CN115595459A - Preparation method of high-strength high-conductivity aluminum alloy monofilament and aluminum alloy monofilament - Google Patents

Preparation method of high-strength high-conductivity aluminum alloy monofilament and aluminum alloy monofilament Download PDF

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CN115595459A
CN115595459A CN202211138996.3A CN202211138996A CN115595459A CN 115595459 A CN115595459 A CN 115595459A CN 202211138996 A CN202211138996 A CN 202211138996A CN 115595459 A CN115595459 A CN 115595459A
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aluminum
aluminum alloy
percent
alloy monofilament
monofilament
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CN115595459B (en
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白清领
陆伟
薛驰
王鑫寓
徐达惠
顾志成
周峰
单小龙
曹天垚
钱秀勇
徐一峰
缪姚军
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Shanghai Zhongtian Aluminium Wire Co ltd
Jiangsu Zhongtian Technology Co Ltd
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Shanghai Zhongtian Aluminium Wire Co ltd
Jiangsu Zhongtian Technology Co Ltd
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    • 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
    • C22C1/026—Alloys based on aluminium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • 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
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Abstract

The application provides a preparation method of a high-strength and high-conductivity aluminum alloy monofilament and the aluminum alloy monofilament prepared by the method, wherein the aluminum alloy monofilament consists of the following components in percentage by mass: 0.5 to 0.8 percent of Mg, 0.3 to 0.5 percent of Si, 0.1 to 0.5 percent of Zn, less than or equal to 0.15 percent of Fe, 0.02 to 0.05 percent of RE, 0.001 to 0.01 percent of B, less than or equal to 0.02 percent of Cr + Mn + V + Ti, and the balance of Al and other inevitable impurity elements, wherein the content of each element in the other inevitable impurity elements is less than or equal to0.005 percent and less than or equal to 0.02 percent of total weight, wherein RE is La/Ce mixed rare earth elements with equal proportion. The aluminum alloy rod material is pre-aged, so that Mg, si, zn and other elements dissolved in aluminum phase are precipitated in the form of clusters (GP zone), adverse effects on the mechanical properties of the alloy caused by natural aging are avoided, the clusters precipitated by pre-aging provide nucleation points for subsequent artificial aging, and the alloy elements are beta' (Mg) during artificial aging 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) And the metastable strengthening phase is fully precipitated to form a dispersion strengthening effect to improve the tensile strength of the aluminum alloy monofilament.

Description

Preparation method of high-strength high-conductivity aluminum alloy monofilament and aluminum alloy monofilament
Technical Field
The application relates to the field of power transmission lines, in particular to a preparation method of a high-strength high-conductivity aluminum alloy monofilament and the aluminum alloy monofilament.
Background
China has built the longest overhead conductor transmission line in the world and becomes an energy source aorta for promoting national economic development, but the existing long-distance and large-span overhead transmission line mainly consists of common steel-cored aluminum stranded wires and has larger electric energy loss. The energy-saving lead replaces a steel-cored aluminum strand to greatly reduce the electric energy loss of the power transmission line, and becomes an important development trend in the field of overhead power transmission. The national standard high-strength aluminum alloy wire has the strength of 315 to 325MPa and the electric conductivity of 52.5 percent IACS, has no remarkable energy-saving and consumption-reducing effects, and has great economic and social benefits when alloy materials with higher strength and electric conductivity are continuously developed. The strength and the conductivity of the Al-Mg-Si alloy wire are mutually restricted, and the conductivity is usually obviously reduced when the strength is improved, and vice versa. Improvement of the strength and conductivity of the alloy has been achieved by experience improvement by domestic technicians, but there is still room for further improvement.
At present, the domestic aluminum alloy wire is mainly made of aluminum magnesium silicon alloy, and the production process route is generally smelting → continuous casting and continuous rolling → drawing → aging → stranding. By means of a single Mg 2 The Si phase precipitation strengthening method limits further breakthrough of alloy strength, natural aging in the conventional process also has certain negative influence on the precipitation strengthening effect, and the stranding process can cause damage to the strength and the elongation of finished monofilaments, particularly obviously reduce the elongation of the stranded monofilaments and even be difficult to meet standard requirements.
