Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
  • B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
  • B21C47/02—Winding-up or coiling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/06—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
  • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
  • C21D9/54—Furnaces for treating strips or wire
  • C21D9/56—Continuous furnaces for strip or wire
  • C21D9/573—Continuous furnaces for strip or wire with cooling
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/005—Ferrite
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/009—Pearlite

Definitions

• the present disclosure relates to a non-quenched and tempered steel rod wire with improved machinability and impact toughness and a method for manufacturing the same, and more particularly, to a non-quenched and tempered steel rod wire suitable for use as a material for automobiles or mechanical parts and a method for manufacturing the same.
• non-quenched and tempered steels are not only economically advantageous by reducing heat treatment costs, simplifying processes to shorten delivery time, and improving productivity, but also eco-friendly by reducing CO 2 that is generated by operating a furnace during heat treatment.
• non-quenched and tempered steels were applied only to parts that do not require high toughness due to relatively inferior toughness thereof to that of quenched and tempered steel.
• the present disclosure provides a non-quenched and tempered steel rod wire whose toughness, inferior to that of conventional quenched and tempered steels, is improved and having both impact toughness and machinability by decreasing grain sizes via TiN and AlN formation and inhibiting elongation of MnS via Ca addition without additional heat treatment, and a method for manufacturing same.
• a non-quenched and tempered steel rod wire with improved machinability and impact toughness includes, in percent by weight (wt%), 0.3% to 0.5% of C, 0.4% to 0.9% of Si, 0.5% to 1.2% of Mn, 0.02% or less of P, 0.01% to 0.05% of S, 0.01% to 0.05% of sol.Al, 0.1% to 0.3% of Cr, 0.01% to 0.02% of Ti, 0.0005% to 0.002% of Ca, 0.007% to 0.02% of N, and the remainder being Fe and inevitable impurities, also includes ferrite and pearlite as microstructures, and satisfies Relational Expression 1 below. 2 ⁇ Al + Ti / N ⁇ 5
• a method for manufacturing a non-quenched and tempered steel rod wire with improved machinability and impact toughness includes: reheating a steel piece including, in percent by weight (wt%), 0.3% to 0.5% of C, 0.4% to 0.9% of Si, 0.5% to 1.2% of Mn, 0.02% or less of P, 0.01% to 0.05% of S, 0.01% to 0.05% of sol.Al, 0.1% to 0.3% of Cr, 0.01% to 0.02% of Ti, 0.0005% to 0.002% of Ca, 0.007% to 0.02% of N, and the remainder being Fe and inevitable impurities in a temperature range of 950°C to 1120°C; finish rolling the reheated steel piece into a steel rod wire at a temperature of 750°C to 850°C; and winding the steel rod wire and cooling the steel rod wire to 400°C in an average cooling rate range of 0.1°C/s to 5.0°C/s.
• Ti and Al combine with N to form nitrides such as TiN and AlN, and such nitrides interfere with the growth of grain boundaries to decrease grain sizes, thereby improving toughness.
• a Ca-based oxide resulting from addition of Ca serves as a nucleus of MnS formation and inhibits elongation of MnS during rolling to improve machinability and toughness. Therefore, even if heat treatment is omitted, the steel rod wire may be applied to materials for automobiles or mechanical parts that require both machinability and toughness.
• a non-quenched and tempered steel rod wire with improved machinability and impact toughness includes, in percent by weight (wt%), 0.3% to 0.5% of C, 0.4% to 0.9% of Si, 0.5% to 1.2% of Mn, 0.02% or less of P, 0.01% to 0.05% of S, 0.01% to 0.05% of sol.Al, 0.1% to 0.3% of Cr, 0.01% to 0.02% of Ti, 0.0005% to 0.002% of Ca, 0.007% to 0.02% of N, and the remainder being Fe and inevitable impurities, also includes ferrite and pearlite as microstructures, and satisfies Relational Expression 1 below. 2 ⁇ Al + Ti / N ⁇ 5
• the present inventors have examined a method for providing a steel rod wire with machinability and impact toughness from various angles and have found that machinability and toughness may be obtained by appropriately controlling a composition of alloying elements and a microstructure of the steel rod wire without a separate heat treatment, thereby completing the present disclosure.
