CN113035457B - Preparation method of aluminum-clad steel core aluminum alloy stranded wire - Google Patents
Preparation method of aluminum-clad steel core aluminum alloy stranded wire Download PDFInfo
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- CN113035457B CN113035457B CN201911252863.7A CN201911252863A CN113035457B CN 113035457 B CN113035457 B CN 113035457B CN 201911252863 A CN201911252863 A CN 201911252863A CN 113035457 B CN113035457 B CN 113035457B
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Abstract
The invention provides a preparation method of an aluminum-clad steel core aluminum alloy stranded wire, which is characterized in that an aluminum-clad steel wire arranged on a wire core and an aluminum alloy wire arranged on the periphery of the wire core are stranded into the aluminum-clad steel core aluminum alloy stranded wire, and the performance of the aluminum-clad steel wire meets the following conditions: the tensile strength is more than or equal to 1850MPa; the elongation at break is more than or equal to 2.5 percent; the elongation after fracture is more than or equal to 2.0 percent; the torsion is more than or equal to 20 circles; the aluminum alloy wire is formed by performing online stable casting on an aluminum-magnesium-silicon alloy melt after ceramic filter plates and multistage electromagnetic purification, wherein the residual rate of impurities with the particle size of more than 1 mu m in the purified aluminum-magnesium-silicon alloy melt is less than or equal to 6.2%. The invention eliminates the potential fatigue crack source by improving the matching degree of the elongation after fracture of the aluminum-clad steel wire core layer and the aluminum alloy wire and controlling the impurity content of the aluminum alloy wire, thereby improving the integral breaking force and the anti-fatigue property of the stranded wire.
Description
Technical Field
The invention relates to the technical field of metal wires, in particular to a preparation method of an aluminum-clad steel core aluminum alloy stranded wire.
Background
GB/T17937-2009 "electrician aluminum clad steel wire" stipulates that the elongation after fracture of the aluminum clad steel wire is not less than 1.0%, GB/T23308-2009 "aluminum-magnesium-silicon alloy round wire for overhead stranded wire" stipulates that the elongation of the LHA1 type aluminum alloy wire is not less than 3.0%. To traditional aluminum alloy core aluminum stranded conductor, because the elongation mismatch after the disconnected of sandwich layer aluminium package copper wire and conductor layer aluminum alloy wire, when the wire received the load, the preferential fracture of sandwich layer aluminium package steel for the tensile strength of aluminium package steel core can not exert completely, thereby influences the power of breaking of whole wire. Even if the monofilament with standard requirements is used, the requirement that the actual breaking force of the finished stranded wire is more than or equal to 95 percent of rated breaking force specified in GB/T1179-2017 circular wire concentric stranded overhead conductor cannot be met. The defect restricts the wide application of the aluminum-clad steel wire in the overhead transmission line. In order to solve the problem of exertion of the breaking force of the aluminum (aluminum alloy) stranded wire of the aluminum-clad steel core, manufacturers of the wires actually set respective internal control indexes on the basis of standard values, and usually need to improve 50-100MPa on the basis of the standard, namely, the breaking force required by the design is ensured by improving the tensile strength of the aluminum-clad steel core single wire.
However, for the aluminum-clad steel core aluminum alloy stranded wire for large span, the requirement of large span can be met by adopting the high-strength aluminum-clad steel core aluminum alloy stranded wire in the design process because the line condition is harsh. However, when the conductor manufacturers supply the materials, the tensile strength of the aluminum-clad steel wire reaches the limit, and cannot be realized by improving the internal control index, so the actual breaking force of the large-span conductor cannot meet the design requirement. If the breaking force of the large-span lead cannot be guaranteed, great hidden danger is brought to the safety of the large-span line. Furthermore, the lack of fatigue resistance of current wires also makes the use of large-span lines of limited safety and stability.
Disclosure of Invention
In view of the above, there is a need for an improved method for preparing aluminum-clad steel-cored aluminum alloy strand.
