High-performance aluminum alloy wire and preparation method thereof

Abstract

The invention relates to the field of aluminum alloy material processing, in particular to a high-performance aluminum alloy wire, which comprises the following components in percentage by weight: 0.1-0.2% of Si; the content of Fe is 0.6 to 0.7 percent; the content of Cu is 0.02 to 0.03 percent; the content of Ni is 2.6 to 2.8 percent; the content of Mn is 0.01 to 0.02 percent; the content of Mg is 0.004 to 0.02 percent; the content of Cr is 0.01 to 0.05 percent; the content of Zn is 0.02 to 0.05 percent; the content of TiB2 is 2.5 to 2.8 percent; the content of Ce is 3 to 4.5 percent; the single content of other impurity elements is less than or equal to 0.05%; the total content of other impurity elements is less than or equal to 0.15%; the as-cast conductivity of the wire can reach 48-50% IACS (International Annealed Copper Standard), the error is within 1.5% IACS, and meanwhile, a finished product has good corrosion resistance.

Description

Technical Field

[0001] The present invention relates to the technical field of aluminum alloy processing, and in particular to a high-performance aluminum alloy wire and a preparation method thereof. Background Art

[0002] Aluminum alloy has the characteristics of low density, good electrical conductivity, high thermal conductivity, large latent heat of fusion, large light reflection coefficient, small thermal neutron absorption interface area and beautiful appearance color. Aluminum can form a dense and strong oxide film on its surface in the air to prevent the invasion of oxygen, so it has good corrosion resistance. Aluminum alloy can be used as a thermal conductive material due to its low cost, good electrical and thermal conductivity, and corrosion resistance. It is widely used in the production of heat dissipation components in the fields of automobiles, ships, aerospace and electronic equipment. With the updating and iteration of science and technology, various fields have higher and higher requirements for the electrical conductivity, thermal conductivity and mechanical properties of aluminum alloy materials to meet the needs of lightweight transportation and electronic products, high power and low cost.

[0003] The technical problem with conductive aluminum alloys in the prior art is that it is difficult for existing aluminum alloy wires to have both the electrical conductivity, thermal conductivity, and corrosion resistance required to meet production requirements.

[0004] Therefore, there is an urgent need to provide an aluminum alloy wire with high electrical conductivity, thermal conductivity, and corrosion resistance and a preparation method thereof. Summary of the Invention

[0005] The present invention aims to solve the technical problem of how to provide an aluminum alloy wire with high electrical and thermal conductivity and corrosion resistance and a preparation method thereof.

[0006] In order to achieve the above-mentioned object, the first aspect of the present invention provides a high-performance aluminum alloy wire, wherein the components and their weight percentages in the wire are as follows:

[0007] Si content is 0.1-0.2%;

[0008] Fe content is 0.6-0.7%;

[0009] Cu content is 0.02-0.03%;

[0010] Ni content is 2.6-2.8%;

[0011] Mn content is 0.01-0.02%;

[0012] Mg content is 0.004-0.02%;

[0013] Cr content is 0.01-0.05%;

[0014] Zn content is 0.02-0.05%;

[0015] TiB2 content is 2.5-2.8%;

[0016] Ce content is 3-4.5%;

[0017] The content of other impurity elements is ≤0.05%;

[0018] The total content of other impurity elements is ≤0.15%;

[0019] The balance is Al.

[0020] A second aspect of the present invention provides a method for preparing the above-mentioned high-performance aluminum alloy wire, wherein the method comprises:

[0021] Casting, extrusion;

[0022] The casting conditions include: heating pure aluminum, Al-Ce master alloy, Al-Ni master alloy, and Al-Fe master alloy to 750-780°C, keeping the temperature for 25-35 minutes, cooling to 740-760°C, adding Al-10Ce with a particle size of 5-15 mm, melting and cooling to 720-740°C, adding TiB2 nanoparticles, standing, stirring, refining and degassing for 5 minutes, blowing inert gas into the aluminum liquid, cooling to 700°C, and casting.

