Alloy conductor material, preparation method thereof, and cable

Abstract

The present invention provides an alloy conductor material, a preparation method, and a cable. The alloy conductor material comprises: 0.010-0.028% Zr, 0.02-0.03% B, 0.01-0.03% Fe, 0.010-0.028% Si, 0.012-0.050% (V+Ti+Cr+Mn), 0.001-0.048% RE, with the balance being aluminum. This material utilizes ultra-fine rare earth microalloying composition design technology to achieve an online solid solution effect by controlling the precise cooling of the crystallization wheel zones. This material also achieves an online aluminum rod annealing effect by matching the hot rolling speed with the pass size distribution. Furthermore, the material precisely controls the cold drawing speed of wires of different specifications to provide drawing heat for online annealing. This adds a low-temperature stabilization annealing process to the finished wire, improving the uniformity and stability of high-temperature microstructure and properties. This results in higher electrical conductivity and heat resistance.

Description

Technical Field

[0001] The present invention relates to the technical field of aluminum alloys, and in particular to an alloy conductor material, a preparation method thereof, and a cable. Background Art

[0002] As the mainstream method for transmitting and exchanging electrical energy, overhead transmission cables are required to possess comprehensive properties of high strength, high conductivity, and heat resistance. With the rapid development of the national economy, the demand for high-conductivity, heat-resistant, and high-voltage cables has increased annually, and procurement prices have gradually declined. Therefore, manufacturers are required to further shorten the process flow while ensuring uniformity in cable structure and performance to increase output and reduce production costs.

[0003] Furthermore, for heat-resistant aluminum alloy conductors, the technical barriers to achieving a 1% increase in conductivity over the existing level are extremely high. Japan achieved industrial application of 60% IACS heat-resistant aluminum conductors as early as 1970, but until 2010, it still had not fully achieved 61% IACS, or the engineering application of heat-resistant aluminum conductors with an operating temperature of 150°C. Heat-resistant aluminum conductors, which account for 70% of the Japanese transmission line market, still have a conductivity of 60% IACS. Existing technologies generally use alloying methods to optimize the conductivity of aluminum alloy conductors. Chinese patent application number CN201010593503.6 discloses a highly conductive, heat-resistant aluminum alloy conductor and its preparation method. This patented alloy, which incorporates 0.02-0.2% of the precious metal Y and 0.01-0.15% of the precious metal Sc, contains a high level of rare earth elements. This results in high alloy cost, the formation of coarse phases during the casting process, and difficulty controlling the ingot preparation and annealing processes. Furthermore, its conductivity after annealing is only 61% IACS, which lacks the advantages of high conductivity and is unsuitable for large-scale industrial application. Chinese patent application number CN201810414978.0 discloses a method for preparing high-strength, high-conductivity industrial pure aluminum conductors. This method improves the mechanical and electrical properties of the duralumin conductor by enhancing internal grain refinement and texturing. However, this invention does not take into account the high-temperature structural stability that needs to be paid special attention to for heat-resistant aluminum alloy wires. Large cold deformation will form a high density of dislocations in the structure. Once the material is kept warm at high temperature for a long time, the dislocations will easily be annihilated, thereby reducing the high-temperature structural stability of the material and further reducing the heat resistance of the material. Summary of the Invention

[0004] In view of this, the technical problem to be solved by the present invention is to provide an alloy conductor material. The alloy conductor material provided by the present invention adopts the extremely fine rare earth microalloying composition design technology to achieve the improvement of the uniformity and stability of medium and high temperature microstructure performance, and obtain higher electrical conductivity and heat resistance.

[0005] The present invention provides an alloy conductor material, comprising the following raw materials in the following weight percentages:

[0006] Zr 0.010~0.028%, B 0.02~0.03%, Fe 0.01~0.03%, Si 0.010~0.028%, (V+Ti+Cr+Mn) 0.012~0.050%, RE 0.001~0.048%, balance aluminum;

[0007] RE is one or more rare earth elements Er, Y, Yb, and Ce.

[0008] In some specific embodiments, the following raw materials are included in weight percentage:

[0009] Zr 0.010~0.028%, B 0.02~0.03%, Fe 0.01~0.03%, Si 0.010~0.028%, (V+Ti+Cr+Mn) 0.012~0.050%, RE 0.01~0.04%, and the balance is aluminum.

[0010] In some specific embodiments, the obtained alloy conductor material has a conductivity of 62.0-62.8% IACS, a tensile strength of ≥165 MPa, a long-term heat resistance temperature of 180°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of ≥96%.

[0011] The present invention provides a method for preparing the alloy conductor material according to any one of the above technical solutions, comprising the following steps:

[0012] A) melting the component alloys to obtain a melt;

[0013] B) Purifying the melt, skimming, letting it stand, re-melting, letting it stand, skimming, degassing, and obtaining a mixed material;

[0014] C) continuously casting and rolling the mixture obtained in step B) to obtain an aluminum rod;

[0015] D) Drawing, annealing, and heat-insulating the aluminum rod to obtain the aluminum rod.

[0016] In some specific embodiments, in step C) of the continuous casting and rolling, the casting temperature is 720-820°C, the cooling rate in the starting zone of the crystallization wheel is 35-45°C / s, the cooling rate in the ending zone of the crystallization wheel is 65-80°C / s, the crystallization wheel rotation speed is 3.0-4.5 rpm / min, and the ingot outlet temperature is 480-520°C.

