Alloy conductor material, preparation method thereof and cable

Abstract

The invention provides an alloy conductor material, a preparation method thereof and a cable. The alloy conductor material disclosed by the invention comprises the following components in percentage by weight: 0.010 to 0.028 percent of Zr, 0.02 to 0.03 percent of B, 0.01 to 0.03 percent of Fe, 0.010 to 0.028 percent of Si, 0.012 to 0.050 percent of (V + Ti + Cr + Mn), 0.001 to 0.048 percent of RE and the balance of aluminum. An extremely micro rare earth microalloying component design technology is adopted, an online solid solution effect is provided by controlling partition precise cooling of a crystallization wheel, an online aluminum rod annealing effect is formed by matching hot continuous rolling speed and pass size distribution, meanwhile, drawing heat is provided for precise control of cold drawing speed of wires of different specifications, and the online annealing effect of the wires is achieved. And a low-temperature stable annealing process of the finished wire rod is added, so that the uniformity and stability of high-temperature structure performance are improved. And the conductivity and the heat resistance are higher.

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 way of transmitting and exchanging electric energy, overhead transmission cables are required to have comprehensive properties of high strength, high conductivity, and heat resistance. With the rapid development of the national economy, the demand for high-conductivity and heat-resistant high-voltage cables has been increasing year by year, and the purchase price has gradually decreased. Therefore, it is required that the production end further shorten the process flow while ensuring the uniformity of the cable tissue performance, so as to increase the output and reduce the production cost.

[0003] In addition, for heat-resistant aluminum alloy conductors, it is extremely difficult to increase the conductivity by 1% on the existing basis. Japan achieved the industrial application of 60% heat-resistant aluminum conductors as early as 1970, but until 2010, the engineering application of heat-resistant aluminum conductors with a conductivity of 61% IACS and a service temperature of 150 °C was still not fully realized. The conductivity of heat-resistant aluminum conductors with a market occupancy rate of up to 70% in the Japanese transmission line market is still 60% IACS. In the prior art, the method of optimizing the addition of alloy components is generally used to improve the conductivity of aluminum alloy conductors. Chinese Patent with Application No. CN201010593503.6 provides a high-conductivity and heat-resistant aluminum alloy conductor and a preparation method thereof. The alloy of this patent adds noble metal elements Y 0.02-0.2% and Sc 0.01-0.15%. The addition amount of rare earth is relatively high, the alloy cost is relatively high, it is easy to form coarse phases during the melting and casting process, the ingot preparation and annealing processes are difficult to control, and its conductivity after annealing is only 61% IACS, without showing the advantage of high conductivity, and it is not suitable for large-scale industrial promotion and application. Chinese Patent with Application No. CN201810414978.0 provides a preparation method of a high-strength and high-conductivity commercially pure aluminum conductor, which improves the mechanical properties and conductivity of hard aluminum conductors through "grain elongation" and "texturing" inside the aluminum conductor. However, this invention does not consider the high-temperature tissue stability that needs to be focused on for heat-resistant aluminum alloy conductors. A large cold deformation amount will form a high density of dislocations in the tissue. Once heated at high temperature for a long time, the dislocations are easily annihilated, thereby reducing the high-temperature tissue 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 an extremely low rare earth microalloying composition design technology to improve the uniformity and stability of the medium- and high-temperature tissue properties, and obtain higher conductivity and heat resistance.

[0005] The present invention provides an alloy conductor material, comprising 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%, with the balance being aluminum;

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

[0008] In some specific embodiments, the raw materials include the following weight percentages:

[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%, with the balance being aluminum.

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

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

[0012] A) Melting each component alloy to obtain a melt;

[0013] B) Purifying the melt, skimming the slag, standing, remelting, standing, skimming the slag, and degassing to obtain a mixture;

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

[0015] D) Drawing and annealing the aluminum rod, and maintaining the temperature to obtain the product.

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

[0017] In some specific embodiments, in the continuous casting and rolling in step C): the rough rolling is divided into 4 passes, the starting rolling temperature of the rough rolling is 530 - 580 °C, and the final rolling temperature of the rough rolling is 410 - 430 °C; the finish rolling is divided into 6 - 10 passes, the inlet temperature of the finish rolling is 400 - 430 °C, and the outlet temperature of the finish rolling is 220 - 350 °C; 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-sectional area at the rough rolling inlet is 2750 - 2950 mm 2 , and the cross-sectional area at the rough rolling outlet is 850 - 1080 mm 2 ; the odd passes of the finish rolling are triangular, and the even passes are circular. The cross-sectional area at the finish rolling inlet is 850 - 1080 mm 2 , and the outlet cross-section is φ9.5 - 15 mm.