[0023] The beneficial effects of the present invention are:

[0024] The present invention optimizes the alloy composition and controls the melting and casting process, thereby greatly improving the cast conductivity of the aluminum alloy bar while ensuring the stability of the profile size. The cast conductivity can reach 48-50% IACS, with an error within 1.5% IACS. At the same time, the finished product has good corrosion resistance, which improves the quality of the finished product. Furthermore, the extrusion process parameters are regulated to make the performance of the wire even better. BRIEF DESCRIPTION OF THE DRAWINGS

[0025] Figure 1 This is a cross-sectional view of the extrusion die, in which: 1. diversion pit; 2. working belt; 3. empty knife; 4. runner. DETAILED DESCRIPTION

[0026] The endpoints of the ranges and any values disclosed herein are not limited to the precise ranges or values, and these ranges or values should be understood to include values close to these ranges or values. For numerical ranges, the endpoints of each range, the endpoints of each range and individual point values, and the individual point values can be combined with each other to obtain one or more new numerical ranges, which should be considered to be specifically disclosed herein.

[0027] In the present invention, since the profile is a smaller-sized aluminum alloy wire profile, and the actual operation of the later conductivity detection of the small-aperture wire profile is relatively difficult, and the extrusion of the aluminum alloy wire has little effect on the metal conductivity or even slightly improves it, the detection of the cast conductivity of this alloy can represent the conductivity of the finished wire.

[0028] In the prior art, it is difficult to prepare highly conductive and corrosion-resistant aluminum alloy wires with existing alloy compositions and preparation processes, making it difficult for the conductive and corrosion-resistant properties of the aluminum alloy wires to meet the requirements.

[0029] In the present invention, the inventors found that by controlling the alloy composition and adjusting the processing technology, the performance of the aluminum alloy wire can meet the requirements and have excellent electrical conductivity and corrosion resistance.

[0030] To achieve this goal, the inventors attempted to optimize the composition and processing technology of the aluminum alloy wire. The inventors found that the above purpose can be achieved through a specific composition of the components and a melting and casting process. Furthermore, a specific extrusion process makes the performance of the aluminum alloy wire even better.

[0031] A first aspect of the present invention provides a high-performance aluminum alloy wire, wherein the components and their weight percentages in the wire are:

[0032] Si content is 0.1-0.2%;

[0033] Fe content is 0.6-0.7%;

[0034] Cu content is 0.02-0.03%;

[0035] Ni content is 2.6-2.8%;

[0036] Mn content is 0.01-0.02%;

[0037] Mg content is 0.004-0.02%;

[0038] Cr content is 0.01-0.05%;

[0039] Zn content is 0.02-0.05%;

[0040] TiB2 content is 2.5-2.8%;

[0041] Ce content is 3-4.5%;

[0042] The content of other impurity elements is ≤0.05%;

[0043] The total content of other impurity elements is ≤0.15%;

[0044] The balance is Al.

[0045] In the present invention, excessive addition of silicon to the alloy will reduce the electrical conductivity and thermal conductivity of the aluminum alloy to a certain extent. Controlling the silicon content within a range of 0.1-0.2% can greatly improve the electrical and thermal conductivity of the alloy. To improve the electrical and thermal conductivity of the alloy, the silicon content is reduced by a zone melting method during the melting and ingot casting of the test aluminum alloy. This method utilizes the difference in the distribution coefficient of impurities (including silicon) during the solidification and melting of the alloy to purify it. Since the solubility of impurities such as silicon in liquid and solid aluminum is different, silicon in solid aluminum tends to transfer to liquid aluminum in the melting zone. Therefore, during the zone melting process, the heating element slowly moves through the aluminum alloy ingot to form a narrow melting zone. As the melting zone slowly moves, impurities such as silicon are concentrated at one end of the ingot, thereby reducing the silicon content of the remaining aluminum alloy.