[0017] In some specific embodiments, in the continuous casting and rolling in step C), rough rolling is performed in 4 passes, with a starting temperature of 530-580° C. and a finishing temperature of 410-430° C.; finishing rolling is performed in 6-10 passes, with a finishing inlet temperature of 400-430° C. and a finishing outlet temperature of 220-350° C.; and the rolling speed is 7-18 m / s.

[0018] In some specific embodiments, the cross section of the rough rolling blank in step C) is trapezoidal, and the cross section area of the rough rolling inlet is 2750-2950 mm 2 , rough rolling outlet cross-sectional area 850~1080mm 2 The odd-numbered passes of finishing rolling are triangular, the even-numbered passes are circular, and the cross-sectional area of the finishing rolling entrance is 850~1080mm 2 , the outlet section is φ9.5~15mm.

[0019] In some specific embodiments, in step C) the aluminum rod <100> The directional recrystallized texture accounts for 35~48%, and the recrystallized grains account for 5~20.0%.

[0020] In some specific embodiments, in step D), when the aluminum rod diameter ranges from φ9 to 15 mm, the drawing speed is 60 to 80 m / min; when the aluminum rod diameter ranges from φ4 to 9 mm, the drawing speed is 40 to 55 m / min; when the aluminum rod diameter ranges from φ1.2 to 4 mm, the drawing speed is 30 to 38 m / min.

[0021] In some specific embodiments, the annealing temperature in step D) is 180-230° C., and the holding time is 5-15 hours.

[0022] The present invention provides a cable, comprising the conductor material described in any one of the above technical solutions or prepared from the conductor material described in any one of the above technical solutions.

[0023] Compared to the prior art, the present invention provides an alloy conductor material comprising the following raw materials by weight: Zr 0.010-0.028%, B 0.02-0.03%, Fe 0.01-0.03%, Si 0.010-0.028%, (V+Ti+Cr+Mn) 0.012-0.05%, RE 0.001-0.048%, with the balance being aluminum; RE is one or more of the rare earth elements Er, Y, Yb, and Ce. This invention utilizes ultra-fine rare earth microalloying composition design technology to achieve an online solid solution effect by precisely controlling the cooling of the crystallization wheel in different zones. It also precisely matches the hot rolling speed with the pass size distribution to achieve an online aluminum rod annealing effect. Furthermore, it precisely controls the cold drawing speed of wires of different specifications to provide drawing heat for online annealing. This adds a low-temperature stabilization annealing process to the finished wire, improving the uniformity and stability of high-temperature microstructure and properties during application. Higher electrical conductivity, heat resistance and shorter preparation process make it suitable for engineering applications in the field of large-capacity and low-cost power transmission, with significant economic and environmental benefits. BRIEF DESCRIPTION OF THE DRAWINGS

[0024] Figure 1 This is the grain morphology of the aluminum rod of Example 1;

[0025] Figure 2 This is the grain morphology of the aluminum rod in Comparative Example 1. DETAILED DESCRIPTION

[0026] The present invention provides an alloy conductor material, a method for preparing the same, and a cable. Those skilled in the art can refer to the contents herein and appropriately modify the process parameters to achieve the desired results. It is particularly important to note that all similar substitutions and modifications will be readily apparent to those skilled in the art and fall within the scope of protection of the present invention. The methods and applications of the present invention have been described through preferred embodiments. It is apparent that those skilled in the art can modify, alter, and combine the methods and applications herein to implement and apply the technology of the present invention without departing from the content, spirit, and scope of the present invention.

[0027] The present invention provides an alloy conductor material, comprising the following raw materials in the following weight percentages:

[0028] Zr 0.010~0.028%, B 0.02~0.03%, Fe 0.01~0.03%, Si 0.010~0.028%, (V+Ti+Cr+Mn) 0.012~0.05%, RE 0.001~0.048%, balance aluminum;

[0029] RE is one or more rare earth elements Er, Y, Yb, and Ce.

[0030] In some specific embodiments, the raw materials are included in the following weight percentages:

[0031] Zr 0.010~0.028%, B 0.02~0.03%, Fe 0.01~0.03%, Si 0.010~0.028%, (V+Ti+Cr+Mn) 0.012~0.050%, RE 0.01~0.04%, and the balance is aluminum.

[0032] In a specific embodiment, the raw materials are included in the following weight percentages:

[0033] Zr 0.01%, B 0.015%, Fe 0.01%, Si 0.01%, (V+Ti+Cr+Mn) 0.012%, Er+Yb0.048%, and the balance is aluminum.

[0034] In a specific embodiment, the raw materials are included in the following weight percentages:

[0035] Zr 0.028%, B 0.03%, Fe 0.03%, Si 0.028%, (V+Ti+Cr+Mn) 0.05%, Er+Yb+Y+Ce 0.001%, and the balance is aluminum.

[0036] In a specific embodiment, the raw materials are included in the following weight percentages:

[0037] Zr 0.02%, B 0.025%, Fe 0.02%, Si 0.02%, (V+Ti+Cr+Mn) 0.04%, Er 0.04%, and the balance is aluminum.

[0038] The present invention adopts rare earth ultrafine alloying component design to achieve large-scale targeted solid solution control in the solidification zone, greatly improve the cooling rate during the solidification and crystallization process, and achieve an online solid solution effect.