[0019] In some specific embodiments, the proportion of the <100> - direction recrystallization texture in the aluminum rod described in step C) is 35 - 48%, and the proportion of recrystallized grains is 5 - 20.0%.

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

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

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

[0023] Compared with the prior art, the present invention provides an alloy conductor material, which includes raw materials with 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 - 0.05%, RE 0.001 - 0.048%, and the balance is aluminum; wherein RE is one or more of rare earth elements Er, Y, Yb, Ce. The present invention adopts an extremely micro - rare - earth micro - alloying composition design technology, provides an on - line solid - solution effect by controlling the precise cooling of the crystallization wheel partition, precisely matches the hot continuous rolling speed and the pass size distribution to form an on - line aluminum rod annealing effect, and at the same time precisely controls the cold drawing speed of different - specification wires to provide drawing heat to achieve the on - line annealing effect of the wires, and adds a low - temperature stabilization annealing process for the finished wire rods, so as to improve the uniformity and stability of the high - temperature tissue performance during the application process. It has higher electrical conductivity, heat - resistant performance and a shorter - process preparation process, is suitable for the engineering application in the field of large - capacity and low - cost power transmission, and has remarkable economic and environmental benefits. BRIEF DESCRIPTION OF THE DRAWINGS

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

[0025] Figure 2 The grain morphology of the aluminum rod in Comparative Example 1. Detailed implementation manners

[0026] The present invention provides an alloy conductor material, a preparation method thereof, and a cable. Those skilled in the art can draw on the content of this article and appropriately modify the process parameters to achieve. It should be particularly noted that all similar substitutions and modifications are obvious to those skilled in the art, and they all fall within the protection scope of the present invention. The methods and applications of the present invention have been described through preferred embodiments, and those skilled in the art can obviously make changes or appropriate modifications and combinations to the methods and applications in this article without departing from the content, spirit, and scope of the present invention to implement and apply the technology of the present invention.

[0027] The present invention provides an alloy conductor material, comprising 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%, the balance being aluminum;

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

[0030] In some specific embodiments, it comprises raw materials 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%, the balance being aluminum.

[0032] In a specific embodiment, it comprises raw materials 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 + Yb 0.048%, the balance being aluminum.

[0034] In a specific embodiment, it comprises raw materials 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%, the balance being aluminum.

[0036] In a specific embodiment, the raw materials include the following components by weight percentage:

[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 a rare earth ultra-micro alloying composition design to achieve large-range targeted solid solution regulation in the solidification zone, greatly increasing the cooling rate during the solidification and crystallization process, and realizing the on-line solid solution effect.

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

[0040] A) Melting each component alloy to obtain a melt;

[0041] B) Purifying the melt, skimming the slag, standing still, remelting, standing still, skimming the slag, and degassing to obtain a mixed material;

[0042] C) Continuously casting and rolling the mixed material obtained in step B) to obtain an aluminum rod;

[0043] D) Drawing and annealing the aluminum rod, and keeping it warm to obtain the product.

[0044] The preparation method for the alloy conductor material provided by the present invention first melts each component alloy to obtain a melt.

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

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

[0047] Purify the melt. The melt purification parameters include controlling the melt temperature at 720 - 780 °C, adding an Al-B master alloy for boronizing treatment, stirring for 5 - 30 min, and standing still for 70 - 150 min.

[0048] Melt purification is an important link to improve the quality of metal materials. By removing impurities such as gases and inclusions in the melt, the metal properties are improved.

[0049] After melt purification, skimming the slag and standing still are carried out. The skimming parameters of the present invention include using a skimming rake to repeatedly remove the surface floating slag, and controlling the temperature drop of the melt within 5%.

[0050] The heat preservation time for standing still in the present invention is 60 min.

[0051] During the metal smelting process, various inclusions will be generated, such as metal oxides, sulfides, etc. The slag skimming operation can directly remove these inclusions floating on the surface of the molten metal, thereby improving the purity of the molten metal. If the slag is not skimmed in time, these inclusions may re-mix into the molten metal, causing secondary pollution and affecting the performance of metal products. By skimming the slag, this situation can be avoided, ensuring the stability of the molten metal quality.