Disclosure of Invention
The embodiment of the application provides a preparation method of a high-strength high-conductivity aluminum alloy monofilament, which comprises the following steps:
smelting aluminum liquid: adding an aluminum ingot with the purity of more than 99.7 percent, a zinc ingot, aluminum-silicon alloy and aluminum-rare earth alloy into a smelting furnace, heating and melting, pressing the magnesium ingot into molten aluminum, stirring and melting, sampling, carrying out spectral analysis, and controlling the components of a melt to be in a required range;
refining in a furnace: transferring the molten aluminum in the smelting furnace into a refining furnace, adding an aluminum-boron alloy into the molten aluminum for boronizing treatment and fully stirring, and then refining and slagging off the molten aluminum in the furnace;
and (3) online refining: after casting is started, a rotary blowing degassing box and double-stage foamed ceramic filtering are used for carrying out online degassing and filtering impurity removal on the melt, the hydrogen content in the treated melt is less than or equal to 0.12ml/100g, and more than 80% of impurities with the size of more than 5 microns in the melt are removed;
continuous casting and rolling: pouring the aluminum liquid after on-line stirring into a wheel type crystallizer for continuous casting to form a casting blank, and processing the casting blank to obtain a rod material;
pre-aging of the rod material: the aging heating temperature is 100 to 140 ℃, and the heat preservation time is 5 to 10 hours;
drawing: drawing the pre-aged alloy rod on a sliding wire drawing machine, wherein the diameter of the aluminum-magnesium-silicon alloy monofilament after drawing is 2.0-4.5 mm;
stranding: and (3) stranding the aluminum alloy monofilaments by using a frame stranding machine, wherein an automatic control preforming and post-shaping control system is adopted in the stranding process, and the stranding parameters of the lead are accurately controlled. Twisting to obtain an all-aluminum alloy lead;
artificial aging: and (3) carrying out artificial aging treatment on the stranded conductor, wherein the aging process is carried out at the temperature of 150-180 ℃ and the heat preservation time is 6-15 hours.
In one possible embodiment, in the rod material pre-aging, the rod material is pre-aged within 5 hours after being taken off the machine, so that Mg, si, and Zn elements in the aluminum phase are precipitated and form Mg/Si atomic clusters and Mg/Zn atomic clusters.
In one possible embodiment, the artificial aging takes Mg/Si atom clusters and Mg/Zn atom clusters as nucleation points to form beta' (Mg) in the aluminum phase 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) A metastable hardening phase.
In one possible embodiment, in the in-furnace refining, the refining furnace is a 10-ton capacity tilting holding furnace, after the boronizing treatment is started, a furnace bottom electromagnetic stirring device is started to fully stir the melt, and after the molten aluminum is subjected to slagging-off, the temperature is adjusted to 720-730 ℃ for standing treatment.
In one possible embodiment, in the online refining, a rotary blowing type degassing box is adopted to carry out online degassing on the aluminum liquid, high-purity nitrogen is taken as a degassing medium, and the rotating speed of a rotor is 400-500 r/min; and a double-stage foamed ceramic filter plate is adopted to filter the aluminum liquid on line, and the porosity of the double-stage foamed ceramic filter plate is 30/50PPI.
In one possible embodiment, in the continuous casting and rolling, a wheel type crystallizer is used for casting continuous casting billets, and the continuous casting billets are led into a 15-frame three-roll continuous rolling unit after coming out, so that aluminum alloy rod materials with the diameter of 9-12 mm are rolled. During rolling, a casting blank is heated by a medium-frequency heating device, the rolling temperature is controlled to be 520-550 ℃, meanwhile, the preheating temperature of the emulsion is adjusted to be 40-60 ℃, the final rolling temperature is ensured to be more than 350 ℃, and the bar is retracted after online quenching and cooling.
The embodiment of the application also provides an aluminum alloy monofilament, which is prepared by the preparation method of the high-strength and high-conductivity aluminum alloy monofilament, and the aluminum alloy monofilament consists of the following components in percentage by mass: 0.5 to 0.8 percent of Mg, 0.3 to 0.5 percent of Si, 0.1 to 0.5 percent of Zn, less than or equal to 0.15 percent of Fe, 0.02 to 0.05 percent of RE, 0.001 to 0.01 percent of B, less than or equal to 0.02 percent of Cr + Mn + V + Ti, the balance of Al and inevitable other impurity elements, the content of each element in the inevitable other impurity elements is less than or equal to 0.005 percent, and the total amount is less than or equal to 0.02 percent, wherein RE is La/Ce mixed rare earth elements with equal proportion.