[0039] The present invention provides a method for preparing the alloy conductor material according to any one of the above technical solutions, comprising the following steps:

[0040] A) melting the component alloys to obtain a melt;

[0041] B) Purifying the melt, skimming, letting it stand, re-melting, letting it stand, skimming, degassing, and obtaining a mixed material;

[0042] C) continuously casting and rolling the mixture obtained in step B) to obtain an aluminum rod;

[0043] D) Drawing, annealing, and heat-insulating the aluminum rod to obtain the aluminum rod.

[0044] The preparation method of the alloy conductor material provided by the present invention firstly smelts the alloy components to obtain a melt.

[0045] The present invention has clearly described the above specific alloy components and will not be repeated here.

[0046] The smelting parameters of the present invention include melting the high-purity aluminum ingot at 680-780°C.

[0047] The melt is purified, and the melt purification parameters include controlling the melt temperature at 720-780° C., adding Al-B master alloy for boronization treatment, stirring for 5-30 minutes, and standing for 70-150 minutes.

[0048] Melt purification is an important step in improving the quality of metal materials. It improves metal properties by removing impurities such as gas and inclusions in the melt.

[0049] After the melt is purified, the slag is removed and the melt is allowed to stand. The parameters of the slag removal process include using a slag rake to cyclically remove surface slag and controlling the melt temperature to drop within 5%.

[0050] The heat preservation time of the present invention is 60 minutes.

[0051] During the metal smelting process, various inclusions, such as metal oxides and sulfides, are generated. Slag skimming directly removes these inclusions floating on the surface of the molten metal, thereby improving its purity. If slag is not promptly removed, these inclusions may re-integrate into the molten metal, causing secondary contamination and affecting the performance of metal products. Slag skimming prevents this from happening and ensures the stability of the molten metal quality.

[0052] After standing, the mixture is transferred to a second melting furnace for further melting. The melting parameters of the present invention include a holding temperature of 730-820°C and the addition of Al-Zr and Al-RE master alloys.

[0053] Compared with single smelting, the double smelting method of the present invention can improve purity, reduce gas content, improve component uniformity, optimize organizational structure and enhance the stability of the wire.

[0054] The mixture was melted again, allowed to stand, slag removed, and degassed to obtain a mixed material. The process parameters of the present invention include degassing with a mixed gas of argon, nitrogen, and chlorine, and heat preservation and standing for 300 minutes.

[0055] The mixed material obtained in the continuous casting and rolling step B) is used to obtain an aluminum rod.

[0056] In some specific embodiments, during the continuous casting and rolling, the casting temperature is 720-820°C, specifically 720°C, 730°C, 740°C, 750°C, 760°C, 770°C, 780°C, 790°C, 800°C, 810°C, 820°C; or a range between any two of the above.

[0057] The cooling rate in the initial zone of the crystallization wheel is 35-45°C / s, specifically 35°C / s, 36°C / s, 37°C / s, 38°C / s, 39°C / s, 40°C / s, 41°C / s, 42°C / s, 43°C / s, 44°C / s, 45°C / s; or a range between any two of the above.

[0058] The cooling rate in the final zone of the crystallization wheel is 65-80°C / s, specifically 65°C / s, 66°C / s, 67°C / s, 68°C / s, 69°C / s, 70°C / s, 71°C / s, 72°C / s, 73°C / s, 74°C / s, 75°C / s, 76°C / s, 77°C / s, 78°C / s, 79°C / s, 80°C / s; or a range between any two of the above.

[0059] The crystallization wheel speed is 3.0-4.5 rpm; specifically, it can be 3.0 rpm, 3.1 rpm, 3.2 rpm, 3.3 rpm, 3.4 rpm, 3.5 rpm, 3.6 rpm, 3.7 rpm, 3.8 rpm, 3.9 rpm, 4.0 rpm, 4.1 rpm, 4.2 rpm, 4.3 rpm, 4.4 rpm, and 4.5 rpm.

[0060] The ingot outlet temperature is 480~520℃; specifically, it can be 480℃, 485℃, 490℃, 495℃, 500℃, 505℃, 510℃, 515℃, or 520℃.

[0061] In some specific embodiments, in the continuous casting and rolling, the rough rolling is divided into 4 passes, and the starting rolling temperature of the rough rolling is 530-580°C, specifically 530°C, 535°C, 540°C, 545°C, 550°C, 555°C, 560°C, 565°C, 570°C, 575°C, and 580°C;

[0062] Rough rolling and finishing rolling temperature 410~430℃; 410℃, 412℃, 414℃, 416℃, 418℃, 420℃, 422℃, 424℃, 426℃, 428℃, 430℃;

[0063] Finish rolling is divided into 6 to 10 passes, specifically 6 passes, 7 passes, 8 passes, 9 passes or 10 passes;

[0064] Finishing rolling inlet temperature is 400~430℃, specifically 400℃, 405℃, 410℃, 415℃, 420℃, 425℃, 430℃

[0065] The finishing rolling outlet temperature is 220-350°C; specifically, it can be 220°C, 230°C, 240°C, 250°C, 260°C, 270°C, 280°C, 290°C, 300°C, 310°C, 320°C, 330°C, 340°C, or 350°C;

[0066] The rolling speed is 7-18 m / s, specifically 7 m / s, 8 m / s, 9 m / s, 10 m / s, 11 m / s, 12 m / s, 13 m / s, 14 m / s, 15 m / s, 16 m / s, 17 m / s, and 18 m / s.