• a non-quenched and tempered steel rod wire with improved machinability and impact toughness includes, in percent by weight (wt%), 0.3% to 0.5% of C, 0.4% to 0.9% of Si, 0.5% to 1.2% of Mn, 0.02% or less of P, 0.01% to 0.05% of S, 0.01% to 0.05% of sol.Al, 0.1% to 0.3% of Cr, 0.01% to 0.02% of Ti, 0.0005% to 0.002% of Ca, 0.007% to 0.02% of N, and the remainder being Fe and inevitable impurities and satisfies Relational Expression 1 below. 2 ⁇ Al + Ti / N ⁇ 5
• the content of C is 0.3% to 0.5%.
• Carbon (C) is an element serving to improve strength of a steel rod wire. To obtain the above-described effect, it is preferable to include C in an amount of 0.3% or more. However, an excessive C content may deteriorate toughness and machinability, and thus the upper limit of the C content may be controlled to 0.5%.
• the content of Si is 0.4% to 0.9%.
• the content of Mn is 0.5% to 1.2%.
• Manganese (Mn) is an element effective as a deoxidizer and a desulfurizer. With a Mn content less than 0.5%, the above-described effect cannot be obtained. With a Mn content exceeding 1.2%, strength of the steel excessively increases to rapidly increase deformation resistance of the steel, resulting in deterioration of cold workability. Therefore, the upper limit of the Mn content may be controlled to 1.2%.
• the content of Cr is 0.1% to 0.3%.
• Chromium (Cr) is an element serving to promote transformation of ferrite and pearlite during hot rolling.
• Cr does not increase the strength of the steel more than necessary, reduces an amount of solid solution of C by precipitating carbides, and contributes to reduction in dynamic strain aging caused by solid solution of carbon.
• the upper limit of the Cr content may be controlled to 0.3%.
• the content of P is 0.02% or less.
• Phosphorus (P) is a major causative element of segregation into grain boundaries resulting in deterioration of toughness and reduction in delayed fracture resistance. Therefore, it is preferable to control the P content as low as possible. Theoretically, it is preferable to control the P content to 0% but P is inevitably included therein during a manufacturing process. Therefore, it is important to control the upper limit, and the upper limit of the P content may be controlled to 0.02% in the present disclosure.
• the content of S is 0.01% to 0.05%.
• S Sulfur
• MnS MnS
• the S content is controlled within a range of 0.01% to 0.05% in the present disclosure in consideration of an S content effective for improvement of machinability without significantly impairing toughness of the steel.
• the content of sol.Al is 0.01% to 0.05%.
• the sol.Al is an element effective as a deoxidizer.
• the sol.Al may be contained in an amount of 0.01% to obtain the above-describe effect.
• the upper limit of the Al content may be controlled to 0.05% in the present disclosure.
• the content of Ti is 0.01% to 0.02%.
• Titanium (Ti) is an element that plays a major role in improving toughness of a steel by decreasing grain sizes of a final structure by forming TiN precipitates during a solidification process of the steel to inhibit the growth of austenite crystal grains during heating and hot rolling processes of a slab. With a Ti content less than 0.01%, it is difficult to obtain a sufficient amount of TiN precipitates to inhibit migration of austenite grain boundaries. On the contrary, with a T content exceeding 0.02%, a coarse titanium nitride may be formed rather deteriorating toughness, and thus the upper limit of the Al content may be controlled to 0.02% in the present disclosure.
• the content of Ca is 0.0005% to 0.002%.
• Ca is an essential element to implement an effect on improving machinability and impact toughness by reducing an aspect ratio of MnS.
• Addition of Ca causes formation of an oxide, which serves as a nucleus of MnS, to inhibit elongation of MnS while rolling the steel rod wire and maintain a low aspect ratio.
• the low aspect ratio of MnS not only improves machinability but also inhibits deterioration of toughness by reducing anisotropy of a microstructure.
• Ca should be added in an amount of 0.0005% or more to obtain the above-described effects, but a Ca content exceeding 0.002% may cause difficulties in a manufacturing process. Therefore, the upper limit of the Ca content is controlled to 0.002%
• the content of N is 0.007% to 0.02%.
• N is an essential element for implementing an effect on improving impact toughness by decreasing grain sizes via formation of a nitride with Ti and Al.
• a N content less than 0.007%, it is difficult to obtain a sufficient amount of the nitride, resulting in a decrease in production of precipitates of Al, Ti, and the like, failing to obtain toughness desired in the present disclosure.
• a N content exceeding 0.02% a solid solution of N, not present as a nitride, increases to deteriorate toughness and ductility of the steel rod wire. Therefore, the upper limit of the N content may be controlled to 0.02% in the present disclosure.
• the remaining component of the non-quenched and tempered steel rod wire of the present disclosure is iron (Fe).