The technical scheme provided by the invention is as follows: a preparation method of an aluminum-clad steel core aluminum alloy stranded wire comprises the steps of stranding an aluminum-clad steel wire arranged on a wire core and an aluminum alloy wire arranged on the periphery of the wire core into the aluminum-clad steel core aluminum alloy stranded wire,
the performance of the aluminum-clad steel wire meets the following conditions:
the tensile strength is more than or equal to 1850MPa;
the elongation at break is more than or equal to 2.5 percent;
the elongation after fracture is more than or equal to 2.0 percent;
the torsion is more than or equal to 20 circles;
the aluminum alloy wire is formed by performing online stable casting on an aluminum-magnesium-silicon alloy melt after ceramic filter plates and multistage electromagnetic purification, wherein the residual rate of impurities with the particle size of more than 1 mu m in the purified aluminum-magnesium-silicon alloy melt is less than or equal to 6.2%.
Further, the preparation of the aluminum-clad steel wire comprises aging treatment and/or surface treatment after the aluminum-clad steel material is coated, wherein the step of surface treatment is arranged after the step of aging treatment.
Further, the aging treatment comprises offline aging treatment or online aging treatment, wherein the temperature in an aging furnace in the offline aging treatment is controlled to be 150-300 ℃, and the heat preservation time is controlled to be 3-8h; the heating power of the induction heating device in the online aging treatment is controlled to be 10-20kw, and the drawn speed of the aluminum material coated steel is controlled to be 100-180m/min.
Further, the surface treatment is realized by drawing the aluminum material coated steel material out of a die with the aperture of 1-3mm smaller than the wire diameter of the aluminum material coated steel material, wherein the drawing speed is controlled at 2-5m/s.
Further, before the step of the aluminum-magnesium-silicon alloy melt passing through the ceramic filter plate and the multistage electromagnetic purification, the method comprises the following steps:
mixing aluminum ingots with the purity of 99.7%, aluminum-silicon alloy ingots and magnesium ingots, and removing slag and gas by using a refining agent;
heating the aluminum-magnesium-silicon alloy melt to 730 +/-15 ℃ and stirring with a rotor, wherein the stirring speed of the rotor is 450 +/-50 r/min.
Further, the step of heating the aluminum magnesium silicon alloy melt to 730 ± 15 ℃ and stirring with the rotor and the step of subjecting the aluminum magnesium silicon alloy melt to ceramic filter plate and multistage electromagnetic purification comprises: the heated Al-Mg-Si alloy melt is degassed by electromagnetic stirring, and the hydrogen content is controlled at 0.15ml/100g AL by online measurement.
Further, the number of meshes per centimeter length of the ceramic filter plate is 20-30.
Further, the ceramic filter plate comprises a multi-layer screen.
Furthermore, the multistage electromagnetic purification is characterized in that a multilayer coil is vertically wound outside the ceramic tube, an axial alternating magnetic field is formed in the flow direction of the aluminum-magnesium-silicon alloy melt, the ceramic tube contains a porous channel, and tiny impurities with the particle size ranging from 1 mu m to 10 mu m deviate to the inner wall of the ceramic tube under the action of electromagnetic force when the aluminum-magnesium-silicon alloy melt flows through.
Furthermore, the ceramic tube contains a plurality of stages of porous channels, and the angular point of the outer wall of the next stage of porous channel is over against the center of the current stage of porous channel; or the outer wall corner point of the next-stage porous channel is over against the center of the overlapping hole of the previous multi-stage porous channel; or the porous channels with different pore sizes are arranged at intervals in a grading way; or the size of the holes of the porous channel is gradually reduced along with the flow direction of the aluminum-magnesium-silicon alloy melt.
Compared with the prior art, the preparation method of the aluminum-clad steel core aluminum alloy stranded wire provided by the invention has the advantages that the aluminum-clad steel wire with high strength and large elongation and the high-purity aluminum alloy wire are selected as raw materials to be stranded; on one hand, the elongation matching performance of the aluminum-clad steel wire of the core layer and the aluminum alloy wire of the outer layer is high, so that the actual breaking force of the finished stranded wire is improved, and the safety of the overhead output line is ensured; on the other hand, impurities are effectively removed through filtering and multi-stage magnetic purification treatment of the aluminum-magnesium-silicon alloy melt, the crystallinity of the aluminum alloy wire is ensured through online stable casting, and a potential fatigue crack source is greatly eliminated, so that the fatigue resistance of the finished stranded wire is improved.