[0067] In some specific embodiments, the cross section of the rough rolling billet is trapezoidal, and the cross-sectional area of the rough rolling inlet is 2750-2950mm. 2 , rough rolling outlet cross-sectional area 850~1080mm 2 ;

[0068] The odd-numbered passes of finishing rolling are triangular, the even-numbered passes are circular, and the cross-sectional area of the finishing rolling entrance is 850~1080mm2 , the outlet section is φ9.5~15mm.

[0069] In some specific embodiments, the aluminum rod <100> The directional recrystallization texture accounts for 35~48%, which can be 35%, 36%, 37%, 38%, 39%, 40%, 41%, 42%, 43%, 44%, 45%, 46%, 47%, and 48%;

[0070] The proportion of recrystallized grains is 5~20.0%. Specifically, it can be: 5%, 6%, 7%, 8%, 9%, 10%, 11%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, 19%, 20.0%

[0071] The aluminum rod is drawn.

[0072] In some specific embodiments,

[0073] When the diameter of the aluminum rod is φ9~15mm, the drawing speed is 60~80m / min;

[0074] When the diameter of the aluminum rod is φ4~9mm, the drawing speed is 40~55m / min;

[0075] When the diameter of the aluminum rod ranges from φ1.2 to 4 mm, the drawing speed is 30 to 38 m / min.

[0076] By controlling the drawing speed based on different wire diameters, this invention increases the wire drawing process temperature and enables in-line annealing, ensuring high wire elongation and preventing wire breakage due to insufficient plasticity. The high-deformation drawing process is complemented by a low-temperature, short-term stabilization annealing process. This process reduces vertical grain boundaries while maintaining long, straight grain boundaries, lowering deformation energy storage, and improving the high-temperature stability of the single-filament structure. This simultaneously increases electrical conductivity and heat resistance (retained strength), significantly enhancing overall performance.

[0077] The conductor material is obtained by annealing after drawing. The annealing temperature of the present invention is 180-230°C, and can be specifically 180°C, 185°C, 190°C, 195°C, 200°C, 205°C, 210°C, 215°C, 220°C, 225°C, or 230°C.

[0078] The holding time is 5 to 15 hours, specifically 5 hours, 6 hours, 7 hours, 8 hours, 9 hours, 10 hours, 11 hours, 12 hours, 13 hours, 14 hours, or 15 hours.

[0079] The hot rolling speed and pass size distribution of the present invention form an online aluminum rod annealing effect. At the same time, the cold drawing speed of wires of different specifications is accurately controlled to provide drawing heat to achieve the online annealing effect of the wires, increase the low-temperature stabilization annealing process of the finished wire, and realize the uniformity and stability of high-temperature microstructure performance during application.

[0080] The conductor material of the present invention is preferably a wire. The high-strength and high-conductivity wire prepared by the present invention has a diameter of φ1.2-4.5mm, a conductivity of 62.0-62.8% IACS, a tensile strength ≥165MPa, a long-term heat resistance temperature of 180°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate ≥96%.

[0081] The present invention provides a cable, comprising the conductor material described in any one of the above technical solutions or prepared from the conductor material described in any one of the above technical solutions.

[0082] The conductor material of the present invention is preferably a wire. The high-strength and high-conductivity wire obtained by the present invention has a diameter of φ1.2-4.5mm, a conductivity of 62.0-62.8% IACS, a tensile strength ≥165MPa, a long-term heat resistance temperature of 180°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate ≥96%.

[0083] The above-mentioned conductors can be made into cables, especially overhead transmission cables. The present invention does not limit the specific preparation method, which is well known to those skilled in the art.

[0084] The present invention has the following beneficial effects:

[0085] 1) The present invention provides a temperature-controlled and cooling-controlled preparation process for a high-strength, high-conductivity, and heat-resistant conductor. The process adopts a rare earth micro-alloying composition design, rationally matches the casting temperature, crystallization wheel speed, cooling water flow rate, and rolling speed, and utilizes cooling control in different upper and lower temperature zones to achieve large-scale targeted solid solution regulation in the solidification zone, greatly improve the cooling rate during the solidification and crystallization process, achieve an online solid solution effect, effectively refine the grain structure, and achieve sufficient solid solution of rare earth elements, thereby obtaining a high-conductivity aluminum alloy ingot with refined grains, uniform structure, and high supersaturation, and the area fraction of the primary phase containing RE in the ingot is greatly reduced.

[0086] 2) By matching dynamic aging with high temperature and low speed rolling, without offline annealing process, the online annealing effect is used to induce the precipitation of dispersed phases and dynamic recrystallization nucleation, so that the rolled aluminum alloy <100> The directional recrystallization texture and the proportion of recrystallized grains increased significantly, effectively improving the uniformity of the hot-rolled aluminum rod structure and the consistency of performance.

[0087] 3) Based on the genetic effect of the organization of high uniformity hot-rolled aluminum rod, large diameter hot-rolled aluminum rod (φ9.5-φ15mm) is used to obtain strong shear strength through large cold deformation and precise control of cold drawing deformation. <111> The texture is coupled with the organization of long straight grain boundaries to achieve grain shape and orientation control, and obtain slender grain high-conductivity aluminum wires.