[0046] In order to improve the electrical conductivity and thermal conductivity of aluminum alloy, the aluminum alloy wire provided by the present invention is added with rare earth elements Ce and TiB2. The added Ce element has a certain effect of improving the electrical conductivity of the aluminum alloy, because adding an appropriate amount of Ce element to the alloy can purify the matrix and form a metal compound AlxCe with impurities. y , change the morphology and distribution of the impurity phase in the aluminum matrix, thereby reducing the hindrance of the impurities in the matrix to the electron migration, thereby improving the electrical conductivity. Although adding an appropriate amount of TiB2 has a weak effect on improving the electrical conductivity of the alloy and may even slightly reduce the electrical conductivity due to the second phase formed in the alloy hindering the movement of electrons, if TiB2 is evenly and finely distributed in the matrix, the equiaxed second phase formed is distributed in the grain boundary grains, which has little effect on the electrical conductivity and will significantly refine the grains of the alloy, improve the mechanical properties and thermal stability, the appropriate addition of Fe element helps to improve the corrosion resistance of aluminum alloy, because Fe can form fine dispersed second phase particles with other elements, which plays a role in refining Grains, reducing the electrochemical corrosion sensitivity at the grain boundaries, thereby enhancing the corrosion resistance of the aluminum alloy to a certain extent. At the same time, the addition of Fe elements can promote the refinement of the aluminum alloy grains, thereby improving the strength and toughness of the alloy. The addition of Ni elements can also improve the corrosion resistance of the aluminum alloy to a certain extent. This is because Ni elements can form some stable compounds or phases in aluminum alloys, which help to prevent the invasion of corrosive media. Therefore, the composition design of the aluminum alloy wire provided by the present invention, on the basis of ensuring the metal filling ability, better improves the alloy conductivity, improves the alloy mechanical properties and corrosion resistance, and enhances the ability of aluminum alloy products to adapt to the environment.

[0047] A second aspect of the present invention provides a method for preparing the above-mentioned high-performance aluminum alloy wire, wherein the method comprises:

[0048] Casting, extrusion;

[0049] The casting conditions include: heating pure aluminum, Al-Ce master alloy, Al-Ni master alloy, and Al-Fe master alloy to 750-780°C, keeping the temperature for 25-35 minutes, cooling to 740-760°C, adding Al-10Ce with a particle size of 5-15 mm, melting and cooling to 720-740°C, adding TiB2 nanoparticles, standing, stirring, refining and degassing for 5 minutes, blowing inert gas into the aluminum liquid, cooling to 700°C, and casting.

[0050] In the present invention, the Ce content in the Al-Ce master alloy is 10-20%, the Ni content in the Al-Ni master alloy is 10-15%, the Fe content in the Al-Fe master alloy is 10-20%, and Al-10Ce represents an Al-Ce alloy with a cerium content of 10%.

[0051] In this invention, inert gas is blown into the molten aluminum through a specially designed nozzle, forming tiny bubbles. As these bubbles rise, they absorb hydrogen and inclusions from the molten aluminum and remove them from the liquid, achieving the purpose of degassing and refining. To further enhance the efficiency of aluminum alloy casting and refining, this experiment abandoned the single-hole nozzle used in traditional refining and instead used a high-temperature-resistant porous ceramic nozzle that effectively improves refining efficiency and quality. The multi-porous design allows the ejected gas to form more tiny bubbles, increasing the contact area with the molten aluminum and improving the refining effect.

[0052] According to the present invention, the melting zone moving speed is 5-10 mm / h, the melting zone width is 5-20 mm, preferably 10 mm, and the melting process is repeated twice.

[0053] In the present invention, in the aluminum alloy casting zone melting method, the melt zone movement rate and width are key parameters. To better remove impurities such as silicon, the casting process of the present invention adopts a melt zone movement rate of 5-10 mm / h and a melt zone width of 5-20 mm, preferably 10 mm. The melting process is repeated twice, allowing impurity atoms in the alloy sufficient time to distribute at the steeper solid-liquid interface, thereby improving the purification effect. At the same time, to achieve a better purification effect, the content of impurities such as silicon in the alloy is significantly reduced after repeating the zone melting twice.

[0054] According to the present invention, the extrusion conditions include: an extrusion diameter of 8-15 mm, an extrusion die of a double-hole die, and an extrusion ratio of 20-50.

[0055] In the present invention, the double-hole mold can not only improve production efficiency compared to the single-hole mold, but more importantly, it can make the metal flow more uniform. The two mold holes of the double-hole mold can play the role of diverting and balancing the metal flow. The more uniform flow of metal in the mold can reduce the problems of stress concentration inside the profile, uneven chemical composition, etc., which is conducive to ensuring the stability of the metal's mechanical properties and surface quality. In order to improve the metal fluidity of the aluminum alloy in the mold, improve the extrusion performance and the uniformity of the alloy forming components, balance the metal liquid flow rate, ensure that the forming speed of each part of the aluminum alloy profile during the extrusion process remains basically consistent, enable the aluminum liquid to evenly fill the mold cavity, avoid the turbulent flow of the metal liquid in the mold, reduce defects caused by uneven flow, ensure the stability of mechanical properties, and reduce impurities in the aluminum liquid. Reduce the local pressure of the mold, make the extrusion force on the mold more evenly dispersed, reduce the peak pressure, thereby reducing the stress concentration of the mold during the extrusion process, and increase the service life.