Drawings
The present invention will be described in further detail with reference to the accompanying drawings and specific embodiments.
Fig. 1 is a flow chart of manufacturing an aluminum-clad steel core aluminum alloy stranded wire in an embodiment of the present invention.
Fig. 2 is a schematic diagram of a multi-stage electromagnetic purification module according to an embodiment of the present invention.
Fig. 3 is another schematic view of the module of fig. 2.
Fig. 4 is a first structural view of the ceramic tube shown in fig. 2.
Fig. 5 is a second structural schematic diagram of the ceramic tube shown in fig. 2.
Fig. 6 is a third schematic structural view of the ceramic tube shown in fig. 2.
Fig. 7 is a fourth schematic structural view of the ceramic tube shown in fig. 2.
Fig. 8 is a schematic structural diagram of an aluminum-clad steel core aluminum alloy stranded wire in an embodiment of the invention.
Description of reference numerals:
Overlapping holes 13b of multi-stage channels
Overlapping holes 135b of multi-stage channels
Primary porous channel 101
Secondary porous channel 103
Tertiary porous channel 105
Aluminum clad steel core aluminum alloy stranded wire 3
Aluminium clad steel wire 1
Aluminum alloy wire 2
The following detailed description further illustrates embodiments of the invention in conjunction with the above-described figures.
Detailed Description
So that the manner in which the above recited objects, features and advantages of embodiments of the present invention can be understood in detail, a more particular description of the invention, briefly summarized above, may be had by reference to the embodiments thereof which are illustrated in the appended drawings. In addition, the features of the embodiments of the present application may be combined with each other without conflict.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of embodiments of the invention, and the described embodiments are merely some, but not all embodiments of the invention. All other embodiments obtained by a person of ordinary skill in the art based on the embodiments of the present invention without any creative effort belong to the protection scope of the embodiments of the present invention.
As used herein, "elongation at break" refers to the percentage of the length of a material before and after stretching to the length before stretching when the material is subjected to an external force until it is broken by stretching.
As used herein, "elongation after elongation" refers to the percentage of the elongation before and after stretching to the elongation before stretching after the material is subjected to an external force (tensile force) until it breaks.
The refining agent is white powder or granular flux, is prepared by drying multiple inorganic salts and mixing the inorganic salts according to a certain proportion, and is mainly used for removing hydrogen and floating oxidation slag inclusion in molten aluminum. Is mainly purchased from the market.
In the present context, "skin effect", when there is an alternating current or an alternating electromagnetic field in a conductor, the current distribution inside the conductor is not uniform, and the current is concentrated on the "skin" part of the conductor, that is, the current is concentrated on a thin layer on the outer surface of the conductor, and the closer to the surface of the conductor, the higher the current density is, and the smaller the current is actually inside the conductor. As a result, the resistance of the conductor increases, so that its power loss also increases. This phenomenon is called skin effect.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which embodiments of the present invention belong. The terminology used herein in the description of the invention is for the purpose of describing particular embodiments only and is not intended to be limiting of the embodiments of the invention.
Referring to fig. 1, the present invention provides a method for preparing an aluminum-clad steel core aluminum alloy stranded wire 3, which improves the defects of the finished stranded wire (wire) in terms of breaking force and fatigue resistance, so as to meet the use requirements of a long span line.
The method comprises the following specific steps:
step S1: an aluminum clad steel wire 1 and an aluminum alloy wire 2 were prepared. Wherein, the first and the second end of the pipe are connected with each other,
(S11) the performance of the aluminum-clad steel wire 1 meets the following conditions:
the tensile strength is more than or equal to 1850MPa;
the elongation at break is more than or equal to 2.5 percent;
the elongation after fracture is more than or equal to 2.0 percent;
the torsion is more than or equal to 20 circles.
The aluminum-clad steel wire 1 meeting the above properties can be modified by the following process:
the method I comprises the following steps: after the aluminum material is coated with the steel material, the aging treatment is performed.