[0088] 4) Different drawing speeds are used during the cold drawing process for different wire rod specifications, increasing the drawing temperature and enabling in-line annealing during the drawing process. This ensures high wire elongation and prevents wire breakage due to insufficient plasticity. A low-temperature, short-term stabilization annealing process complements the high-deformation drawing process. This process reduces vertical grain boundaries while maintaining long, straight grain boundaries, lowering deformation energy storage and improving the high-temperature stability of the single-wire structure. This results in simultaneous increases in electrical conductivity and heat resistance (retained strength), significantly enhancing overall performance.

[0089] It should be understood that the expression "one or more of" includes individually each of the items recited after the expression and various combinations of two or more of the recited items, unless otherwise apparent from the context and usage. The expression "and / or" in conjunction with three or more recited items should be understood to have the same meaning, unless otherwise apparent from the context.

[0090] The terms "comprising", "having" or "containing", including their grammatical synonyms, should generally be understood as open and non-restrictive, e.g., not excluding other unrecited elements or steps, unless otherwise specifically stated or understood from the context.

[0091] In this application, the term "and / or" describes the association relationship between associated objects, indicating that three relationships may exist. For example, A and / or B can mean: A exists alone, A and B exist at the same time, and B exists alone. A and B can be singular or plural.

[0092] In this application, "at least one" means one or more, and "more than one" means two or more. "At least one of the following" or similar expressions refers to any combination of these items, including any combination of single or plural items.

[0093] It should be understood that the order of steps or the order in which certain actions are performed are not important as long as the present invention remains operable. Additionally, two or more steps or actions may be performed simultaneously.

[0094] The use of any and all examples or exemplary language such as "for example" or "including" herein is intended only to better illustrate the present invention and does not limit the scope of the present invention otherwise. No language in this specification should be construed as indicating any non-claimed element is essential to the practice of the present invention.

[0095] In addition, the numerical ranges and parameters used to define the present invention are approximate values. The relevant numerical values in the specific examples have been presented as accurately as possible. However, any numerical value inherently inevitably contains standard deviations due to individual testing methods. Therefore, unless otherwise expressly stated, it should be understood that all ranges, amounts, values, and percentages used in this disclosure are modified by the word "about." As used herein, "about" generally means that the actual value is within plus or minus 10%, 5%, 1%, or 0.5% of a particular value or range.

[0096] It should be understood that in the various embodiments of the present application, the size of the serial numbers of the above-mentioned processes does not mean the order of execution. Some or all of the steps can be executed in parallel or sequentially. The execution order of each process should be determined by its function and internal logic, and should not constitute any limitation on the implementation process of the embodiments of the present application.

[0097] Some cases are described in the embodiments and comparative examples of the present invention, wherein the embodiments illustrate certain implementations of the present invention. However, this does not mean that the effects of the present invention can only be achieved in these cases.

[0098] To further illustrate the present invention, an alloy conductor material, a preparation method thereof, and a cable provided by the present invention are described in detail below with reference to embodiments.

[0099] Example 1

[0100] This embodiment provides a process for preparing a high-strength, high-conductivity, heat-resistant conductor by controlling temperature and cooling. The actual operation steps are as follows:

[0101] 1. In a first melting furnace, smelt the alloy components, including: Zr 0.01%, B 0.02%, Fe 0.01%, Si 0.01%, (V + Ti + Cr + Mn) 0.012%, RE (Er + Yb) 0.048%, and the balance being aluminum.

[0102] 2. Purify the melt, remove slag, let it stand, transfer it to the second melting furnace, let it stand, remove slag, and degas;

[0103] 3. Continuous casting and rolling of the mixture obtained in step 2, wherein the casting temperature is 720°C, the cooling rate in the initial zone of the crystallization wheel is 35°C / s, the cooling rate in the final zone of the crystallization wheel is 65°C / s, and the crystallization wheel speed is 3.0 rpm. Rough rolling is divided into 4 passes, with the rough rolling start temperature of 530°C and the rough rolling end temperature of 410°C; finishing rolling is divided into 6 passes, with the finishing rolling entrance temperature of 400°C and the finishing rolling exit temperature of 220°C. The cross-section of the rough rolled billet is trapezoidal, with a cross-sectional area of 2750mm at the rough rolling entrance. 2 , rough rolling outlet cross-sectional area 850mm 2 The odd-numbered passes of finishing rolling are triangular, the even-numbered passes are circular, and the cross-sectional area of the finishing rolling entrance is 850mm 2, the outlet section is φ15mm. The obtained aluminum rod <100> The directional recrystallized texture accounts for 35%, and the recrystallized grains account for 5.0%.

[0104] 4. Drawing the aluminum rod obtained in step 3 to obtain aluminum wire, when the aluminum rod diameter range is φ9-15mm, the drawing speed is 60m / min; when the aluminum rod diameter range is φ4-9mm, the drawing speed is 40m / min; when the aluminum rod diameter range is φ1.2-4mm, the drawing speed is 30m / min; and φ1.2mm aluminum wire is obtained.

[0105] 5. The aluminum wire obtained in step 4 is subjected to low-temperature stabilization annealing at a temperature of 180° C. for 15 hours to obtain a high-strength, high-conductivity, and heat-resistant wire.

