CN114734009B - Steel wire rod for ultrahigh-strength card clothing and manufacturing method thereof - Google Patents
Steel wire rod for ultrahigh-strength card clothing and manufacturing method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 64
- 239000010959 steel Substances 0.000 title claims abstract description 64
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 20
- 238000001816 cooling Methods 0.000 claims abstract description 24
- 238000005096 rolling process Methods 0.000 claims abstract description 22
- 238000000034 method Methods 0.000 claims abstract description 18
- 238000009749 continuous casting Methods 0.000 claims abstract description 15
- 238000000137 annealing Methods 0.000 claims abstract description 11
- 230000008569 process Effects 0.000 claims abstract description 10
- 238000005204 segregation Methods 0.000 claims abstract description 9
- 238000009987 spinning Methods 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 239000000126 substance Substances 0.000 claims abstract description 7
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 238000004321 preservation Methods 0.000 claims description 33
- 238000010438 heat treatment Methods 0.000 claims description 14
- FBPFZTCFMRRESA-JGWLITMVSA-N D-glucitol Chemical compound OC[C@H](O)[C@@H](O)[C@H](O)[C@H](O)CO FBPFZTCFMRRESA-JGWLITMVSA-N 0.000 claims description 13
- 238000007670 refining Methods 0.000 claims description 11
- 229910052799 carbon Inorganic materials 0.000 claims description 10
- 230000009467 reduction Effects 0.000 claims description 10
- 239000000463 material Substances 0.000 claims description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 238000005516 engineering process Methods 0.000 claims description 5
- 229910001562 pearlite Inorganic materials 0.000 claims description 5
- 238000013461 design Methods 0.000 claims description 4
- 238000007599 discharging Methods 0.000 claims description 4
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 3
- 238000003723 Smelting Methods 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 3
- 238000007664 blowing Methods 0.000 claims description 3
- 238000006243 chemical reaction Methods 0.000 claims description 3
- 229910052739 hydrogen Inorganic materials 0.000 claims description 3
- 239000001257 hydrogen Substances 0.000 claims description 3
- 229910052760 oxygen Inorganic materials 0.000 claims description 3
- 239000001301 oxygen Substances 0.000 claims description 3
- 238000012545 processing Methods 0.000 claims description 3
- 238000010079 rubber tapping Methods 0.000 claims description 3
- 238000003756 stirring Methods 0.000 claims description 3
- 238000004381 surface treatment Methods 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 238000006073 displacement reaction Methods 0.000 claims description 2
- 230000006698 induction Effects 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 238000009792 diffusion process Methods 0.000 claims 1
- 238000003825 pressing Methods 0.000 claims 1
- 230000002035 prolonged effect Effects 0.000 claims 1
- 238000010583 slow cooling Methods 0.000 claims 1
- 238000005554 pickling Methods 0.000 abstract description 3
- 239000012467 final product Substances 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 5
- 229910001567 cementite Inorganic materials 0.000 description 4
- 235000013339 cereals Nutrition 0.000 description 4
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910000677 High-carbon steel Inorganic materials 0.000 description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 3
- 238000009960 carding Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 238000002360 preparation method Methods 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 239000011593 sulfur Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 239000004753 textile Substances 0.000 description 3
- BPQQTUXANYXVAA-UHFFFAOYSA-N Orthosilicate Chemical compound [O-][Si]([O-])([O-])[O-] BPQQTUXANYXVAA-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- 238000010622 cold drawing Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000007613 environmental effect Effects 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000011068 loading method Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000002893 slag Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229920000742 Cotton Polymers 0.000 description 1
- 229910019582 Cr V Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910052729 chemical element Inorganic materials 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
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- 230000007423 decrease Effects 0.000 description 1
- 230000001934 delay Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 235000013312 flour Nutrition 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000011229 interlayer Substances 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000010534 mechanism of action Effects 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 1
- 238000005502 peroxidation Methods 0.000 description 1
- 230000005501 phase interface Effects 0.000 description 1
- 238000006116 polymerization reaction Methods 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 230000001932 seasonal effect Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- -1 wool Substances 0.000 description 1
- 210000002268 wool Anatomy 0.000 description 1
Classifications
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- 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
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/10—Supplying or treating molten metal