Wherein the aging treatment comprises offline aging treatment or online aging treatment, the temperature in an aging furnace in the offline aging treatment is controlled to be 150-300 ℃, and the heat preservation time is controlled to be 3-8h; the heating power of the induction heating device in the online aging treatment is controlled to be 10-20kw, and the drawn speed of the aluminum material coated steel is controlled to be 100-180m/min.
The second method comprises the following steps: after the aluminum material is coated with the steel material, the surface treatment is performed thereon. Specifically, the surface treatment is to realize surface hardening by drawing the aluminum-coated steel material out of a die having a hole diameter of 1 to 3mm smaller than the wire diameter thereof, wherein the drawing speed is controlled to 2 to 5m/s.
The third method comprises the following steps: after the aluminum material is coated with the steel material, the aging treatment of the first embodiment and the surface treatment of the second embodiment are sequentially performed. According to practical experience, the aluminum-clad steel wire 1 modified by the method has good comprehensive performance and high matching degree of strength, elongation after fracture and aluminum alloy wires.
(S12) the aluminum alloy wire 2 is formed by casting the aluminum-magnesium-silicon alloy melt stably on line after ceramic filter plates and multi-stage electromagnetic purification. The ceramic filter plate is used for filtering and removing more than 90% of particles with the particle size of more than 10 mu m. The residual rate of impurities with the particle size of more than 1 mu m in the aluminum-magnesium-silicon alloy melt after the multi-stage electromagnetic purification is less than or equal to 6.2 percent.
The specific preparation steps of the aluminum alloy wire 2 refer to the following:
s121: mixing an aluminum ingot, an aluminum-silicon alloy ingot and a magnesium ingot with the purity of 99.7 percent, and deslagging and degassing (mainly hydrogen) by adopting a refining agent.
S123: heating the aluminum-magnesium-silicon alloy melt to 730 +/-15 ℃ and stirring with a rotor, wherein the stirring speed of the rotor is 450 +/-50 r/min.
S125: the Al-Mg-Si alloy melt flows through the ceramic filter plate for filtering. The removal rate of the particles with the size of more than 10 mu m can reach 90 percent through the step. Specifically, the mesh number in each centimeter of length of the ceramic filter plate is 20-30, the large particle removal effect is not ideal enough when the mesh number is large, and the melt flow speed is limited and the treatment efficiency is low when the mesh number is small. In a specific embodiment, the ceramic filter plate may comprise a plurality of layers of screens, and the large-particle impurities with the particle size of more than 10 μm are removed by multiple filtration considering the melt flow rate.
S127: and performing multistage electromagnetic evolution on the filtered aluminum-magnesium-silicon alloy melt. In a specific embodiment, the multi-stage electromagnetic purification is implemented by vertically wrapping a multi-layer coil 30 outside the ceramic tube 10, as shown in fig. 2 and 3, forming an axial alternating magnetic field in the flow direction of the almgsi melt, wherein the ceramic tube 10 contains a porous channel 100, and when the almgsi melt flows through, tiny impurities with particle size ranging from 1 μm to 10 μm are deflected to the inner wall of the ceramic tube 10 under the electromagnetic force, that is, an induced magnetic field is formed inside the almgsi melt by passing an alternating current inside the coil, and a lorentz force is generated under the action of the alternating magnetic field. According to the lorentz law, the electrical conductors are subjected to a lorentz force directed towards the middle of the ceramic tube, and the non-conductive inclusions are forced to gather towards the wall of the ceramic tube 10 and are captured by the wall of the tube during the flow. Specifically, the ceramic tube 10 is viewed from the front in the flow direction of the aluminum-magnesium-silicon alloy melt, and contains a multi-stage porous channel. For example, in the first embodiment shown in fig. 4, an outer wall corner point of a subsequent-stage porous channel is directly opposite to the center of a current-stage porous channel, taking a first-stage porous channel 101 and a second-stage porous channel 103 as an example, an outer wall corner point 103a of a certain second-stage channel is directly opposite to the center of a hole of the first-stage porous channel, or in other words, an outer wall corner point 103a of the second-stage channel is located at the center of a hole surrounded by outer wall corner points 101a of four first-stage channels, or multiple