[0106] 6. The high-strength, high-conductivity, heat-resistant wire obtained in step 5 has a diameter of φ1.2mm, a conductivity of 62.8%IACS, a tensile strength of 165MPa, a long-term heat-resistant temperature of 180°C, a short-term heat-resistant temperature of 260°C / 1h, and a strength retention rate of 96%.

[0107] Example 2

[0108] This embodiment provides a process for preparing a high-strength, high-conductivity, heat-resistant conductor by controlling temperature and cooling. The actual operation steps are as follows:

[0109] 1. In a first melting furnace, melt the component alloys, including: Zr 0.028%, B 0.03%, Fe 0.03%, Si 0.028%, (V + Ti + Cr + Mn) 0.05%, RE (Er + Yb + Y + Ce) 0.001%, and the balance being aluminum.

[0110] 2. Purify the melt, remove slag, let it stand, transfer it to the second melting furnace, let it stand, remove slag, and degas;

[0111] 3. Continuous casting and rolling of the mixture obtained in step 2, wherein the casting temperature is 820°C, the cooling rate in the initial zone of the crystallization wheel is 45°C / s, the cooling rate in the final zone of the crystallization wheel is 80°C / s, and the crystallization wheel speed is 4.5rpm. Rough rolling is divided into 4 passes, with the rough rolling start temperature of 550°C and the rough rolling end temperature of 430°C; finishing rolling is divided into 10 passes, with the finishing rolling entrance temperature of 430°C and the finishing rolling exit temperature of 350°C. The cross-section of the rough rolling billet is trapezoidal, with a cross-sectional area of 2950mm at the rough rolling entrance. 2 , rough rolling outlet cross-sectional area 1080mm 2 The odd-numbered passes of finishing rolling are triangular, the even-numbered passes are circular, and the cross-sectional area of the finishing rolling entrance is 1080mm 2 , the outlet cross section is φ9.5mm. The obtained aluminum rod <100> The directional recrystallized texture accounts for 48%, and the recrystallized grains account for 20.0%.

[0112] 4. Drawing the aluminum rod obtained in step 3 to obtain aluminum wire, when the diameter of the aluminum rod is in the range of φ9-9.5mm, the drawing speed is 80m / min; when the diameter of the aluminum rod is in the range of φ4.5-9mm, the drawing speed is 55m / min; and φ4.5mm aluminum wire is obtained.

[0113] 5. The aluminum wire obtained in step 4 is subjected to low-temperature stabilization annealing at a temperature of 230° C. for 5 hours to obtain a high-strength, high-conductivity, and heat-resistant wire.

[0114] 6. The high-strength, high-conductivity, heat-resistant wire obtained in step 5 has a diameter of φ4.5 mm, a conductivity of 62.0% IACS, a tensile strength of 170 MPa, a long-term heat-resistant temperature of 180°C, a short-term heat-resistant temperature of 260°C / 1h, and a strength retention rate of 98%.

[0115] Example 3

[0116] This embodiment provides a process for preparing a high-strength, high-conductivity, heat-resistant conductor by controlling temperature and cooling. The actual operation steps are as follows:

[0117] 1. In a first melting furnace, melt the component alloys, including: Zr 0.02%, B 0.025%, Fe 0.02%, Si 0.02%, (V+Ti+Cr+Mn) 0.04%, RE (Er) 0.04%, and the balance being aluminum.

[0118] 2. Purify the melt, remove slag, let it stand, transfer it to the second melting furnace, let it stand, remove slag, and degas;

[0119] 3. Continuous casting and rolling of the mixture obtained in step 2, wherein the casting temperature is 750°C, the cooling rate in the initial zone of the crystallization wheel is 40°C / s, the cooling rate in the final zone of the crystallization wheel is 70°C / s, and the crystallization wheel speed is 3.8rpm. Rough rolling is divided into 4 passes, with the rough rolling start temperature of 580°C and the rough rolling end temperature of 420°C; finishing rolling is divided into 8 passes, with the finishing rolling entrance temperature of 420°C and the finishing rolling exit temperature of 300°C. The cross-section of the rough rolling billet is trapezoidal, and the cross-sectional area of the rough rolling entrance is 2800mm 2 , rough rolling outlet cross-sectional area 1000mm 2 The odd-numbered passes of finishing rolling are triangular, the even-numbered passes are circular, and the cross-sectional area of the finishing rolling entrance is 1000mm 2 , the outlet section is φ12mm. The obtained aluminum rod <100> The directional recrystallized texture accounts for 42%, and the recrystallized grains account for 8.0%.

[0120] 4. Drawing the aluminum rod obtained in step 3 to obtain aluminum wire. When the aluminum rod diameter ranges from φ12-15 mm, the drawing speed is 70 m / min; when the aluminum rod diameter ranges from φ4-9 mm, the drawing speed is 45 m / min; when the aluminum rod diameter ranges from φ3-4 mm, the drawing speed is 30 m / min; and φ3.0 mm aluminum wire is obtained.

[0121] 5. The aluminum wire obtained in step 4 is subjected to low-temperature stabilization annealing at a temperature of 200°C for 10 hours to obtain a high-strength, high-conductivity, and heat-resistant wire.

[0122] 6. The high-strength, high-conductivity, heat-resistant wire obtained in step 5 has a diameter of φ3.0 mm, a conductivity of 62.5% IACS, a tensile strength of 168 MPa, a long-term heat-resistant temperature of 180°C, a short-term heat-resistant temperature of 260°C / 1h, and a strength retention rate of 97%.