[0056] According to the present invention, the double-hole mold is provided with a trapezoidal diversion pit, the depth of the diversion pit is 2-3 mm, the slope is 15-30°, and the width of the mold working zone is 3-6 mm.

[0057] In the present invention, the trapezoidal structure design of the diversion pit can make the flow path of the molten metal in the mold more regular, gradually accelerate and converge the molten metal during the flow process, and improve the fluidity and uniformity of the metal. At the same time, the electrical conductivity requirement is relatively high, and the impurities in the alloy have a greater impact on the electrical conductivity. The trapezoidal-shaped diversion pit can play a certain filtering role on the molten metal, concentrating some impurities in the wider part of the diversion pit, thereby purifying the chemical composition of the metal, stabilizing the product performance, and improving the product conductivity.

[0058] In the present invention, the extrusion ratio is slightly higher, and a deeper guide pit is required to ensure that the metal can flow evenly. However, considering that the alloy designed in the composition of the present invention has a high aluminum content and a low degree of alloying, the relative metal fluidity is high, and the depth of the guide pit can be appropriately reduced. In addition, the aluminum alloy wire of the present invention has a simple shape and a small size, and the depth of the guide pit can be shallower. Therefore, limiting the parameter range mentioned above is sufficient to guide the molten metal to fill the cavity.

[0059] In the present invention, if the working belt is too short, the metal flow rate will be too fast, which will easily cause metal turbulence inside the mold, resulting in scratches and other defects on the product surface. At the same time, when the metal flow rate is too fast, the friction between the metal and the working belt surface will be too short, and it may not be possible to form a good surface quality, resulting in a rough surface. If the working belt is too long, the metal flow resistance will increase, the flow rate will slow down, and the aluminum alloy will stay in the working belt for too long, which may cause the local temperature to drop too quickly, affecting the fluidity of the aluminum alloy, thereby causing defects such as cold shut and orange peel on the product surface. An overly long working belt will also easily cause the metal to oxidize during the flow process, causing the color and finish of the product surface to deteriorate. Since the present invention provides a simple wire profile with good alloy fluidity, the mold used is a flat mold with a high extrusion ratio. In order to control the metal flow rate and reduce the extrusion force, the mold working belt is shortened to the range specified by the present invention.

[0060] According to the present invention, the double-hole die is made of high-chromium-molybdenum steel with a chromium content of 4-6wt%.

[0061] According to the present invention, the extrusion conditions include: an extrusion peak breakthrough pressure of 15-20 MPa, a mold heating temperature of 450-500°C, and an ingot heating temperature of 470-500°C.

[0062] In the present invention, the extrusion peak breakthrough pressure provided can extend the service life of the mold. The mold heating temperature helps the aluminum alloy to have better fluidity during the extrusion process, reduces the extrusion force, makes the extrusion process smoother, and can effectively improve the surface quality and dimensional accuracy of the profile. If the mold heating temperature is lower than 450°C, the metal flow will deteriorate due to the decrease in temperature, making it difficult to fill every corner of the mold cavity, resulting in incomplete filling, thereby affecting the forming effect of the profile. At the same time, the deterioration of the metal fluidity means that the resistance to the flow of the molten metal increases, and the direct consequence is that the extruder needs to apply a greater extrusion force to squeeze the molten aluminum from the mold mouth. This will not only increase the wear and energy consumption of the equipment, affecting its service life and production efficiency, but also cause wear of the mold and defects such as roughness and scratches on the profile surface due to the increase in extrusion pressure. If the mold heating temperature is higher than 500℃, the performance of the mold material will be affected, which may cause the mold to soften and slight deformation inside, affecting the surface quality and dimensional accuracy of the extruded profile. Excessively high mold heating temperature will also increase the possibility of chemical reaction between the aluminum alloy and the mold, resulting in oxidation and peeling on the profile surface, causing irreversible surface defects such as coarse aluminum alloy grains, and reducing the profile surface quality and mechanical properties, such as reduced strength and hardness.