In one possible embodiment, RE is added in the form of an Al-RE master alloy.
In one possible embodiment, the aluminum alloy monofilament has a strength of greater than or equal to 340MPa, an electrical conductivity of greater than or equal to 55% IACS, and an elongation of greater than or equal to 5%.
In one possible embodiment, β "(Mg) is present in the aluminum alloy monofilament 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) A metastable hardening phase.
Compared with the prior art, the preparation method of the high-strength high-conductivity aluminum alloy monofilament has the advantages that the aluminum alloy rod is subjected to pre-aging treatment, elements such as Mg, si and Zn are precipitated in the form of clusters, adverse effects on mechanical properties of the alloy caused by natural aging are avoided, and meanwhile, the clusters precipitated by pre-aging provide nucleation points for subsequent artificial aging, so that the alloy elements are subjected to beta' (Mg) during artificial aging 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) And the metastable strengthening phase is fully precipitated to form a dispersion strengthening effect to improve the tensile strength of the aluminum alloy monofilament. Moreover, a metastable strengthening phase containing Zn is introduced into the alloy, so that the strength of the alloy is greatly improved, and the influence of Zn on the conductivity of the alloy is small. And moreover, artificial aging is carried out after stranding, so that the damage of torsional deformation in the stranding process to the strength and the elongation of the single wire is eliminated, and the stranded aluminum alloy wire has better comprehensive performance. The tensile strength of the aluminum alloy monofilament prepared by the preparation method of the high-strength high-conductivity aluminum alloy monofilament is greater than or equal to 340MPa, the electric conductivity of the aluminum alloy monofilament is greater than or equal to 55% IACS, and the elongation of the aluminum alloy monofilament is greater than or equal to 5%.
Drawings
Fig. 1 is a schematic flow chart of a method for preparing a high-strength high-conductivity aluminum alloy monofilament provided in an embodiment of the present application.
The following detailed description will further illustrate the present application in conjunction with the above-described figures.
Detailed Description
The following description refers to the accompanying drawings to more fully describe the present disclosure. There is shown in the drawings exemplary embodiments of the present application. This application may, however, be embodied in many different forms and should not be construed as limited to the exemplary embodiments set forth herein. These exemplary embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the scope of the disclosure to those skilled in the art. Like reference numerals designate identical or similar components.
The terminology used herein is for the purpose of describing particular example embodiments only and is not intended to be limiting of the application. As used herein, the singular forms "a", "an" and "the" are intended to include the plural forms as well, unless the context clearly indicates otherwise. Further, as used herein, "comprises" and/or "comprising" and/or "having," integers, steps, operations, components, and/or components, but does not preclude the presence or addition of one or more other features, regions, integers, steps, operations, components, and/or groups thereof.
Unless otherwise defined, all terms (including technical and scientific terms) used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this application belongs. Furthermore, unless otherwise defined herein, terms such as those defined in commonly used dictionaries should be interpreted as having a meaning that is consistent with their meaning in the context of the relevant art and the present application and will not be interpreted in an idealized or overly formal sense.
Embodiments of the present application will now be described in further detail with reference to the accompanying drawings.
As shown in fig. 1, an embodiment of the present application provides a method for preparing a high-strength high-conductivity aluminum alloy monofilament, including the following steps:
smelting aluminum liquid: adding aluminum ingots with the purity of more than 99.7 percent, zinc ingots, aluminum-silicon alloy and aluminum rare earth alloy into a smelting furnace, heating and melting, pressing magnesium ingots into molten aluminum, stirring and melting, sampling for spectral analysis, and controlling the components of the melt within the required range.
Refining in a furnace: transferring the molten aluminum in the smelting furnace into a refining furnace, adding an aluminum-boron alloy into the molten aluminum for boronizing treatment and fully stirring, and then refining and slagging off the molten aluminum in the furnace.
In one embodiment, in the in-furnace refining, the refining furnace is a 10-ton capacity tilting holding furnace, the furnace bottom electromagnetic stirring device is started to fully stir the melt after the boronization treatment is started, and the temperature is adjusted to 720 to 730 ℃ after the molten aluminum is subjected to slagging-off and is subjected to standing treatment.