stages of similar combinations are alternately arranged; as shown in fig. 5, in the second embodiment, the corner point of the outer wall of the subsequent multi-stage porous channel is opposite to the center of the overlapping hole of the previous multi-stage porous channel; taking the first-stage porous channel 101, the second-stage porous channel 103 and the third-stage porous channel 105 as examples, the holes formed by the outer wall corner points 101a of the four first-stage porous channels and the holes formed by the outer wall corner points 103a of the four second-stage porous channels have overlapping holes 13b, and in the embodiment, the overlapping holes 13b are one fourth of a single hole of the porous channel; the holes formed by the corner points 105a of the outer walls of the four tertiary porous channels and the overlapped holes 13b also form new overlapped holes 135b, and in the embodiment, the overlapped holes 135b are one fourth of the overlapped holes 13b, or are alternately arranged in a multi-stage similar combination manner; as shown in fig. 6, the porous channels with different pore sizes in the third embodiment are arranged at intervals in a graded manner, for example, in this embodiment, the pore size of the secondary channel 103 is one fourth of the pore size of the primary channel 101, or multiple stages of similar combinations are alternately arranged; in a fourth embodiment as shown in fig. 7, the size of the single pores of the porous channels (101, 103, 105) is gradually reduced along the flow direction of the aluminum-magnesium-silicon alloy melt. In a specific embodiment, the high removal rate of the micro particles is realized in the form of a weak processing area which is gradually contracted or strengthened by overlapping in the central area of the channel with weaker magnetic field intensity. In other embodiments, the above embodiments may be combined or modified, for example, the size of the overlapped holes is not one fourth, and the like, and the equivalent effect of removing the micro-impurities with a removal rate of 93% or more in the range of 1 μm to 10 μm can be achieved.
S129: and (4) performing on-line stable flow casting to form the aluminum alloy wire.
In a specific embodiment, after step S123 and before step S125, step S124 may be further included: and degassing the heated Al-Mg-Si alloy melt through electromagnetic stirring, wherein the gas in the step is mainly hydrogen, and the content of the hydrogen is controlled to be 0.15ml/100g AL through online measurement. The on-line stable casting means that the real-time monitoring of the casting liquid level is realized through a high-precision laser liquid level meter (for example, the precision is 1 mm), and the automatic control of the casting liquid level is realized by adjusting a lever mechanism through a monitored liquid level signal.
Step S2: a plurality of aluminum-clad steel wires are bundled together to form a wire core, aluminum alloy wires are arranged on the periphery of the wire core, and then the aluminum-clad steel wires and the aluminum alloy wires are twisted into the aluminum-clad steel core aluminum alloy stranded wire.
Through the steps, the breaking force of the formed aluminum-clad steel-cored aluminum alloy stranded wire JLHA1/QSLB14-500/230-42/37 is not less than 483.23KN; the anti-fatigue vibration times of the stranded wire is more than or equal to 3.0 x 10 7 And secondly, the aluminum alloy wire and the aluminum-clad steel wire have no broken strands.
The properties of the aluminum-clad steel core aluminum alloy stranded wire formed by the method of the invention are compared with those of the existing product.
Example 1
The high-strength high-elongation aluminum-clad steel wire is prepared by taking a high-carbon steel wire rod and an electrical round aluminum rod as raw materials, putting the high-carbon steel wire rod and the electrical round aluminum rod into an aging furnace, heating to 180 ℃, and preserving heat for 6 hours to modify the aluminum-clad steel wire.
The aluminum alloy wire with high fatigue resistance takes an aluminum ingot with the purity of 99.7 percent as a raw material, and the aluminum ingot, the aluminum-silicon alloy ingot and the magnesium ingot are smelted and cast into the aluminum alloy wire in the following process:
(1) In the heat-insulating furnace, powdery refining agent and inert gas (such as argon or nitrogen) are mixed and sprayed into molten aluminum through a spray pipe to remove slag and gas.
(2) The aluminum liquid flows to a refining furnace through a heat preservation furnace, the refining furnace is heated to 730 +/-15 ℃, and the rotor speed of the refining furnace is 450 +/-50 revolutions per minute. With electromagnetic stirring, degassing was again carried out, and the hydrogen content was controlled at 0.15ml/100g AL by on-line measurement.