- B22D11/11—Treating the molten metal
- B22D11/114—Treating the molten metal by using agitating or vibrating means
- B22D11/115—Treating the molten metal by using agitating or vibrating means by using magnetic fields
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D41/00—Casting melt-holding vessels, e.g. ladles, tundishes, cups or the like
- B22D41/005—Casting melt-holding vessels, e.g. ladles, tundishes, cups or the like with heating or cooling means
- B22D41/01—Heating means
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/06—Deoxidising, e.g. killing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
-
- 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 by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
The invention relates to a steel wire rod for ultra-high strength card clothing and a manufacturing method thereof, wherein the steel wire rod comprises the following chemical components in percentage by mass: c:0.96% -1.20%, mn:0.20% -0.60%, si:0.10% -0.40%, P is less than or equal to 0.02%, S is less than or equal to 0.015%, cr:0.20% -0.60%, nb:0.01% -0.05%, V:0.05% -0.50% and the balance of Fe and unavoidable impurities. The production process of the invention comprises the following steps: continuous casting, cogging, rolling, spinning, stelmor cooling, and pickling annealing. The performance of the final product is ensured mainly through staged stelmor cooling control and a staged spheroidizing annealing process, and the final wire rod meets the following conditions: the tensile strength of the hot rolled wire rod with the specification phi of 5.5mm exceeds 1350Mpa, the surface shrinkage exceeds 30%, the microstructure grade of the annealed wire rod is less than or equal to 3 grades according to GB/T18254, the hardness is less than or equal to 210HV, and the center segregation is not more than 1 grade.
Description
Technical Field
The invention belongs to the technical field of iron-based special wires, and particularly relates to a steel wire for ultra-high strength card clothing and a manufacturing method thereof.
Background
Card clothing is an important spinning machine for carding textile fibers such as cotton, wool, chemical fibers and the like, and the surface is usually needle or tooth, and can be generally divided into two main types, namely elastic card clothing and metal card clothing. The comb is mainly made of high-carbon steel, and the failure mode is mainly abrasion and breakage, so the steel for the comb has high carbon content to meet the requirement of good abrasion resistance. In addition, since the drawing of a large deformation amount is required in the manufacturing process of the pin, the steel for the pin should also have excellent cold drawing properties and spheroidizing annealing properties.
For a long time, domestic clothing manufacturers mainly use foreign imported 80WV steel to manufacture high-performance comb needles, the performance of producing comb needles by using the steel tends to be limited, and imported steel products are high in cost and long in supply period, so that great trouble is caused to the domestic clothing manufacturers; with the progress of the technology, the requirements on the steel for card clothing and carding wires are also higher and higher, especially in the aspect of wear resistance, so that the development of a novel card clothing and carding wire alloy steel with higher carbon content and better performance is urgent.
The patent number CN 105838981A discloses a steel for card clothing, and particularly relates to the technical field of metal card clothing processing. The metal card clothing has high requirements on the strength, hardness and wear resistance of the material, and the components are designed by adding Nb, V and Ti into high-carbon steel for microalloying to form C, N compound to refine grains, so that the strength and the wear resistance are improved. However, the wire rod manufactured by the invention has lower carbon content and tensile strength, and can not meet the requirement of higher wear resistance of the existing card clothing card wire steel.
The patent publication No. CN 110295316A discloses a steel wire rod for a textile fluffing elastic card clothing and a preparation method thereof, and particularly relates to a steel wire rod for a wet fluffing elastic card clothing in the textile field and a production method thereof. The elastic card clothing is used for obtaining the card clothing steel wire rod which has good tissue performance, excellent surface quality and internal quality and is suitable for deep drawing by optimizing the element design of Mn, cr and Al in high-carbon steel and simultaneously optimizing the technological parameters of wire rod preparation, but the tensile strength of the wire rod manufactured by adopting the method cannot meet the requirements.
The patent CN 112899583A discloses a high-elasticity high-nickel alloy card clothing steel wire and a preparation method thereof, in particular to a wire for stainless steel wire card clothing and a production method thereof. The elastic clothing is used in wet weak alkaline environment by adding Ni and rare earth elements, has the characteristics of high elasticity, strong corrosion resistance and long service life, but the wire rod manufactured by adopting the invention has high manufacturing cost due to the addition of precious alloy and rare earth elements, and is not suitable for the trend of market cost reduction at present.