And (3) online refining: after casting is started, a rotary blowing degassing box and double-stage foamed ceramic filtration are used for carrying out online degassing and filtration impurity removal on the melt, the hydrogen content in the treated melt is less than or equal to 0.12ml/100g, and more than 80% of impurities with the size larger than 5 mu m in the melt are removed.
In one embodiment, in the online refining, a rotary blowing degassing box is adopted to carry out online degassing on aluminum liquid, high-purity nitrogen is used as a degassing medium, and the rotating speed of a rotor is 400-500 r/min; and a double-stage foamed ceramic filter plate is adopted to filter the aluminum liquid on line, and the porosity of the double-stage foamed ceramic filter plate is 30/50PPI.
Continuous casting and rolling: and pouring the aluminum liquid after on-line stirring into a wheel type crystallizer for continuous casting to form a casting blank, and processing the casting blank to obtain the rod material.
In one embodiment, in the continuous casting and rolling, a wheel type crystallizer is used for casting a continuous casting blank, and the continuous casting blank is led into a 15-frame three-roller continuous rolling unit after coming out and is used for rolling an aluminum alloy rod material with the diameter of 9-12 mm. And heating the casting blank by using an intermediate frequency heating device during rolling, controlling the rolling temperature to be 520-550 ℃, simultaneously adjusting the preheating temperature of the emulsion to be 40-60 ℃, ensuring the final rolling temperature to be more than 350 ℃, and retracting the rod after online quenching and cooling.
Pre-aging of the rod material: the aging heating temperature is 100 to 140 ℃, and the heat preservation time is 5 to 10 hours.
In one embodiment, in the rod pre-aging, after the rod is taken off the machine, the rod is subjected to pre-aging treatment within 5 hours, so that Mg, si and Zn elements in the aluminum phase are precipitated in the form of clusters (GP zones) and form Mg/Si atomic clusters and Mg/Zn atomic clusters, so as to form a metastable hardening phase in the subsequent artificial aging. The natural aging process is inhibited by pre-aging the rod material, so that the adverse effect of the natural aging on the mechanical property is avoided.
Drawing: drawing the pre-aged alloy rod on a sliding wire drawing machine, wherein the diameter of the aluminum-magnesium-silicon alloy monofilament after drawing is 2.0-4.5 mm;
stranding: and (3) stranding the aluminum alloy monofilaments by using a frame stranding machine, wherein an automatic control preforming and post-shaping control system is adopted in the stranding process, and the stranding parameters of the lead are accurately controlled. And twisting to obtain the all-aluminum alloy wire.
Artificial aging: and (3) carrying out artificial aging treatment on the stranded conductor, wherein the aging process is carried out at the temperature of 150-180 ℃ and the heat preservation time is 6-15 hours.
In one embodiment, the artificial aging takes Mg/Si atomic clusters and Mg/Zn atomic clusters as nucleation points to form beta' (Mg/Zn atomic clusters) in the aluminum phase 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) Metastable strengthening phase to form dispersion strengthening effect to improve the aluminum alloy sheetTensile strength of the filament.
Furthermore, according to the preparation method of the high-strength high-conductivity aluminum alloy monofilament, pre-aging treatment is carried out on an aluminum alloy rod material, so that elements such as Mg, si and Zn are precipitated in the form of clusters (GP zones), adverse effects on mechanical properties of the alloy caused by natural aging are avoided, and meanwhile, the clusters precipitated by pre-aging provide nucleation points for subsequent artificial aging, so that the alloy elements are subjected to beta' (Mg) during artificial aging 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) And fully precipitating a metastable strengthening phase to form a dispersion strengthening effect and improve the tensile strength of the aluminum alloy monofilament. Moreover, a metastable strengthening phase containing Zn is introduced into the alloy, so that the strength of the alloy is greatly improved, and the Zn element has small influence on the conductivity of the alloy. And moreover, artificial aging is carried out after stranding, so that the damage of torsional deformation in the stranding process to the strength and the elongation of the single wire is eliminated, and the stranded aluminum alloy wire has better comprehensive performance.
The embodiment of the application also provides an aluminum alloy monofilament, which is prepared by the preparation method of the high-strength high-conductivity aluminum alloy monofilament, and the aluminum alloy monofilament consists of the following components in percentage by mass: 0.5 to 0.8 percent of Mg, 0.3 to 0.5 percent of Si, 0.1 to 0.5 percent of Zn, less than or equal to 0.15 percent of Fe, 0.02 to 0.05 percent of RE, 0.001 to 0.01 percent of B, less than or equal to 0.02 percent of Cr + Mn + V + Ti, the balance of Al and inevitable other impurity elements, the content of each element in the inevitable other impurity elements is less than or equal to 0.005 percent, and the total amount is less than or equal to 0.02 percent, wherein RE is La/Ce mixed rare earth elements with equal proportion.