[0052] After standing, it is transferred to the second smelting furnace and smelted again. The parameters of the smelting described in the present invention include a holding temperature of 730 - 820 °C, and adding Al-Zr and Al-RE master alloys.

[0053] The present invention undergoes two smelting processes. Compared with one-time smelting, it can improve purity, reduce gas content, improve compositional uniformity, optimize the organizational structure, and enhance the stability of the wire.

[0054] Smelt again, stand, skim the slag, and degas to obtain a mixture; the above process parameters of the present invention include degassing with a mixed gas of argon, nitrogen, and chlorine, and holding and standing for 300 min.

[0055] Continuous casting and rolling of the mixture obtained in step B) to obtain aluminum rods.

[0056] In some specific embodiments, in the continuous casting and rolling: the casting temperature is 720 - 820 °C, specifically it can be 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 value between any two of the above.

[0057] The cooling rate in the starting area of the crystallizing wheel is 35 - 45 °C / s, specifically it can be 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 value between any two of the above.

[0058] The cooling rate in the ending area of the crystallizing wheel is 65 - 80 °C / s, specifically it can be 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 value between any two of the above.

[0059] The rotational speed of the crystallization wheel 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, 4.5 rpm.

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

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

[0062] The rough rolling final temperature is 410 - 430 °C; 410 °C, 412 °C, 414 °C, 416 °C, 418 °C, 420 °C, 422 °C, 424 °C, 426 °C, 428 °C, 430 °C;

[0063] The finish rolling is divided into 6 - 10 passes, specifically, it can be 6 passes, 7 passes, 8 passes, 9 passes or 10 passes;

[0064] The finish rolling inlet temperature is 400 - 430 °C, specifically, it can be 400 °C, 405 °C, 410 °C, 415 °C, 420 °C, 425 °C, 430 °C

[0065] The finish 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, 350 °C;

[0066] The rolling speed is 7 - 18 m / s, specifically, it can be 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, 18 m / s.

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

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

[0069] In some specific embodiments, the proportion of the recrystallization texture in the <100> direction of the aluminum rod is 35 - 48%, which can be 35%, 36%, 37%, 38%, 39%, 40%, 41%, 42%, 43%, 44%, 45%, 46%, 47%, 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] Draw the aluminum rod.

[0072] In some specific embodiments,

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

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

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

[0076] In the present invention, by controlling different drawing speeds according to different diameters, the temperature during the wire drawing process can be increased, on-line annealing during the drawing process can be achieved, the high elongation rate of the wire can be ensured, and wire breakage due to insufficient plasticity can be prevented. The large-deformation drawing is matched with the supplementary low-temperature short-time stabilization annealing process, which reduces the vertical grain boundaries while ensuring the long straight grain boundaries, reduces the deformation energy storage, improves the high-temperature stability of the single-wire structure, and realizes the synchronous improvement of the conductivity and heat resistance (strength retention rate), and the comprehensive performance is greatly improved.

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

[0078] The holding time is 5 - 15 h. Specifically, it can be 5 h, 6 h, 7 h, 8 h, 9 h, 10 h, 11 h, 12 h, 13 h, 14 h, 15 h.

[0079] The hot continuous rolling speed and the pass size distribution in the present invention form the on-line annealing effect of the aluminum rod, and at the same time, the precise control of the cold drawing speed of different specifications of conductors provides the drawing heat to achieve the on-line annealing effect of the conductors, and the low-temperature stabilization annealing process of the finished wire is increased, realizing the improvement of the uniformity and stability of the high-temperature tissue performance during the application process.

[0080] The above-mentioned 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 - 4.5 mm, a conductivity of 62.0 - 62.8% IACS, a tensile strength of ≥165 MPa, a long-term heat-resistant temperature of 180 °C, and a short-term heat-resistant strength residual rate of ≥96% at 260 °C / 1 h.

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

[0082] The above-mentioned 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 - 4.5 mm, a conductivity of 62.0 - 62.8% IACS, a tensile strength of ≥165 MPa, a long-term heat-resistant temperature of 180 °C, and a short-term heat-resistant strength residual rate of ≥96% at 260 °C / 1 h.