Disclosure of Invention
The technical problem to be solved by the invention is to provide an ultra-high strength card clothing steel wire and a manufacturing method thereof aiming at the prior art, and the obtained card clothing steel wire has the characteristics of high tensile strength and good toughness through chemical composition design and key production process parameter control.
The invention solves the problems by adopting the following technical scheme: the steel wire for the ultra-high strength card clothing comprises the following chemical components in percentage by mass: c:0.96% -1.20%, mn:0.20% -0.60%, si:0.10% -0.40%, P is less than or equal to 0.02%, S is less than or equal to 0.015%, cr:0.20% -0.60%, nb:0.01% -0.05%, V:0.05 to 0.50 percent, and the balance of Fe and unavoidable impurities, wherein C+Si+Mn+Cr is more than or equal to 1.5 percent, and Nb+V is more than or equal to 0.1 percent.
The mechanism of action of the chemical elements of the metal card clothing steel wire rod is as follows:
c is a main strengthening element in steel, the strength of the steel can be obviously improved through solid solution strengthening and precipitation strengthening, the strength is obviously increased along with the increase of the content of C, meanwhile, the hardening of the wire after cold drawing processing is obvious, the realization of the strength of a finished steel wire is facilitated, the content of C is improved, and the proportion of sorbite in the wire structure obtained through stelmor cooling is high, so that the content of C is controlled to be more than 0.96%.
Si is added into steel as deoxidizer to react with FeO in molten steel to form silicate for removal, so that purity of molten steel is improved, silicate inclusion is easy to extend and deform in a drawing direction in wire rod, damage of broken wire in drawing is avoided, solid solution strengthening of Si element improves work hardening rate of steel, cold workability of steel can be remarkably deteriorated, grain boundary segregation of element P, S is promoted, and therefore Si is 0.10-0.40% by weight.
Mn is added to steel as a strong deoxidizer, and Mn can improve the strength and wear resistance of steel, but for steel having a high C content, as the Mn content increases, the plasticity of steel decreases. Thus, the weight percentage of Mn is 0.20-0.60%.
Cr can improve the hardenability, strength, hardness and wear resistance of steel, in addition, cr can refine the interlayer spacing of pearlite sheets, is favorable for improving the sorbite proportion, is favorable for improving the drawing performance of the wire rod and inhibits the expansion of microcracks, but excessive Cr content can easily generate undissolved cementite, prolong the phase transformation ending time, easily generate supercooled structures such as troostite, martensite or bainite in hot rolled wire rods or drawn steel wires, has excessively high strength and poor plasticity, and obviously affects the drawing processability of the steel, so the weight percentage of Cr is 0.20-0.40%.
The Nb element can obviously improve the coarsening temperature and the recrystallization temperature of austenitization, and the size of sorbite is reduced while austenite grains are obviously refined. The smaller the sorbite mass size and lamellar spacing, the higher the wire strength and the better the plasticity. The reason for this is mainly that when ferrite and cementite sheets are thin, the phase interface increases, and the plastic deformation resistance increases under the action of external force. Moreover, since ferrite and cementite sheets are thin, the plastic deformability of the steel is increased. The size of the pearlite colony is reduced, which indicates that the arrangement direction of pearlite sheets in unit volume is increased, the size of plastic deformation is reduced, and the possibility of stress concentration caused by a great amount of plastic deformation locally is reduced, so that the strength of the wire rod is improved, and the plasticity of the wire rod is improved. In addition, nb element is slightly biased to grain boundary by Nb (C, N) in steel, thereby reducing mobility of the grain boundary and abnormal growth of austenite grain size of the tissue material in the heating process. In addition, nb exists in the steel in the form of substitution solute atoms, has a size larger than that of iron atoms, is easy to be biased to a dislocation line, has a strong dragging effect on the dislocation line, delays austenite deformation and recrystallization in the rolling process, and refines grains. Thus, the weight percentage of Nb is 0.01-0.05%.