• the non-quenched and tempered steel rod wire may include other impurities incorporated during common industrial manufacturing processes of steels.
• the impurities are not specifically mentioned in the present disclosure, as they are known to any person skilled in the art of manufacturing.
• the non-quenched and tempered steel rod wire according to an embodiment of the present disclosure may satisfy Relational Expressions 1 to 3.
• Relational Expression 1 is an expression related to toughness.
• TiN and AlN are formed by adding high contents of N, Ti, and Al. Because precipitation of fine TiN and AlN in the steel inhibits the growth of crystal grains, grains are refined to improve impact toughness of the non-quenched and tempered steel rod wire according to the present disclosure. It is preferably to form TiN and AlN precipitates with a size of about 50 nm as many as possible to obtain the above-described effects, and to this end, the ([Al]+[Ti])/[N] ratio needs to be controlled in a range of 2 to 5. At a ([Al]+[Ti])/[N] ratio less than 2, the precipitates cannot be formed sufficiently.
• Relational Expression 2 is an expression related to machinability and impact toughness.
• MnS is formed by adding a high S content.
• MnS as an elongated inclusion, has a shape and an orientation elongated in a rolling direction and significantly improves machinability of the non-quenched and tempered steel rod wire of the present disclosure.
• MnS serving as a starting point of cracks and a propagation path thereof in the case of impact applied thereto, thereby deteriorating impact toughness. Therefore, Ca is added to inhibit elongation of MnS, and to this end, it is preferable to control the S/Ca ratio in the range of 10 to 70.
• Relational Expression 3 is an expression related to strength. C, Si, and Mn are elements with great solid solution strengthening effects. On the contrary, because S forms MnS to decrease an amount of Mn effective for contributing to solid solution strengthening, strength decreases. Therefore, the value of Relational Expression 3 needs to be controlled to 700 or more to obtain a strength of the steel rod wire of 700MPa or more.
• the non-quenched and tempered steel rod wire according to an embodiment of the present disclosure includes ferrite and pearlite as microstructures, and an average inter-layer spacing between ferrite and pearlite may be 10.0 to 15.0 ⁇ m, preferably, 12.0 to 13.0 ⁇ m.
• non-quenched and tempered steel rod wire may have a ferrite's thickness of 5.0 to 10.0 ⁇ m, preferably, 7.0 to 9.0 ⁇ m.
• non-quenched and tempered steel rod wire may have a ferrite's aspect ratio of 4 or less.
• non-quenched and tempered steel rod wire may have a tensile strength of 700 MPa or more.
• non-quenched and tempered steel rod wire may have a yield strength of 350 to 450 MPa.
• non-quenched and tempered steel rod wire may have a yield ratio of 0.45 to 0.65.
• non-quenched and tempered steel rod wire may have an impact toughness of 60 J/cm 2 or more.
• non-quenched and tempered steel rod wire may have a product of tensile strength and impact toughness of 30000 to 60000.
• the non-quenched and tempered steel rod wire with improved machinability and impact toughness according to the present disclosure may be manufactured by using various methods, and the methods are not particularly limited. However, the steel rod wire may be manufactured by using the following method according to an embodiment.
• a method for manufacturing a non-quenched and tempered steel rod wire with improved machinability and impact toughness includes: reheating a steel piece including, in percent by weight (wt%), 0.3% to 0.5% of C, 0.4% to 0.9% of Si, 0.5% to 1.2% of Mn, 0.02% or less of P, 0.01% to 0.05% of S, 0.01% to 0.05% of sol.Al, 0.1% to 0.3% of Cr, 0.01% to 0.02% of Ti, 0.0005% to 0.002% of Ca, 0.007% to 0.02% of N, and the remainder being Fe and inevitable impurities, and also including ferrite and pearlite as microstructures; hot rolling the reheated steel piece into a steel rod wire; and winding and cooling the steel rod wire.
• a bloom satisfying the above-described composition of alloying elements is heated and rolled into a billet.
• the reheating process is a process for lowering a rolling load while rolling the steel rod wire.
• the reheating may be performed at a temperature of 950°C to 1120°C.
• the rolling load may increase causing difficulties in the manufacturing method.
• a reheating temperature above 1,120°C all AlN finely formed in the pieces of the steel may form a solid solution again during heating, thereby significantly decreasing a grain refinement effect.
• the reheated pieces of the steel are hot-rolled into a steel rod wire.
• a finish rolling temperature of the hot rolling may be 750°C to 850°C.
