perform low-temperature artificial aging on the aluminum wire drawn at room temperature to obtain ultra-high strength TiB2 / Al-Mg-Si conductor material; The aluminum rods after artificial aging were drawn at room temperature, with a deformation of 60-99% and a drawing speed of 10-20 m / min. Aluminum wires drawn at room temperature are subjected to low-temperature artificial aging at an aging temperature of 130~150℃ for 1~8 hours.

2. The preparation method of the ultra-high strength TiB2 / Al-Mg-Si conductor material according to claim 1, characterized in that, In step 1, Al-TiB2 precursor, pure aluminum, Al-Mg master alloy, and Al-Si master alloy are used for batching, including: the mass fraction of TiB2 particles in the Al-TiB2 precursor is 5~7%, and the B / Ti stoichiometric ratio is 2.0~2.1; the mass fractions of Al-Mg master alloy and Al-Si master alloy added are 7~9% and 5~6%, respectively; the mass fraction of Mg element in the Al-Mg master alloy is 9~11%, and the mass fraction of Si element in the Al-Si master alloy is 11~13%.

3. The preparation method of the ultra-high strength TiB2 / Al-Mg-Si conductor material according to claim 1, characterized in that, In step 1, the Al-TiB2 precursor is remelted and diluted to prepare TiB2 / Al-Mg-Si ceramic-aluminum alloy ingots: a. Melt the Al-TiB2 precursor and pure aluminum and heat to 720~750℃, stir to make them fully mixed and react, add Al-Mg master alloy and Al-Si master alloy to alloy, and obtain the melt. b. Refining the melt using high-purity argon gas; c. Pour the melt into a steel mold at a pouring temperature of 720~750℃ to obtain TiB2 / Al-Mg-Si ceramic-aluminum alloy ingots.

4. The preparation method of the ultra-high strength TiB2 / Al-Mg-Si conductor material according to claim 1, characterized in that, In step 2, the TiB2 / Al-Mg-Si ceramic-aluminum alloy is subjected to homogenization annealing, including: holding at 540~570℃ for 12~24h, cooling to 250~300℃, and air cooling.

5. The method for preparing the ultra-high strength TiB2 / Al-Mg-Si conductor material according to claim 1, characterized in that, In step 3, the ingot is preheated to 350~380℃ and then subjected to hot extrusion deformation. The extrusion speed is 0.2~0.5 m / min and the extrusion ratio is 1:18~25.

6. The method for preparing the ultra-high strength TiB2 / Al-Mg-Si conductor material according to claim 1, characterized in that, In step 4, the extrusion rod is subjected to solution treatment at a temperature of 550~570℃ for 30~60min, followed by water quenching at room temperature.

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