The V element is a strong carbide forming element, and is used for forming very stable special carbide in the steel wire, so that the temperature range of card clothing quenching heating is widened, the austenite structure is thinned, and a fine martensite structure can be obtained after quenching. Meanwhile, the carbide has extremely high hardness, and after the card clothing is quenched, the carbide can be dispersed on a martensitic matrix, so that a microstructure with good toughness and high wear resistance can be obtained, and the wear resistance of the card clothing is effectively improved. However, these high hardness small particle carbides increase the deformation resistance of the semi-finished gauge steel wire upon cold rolling, so the amount added should not be too great. Thus, the weight percentage of V is 0.05-0.5%.
The P element belongs to harmful elements in the clothing steel, so that the plasticity and toughness of the steel are obviously reduced, and the performance is deteriorated. Meanwhile, phosphorus is easy to generate crystal segregation in the crystallization process, so that the phosphorus content in a local area is higher, the cold-embrittlement transformation temperature is increased, and cold-embrittlement occurs. The product needs to meet the requirements of a customer quenching and tempering process, and P needs to be controlled to be less than or equal to 0.02 percent in order to prevent the plastic toughness of the material from being reduced and the tempering brittleness from occurring.
The S element also belongs to harmful elements in the clothing steel, and reduces the ductility and toughness of the steel. In the solid state, sulfur has very little solubility in iron, but exists in the steel in the form of FeS. Because of the poor plasticity of FeS, steel with more sulfur is more brittle. More seriously, feS and Fe may form eutectic with low melting point (985 ℃ C.) and are distributed on the austenite grain boundaries. When the steel is heated to about 1200 ℃ for hot press working, eutectic crystals on grain boundaries are melted, inter-grain bonds are broken, and the steel is cracked along the grain boundaries during the working, i.e., hot shortness. In addition, sulfide nonmetallic inclusions formed by the partial polymerization of sulfur elements can form fibrous structures during rolling, so that the mechanical properties of the high-strength steel product are reduced. The product needs to be rolled by high-temperature heating and large rolling reduction, so that the S content is strictly controlled to be less than or equal to 0.015 percent.
The manufacturing method of the ultra-high strength card clothing steel wire comprises the following steps:
(1) Preparing materials according to design components, smelting by adopting a converter, strictly controlling tapping temperature to be more than 1620 ℃ and endpoint C% to be more than 0.15%, preventing peroxidation, refining by adopting a refining furnace, and refining by adopting special synthetic slag to ensure that impurities are removed by full deoxidation, accurately controlling according to target components, matching RH soft argon blowing after refining is finished, further removing impurities and ensuring molten steel uniformity;
(2) The continuous casting tundish adopts an induction heating technology to ensure low superheat degree pouring, the pulling speed is 0.5m/min, the soft reduction adopts a displacement mode, the reduction is carried out according to the set reduction, the pressure difference between each flow is combined to carry out proper adjustment, the end electromagnetic stirring technology is matched, the continuous casting blank is ensured to have no obvious soft reduction cracks, central shrinkage cavities and V-shaped segregation, the continuous carbon bias analysis is carried out in the inner arc direction and the outer arc direction of the intermediate blank, the carbon bias index is between 0.95 and 1.05, and the uniformity of the structure and the components of the continuous casting blank is ensured;
(3) Cogging a bloom continuous casting blank 390mm and 510mm into a 155mm and 155mm intermediate blank, heating and diffusing the blank at a high temperature above 1200 ℃ for more than 10 hours, effectively solving the problems of homogeneity and compactness of materials, ensuring good carbon segregation uniformity of wire rods, carrying out surface treatment on the intermediate blank to ensure no defects on the surface, heating the intermediate blank to above 1100 ℃, controlling the residual oxygen content in a furnace to be below 5%, carrying out heat preservation for 2 hours, discharging, and carrying out rolling after descaling by high-pressure water: the initial rolling temperature is 1000 ℃, the rolling process is divided into 39 passes of rolling, the rolling speed is set to 105m/s, and the wire rod with phi of 5.5mm is rolled;