In one embodiment, RE is added in the form of Al-RE master alloy to improve the conductivity of the aluminum alloy monofilament.
In one embodiment, the aluminum alloy monofilament has a strength of greater than or equal to 340Mpa, an electrical conductivity of greater than or equal to 55% iacs, and an elongation of greater than or equal to 5%.
In one embodiment, β "(Mg) is present in the aluminum alloy monofilament 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) A metastable hardening phase.
Further, the high strength and high conductivity aluminum alloy monofilament of the present invention has a tensile strength of 340MPa or more, an electric conductivity of 55% IACS or more, an elongation of 5% or more, and excellent properties and comprehensive properties.
Example 1
The method comprises the following steps: adding an aluminum ingot with the purity of more than 99.7 percent, a zinc ingot, an aluminum-silicon alloy and an aluminum rare earth alloy into a smelting furnace, heating and melting, and then pressing the magnesium ingot into the aluminum liquid to stir and melt.
Step two: transferring the aluminum liquid to a tilting heat preservation furnace with the capacity of 10 tons, adding a trace amount of aluminum-boron alloy for boronization treatment, and starting an electromagnetic stirring device at the bottom of the furnace to fully stir the melt. And refining the aluminum melt in a furnace, slagging off, adjusting the temperature to 720 ℃, and standing.
Step three: and after the casting is started, carrying out online degassing and filtering treatment on the melt, wherein the online degassing adopts a rotary blowing degassing box, and high-purity nitrogen is used as a degassing medium. The on-line filtration uses a double-stage ceramic foam filter plate with a porosity of 30/50PPI.
Step four: and (3) casting a continuous casting blank by adopting a wheel type crystallizer, guiding the continuous casting blank into a 15-frame three-roller continuous rolling mill set after the continuous casting blank comes out, and rolling an aluminum alloy rod material with the diameter of 9.5 mm. During rolling, a casting blank is heated by a medium-frequency heating device, the rolling temperature is controlled to be 530 ℃, the preheating temperature of the emulsion is adjusted to be 45 ℃, and the bar is retracted after online quenching and cooling.
Step five: and (3) performing pre-aging treatment 3 hours after the rod is taken out of the machine, wherein the aging heating temperature is 120 ℃, and the heat preservation time is 7 hours.
Step six: and drawing the pre-aged alloy rod on a sliding wire drawing machine, wherein the diameter of the aluminum-magnesium-silicon alloy monofilament after drawing is 3.5mm.
Step seven: and stranding the aluminum alloy monofilament by using a frame stranding machine, wherein the stranding process adopts an automatic control preforming and post-shaping control system, and the stranding parameters of the lead are accurately controlled. And twisting to obtain the all-aluminum alloy wire.
Step eight: and (3) carrying out artificial aging treatment on the twisted wire, wherein the aging process is at 155 ℃ and the heat preservation time is 8 hours.
Through analysis and detection, the alloy in the embodiment comprises the following components: 0.68% of Mg, 0.42% of Si, 0.14% of Fe, 0.3% of Zn, 0.03% of RE, 0.004% of B, and 0.018% of Cr + Mn + V + Ti, wherein the resultant twisted monofilament has a strength of 348MPa, an elongation of 6.2% and an electric conductivity of 55.7% IACS.
Example 2
The method comprises the following steps: adding an aluminum ingot with the purity of more than 99.7 percent, a zinc ingot, an aluminum-silicon alloy and an aluminum rare earth alloy into a smelting furnace, heating and melting, and then pressing the magnesium ingot into the aluminum liquid to stir and melt.
Step two: transferring the molten aluminum to a tilting holding furnace with the capacity of 10 tons, adding a trace amount of aluminum-boron alloy for boronization, and starting an electromagnetic stirring device at the bottom of the furnace to fully stir the melt. And refining the aluminum melt in a furnace, slagging off, adjusting the temperature to 725 ℃ and standing.