[0083] And the above-mentioned wire can be used to prepare cables. Especially overhead transmission cables. The present invention does not limit the specific preparation method, and those well-known to those skilled in the art can be used.

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

[0085] 1) The present invention provides a high-strength, high-conductivity and heat-resistant conductor temperature control and cooling preparation process. By using a rare-earth ultra-micro alloying composition design, reasonably matching the casting temperature, the rotation speed of the crystallization wheel, the cooling water flow rate and the rolling speed, and using different upper and lower temperature zone cooling controls, a large-range targeted solid solution regulation in the solidification zone is realized, the cooling rate during the solidification and crystallization process is greatly increased, the on-line solid solution effect is realized, the grain structure is effectively refined and the full solid solution of rare-earth elements is achieved, obtaining a high-conductivity aluminum alloy casting blank with refined grains, uniform structure and high supersaturation, and the area fraction of the RE primary phase in the casting blank is greatly reduced.

[0086] 2) By matching high-temperature and low-speed rolling with dynamic aging, without an off-line annealing process, using the on-line annealing effect to induce the precipitation of dispersion phases and the nucleation of dynamic recrystallization by deformation, the proportion of the <100> direction recrystallization texture and recrystallized grains in the rolled aluminum alloy is greatly increased, effectively improving the uniformity of the structure and the consistency of the performance of the hot-rolled aluminum rod.

[0087] 3) Based on the tissue genetic effect of the high-uniformity hot-rolled aluminum rod, using a large-diameter hot-rolled aluminum rod (φ9.5 - φ15 mm), through a large cold deformation amount and precise control of the cold drawing deformation amount, a structure with strong shear <111> texture coupled with long straight grain boundaries is obtained, realizing the regulation of grain shape and orientation, and obtaining a slender-crystal high-conductivity aluminum wire.

[0088] 4) Different drawing speeds are adopted during the cold drawing of wire rods of different specifications to increase the temperature during the drawing process of wire rods, achieve in-line annealing during the drawing process, ensure a high elongation rate of the wire rods, and prevent wire breakage due to insufficient plasticity. The large-deformation drawing is matched with a supplementary low-temperature short-time stabilization annealing process to reduce the vertical grain boundaries while ensuring long straight grain boundaries, reduce the deformation energy storage, improve the high-temperature stability of the single-wire structure, and achieve simultaneous improvement in conductivity and heat resistance (strength retention rate), thus greatly enhancing the comprehensive performance.

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

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

[0091] In this application, the term "and / or" describes the relationship between related objects and indicates that there can be three relationships. For example, A and / or B can represent: A exists alone, A and B exist simultaneously, and B exists alone. Where A and B can be singular or plural.

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

[0093] It should be understood that as long as the present invention remains operable, the order of steps or the order of performing certain actions is not important. In addition, two or more steps or actions can be performed simultaneously.

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

[0095] In addition, the numerical ranges and parameters used to define the present invention are approximate values. Here, the relevant values in the specific embodiments have been presented as precisely as possible. However, any value will inevitably contain standard deviations caused by individual testing methods. Therefore, unless otherwise clearly stated, it should be understood that all ranges, quantities, values, and percentages used in this disclosure are modified by "about". Here, "about" generally means that the actual value is within plus or minus 10%, 5%, 1%, or 0.5% of a specific value or range.

[0096] It should be understood that in various embodiments of the present application, the magnitudes of the serial numbers of the above processes do not imply 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 to 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, where the embodiments show certain implementation manners 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, the following provides a detailed description of an alloy conductor material, its preparation method, and a cable provided by the present invention in combination with embodiments.

[0099] Example 1

[0100] The actual operation steps of a high-strength, high-conductivity, heat-resistant conductor temperature control and cooling preparation process in this embodiment are as follows:

[0101] I. Melting each component alloy in a first melting furnace, 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 is aluminum.