[0123] Comparative Example 1

[0124] The actual operation steps of this comparative example are as follows:

[0125] 1. In a first melting furnace, the component alloys are melted, including: B 0.01%, Fe 0.01%, Si 0.01%, (V+Ti+Cr+Mn) 0.02%, and the balance being aluminum.

[0126] 2. Purify the melt, remove slag, let it stand, transfer it to the second melting furnace, let it stand, remove slag, and degas;

[0127] 3. Continuous casting and rolling of the mixture obtained in step 2, wherein the casting temperature is 700°C, the cooling rate in the initial zone of the crystallization wheel is 30°C / s, the cooling rate in the final zone of the crystallization wheel is 55°C / s, and the crystallization wheel speed is 2.0 rpm / min. Rough rolling is divided into 4 passes, with the rough rolling start temperature of 550°C and the rough rolling end temperature of 400°C; finishing rolling is divided into 6 passes, with the finishing rolling entrance temperature of 380°C and the finishing rolling exit temperature of 200°C. The cross-section of the rough rolling billet is trapezoidal, with a cross-sectional area of 2750mm at the rough rolling entrance. 2 , rough rolling outlet cross-sectional area 850mm 2 The odd-numbered passes of finishing rolling are triangular, the even-numbered passes are circular, and the cross-sectional area of the finishing rolling entrance is 850mm 2 , the outlet section is φ15mm. The obtained aluminum rod <100> The directional recrystallized texture accounts for 20%, and the recrystallized grains account for 5.5%.

[0128] 4. Drawing the aluminum rod obtained in step 3 to obtain aluminum wire. When the aluminum rod diameter ranges from φ9 to 15 mm, the drawing speed is 40 m / min; when the aluminum rod diameter ranges from φ4 to 9 mm, the drawing speed is 30 m / min; when the aluminum rod diameter ranges from φ1.2 to 4 mm, the drawing speed is 25 m / min; and φ1.2 mm aluminum wire is obtained.

[0129] 5. The aluminum wire obtained in step 4 is subjected to low-temperature stabilization annealing at a temperature of 150° C. for 3 hours to obtain a conductive wire.

[0130] 6. The wire obtained in step 5 has a diameter of φ1.2mm, a conductivity of 61.8%IACS, a tensile strength of 110MPa, a long-term heat resistance temperature of 100°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 56%.

[0131] Comparative Example 2

[0132] The difference between this comparative example and Example 1 is that in step 1, the alloy components are smelted in the first smelting furnace, including: Zr 0.01%, B 0.01%, Fe 0.01%, Si 0.01%, (V+Ti+Cr+Mn) 0.02%, and the balance is aluminum. <100> The directional recrystallized texture accounts for 22%, and the recrystallized grains account for 6.0%. The wire obtained in step 6 has a conductivity of 61.0% IACS, a tensile strength of 120 MPa, a long-term heat resistance temperature of 120°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 60%.

[0133] Comparative Example 3

[0134] The difference between this comparative example and Example 1 is that in step 1, the alloy components are smelted in the first smelting furnace, including: Zr 0.05%, B 0.02%, Fe 0.12%, Si 0.03%, (V+Ti+Cr+Mn) 0.01%, RE (Er) 0.1%, and the balance is aluminum. <100> The directional recrystallized texture accounts for 20%, and the recrystallized grains account for 4.0%. The wire obtained in step 6 has a conductivity of 61.6% IACS, a tensile strength of 160 MPa, a long-term heat resistance temperature of 150°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 74%.

[0135] Comparative Example 4

[0136] The difference between this comparative example and Example 1 is that the casting temperature in step 3 is 700°C. <100> The directional recrystallized texture accounts for 16%, and the recrystallized grains account for 3.0%. The wire obtained in step 6 has a conductivity of 60.8% IACS, a tensile strength of 124 MPa, a long-term heat resistance temperature of 130°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 55%.

[0137] Comparative Example 5

[0138] The difference between this comparative example and Example 1 is that the cooling rate of the initial area of the crystallization wheel in step 3 is 20°C / s. <100> The directional recrystallized texture accounts for 12%, and the recrystallized grains account for 3.4%. The wire obtained in step 6 has a conductivity of 60.6% IACS, a tensile strength of 132 MPa, a long-term heat resistance temperature of 130°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 65%.

[0139] Comparative Example 6

[0140] The difference between this comparative example and Example 1 is that the cooling rate of the final zone of the crystallization wheel in step 3 is 40°C / s. <100> The directional recrystallized texture accounts for 16%, and the recrystallized grains account for 2.8%. The wire obtained in step 6 has a conductivity of 61.1% IACS, a tensile strength of 117 MPa, a long-term heat resistance temperature of 140°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 62%.

[0141] Comparative Example 7

[0142] The difference between this comparative example and Example 1 is that the crystallization wheel speed in step 3 is 2.0 rpm. <100> The directional recrystallized texture accounts for 12%, and the recrystallized grains account for 3.8%. The wire obtained in step 6 has a conductivity of 61.9% IACS, a tensile strength of 122 MPa, a long-term heat resistance temperature of 160°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 58%.