(3) A 30-mesh ceramic filter plate is used in a launder for primary filtration to remove large-particle non-metallic impurities;
(4) After primary filtration, a multi-stage electromagnetic purification system is added in the flow tank for fine filtration, so that impurities with the particle size of more than 1 micron are effectively removed;
(5) After the aluminum alloy liquid is subjected to double filtration, the impurity removal rate of more than 1 mu m reaches 93.8 percent, and then the aluminum alloy liquid is remained to a pouring ladle opening through a launder for on-line stable casting to form an aluminum alloy wire.
Arranging the high-strength high-elongation aluminum-clad steel core aluminum alloy stranded wires JLHA1/QSLB14-500/230-42/37 according to the structural form shown in FIG. 8, taking 37 high-strength high-elongation 14-percent IACS aluminum-clad steel wires in four layers as reinforcing cores, and sequentially arranging the reinforcing cores into 1 layer, 6 layers, 12 layers and 18 layers; the reinforced core is spirally wound with two layers of 42 LHA1 type aluminum alloy wires, the aluminum alloy wires are sequentially arranged into 18 layers and 24 layers, and the spiral winding directions of the two adjacent layers of aluminum alloy wires are opposite. And integrally twisting to obtain the aluminum-clad steel core aluminum alloy stranded wire.
By design, the rated breaking force of the aluminum-clad steel core aluminum alloy strand JLHA1/QSLB14-500/230-42/37 strand of the embodiment is not less than 508.66KN, and the actual breaking force thereof needs not less than 483.23KN (508.66 multiplied by 0.95). Through detection, the actual breaking force is 516.8KN, compared with the existing product, the actual breaking force in the example is more than or equal to 95% of the rated breaking force, and the actual breaking force in the example far exceeds the design requirement and can meet the use requirement of a large-span lead.
The method for detecting the fatigue resistance of the stranded wire is carried out according to Q/FSDYS 007 'overhead line and ground wire vibration fatigue test method', and the test result shows that the fatigue resistance vibration times of the stranded wire are more than or equal to 3.0 x 10 7 Next, no broken strands of aluminum alloy wire and aluminum-clad steel wire were found.
In other embodiments, the aluminum-clad steel wire can be stranded into a stranded wire by adopting an aluminum alloy wire obtained under the conditions of online aging treatment, online aging treatment and surface treatment, or other multi-stage electromagnetic purification systems, and the actual breaking force of the stranded wire is also far greater than 95% of the standard required rated breaking force through a performance test; and the anti-fatigue vibration times of the stranded wire is more than or equal to 3.0 x 10 7 And secondly, the aluminum alloy wire and the aluminum-clad steel wire do not have the phenomenon of strand breakage.
In conclusion, the aluminum-clad steel wire with high elongation and high strength is obtained through modification, so that the elongation of the aluminum-clad steel wire after the aluminum alloy wire is broken is matched, and the actual breaking force of the stranded wire is improved. And the Al-Mg-Si alloy melt is purified on line through double filtration, ceramic filtration (primary filtration) and a multi-stage electromagnetic purification technology (fine filtration) of the aluminum alloy melt, impurities with the size of more than 1 mu m are effectively removed, and a potential fatigue crack source is greatly eliminated, so that the fatigue resistance of the finished aluminum alloy wire is improved.
Although the embodiments of the present invention have been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that various changes may be made and equivalents may be substituted without departing from the spirit and scope of the embodiments of the present invention.