[0102] II. Purifying the melt, skimming the slag, standing still, transferring to a second melting furnace, standing still, skimming the slag, and degassing;

[0103] III. Continuously casting and rolling the mixture obtained in step II, where the casting temperature is 720 °C, the cooling rate in the starting area of the crystallization wheel is 35 °C / s, the cooling rate in the end area of the crystallization wheel is 65 °C / s, and the rotation speed of the crystallization wheel is 3.0 rpm. The rough rolling is divided into 4 passes, the starting rolling temperature of the rough rolling is 530 °C, and the final rolling temperature of the rough rolling is 410 °C; the finish rolling is divided into 6 passes, the inlet temperature of the finish rolling is 400 °C, and the outlet temperature of the finish rolling is 220 °C. The cross-section of the rough rolling billet is trapezoidal, the cross-sectional area at the inlet of the rough rolling is 2750 mm 2 , and the cross-sectional area at the outlet of the rough rolling is 850 mm 2 ; the odd-numbered passes of the finish rolling are triangular, the even-numbered passes are circular, and the cross-sectional area at the inlet of the finish rolling is 850 mm 2, the outlet cross-section is φ15mm. The proportion of the <100> - direction recrystallization texture in the obtained aluminum rod is 35%, and the proportion of recrystallized grains is 5.0%.

[0104] IV. The aluminum rod obtained in the third drawing step is drawn into aluminum wire. When the diameter range of the aluminum rod is φ9 - 15mm, the drawing speed is 60m / min; when the diameter range of the aluminum rod is φ4 - 9mm, the drawing speed is 40m / min; when the diameter range of the aluminum rod is φ1.2 - 4mm, the drawing speed is 30m / min; and the φ1.2mm aluminum wire is obtained.

[0105] V. The aluminum wire obtained in step IV is subjected to low - temperature stabilization annealing. The annealing heat treatment temperature is 180°C, and the holding time is 15h. A high - strength, high - conductivity and heat - resistant wire is obtained.

[0106] VI. The high - strength, high - conductivity and heat - resistant wire obtained in step V 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, and a residual strength rate of 96% after short - term heat - resistance at 260°C / 1h.

[0107] Example 2

[0108] The actual operation steps of a preparation process for a high - strength, high - conductivity and heat - resistant conductor with temperature control and cooling in this example are as follows:

[0109] I. Melting the alloy of each component in the first melting furnace, 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 is aluminum.

[0110] II. Purifying the melt, skimming the slag, standing still, transferring to the second melting furnace, standing still, skimming the slag, and degassing;

[0111] III. Continuously casting and rolling the mixture obtained in step II, where the casting temperature is 820°C, the cooling rate in the starting area of the crystallizing wheel is 45°C / s, the cooling rate in the ending area of the crystallizing wheel is 80°C / s, and the rotation speed of the crystallizing wheel is 4.5rpm. The rough rolling is divided into 4 passes, the starting rolling temperature of the rough rolling is 550°C, and the final rolling temperature of the rough rolling is 430°C; the finish rolling is divided into 10 passes, the inlet temperature of the finish rolling is 430°C, and the outlet temperature of the finish rolling is 350°C. The cross - section of the rough - rolled billet is trapezoidal, the cross - sectional area at the inlet of the rough rolling is 2950mm 2 , the cross - sectional area at the outlet of the rough rolling is 1080mm 2 ; the odd - numbered passes of the finish rolling are triangular, the even - numbered passes are circular, the cross - sectional area at the inlet of the finish rolling is 1080mm 2 , and the outlet cross - section is φ9.5mm. The proportion of the <100> - direction recrystallization texture in the obtained aluminum rod is 48%, and the proportion of recrystallized grains is 20.0%.

[0112] IV. The aluminum rod obtained in the third drawing step is drawn into an aluminum wire. When the diameter range of the aluminum rod is φ9 - 9.5 mm, the drawing speed is 80 m / min; when the diameter range of the aluminum rod is φ4.5 - 9 mm, the drawing speed is 55 m / min; an aluminum wire with a diameter of φ4.5 mm is obtained.

[0113] V. The aluminum wire obtained in step IV is subjected to low-temperature stabilization annealing. The annealing heat treatment temperature is 230 °C and the holding time is 5 h. A high-strength, high-conductivity and heat-resistant wire is obtained.

[0114] VI. The high-strength, high-conductivity and heat-resistant wire obtained in step V 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, and a residual strength ratio of 98% at 260 °C / 1 h for short-term heat resistance.

[0115] Example 3

[0116] The preparation process of a high-strength, high-conductivity and heat-resistant conductor with controlled temperature and controlled cooling in this example is as follows:

[0117] I. Melting the alloy of each component in the first melting furnace, 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 is aluminum.