Step three: and after the casting is started, carrying out online degassing and filtering treatment on the melt, wherein the online degassing adopts a rotary blowing degassing box, and high-purity nitrogen is used as a degassing medium. The on-line filtration uses a double-stage ceramic foam filter plate with a porosity of 30/50PPI.
Step four: and (3) casting a continuous casting blank by adopting a wheel type crystallizer, guiding the continuous casting blank into a 15-frame three-roller continuous rolling mill set after the continuous casting blank comes out, and rolling an aluminum alloy rod material with the diameter of 9.5 mm. And heating the casting blank by using a medium-frequency heating device during rolling, controlling the rolling temperature to be 540 ℃, adjusting the preheating temperature of the emulsion to be 50 ℃, and performing on-line quenching and cooling to retract the rod.
Step five: and (3) performing pre-aging treatment 4 hours after the rod is taken out of the machine, wherein the aging heating temperature is 130 ℃, and the heat preservation time is 6 hours.
Step six: and drawing the pre-aged alloy rod on a sliding wire drawing machine, wherein the diameter of the aluminum-magnesium-silicon alloy monofilament after drawing is 3.8mm.
Step seven: and stranding the aluminum alloy monofilament by using a frame stranding machine, wherein the stranding process adopts an automatic control preforming and post-shaping control system, and the stranding parameters of the lead are accurately controlled. And twisting to obtain the all-aluminum alloy wire.
Step eight: and (3) carrying out artificial aging treatment on the stranded conductor, wherein the aging temperature is 160 ℃, and the heat preservation time is 8 hours.
Through analysis and detection, the alloy in the embodiment comprises the following components: 0.66% of Mg, 0.45% of Si, 0.15% of Fe, 0.4% of Zn, 0.05% of RE, 0.007% of B, 0.015% of Cr + Mn + V + Ti, 352MPa of monofilament strength after stranding, 5.5% of elongation and 55.2% of conductivity IACS.
Comparative example 1
The method comprises the following steps: adding an aluminum ingot with the purity of more than 99.7 percent, a zinc ingot, an aluminum-silicon alloy and an aluminum rare earth alloy into a smelting furnace, heating and melting, and then pressing the magnesium ingot into the aluminum liquid to stir and melt.
Step two: transferring the molten aluminum to a tilting holding furnace with the capacity of 10 tons, adding a trace amount of aluminum-boron alloy for boronization, and starting an electromagnetic stirring device at the bottom of the furnace to fully stir the melt. And refining the aluminum melt in a furnace, slagging off, adjusting the temperature to 725 ℃ and standing.
Step three: and after the casting is started, carrying out online degassing and filtering treatment on the melt, wherein online degassing adopts a rotary blowing degassing box, and high-purity nitrogen is used as a degassing medium. The on-line filtration uses a double-stage ceramic foam filter plate with a porosity of 30/50PPI.
Step four: and (3) casting a continuous casting blank by adopting a wheel type crystallizer, guiding the continuous casting blank into a 15-frame three-roller continuous rolling mill set after the continuous casting blank comes out, and rolling an aluminum alloy rod material with the diameter of 9.5 mm. The rolling temperature of the casting blank is 530 ℃, the preheating temperature of the emulsion is adjusted to be 40 ℃, and the rod is taken down after on-line quenching and cooling.
Step five: and (3) performing pre-aging treatment 5 hours after the rod is taken off the machine, wherein the aging heating temperature is 130 ℃, and the heat preservation time is 6 hours.
Step six: and drawing the pre-aged alloy rod on a sliding wire drawing machine, wherein the diameter of the aluminum-magnesium-silicon alloy monofilament after drawing is 3.5mm.
Step seven: and carrying out artificial aging treatment on the drawn monofilament, wherein the aging temperature is 155 ℃, and the heat preservation time is 8 hours.
Step eight: and stranding the aluminum alloy monofilament by using a frame stranding machine, wherein the stranding process adopts an automatic control preforming and post-shaping control system, and the stranding parameters of the lead are accurately controlled. And twisting to obtain the all-aluminum alloy wire.
Through analysis and detection, the alloy in the embodiment comprises the following components: 0.65% of Mg, 0.48% of Si, 0.15% of Fe, 0.2% of Zn, 0.02% of RE, 0.005% of B, 0.018% of Cr + Mn + V + Ti, and the resulting stranded wire has a monofilament strength of 340MPa, an elongation of 3.8% and an electric conductivity of 55.5% IACS.