(4) Spinning, wherein the spinning temperature is 850-950 ℃;
(5) The stelmor cooling line is subjected to air cooling, the conversion of sorbite is realized in the air cooling process, the opening degree of a fan is adjusted online, the cooling rate between 900 ℃ and 700 ℃ of spinning temperature is ensured to be more than 20 ℃/s, and the wire rod is ensured to be rapidly cooled to inhibit the precipitation of the network cementite; when the temperature is 700-650 ℃, the cooling rate is ensured to be more than 15 degrees/s, and the sorbite proportion is ensured to be more than 90 percent; when the temperature reaches 600-650 ℃, the opening degree of the fan is properly reduced, and is generally maintained for 10-12 seconds, so that the full phase transformation of sorbite is ensured, the low-temperature phase transformation below 550 ℃ is avoided to generate low-temperature structures such as troostite, bainite and the like, the proportion of sorbite is improved, and the tensile property of the wire is improved. In practical application, the opening degree of the No. 1-7 fans on the Steyr cooling line is adjusted, and all the No. 7 rear fans are closed: setting the roller speed to be 0.85-0.95m/s, setting the ambient temperature to be 15-25 ℃, and setting the opening degree of a No. 1-7 fan: no. 1: 70-90%, no. 2: 60-80%, no. 3: 30-50%, number 4: 30-50%, no. 5: 30-50%, no. 6: 20-40%, no. 7: 20-40%;
(6) Loading the hot rolled wire rods into a bell-type furnace for spheroidizing annealing after pickling, adopting hydrogen protection in the whole process, and rapidly heating the hot rolled wire rods to 650 ℃ along with the furnace for the first time for heat preservation, wherein the heat preservation is carried out for 0.5-1h; after the first heat preservation, the wire rod is quickly heated to 790 ℃ for heat preservation for 0.5-1h; after the second heat preservation, the wire rod is controlled to be cooled to 780 ℃ for heat preservation for 4-5 hours; after the third heat preservation, the wire rod is rapidly cooled to 700 ℃ for heat preservation for 0.5-1h; and after the fourth heat preservation, the wire rod is controlled to be rapidly cooled to 650 ℃ for heat preservation for 3-4 hours, and finally, the wire rod is cooled and discharged from the furnace in a controlled manner, so that the microstructure after spheroidizing annealing is ensured to be granular pearlite, the structure grade is less than or equal to 3, and the hardness is less than or equal to 210HV. The temperature rising stage is set to ensure uniform temperature, the temperature rises to 790 quickly until the two-phase region begins to spheroidize, 780 keeps the temperature until dispersed carbide particles are obtained, 700 lowers the temperature to 700 to obtain tiny spherical carbide, and 650 keeps the temperature to reduce the hardness of the material.
Compared with the prior art, the invention has the advantages that:
based on the chemical components and the production method, the obtained phi 5.5mm hot rolled wire rod has the tensile strength of 1350-1450Mpa, surface shrinkage of 30-40%, the wire rod after spheroidizing annealing is rated according to GB/T18254 to be no more than 1 level, the microstructure level is no more than 3 levels, the hardness is no more than 210HV, and the deep drawing of a user can be satisfied.
Drawings
Fig. 1 is a schematic view of sorbite structure of a card wire according to the present invention;
fig. 2 is a schematic view of a card wire according to the present invention in a low-power;
fig. 3 is a schematic view of spheroidized structure of the card wire rod according to the present invention.
Detailed Description
The present invention is further illustrated by the following examples.
Adopting a converter for smelting at 120t, controlling the tapping temperature to 1650 ℃ and controlling the endpoint C% to 0.18%, then refining by a refining furnace, adopting low-alkalinity synthetic slag for refining to ensure full deoxidization and remove impurities, simultaneously accurately controlling according to target components, matching RH soft argon blowing after refining is finished, further removing impurities and ensuring molten steel uniformity; and then the molten steel is transferred to continuous casting, the pulling speed is 0.5m/min, the total rolling reduction is 12mm, the tail end is electromagnetically stirred at 1.5HZ/300A, and a continuous casting blank with the section size of 390mm and 510mm is cast.