[0118] II. Purifying the melt, skimming the slag, standing still, transferring to the second melting furnace, standing still, skimming the slag, and degassing;

[0119] III. Continuously casting and rolling the mixture obtained in step II, where the casting temperature is 750 °C, the cooling rate in the starting area of the crystallizing wheel is 40 °C / s, the cooling rate in the ending area of the crystallizing wheel is 70 °C / s, and the rotational speed of the crystallizing wheel is 3.8 rpm. The rough rolling is divided into 4 passes, the starting rolling temperature of the rough rolling is 580 °C, and the final rolling temperature of the rough rolling is 420 °C; the finish rolling is divided into 8 passes, the inlet temperature of the finish rolling is 420 °C, and the outlet temperature of the finish rolling is 300 °C. The cross-section of the rough rolling billet is trapezoidal, the cross-sectional area at the inlet of the rough rolling is 2800 mm 2 , and the cross-sectional area at the outlet of the rough rolling is 1000 mm 2 ; the odd passes of the finish rolling are triangular, the even passes are circular, the cross-sectional area at the inlet of the finish rolling is 1000 mm 2 , and the outlet cross-section is φ12 mm. The proportion of the <100> - oriented recrystallization texture in the obtained aluminum rod is 42%, and the proportion of recrystallized grains is 8.0%.

[0120] IV. The aluminum rod obtained in step III is drawn into an aluminum wire. When the diameter range of the aluminum rod is φ12 - 15 mm, the drawing speed is 70 m / min; when the diameter range of the aluminum rod is φ4 - 9 mm, the drawing speed is 45 m / min; when the diameter range of the aluminum rod is φ3 - 4 mm, the drawing speed is 30 m / min; an aluminum wire with a diameter of φ3.0 mm is obtained.

[0121] V. Low-temperature stabilization annealing of the aluminum wire obtained in Step 4, with the annealing heat treatment temperature being 200°C and the holding time being 10 h. A high-strength and high-conductivity heat-resistant wire is obtained.

[0122] VI. The diameter of the high-strength and high-conductivity heat-resistant wire obtained in Step 5 is φ3.0 mm, the conductivity is 62.5% IACS, the tensile strength is 168 MPa, the long-term heat-resistant temperature is 180°C, and the strength residual rate at 260°C / 1 h for short-term heat resistance is 97%.

[0123] Comparative Example 1

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

[0125] I. Melting the alloy of each component in the first melting furnace, including: B 0.01%, Fe 0.01%, Si 0.01%, (V + Ti + Cr + Mn) 0.02%, and the balance being aluminum.

[0126] II. Purifying the melt, skimming the slag, standing still, transferring to the second melting furnace, standing still, skimming the slag, and degassing;

[0127] III. Continuous casting and rolling of the mixture obtained in Step II, with the casting temperature being 700°C, the cooling rate in the starting area of the crystallizing wheel being 30°C / s, the cooling rate in the ending area of the crystallizing wheel being 55°C / s, and the rotational speed of the crystallizing wheel being 2.0 rpm / min. The rough rolling is divided into 4 passes, the starting rolling temperature of the rough rolling is 550°C, and the ending rolling temperature of the rough rolling is 400°C; the finish rolling is divided into 6 passes, the inlet temperature of the finish rolling is 380°C, and the outlet temperature of the finish rolling is 200°C. The cross-section of the rough rolling billet is trapezoidal, the inlet cross-sectional area of the rough rolling is 2750 mm 2 , and the outlet cross-sectional area of the rough rolling is 850 mm 2 ; the odd passes of the finish rolling are triangular, the even passes are circular, the inlet cross-sectional area of the finish rolling is 850 mm 2 , and the outlet cross-section is φ15 mm. The proportion of the <100> -direction recrystallization texture in the obtained aluminum rod is 20%, and the proportion of recrystallized grains is 5.5%.

[0128] IV. Drawing the aluminum rod obtained in Step III to obtain an aluminum wire. When the diameter range of the aluminum rod is φ9 - 15 mm, the drawing speed is 40 m / min; when the diameter range of the aluminum rod is φ4 - 9 mm, the drawing speed is 30 m / min; when the diameter range of the aluminum rod is φ1.2 - 4 mm, the drawing speed is 25 m / min; an aluminum wire with a diameter of φ1.2 mm is obtained.

[0129] V. Low-temperature stabilization annealing of the aluminum wire obtained in Step IV, with the annealing heat treatment temperature being 150°C and the holding time being 3 h. A wire is obtained.