As can be seen from comparative example 1, the absence of aging treatment after stranding may not eliminate the damage of torsional deformation during stranding on single wire strength and elongation, resulting in lower elongation of the aluminum alloy monofilament.
Comparative example 2
The method comprises the following steps: adding an aluminum ingot with the purity of more than 99.7 percent, a zinc ingot, an aluminum-silicon alloy and an aluminum rare earth alloy into a smelting furnace, heating and melting, and then pressing the magnesium ingot into the aluminum liquid to stir and melt.
Step two: transferring the molten aluminum to a tilting holding furnace with the capacity of 10 tons, adding a trace amount of aluminum-boron alloy for boronization, and starting an electromagnetic stirring device at the bottom of the furnace to fully stir the melt. Refining the aluminum melt in a furnace, slagging off, adjusting the temperature to 725 ℃, and standing.
Step three: and after the casting is started, carrying out online degassing and filtering treatment on the melt, wherein the online degassing adopts a rotary blowing degassing box, and high-purity nitrogen is used as a degassing medium. The on-line filtration uses a double-stage ceramic foam filter plate with a porosity of 30/50PPI.
Step four: and (3) casting a continuous casting blank by adopting a wheel type crystallizer, guiding the continuous casting blank into a 15-frame three-roller continuous rolling mill set after the continuous casting blank comes out, and rolling an aluminum alloy rod material with the diameter of 9.5 mm. And heating the casting blank by using a medium-frequency heating device during rolling, controlling the rolling temperature to be 540 ℃, adjusting the preheating temperature of the emulsion to be 50 ℃, and performing on-line quenching and cooling to retract the rod.
Step six: and (3) drawing the alloy rod on a sliding wire drawing machine, wherein the diameter of the single wire of the aluminum-magnesium-silicon alloy after drawing is 3.5mm.
Step seven: and stranding the aluminum alloy monofilament by using a frame stranding machine, wherein the stranding process adopts an automatic control preforming and post-shaping control system, and the stranding parameters of the lead are accurately controlled. And twisting to obtain the all-aluminum alloy wire.
Step eight: and (3) carrying out artificial aging treatment on the stranded conductor, wherein the aging temperature is 160 ℃, and the heat preservation time is 8 hours.
Through analysis and detection, the alloy in the embodiment comprises the following components: 0.67% of Mg, 0.47% of Si, 0.14% of Fe, 0.3% of Zn, 0.05% of RE, 0.007% of B, 0.016% of Cr + Mn + V + Ti, and a percentage of monofilament strength after stranding of 334MPa, elongation of 5.6% and conductivity of 54.7% of IACS.
As can be seen from comparative example 2, in the absence of the pre-aging treatment step, the strength of the resulting aluminum alloy monofilament was less than 340MPa, and the conductivity was less than 55% IACS.
Hereinbefore, specific embodiments of the present application are described with reference to the drawings. However, those skilled in the art will appreciate that various modifications and substitutions can be made to the specific embodiments of the present application without departing from the scope of the present application. Such modifications and substitutions are intended to be within the scope of the present application.

Claims (10)

1. A preparation method of a high-strength high-conductivity aluminum alloy monofilament is characterized by comprising the following steps:
smelting aluminum liquid: adding an aluminum ingot with the purity of more than 99.7 percent, a zinc ingot, aluminum-silicon alloy and aluminum-rare earth alloy into a smelting furnace, heating and melting, pressing the magnesium ingot into molten aluminum, stirring and melting, sampling, carrying out spectral analysis, and controlling the components of a melt to be in a required range;
refining in a furnace: transferring the molten aluminum in the smelting furnace into a refining furnace, adding an aluminum-boron alloy into the molten aluminum for boronizing treatment and fully stirring, and then refining and slagging off the molten aluminum in the furnace;
online refining: after casting is started, a rotary blowing degassing box and double-stage foamed ceramic filtering are used for carrying out online degassing and filtering impurity removal on the melt, the hydrogen content in the treated melt is less than or equal to 0.12ml/100g, and more than 80% of impurities with the size of more than 5 microns in the melt are removed;
continuous casting and rolling: pouring the aluminum liquid after on-line stirring into a wheel type crystallizer for continuous casting to form a casting blank, and processing the casting blank to obtain a rod material;
pre-aging of the rod material: the pre-aging heating temperature is 100 to 140 ℃, and the heat preservation time is 5 to 10 hours;
drawing: drawing the pre-aged alloy rod on a sliding wire drawing machine, wherein the diameter of the aluminum-magnesium-silicon alloy monofilament after drawing is 2.0-4.5 mm;
stranding: stranding the aluminum alloy monofilament by using a frame stranding machine, accurately controlling the stranding parameters of the conductor by adopting an automatically controlled preforming and post-shaping control system in the stranding process, and obtaining the all-aluminum alloy conductor after stranding;
artificial aging: and (3) carrying out artificial aging treatment on the stranded conductor, wherein the aging process is carried out at the temperature of 150-180 ℃ and the heat preservation time is 6-15 hours.