[0143] Comparative Example 8

[0144] The difference between this comparative example and Example 1 is that the outlet temperature of the ingot in step 3 is 440°C. <100> The directional recrystallized texture accounts for 9%, and the recrystallized grains account for 2%. The wire obtained in step 6 has a conductivity of 55.9% IACS, a tensile strength of 102 MPa, a long-term heat resistance temperature of 90°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 45%.

[0145] Comparative Example 9

[0146] The difference between this comparative example and Example 1 is that the rough rolling and final rolling temperature in step 3 is 390°C. <100> The directional recrystallized texture accounts for 10%, and the recrystallized grains account for 3%. The wire obtained in step 6 has a conductivity of 51.9% IACS, a tensile strength of 122 MPa, a long-term heat resistance temperature of 100°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 65%.

[0147] Comparative Example 10

[0148] The difference between this comparative example and Example 1 is that the final rolling temperature in step 3 is 200°C. <100> The directional recrystallized texture accounts for 6%, and the recrystallized grains account for 1%. The wire obtained in step 6 has a conductivity of 52.2% IACS, a tensile strength of 137 MPa, a long-term heat resistance temperature of 90°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 45%.

[0149] Comparative Example 11

[0150] The difference between this comparative example and Example 1 is that the aluminum rod obtained in step 3 is subjected to stabilization annealing at 110°C for 3 hours. <100> The directional recrystallized texture accounts for 10%, and the recrystallized grains account for 10%. The wire obtained in step 6 has a conductivity of 60.2% IACS, a tensile strength of 144 MPa, a long-term heat resistance temperature of 120°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of 65%.

[0151] Verification results:

[0152] Table 1 Composition of Examples of the Invention and Comparative Examples

[0153]

[0154] Table 2 Process parameters of high-conductivity heat-resistant wires in the embodiments of the present invention and the comparative examples

[0155]

[0156] Table 3 Performance of wires obtained in the embodiments of the present invention and comparative examples

[0157]

[0158] The above is only a preferred embodiment of the present invention. It should be pointed out that for ordinary technicians in this technical field, several improvements and modifications can be made without departing from the principles of the present invention. These improvements and modifications should also be regarded as within the scope of protection of the present invention.

Claims

1. An alloy conductor material, characterized in that: The raw materials include the following weight percentages: Zr 0.010~0.028%, B 0.02~0.03%, Fe 0.01~0.03%, Si 0.010~0.028%, (V+Ti+Cr+Mn) 0.012~0.050%, RE 0.001~0.048%, balance aluminum; Wherein RE is one or more rare earth elements Er, Y, Yb, Ce; The obtained alloy conductor material has a conductivity of 62.0-62.8% IACS, a tensile strength of ≥165 MPa, a long-term heat resistance temperature of 180°C, a short-term heat resistance of 260°C / 1h, and a strength retention rate of ≥96%.

2. The alloy conductor material according to claim 1, characterized in that The raw materials include the following weight percentages: Zr 0.010~0.028%, B 0.02~0.03%, Fe 0.01~0.03%, Si 0.010~0.028%, (V+Ti+Cr+Mn) 0.012~0.050%, RE 0.01~0.04%, and the balance is aluminum.

3. A method for preparing the alloy conductor material according to any one of claims 1 to 2, characterized in that: The steps include: A) melting the component alloys to obtain a melt; B) Purifying the melt, skimming, allowing to stand, re-melting, allowing to stand, skimming, degassing, and obtaining a mixed material; C) continuously casting and rolling the mixture obtained in step B) to obtain an aluminum rod; wherein in the continuous casting and rolling steps, the casting temperature is 720-820°C, the cooling rate in the initial zone of the crystallization wheel is 35-45°C / s, the cooling rate in the final zone of the crystallization wheel is 65-80°C / s, and the crystallization wheel rotation speed is 3.0-4.5 rpm; the ingot outlet temperature is 480-520°C; the rough rolling is performed in four passes, the rough rolling start temperature is 530-580°C, and the rough rolling finish temperature is 410-430°C; the finishing rolling is performed in six to ten passes, the finishing rolling inlet temperature is 400-430°C, the finishing rolling outlet temperature is 220-350°C, and the rolling speed is 7-18 m / s; D) drawing, annealing, and heat-keeping the aluminum rod to obtain the aluminum rod; when the diameter of the aluminum rod is in the range of φ9-15 mm, the drawing speed is 60-80 m / min; when the diameter of the aluminum rod is in the range of φ4-9 mm, the drawing speed is 40-55 m / min; when the diameter of the aluminum rod is in the range of φ1.2-4 mm, the drawing speed is 30-38 m / min; The annealing temperature is 180-230° C., and the holding time is 5-15 hours.

4. The preparation method according to claim 3, characterized in that The cross section of the rough rolling billet is trapezoidal, and the inlet cross section area of the rough rolling is 2750~2950mm 2 , the outlet cross-sectional area of rough rolling is 850~1080mm 2 The odd-numbered passes of the finishing rolling are triangular, the even-numbered passes are circular, and the entrance cross-sectional area of the finishing rolling is 850~1080mm 2 , the outlet cross section is φ9.5~15mm; Step C) the aluminum rod <100> The directional recrystallized texture accounts for 35~48%, and the recrystallized grains account for 5~20.0%.

5. A cable, characterized in that: The invention comprises the alloy conductor material according to any one of claims 1 to 2 or is prepared from the alloy conductor material according to any one of claims 3 to 4.

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