[0130] VI. The diameter of the wire obtained in Step V is φ1.2 mm, the conductivity is 61.8% IACS, the tensile strength is 110 MPa, the long-term heat-resistant temperature is 100°C, and the strength residual rate at 260°C / 1 h for short-term heat resistance is 56%.

[0131] Comparative Example 2

[0132] The difference between this comparative example and Example 1 is as follows: In Step 1, the alloy of each component is melted in the first melting 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. The proportion of recrystallization texture in the <100> direction of the aluminum rod obtained in Step 3 is 22%, and the proportion of recrystallized grains is 6.0%. The conductivity of the wire obtained in Step 6 is 61.0% IACS, the tensile strength is 120 MPa, the long-term heat-resistant temperature is 120 °C, and the residual strength rate at 260 °C / 1 h for short-term heat resistance is 60%.

[0133] Comparative Example 3

[0134] The difference between this comparative example and Example 1 is as follows: In Step 1, the alloy of each component is melted in the first melting 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. The proportion of recrystallization texture in the <100> direction of the aluminum rod obtained in Step 3 is 20%, and the proportion of recrystallized grains is 4.0%. The conductivity of the wire obtained in Step 6 is 61.6% IACS, the tensile strength is 160 MPa, the long-term heat-resistant temperature is 150 °C, and the residual strength rate at 260 °C / 1 h for short-term heat resistance is 74%.

[0135] Comparative Example 4

[0136] The difference between this comparative example and Example 1 is as follows: In Step 3, the casting temperature is 700 °C. The proportion of recrystallization texture in the <100> direction of the aluminum rod obtained in Step 3 is 16%, and the proportion of recrystallized grains is 3.0%. The conductivity of the wire obtained in Step 6 is 60.8% IACS, the tensile strength is 124 MPa, the long-term heat-resistant temperature is 130 °C, and the residual strength rate at 260 °C / 1 h for short-term heat resistance is 55%.

[0137] Comparative Example 5

[0138] The difference between this comparative example and Example 1 is as follows: In Step 3, the cooling rate in the starting area of the crystallizing wheel is 20 °C / s. The proportion of recrystallization texture in the <100> direction of the aluminum rod obtained in Step 3 is 12%, and the proportion of recrystallized grains is 3.4%. The conductivity of the wire obtained in Step 6 is 60.6% IACS, the tensile strength is 132 MPa, the long-term heat-resistant temperature is 130 °C, and the residual strength rate at 260 °C / 1 h for short-term heat resistance is 65%.

[0139] Comparative Example 6

[0140] The differences between this comparative example and Example 1 are as follows: In Step 3, the cooling rate in the final area of the crystallization wheel is 40 °C / s. The proportion of <100> - oriented recrystallization texture in the aluminum rod obtained in Step 3 is 16%, and the proportion of recrystallized grains is 2.8%. The conductivity of the wire obtained in Step 6 is 61.1% IACS, the tensile strength is 117 MPa, the long - term heat - resistant temperature is 140 °C, and the strength retention rate after short - term heat - resistance at 260 °C / 1 h is 62%.

[0141] Comparative Example 7

[0142] The differences between this comparative example and Example 1 are as follows: In Step 3, the rotation speed of the crystallization wheel is 2.0 rpm. The proportion of <100> - oriented recrystallization texture in the aluminum rod obtained in Step 3 is 12%, and the proportion of recrystallized grains is 3.8%. The conductivity of the wire obtained in Step 6 is 61.9% IACS, the tensile strength is 122 MPa, the long - term heat - resistant temperature is 160 °C, and the strength retention rate after short - term heat - resistance at 260 °C / 1 h is 58%.

[0143] Comparative Example 8

[0144] The differences between this comparative example and Example 1 are as follows: In Step 3, the ingot outlet temperature is 440 °C. The proportion of <100> - oriented recrystallization texture in the aluminum rod obtained in Step 3 is 9%, and the proportion of recrystallized grains is 2%. The conductivity of the wire obtained in Step 6 is 55.9% IACS, the tensile strength is 102 MPa, the long - term heat - resistant temperature is 90 °C, and the strength retention rate after short - term heat - resistance at 260 °C / 1 h is 45%.