2. The method for preparing the high-strength high-conductivity aluminum alloy monofilament as claimed in claim 1, wherein in the rod pre-aging, the rod is pre-aged within 5 hours after being taken off the machine, so that Mg, si and Zn elements in the aluminum phase are precipitated and Mg/Si atomic clusters and Mg/Zn atomic clusters are formed.
3. The method for preparing high-strength high-conductivity aluminum alloy monofilament as claimed in claim 2, wherein the artificial aging is carried out by forming β "(Mg/Zn") in the aluminum phase by using Mg/Si atomic cluster and Mg/Zn atomic cluster as nucleation points 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) A metastable hardening phase.
4. The method for preparing the high-strength high-conductivity aluminum alloy monofilament as claimed in claim 1, wherein in the in-furnace refining, a refining furnace is a 10-ton capacity tilting holding furnace, a furnace bottom electromagnetic stirring device is started to fully stir the melt after the boronization is started, and the temperature is adjusted to 720 to 730 ℃ after the molten aluminum is subjected to slagging-off and then is subjected to standing treatment.
5. The method for preparing the high-strength high-conductivity aluminum alloy monofilament as claimed in claim 1, wherein in the online refining, a rotary blowing degassing box is adopted to carry out online degassing on aluminum liquid, high-purity nitrogen is taken as a degassing medium, and the rotating speed of a rotor is 400-500 r/min; and a double-stage foamed ceramic filter plate is adopted to filter the aluminum liquid on line, and the porosity of the double-stage foamed ceramic filter plate is 30/50PPI.
6. The method for preparing the high-strength high-conductivity aluminum alloy monofilament as claimed in claim 1, wherein in the continuous casting and rolling, a wheel type crystallizer is adopted to cast a continuous casting blank, the continuous casting blank is led into a 15-frame three-roll continuous rolling unit after coming out to roll an aluminum alloy rod material with the diameter of 9-12 mm, a medium-frequency heating device is used for heating the casting blank during rolling, the rolling temperature is controlled to be 520-550 ℃, meanwhile, the preheating temperature of emulsion is adjusted to be 40-60 ℃, the final rolling temperature is ensured to be above 350 ℃, and the rod is taken up after on-line quenching and cooling.
7. An aluminum alloy monofilament, characterized in that the aluminum alloy monofilament is prepared by the preparation method of the high-strength high-conductivity aluminum alloy monofilament as claimed in any one of claims 1 to 6, and the aluminum alloy monofilament is composed of the following components by mass percent: 0.5 to 0.8 percent of Mg, 0.3 to 0.5 percent of Si, 0.1 to 0.5 percent of Zn, less than or equal to 0.15 percent of Fe, 0.02 to 0.05 percent of RE, 0.001 to 0.01 percent of B, less than or equal to 0.02 percent of Cr + Mn + V + Ti, the balance of Al and inevitable other impurity elements, the content of each element in the inevitable other impurity elements is less than or equal to 0.005 percent, and the total amount is less than or equal to 0.02 percent, wherein RE is La/Ce mixed rare earth elements with equal proportion.
8. The aluminum alloy monofilament in accordance with claim 7, wherein RE is added in the form of Al-RE master alloy.
9. The aluminum alloy monofilament in accordance with claim 7, wherein said aluminum alloy monofilament has a strength of 340Mpa or more, an electrical conductivity of 55% iacs or more, and an elongation of 5% or more.
10. The aluminum alloy monofilament as claimed in claim 7, wherein β "(Mg) is present in said aluminum alloy monofilament 5 Si 6 )、β’(Mg 9 Si 5 ) And eta' (MgZn) 2 ) A metastable hardening phase.
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