[0063] The ingot heating temperature defined in the present invention can reasonably balance the flow and extrudability of the aluminum alloy and its mechanical properties. If the ingot heating temperature is lower than 470°C, the fluidity of the aluminum alloy will deteriorate, resulting in increased molding difficulty. Too low a temperature will also increase the extrusion force. Similar to the case where the mold heating temperature is too low, poor metal fluidity will directly lead to increased energy consumption and wear of the extrusion equipment and affect the surface quality and mechanical properties of the profile product. Too high an ingot heating temperature may cause the ingot to overburn, that is, during the process of heating at too high a temperature, the low-melting-point eutectic structure inside the alloy melts, and the overburned structure will have a significant negative impact on the performance of the aluminum alloy and subsequent processing. Too high an ingot heating temperature will also cause the grains of the ingot to become coarse, and coarse grains will reduce the mechanical properties of the aluminum alloy, such as reducing the toughness and ductility of the profile.

[0064] According to the present invention, the extrusion conditions include: an extrusion speed of 0.4-0.8 mm / s.

[0065] In the present invention, the extrusion speed is limited to 0.4-0.8 mm / s in combination with the composition characteristics of the alloy, the extrusion equipment and the process parameters.

[0066] According to the present invention, the extrusion conditions include: the profile outlet temperature is 380-420°C.

[0067] Test Method

[0068] The test method for the composition of aluminum alloy wire is in accordance with GB / T7999-2015 Aluminum and Aluminum Alloy Photoelectric Direct Reading Emission Spectroscopy Analysis Method, and the test equipment is ARL-3460 direct reading spectrometer.

[0069] The mechanical properties test method is in accordance with GB / T16865-2013 Specimens and methods for tensile testing of deformed aluminum, magnesium and their alloy products, and the testing equipment is AG-X 100KN electronic universal testing machine.

[0070] The high-magnification microstructure test standard is GB / T6892-2015 General Industrial Aluminum and Aluminum Alloy Extruded Profiles, and the test method is in accordance with GB / T3246.1-2012 Microstructure Test Methods for Wrought Aluminum and Aluminum Alloy Products Part 1: Microstructure Test Methods. The test equipment is an AXIO universal research-grade inverted materials microscope.

[0071] The macroscopic test standard is GB / T6892-2015 General industrial aluminum and aluminum alloy extruded profiles, and the test method is in accordance with GB / T3246.2-2012 Microstructure inspection method for deformed aluminum and aluminum alloy products Part 2: Macrostructure inspection method. The test environment is alkaline corrosive solution.

[0072] The intergranular corrosion test equipment is DK-98II electric constant temperature water bath 12109, GX51 material microscope 5C13575, and the test standard is GB / T 7998-2023.

[0073] The neutral salt spray corrosion test equipment is Q-FOG cyclic salt spray corrosion tester 06-2498-36CCT600, and the test standard is GB / T 6461-2002.

[0074] The conductivity test equipment is SMP-10 eddy current conductivity meter, and the test standard is GB / T 12966-91.

[0075] The technical solution of the present invention is further described in detail below with reference to the accompanying drawings and embodiments. Obviously, the embodiments described herein are only some embodiments of the present invention and are not intended to limit the present invention. Based on the embodiments of the present invention, all other embodiments implemented by those of ordinary skill in the art without making creative improvements are within the scope of protection of the present invention.

[0076] Example 1

[0077] A. Melting and Casting: Prepare aluminum alloy wire raw materials according to the following weight proportions: Si: 0.17%, Fe: 0.65%, Cu: 0.02%, Ni: 2.65%, Mn: 0.02%, Mg: 0.01%, Cr: 0.05%, Zn: 0.05%, TiB2: 2.5%, Ce: 4.5%, the individual content of other impurity elements ≤ 0.05%, the total content of other impurity elements ≤ 0.15%, and the balance Al. Heat pure aluminum, Al-Ce master alloy, Al-Ni master alloy, and Al-Fe master alloy to 780°C, hold the temperature for 30 minutes, cool to 750°C, add Al-10Ce with a particle size of 5 mm, melt, cool to 740°C, add TiB2 nanoparticles, let stand, stir, refine and degas for 5 minutes, blow inert gas into the aluminum liquid, cool to 700°C, and cast;

[0078] C. Extrusion: The extrusion diameter is 9.53 mm, the extrusion die is a double-hole die, the extrusion ratio is 40; the diversion pit depth is 2.5 mm, the slope is 20°, the working belt width is 3 mm, the mold steel molybdenum content is 1.8 wt%, and the chromium content is 5 wt%;

[0079] It is produced using a 500T horizontal extruder, with an extrusion peak breakthrough pressure of 17Mpa, a mold heating temperature of 480℃, an ingot heating temperature of 480℃, an extrusion speed of 0.5m / min, and a profile outlet temperature of 400℃.