Heating and diffusing a continuous casting blank at a high temperature of about 1250 ℃ for more than 10 hours, cogging into 155 mm-155 mm intermediate blanks, carrying out surface treatment on the intermediate blanks to ensure that surface defects are removed completely, heating the continuous casting blank to more than 1100 ℃, controlling the residual oxygen content in a furnace to be below 5%, preserving heat for 2 hours, discharging, and carrying out rolling after descaling by high-pressure water: the initial rolling temperature is 1100 ℃, the rolling process is divided into 39 passes of rolling, the rolling speed is set to 105m/s, and the spinning temperature is controlled to 900 ℃; after rolling, the wire rod is cooled by a Steyr cooling line, the air quantity of a No. 1-7 fan on the cooling line is adjusted according to the seasonal environmental temperature in order to realize the balanced cooling rate on a cooling roller way, the initial roller way speed is 0.9m/s, the initial roller way speed is increased by 0.03m/s, the environmental temperature is 20 ℃, and the opening degree of the No. 1-7 fan is set: no. 1: 80%, no. 2: 70%, no. 3: 30%, no. 4: 30%, no. 5: 30%, no. 6: 20%, no. 7: 20% of a base; the cooling rate between the spinning temperature of 900 ℃ and 3# is ensured to be more than 20 ℃/S, the cooling rate is properly reduced after a 4# fan, the phase transition temperature of the wire rod is controlled to be more than 600 ℃, so that sorbite is fully phase-changed, and the wire rod forms uniform sorbite tissues after passing through the air-cooled roller way. And (3) aging the test sample after the wire rod is taken off line, and detecting the mechanical property and the tissue of the wire rod. Loading the hot rolled wire rods into a bell-type furnace for spheroidizing annealing after pickling, adopting hydrogen protection in the whole process, and rapidly heating the hot rolled wire rods to 650 ℃ along with the furnace for the first time for heat preservation, wherein the heat preservation is carried out for 0.5h; after the first heat preservation, the wire rod is quickly heated to 790 ℃ for heat preservation for 0.5h; after the second heat preservation, the wire rod is controlled to be cooled to 780 ℃ for heat preservation, and the heat preservation is carried out for 4 hours; after the third heat preservation, the wire rod is rapidly cooled to 700 ℃ for heat preservation for 0.5h; and after the fourth heat preservation, controlling the wire rod to be quickly cooled to 650 ℃ for heat preservation, keeping the temperature for 3 hours, controlling cooling and discharging, and finally detecting the tissue, the surface hardness and the center segregation of the wire rod.
The chemical components of the implementation case are as follows:
| sample numbering | C | Si | Mn | P | S | Cr | V | Nb |
| Sample 1 | 0.98 | 0.21 | 0.32 | 0.01 | 0.006 | 0.31 | 0.21 | 0.043 |
| Sample 2 | 0.99 | 0.23 | 0.35 | 0.008 | 0.008 | 0.32 | 0.22 | 0.045 |
| Sample 3 | 0.99 | 0.22 | 0.32 | 0.006 | 0.005 | 0.31 | 0.22 | 0.045 |
| Sample 4 | 0.98 | 0.23 | 0.33 | 0.009 | 0.006 | 0.3 | 0.21 | 0.048 |
| Sample 5 | 0.99 | 0.24 | 0.32 | 0.007 | 0.005 | 0.29 | 0.22 | 0.045 |
Embodiment case hot rolled wire rod test results:
| sample numbering | Tensile strength Mpa | Flour shrinkage% |
| Sample 1 | 1411 | 39 |
| Sample 2 | 1389 | 35 |
| Sample 3 | 1378 | 34 |
| Sample 4 | 1430 | 35 |
| Sample 5 | 1411 | 39 |
After annealing of the embodiment case, the test results:
| sample numbering | Tissue of | Hardness HBW | Center segregation/stage |
| Sample 1 | 3.0 | 200 | 1 |
| Sample 2 | 3.0 | 192 | 1 |
| Sample 3 | 3.0 | 194 | 1 |
| Sample 4 | 3.0 | 189 | 1 |
| Sample 5 | 3.0 | 197 | 1 |
While the preferred embodiments of the present invention have been described in detail, it is to be clearly understood that the same may be varied in many ways by those skilled in the art. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (6)
1. The manufacturing method of the steel wire rod for the ultra-high strength card clothing comprises the following chemical components in percentage by mass: c:0.96% -1.20%, mn:0.20% -0.60%, si:0.10% -0.40%, P is less than or equal to 0.02%, S is less than or equal to 0.015%, cr:0.20% -0.60%, nb:0.01% -0.05%, V:0.05% -0.50%, and the balance of Fe and unavoidable impurities, and is characterized in that: the method comprises the following steps:
(1) Preparing materials according to the design components, smelting by adopting a converter, refining by adopting a refining furnace, precisely controlling according to the target components, and matching RH soft argon blowing after refining is finished to ensure the uniformity of the components of molten steel;
(2) The continuous casting adopts a technique combining low pulling speed, light pressing and electromagnetic stirring to ensure the uniformity of the structure and components of the continuous casting blank;
(3) Feeding the continuous casting bloom into a heating furnace for high-temperature diffusion, then cogging into an intermediate billet, carrying out surface treatment on the intermediate billet, and then rolling into a wire rod with the diameter of 5.5mm, thereby effectively solving the problems of homogeneity and compactness of the material and ensuring the segregation and uniform structure of the wire rod; firstly, cogging a bloom continuous casting blank 390mm and 510mm into a 155mm and 155mm intermediate blank, heating and diffusing the blank at a high temperature of above 1200 ℃ for more than 10 hours, heating the intermediate blank to above 1100 ℃, controlling the residual oxygen content in a furnace to be below 5%, preserving heat for 2 hours, discharging, and rolling after descaling by high-pressure water: the initial rolling temperature is 1000 ℃, the rolling process is divided into 39 passes of rolling, the rolling speed is set to 105m/s, and the wire rod with phi of 5.5mm is rolled;
(4) Spinning, wherein the spinning temperature is 850-950 ℃;
(5) The stelmor cooling line is subjected to air cooling, the conversion of sorbite is realized in the air cooling process, and the full conversion of sorbite is ensured by adopting a process combining strong cooling and slow cooling; the cooling of the Steyr adopts a staged cooling mode, and the fan opening degree is adjusted online in the first stage to ensure that the cooling rate between 900 ℃ and 700 ℃ is more than 20 ℃/s; the second stage keeps the temperature at 700-650 ℃ and the cooling rate is more than 15 DEG/s; the third stage is that the temperature is maintained between 600 ℃ and 650 ℃ for 10 to 20 seconds, the temperature is controlled to return, and the isothermal process is prolonged;
(6) The hot rolled wire rod is pickled and then is put into a bell-type furnace, and is heated to 780-790 ℃ for spheroidizing annealing by adopting hydrogen protection, so that a good spheroidizing structure is obtained, and the subsequent processing is facilitated; the spheroidizing annealing process adopts a staged heat preservation mode, firstly, hot rolled wire rods are charged into a furnace and rapidly heated to 650 ℃ for heat preservation along with the furnace for the first time, and the heat preservation is carried out for 0.5-1h; after the first heat preservation, the wire rod is quickly heated to 790 ℃ for heat preservation for 0.5-1h; after the second heat preservation, the wire rod is controlled to be cooled to 780 ℃ for heat preservation for 4-5 hours; after the third heat preservation, the wire rod is rapidly cooled to 700 ℃ for heat preservation for 0.5-1h; and after the fourth heat preservation, controlling the wire rod to be quickly cooled to 650 ℃ for heat preservation, preserving the heat for 3-4 hours, and finally controlling the wire rod to be cooled and discharged from the furnace.
2. The method for manufacturing a steel wire rod for ultra-high strength clothing according to claim 1, characterized by: the content of C, si, mn, cr in the steel for clothing meets the conditions that C+Si+Mn+Cr is more than or equal to 1.5%, and the content of Nb and V meets the condition that Nb+V is more than or equal to 0.1%.
3. The method for manufacturing a steel wire rod for ultra-high strength clothing according to claim 1, characterized by: the steel for the card clothing is a hot rolled wire rod with the specification phi of 5.5mm, the tensile strength is 1350-1450Mpa, and the surface shrinkage is 30-40%.
4. The method for manufacturing a steel wire rod for ultra-high strength clothing according to claim 1, characterized by: the metallographic structure of the card clothing after steel ball annealing is a granular pearlite structure, the structure level is less than or equal to 3 levels, the hardness is less than or equal to 210HV, and the center segregation is not more than 1 level.