Claims (9)
1. A method for preparing an aluminum-clad steel core aluminum alloy stranded wire comprises stranding an aluminum-clad steel wire arranged on a wire core and an aluminum alloy wire arranged on the periphery of the wire core into a shape of the aluminum-clad steel core aluminum alloy stranded wire,
the performance of the aluminum-clad steel wire meets the following conditions:
the tensile strength is more than or equal to 1850MPa;
the elongation at break is more than or equal to 2.5 percent;
the elongation after fracture is more than or equal to 2.0 percent;
the torsion is more than or equal to 20 circles;
the aluminum alloy wire is formed by online stable casting of an aluminum-magnesium-silicon alloy melt after ceramic filter plates and multistage electromagnetic purification, wherein the residual rate of impurities with the particle size of more than 1 mu m in the purified aluminum-magnesium-silicon alloy melt is less than or equal to 6.2 percent;
the multistage electromagnetic purification is characterized in that a multilayer coil is vertically wound outside a ceramic tube, and an axial alternating magnetic field is formed in the flow direction of the aluminum-magnesium-silicon alloy melt;
wherein the ceramic tube contains a multi-stage porous channel, and the outer wall corner point of the next stage porous channel is over against the center of the current stage porous channel; or the outer wall corner point of the next-stage porous channel is over against the center of the overlapping hole of the previous multi-stage porous channel; or the porous channels with different pore sizes are arranged at intervals in a grading way; or the size of the pores of the porous channel is gradually reduced along with the flow direction of the aluminum-magnesium-silicon alloy melt.
2. The method of manufacturing an aluminum-clad steel-core aluminum alloy strand as claimed in claim 1, wherein the manufacturing of the aluminum-clad steel wire includes an aging treatment and/or a surface treatment after the aluminum-clad steel material is coated, wherein the surface treatment is provided after the aging treatment.
3. The method for manufacturing an aluminum-clad steel core aluminum alloy strand as claimed in claim 2, wherein: the aging treatment comprises offline aging treatment or online aging treatment, wherein the temperature in an aging furnace in the offline aging treatment is controlled to be 150-300 ℃, and the heat preservation time is controlled to be 3-8h; the heating power of the induction heating device in the online aging treatment is controlled to be 10-20kw, and the drawn speed of the aluminum material coated steel is controlled to be 100-180m/min.
4. The method for manufacturing an aluminum-clad steel core aluminum alloy strand as claimed in claim 2, wherein: the surface treatment realizes surface hardening by drawing the aluminum material coated steel material out of a die with the aperture being smaller than the wire diameter of 1-3mm, wherein the drawing speed is controlled at 2-5m/s.
5. The method for preparing the aluminum-clad steel core aluminum alloy stranded wire according to claim 1, wherein the aluminum-magnesium-silicon alloy melt is subjected to a ceramic filter plate and a multistage electromagnetic purification step, and the method comprises the following steps:
mixing an aluminum ingot with the purity of 99.7%, an aluminum-silicon alloy ingot and a magnesium ingot, and deslagging and degassing by adopting a refining agent;
heating the aluminum-magnesium-silicon alloy melt to 730 +/-15 ℃ and stirring with a rotor, wherein the stirring speed of the rotor is 450 +/-50 r/min.
6. The method for preparing the aluminum-clad steel core aluminum alloy stranded wire according to claim 5, wherein the step of heating the aluminum-magnesium-silicon alloy melt to 730 +/-15 ℃ with stirring of a rotor and before the step of subjecting the aluminum-magnesium-silicon alloy melt to ceramic filter plates and multistage electromagnetic purification comprises the following steps: the heated Al-Mg-Si alloy melt is degassed by electromagnetic stirring, and the hydrogen content is controlled at 0.15ml/100g AL by online measurement.
7. The method of manufacturing an aluminum-clad steel core aluminum alloy strand as recited in claim 1, wherein the number of mesh holes per cm length of said ceramic filter plate comprises 20 to 30.
8. The method for manufacturing an aluminum-clad steel core aluminum alloy strand as recited in claim 7, wherein: the ceramic filter plate comprises a multi-layer screen.
9. The method for manufacturing an aluminum-clad steel core aluminum alloy strand as claimed in claim 1, wherein: when the aluminum-magnesium-silicon alloy melt flows through the ceramic tube, tiny impurities with the particle size ranging from 1 mu m to 10 mu m are deflected to the inner wall of the ceramic tube under the electromagnetic force.
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| CN201911252863.7A CN113035457B (en) | 2019-12-09 | 2019-12-09 | Preparation method of aluminum-clad steel core aluminum alloy stranded wire |
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| CN201911252863.7A Active CN113035457B (en) | 2019-12-09 | 2019-12-09 | Preparation method of aluminum-clad steel core aluminum alloy stranded wire |
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