[0080] Aluminum alloy wire A1 was obtained.

[0081] Example 2

[0082] Aluminum alloy wire was prepared according to the processing method of Example 1, except that the aluminum alloy components were Si: 0.1%, Fe: 0.6%, Cu: 0.02%, Ni: 2.6%, Mn: 0.01%, Mg: 0.004%, Cr: 0.01%, Zn: 0.02%, TiB2: 2.5%, and Ce: 3%.

[0083] Aluminum alloy wire A2 is obtained.

[0084] Example 3

[0085] Aluminum alloy wire was prepared according to the processing method of Example 1, except that the aluminum alloy components were Si: 0.2%, Fe: 0.7%, Cu: 0.03%, Ni: 2.8%, Mn: 0.02%, Mg: 0.02%, Cr: 0.05%, Zn: 0.05%, TiB2: 2.8%, and Ce: 4.5%.

[0086] Aluminum alloy wire A3 was obtained.

[0087] Example 4

[0088] Aluminum alloy wires were prepared according to the processing method of Example 1, except that the particle size of Al-10Ce was 5 mm.

[0089] Aluminum alloy wire A4 was obtained.

[0090] Example 5

[0091] Aluminum alloy wires were prepared according to the processing method of Example 1, except that the particle size of Al-10Ce was 15 mm.

[0092] Aluminum alloy wire A5 was obtained.

[0093] Example 6

[0094] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the depth of the guide pit was 2 mm, the slope was 15°, and the width of the die working zone was 3 mm.

[0095] Aluminum alloy wire A6 was obtained.

[0096] Example 7

[0097] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the depth of the guide pit was 3 mm, the slope was 30°, and the width of the die working zone was 6 mm.

[0098] Aluminum alloy wire A7 was obtained.

[0099] Example 8

[0100] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the extrusion peak breakthrough pressure was 15 MPa, the mold heating temperature was 450° C., and the ingot heating temperature was 470° C.

[0101] Aluminum alloy wire A8 was obtained.

[0102] Example 9

[0103] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the extrusion peak breakthrough pressure was 20 MPa, the mold heating temperature was 500° C., and the ingot heating temperature was 500° C.

[0104] Aluminum alloy wire A9 was obtained.

[0105] Example 10

[0106] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the extrusion speed was 0.4 mm / s and the profile outlet temperature was 380°C.

[0107] Aluminum alloy wire A10 was obtained.

[0108] Example 11

[0109] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the extrusion speed was 0.8 mm / s and the profile outlet temperature was 420°C.

[0110] Aluminum alloy wire A11 was produced.

[0111] Comparative Example 1

[0112] Aluminum alloy wire was prepared according to the processing method of Example 1, except that the aluminum alloy components were Si: 0.08%, Fe: 0.5%, Cu: 0.01%, Ni: 2.4%, Mn: 0.008%, Mg: 0.003%, Cr: 0.008%, Zn: 0.15%, TiB2: 2.35%, and Ce: 2.8%.

[0113] Aluminum alloy wire DA1 was produced.

[0114] Comparative Example 2

[0115] Aluminum alloy wire was prepared according to the processing method of Example 1, except that the aluminum alloy components were Si: 0.3%, Fe: 0.9%, Cu: 0.05%, Ni: 2.90%, Mn: 0.03%, Mg: 0.025%, Cr: 0.06%, Zn: 0.06%, TiB2: 3.0%, and Ce: 4.7%.

[0116] Aluminum alloy wire DA2 was obtained.

[0117] Comparative Example 3

[0118] Aluminum alloy wires were prepared according to the processing method of Example 1, except that the particle size of Al-10Ce was 2 mm.

[0119] Aluminum alloy wire DA3 was produced.

[0120] Comparative Example 4

[0121] Aluminum alloy wires were prepared according to the processing method of Example 1, except that the particle size of Al-10Ce was 25 mm.

[0122] Aluminum alloy wire DA4 was produced.

[0123] Comparative Example 5

[0124] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the depth of the guide pit was 1 mm, the slope was 10°, and the width of the die working zone was 2 mm.

[0125] Aluminum alloy wire DA5 was produced.

[0126] Comparative Example 6

[0127] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the depth of the guide pit was 5 mm, the slope was 40°, and the width of the die working zone was 8 mm.