[0145] Comparative Example 9

[0146] The differences between this comparative example and Example 1 are as follows: In Step 3, the finishing rolling temperature in rough rolling is 390 °C. The proportion of <100> - oriented recrystallization texture in the aluminum rod obtained in Step 3 is 10%, and the proportion of recrystallized grains is 3%. The conductivity of the wire obtained in Step 6 is 51.9% IACS, the tensile strength is 122 MPa, the long - term heat - resistant temperature is 100 °C, and the strength retention rate after short - term heat - resistance at 260 °C / 1 h is 65%.

[0147] Comparative Example 10

[0148] The differences between this comparative example and Example 1 are as follows: In Step 3, the finishing rolling temperature in finish rolling is 200 °C. The proportion of <100> - oriented recrystallization texture in the aluminum rod obtained in Step 3 is 6%, and the proportion of recrystallized grains is 1%. The conductivity of the wire obtained in Step 6 is 52.2% IACS, the tensile strength is 137 MPa, the long - term heat - resistant temperature is 90 °C, and the strength retention rate after short - term heat - resistance at 260 °C / 1 h is 45%.

[0149] Comparative Example 11

[0150] The difference between this comparative example and Example 1 lies in that: in Step 5, the stabilizing annealing is carried out at 110°C for 3 h. The proportion of <100> - oriented recrystallization texture in the aluminum rod obtained in Step 3 is 10%, and the proportion of recrystallized grains is 10%. The conductivity of the wire obtained in Step 6 is 60.2% IACS, the tensile strength is 144 MPa, the long - term heat - resistant temperature is 120°C, and the residual strength rate at 260°C / 1 h for short - term heat resistance is 65%.

[0151] Verification results:

[0152] Table 1 Compositions of Examples and Comparative Examples of the Present Invention

[0153]

[0154] Table 2 Process Parameters of High - Conductivity Heat - Resistant Wires of Examples and Comparative Examples of the Present Invention

[0155]

[0156] Table 3 Performance Tables of Wires Obtained from Examples and Comparative Examples of the Present Invention

[0157]

[0158] The above - mentioned are only the preferred embodiments of the present invention. It should be noted that for those of ordinary skill in the art, without departing from the principle of the present invention, several improvements and refinements can be made, and these improvements and refinements should also be regarded as the protection scope 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%, the balance is aluminum; Wherein RE is one or more of the rare earth elements Er, Y, Yb, and Ce.

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. The alloy conductor material according to claim 1, characterized in that: 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 residual rate of ≥96%.

4. A method for preparing the alloy conductor material according to any one of claims 1 to 3, characterized in that: The steps include: A) melting each component alloy to obtain a melt; B) purifying the melt, deslagging, letting it stand, smelting again, letting it stand, deslagging, degassing, and obtaining a mixed material; C) continuously casting and rolling the mixture obtained in step B) to obtain an aluminum rod; D) Drawing, annealing and heat-insulating the aluminum rod to obtain the aluminum rod.

5. The preparation method according to claim 4, characterized in that: Step C) In the continuous casting and rolling step: the casting temperature is 720-820°C, the cooling rate of the crystallization wheel starting zone is 35-45°C / s, the cooling rate of the crystallization wheel ending zone is 65-80°C / s, the crystallization wheel rotation speed is 3.0-4.5rpm; the ingot outlet temperature is 480-520°C.

6. The preparation method according to claim 4, characterized in that: Step C) In the continuous casting and rolling step: the rough rolling is divided into 4 passes, the rough rolling start rolling temperature is 530-580°C, and the rough rolling final rolling temperature is 410-430°C; the finishing rolling is divided into 6-10 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.

7. The preparation method according to claim 6, characterized in that: The rough rolling billet has a trapezoidal cross section, and the rough rolling inlet cross-sectional area 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%.

8. The preparation method according to claim 4, characterized in that: In step D), when the diameter of the aluminum rod is in the range of φ9-15 mm, the pulling speed is 60-80 m / min; when the diameter of the aluminum rod is in the range of φ4-9 mm, the pulling speed is 40-55 m / min; when the diameter of the aluminum rod is in the range of φ1.2-4 mm, the pulling speed is 30-38 m / min.

9. The preparation method according to claim 4, characterized in that: Step D) The annealing temperature is 180-230° C. and the holding time is 5-15 hours.

10. A cable, characterized in that: The invention is prepared by comprising the alloy conductor material according to any one of claims 1 to 3 or the alloy conductor material according to any one of claims 4 to 9.

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