• a rolling load may increase, and at a finish rolling temperature above 850°C, crystal grains may coarsen so that a high toughness desired in the present disclosure may not be obtained.
• a process of winding the steel rod wire manufactured as described above in the shape of a coil may be performed.
• a winding temperature may be 750°C to 850°C. Because a temperature of the steel rod wire obtained by finish rolling may increase by transformation heating, a temperature of the steel rod wire immediately before winding may be higher than a final rolling temperature. In this case, the steel rod wire may be wound after being cooled to a winding temperature or may be wound without a separate cooling process depending on the temperature increased by the heating.
• a winding temperature below 750°C martensite generated in a surface layer during cooling cannot be recovered due to residual heat, and tempered martensite is formed causing a problem of increasing a potential to induce surface defects during a drawing process.
• thick scales may be formed on the surface of the steel rod wire so that surface defects may easily occur during descaling and productivity may deteriorate due to an increase in cooling time in a subsequent cooling process.
• the wound steel rod wire may be cooled, and in this case, the cooling process may be performed to 400°C in an average cooling rate range of 0.1°C/s to 5.0°C/s by air cooling or control cooling after hot forging.
• the cooling process may be performed to 400°C in an average cooling rate range of 0.1°C/s to 5.0°C/s by air cooling or control cooling after hot forging.
• a desired strength cannot be obtained due to excessive formation of proeutectoid ferrite.
• At an average cooling rate higher than 5°C/s low-temperature structures such as martensite may be generated, and thus toughness and machinability may deteriorate.
• a bloom having a composition of alloying elements shown in Table 1 was heated at 1,200°C for 4 hours, and rolled into a billet at a finish rolling temperature of 1,100°C. Then, the billet was heated at 1090°C for 90 minutes, finish-rolled at 800°C, wound at 780°C, and cooled into a steel rod wire having a diameter of 26 mm.
• Steel rod wires including components of Inventive Steels 1 to 7 and Comparative Steels 1 to 4 were manufactured (Table 1) and tensile strength and impact toughness of samples of the steel rod wires were measured and shown in Table 2 below.
• room-temperature tensile strength was measured at the center of the samples of the non-quenched and tempered steels at 25°C
• room-temperature impact toughness was measured at the samples having a U-notch (based on a standard sample, 10x10x55 mm) at 25°C using a Charpy impact energy value obtained by the Charpy impact test.
• the steel rod wire having a diameter of 26 mm were processed with a reduction rate of 14.8% into cold drawn bars (CD-Bars) with a diameter of 24 mm.
• the machinability was evaluated by using a CNC lathe, and fragmentation of turned chips was evaluated after performing turning operations until the diameter of 24 mm of CD-Bars decreased to a diameter of 15 mm.
• cutting was performed under the conditions of a cutting rate of 100 mm/min, a feed rate of 0.1 mm/rev, and a cutting depth of 1.0 mm by using a cutting oil.
• Fragmentation of cut chips was evaluated based on the number of turns of the cut chips produced during a turning process, 5 or less of cut chips was evaluated as good, more than 5 but not more than 10 of cut chips was evaluated as fair, and more than 10 cut chips was evaluated as poor.
• the steel rod wires of Examples 1 to 7 satisfying all of the chemical composition, the relational expressions, and the manufacturing conditions provided in the present disclosure had tensile strengths of 700 MPa or more, impact roughnesses of 60 J/cm 2 or more, and good machinability.
• the steel rod wires of Comparative Examples 1 to 7 not satisfying at least one of the above-described conditions had one or more poor property among tensile strength, machinability, and impact toughness.
• Comparative Example 1 having a low C content could not satisfy the suggested tensile strength or 700 MPa or more, and Comparative Example 2 having an excess of Si and a S/Ca value of only 8 had poor machinability.
• Comparative Example 3 not satisfying the suggested Mn content and Relational Expression 3 could not obtain sufficient strength.
• Comparative Example 4 including an excess of Ti and not satisfying Relational Expression 1 had insufficient toughness.
• Comparative Examples 5 to 7 satisfied the chemical composition suggested by the present disclosure, the heating temperatures were out of the suggested range or the average cooling rates were not satisfied while cooling to 400°C, and thus toughness and tensile strength were out of the target vales.
• a non-quenched and tempered steel rod wire with both improved machinability and toughness may be provided even when heat treatment is omitted, and therefore the present disclosure has industrial applicability.

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• 2023
  • 2023-05-26 CN CN202380034024.6A patent/CN119013428A/zh active Pending
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