[0128] Aluminum alloy wire DA6 was produced.

[0129] Comparative Example 7

[0130] Aluminum alloy wires were prepared according to the processing method of Example 1, except that the extrusion peak breakthrough pressure was 12 MPa, the mold heating temperature was 420°C, and the ingot heating temperature was 450°C.

[0131] Aluminum alloy wire DA7 was produced.

[0132] Comparative Example 8

[0133] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the extrusion peak breakthrough pressure was 27 MPa, the mold heating temperature was 520° C., and the ingot heating temperature was 515° C.

[0134] Aluminum alloy wire A8 was obtained.

[0135] Comparative Example 9

[0136] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the extrusion speed was 0.2 mm / s and the profile outlet temperature was 330°C.

[0137] Aluminum alloy wire DA9 was produced.

[0138] Comparative Example 10

[0139] Aluminum alloy wires were prepared according to the processing method of Example 1, except that, in the extrusion process, the extrusion speed was 1.1 mm / s and the profile outlet temperature was 460°C.

[0140] Aluminum alloy wire DA10 was produced.

[0141] Performance tests were conducted on A1-A11 and DA1-DA10, as shown in Table 1.

[0142] Table 1

[0143]

[0144]

[0145]

[0146] By comparing the examples with the comparative examples, it can be seen that the aluminum alloy wire provided by the present invention has excellent electrical and thermal conductivity and corrosion resistance, and also maintains excellent mechanical properties.

[0147] The aluminum alloy wire provided by the present invention introduces rare earth elements Ce and TiB2 and regulates their contents, reduces the Si content through the preparation process, thereby improving the electrical conductivity, thermal conductivity and corrosion resistance of the wire. Furthermore, the casting process is regulated to solve the problem of how to reduce the Si content. Furthermore, by regulating the extrusion process, the electrical conductivity, thermal conductivity and corrosion resistance of the wire can be made even better.

[0148] The above description is only a preferred specific implementation method of the present invention, but the protection scope of the present invention is not limited thereto. Any technician familiar with the technical field, within the technical scope disclosed by the present invention, can make equivalent replacements or changes based on the technical solutions and inventive concepts of the present invention, which should be covered by the protection scope of the present invention.

Claims

1. A high-performance aluminum alloy wire, characterized in that: The components and their weight percentages in the silk thread are: Si content is 0.1-0.2%; Fe content is 0.6-0.7%; Cu content is 0.02-0.03%; Ni content is 2.6-2.8%; Mn content is 0.01-0.02%; Mg content is 0.004-0.02%; Cr content is 0.01-0.05%; Zn content is 0.02-0.05%; TiB2 content is 2.5-2.8%; Ce content is 3-4.5%; The content of other impurity elements is ≤0.05%; The total content of other impurity elements is ≤0.15%; The balance is Al.

2. A method for preparing the high-performance aluminum alloy wire according to claim 1, characterized in that: The method comprises: Casting, extrusion; The casting conditions include: heating pure aluminum, Al-Ce master alloy, Al-Ni master alloy, and Al-Fe master alloy to 750-780°C, keeping the temperature for 25-35 minutes, cooling to 740-760°C, adding Al-10Ce with a particle size of 5-15 mm, melting and cooling to 720-740°C, adding TiB2 nanoparticles, standing, stirring, refining and degassing for 5 minutes, blowing inert gas into the aluminum liquid, cooling to 700°C, and casting.

3. The method according to claim 2, characterized in that The extrusion conditions include: an extrusion diameter of 8-15 mm, an extrusion die of a double-hole die, and an extrusion ratio of 20-50.

4. The method according to claim 2, characterized in that The double-hole mold is provided with a circular diversion pit with a depth of 2-3 mm and a slope of 15-30 degrees. The width of the mold working zone is 3-6 mm.

5. The method according to claim 2, characterized in that The double-hole die is made of high-chromium-molybdenum steel with a chromium content of 4-6wt%.

6. The method according to claim 2, characterized in that The extrusion conditions include: an extrusion peak breakthrough pressure of 15-20 MPa, a mold heating temperature of 450-500° C., and an ingot heating temperature of 470-500° C.

7. The method according to claim 2, characterized in that The extrusion conditions include: an extrusion speed of 0.4-0.8 mm / s.

8. The method according to claim 2, characterized in that The extrusion conditions include: the profile outlet temperature is 380-420°C.

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