5. The method for manufacturing a steel wire rod for ultra-high strength clothing according to claim 1, characterized by: in the step (1), the tapping temperature is strictly controlled to be more than 1620 ℃ and the endpoint C% is strictly controlled to be more than 0.15%.
6. The method for manufacturing a steel wire rod for ultra-high strength clothing according to claim 1, characterized by: the continuous casting tundish in the step (2) adopts an induction heating technology to ensure low superheat degree pouring, the pulling speed is 0.5m/min, a displacement mode is adopted in light reduction, the reduction is carried out according to the set reduction, the pressure difference among the flows is combined for proper adjustment, and the carbon offset index of the continuous casting blank is ensured to be between 0.95 and 1.05 by matching with a tail end electromagnetic stirring technology.
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Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102851579A (en) * | 2012-09-07 | 2013-01-02 | 首钢总公司 | Nb-containing micro-alloyed high-carbon steel hot-rolled wire rod and manufacturing method thereof |
| CN102936688A (en) * | 2012-11-21 | 2013-02-20 | 武汉钢铁(集团)公司 | Wire with tensile strength>=2000MPa for bridge cable and production method |
| CN107299280A (en) * | 2017-08-22 | 2017-10-27 | 青岛特殊钢铁有限公司 | 2000MPa grades of cable steel wires heat treatment wire rod and production method |
| CN109468530A (en) * | 2018-10-17 | 2019-03-15 | 江阴兴澄合金材料有限公司 | 2000MPa grades or more bridge cable zinc-coated wire gren rod and production method |
| CN110230008A (en) * | 2019-06-26 | 2019-09-13 | 江苏省沙钢钢铁研究院有限公司 | The production method of ultra-fine extra-high strength wire, wire rod and wire rod |
| CN110295316A (en) * | 2019-04-16 | 2019-10-01 | 江阴兴澄特种钢铁有限公司 | A kind of weaving fluffing fillet clothing steel wire rod and its manufacturing method |
| CN110629132A (en) * | 2019-09-26 | 2019-12-31 | 江苏省沙钢钢铁研究院有限公司 | Wire rod for ultra-high strength steel cord and method for producing same |
| CN111321352A (en) * | 2020-03-25 | 2020-06-23 | 中国铁道科学研究院集团有限公司 | Strength 2400 MPa-grade prestressed steel strand and production process thereof |
| CN112899566A (en) * | 2020-10-22 | 2021-06-04 | 江苏省沙钢钢铁研究院有限公司 | Wire rod for 5000MPa grade diamond wire and production method thereof |
| CN113088798A (en) * | 2021-03-31 | 2021-07-09 | 江苏省沙钢钢铁研究院有限公司 | High-carbon steel wire rod and production method thereof |
| CN113652610A (en) * | 2021-08-17 | 2021-11-16 | 江苏联峰实业有限公司 | Ultrahigh-strength stranded wire rod for railway bridge and production process |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5162875B2 (en) * | 2005-10-12 | 2013-03-13 | 新日鐵住金株式会社 | High strength wire rod excellent in wire drawing characteristics and method for producing the same |
-
2022
- 2022-03-23 CN CN202210291434.6A patent/CN114734009B/en active Active
Patent Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102851579A (en) * | 2012-09-07 | 2013-01-02 | 首钢总公司 | Nb-containing micro-alloyed high-carbon steel hot-rolled wire rod and manufacturing method thereof |
| CN102936688A (en) * | 2012-11-21 | 2013-02-20 | 武汉钢铁(集团)公司 | Wire with tensile strength>=2000MPa for bridge cable and production method |
| CN107299280A (en) * | 2017-08-22 | 2017-10-27 | 青岛特殊钢铁有限公司 | 2000MPa grades of cable steel wires heat treatment wire rod and production method |
| CN109468530A (en) * | 2018-10-17 | 2019-03-15 | 江阴兴澄合金材料有限公司 | 2000MPa grades or more bridge cable zinc-coated wire gren rod and production method |
| CN110295316A (en) * | 2019-04-16 | 2019-10-01 | 江阴兴澄特种钢铁有限公司 | A kind of weaving fluffing fillet clothing steel wire rod and its manufacturing method |
| CN110230008A (en) * | 2019-06-26 | 2019-09-13 | 江苏省沙钢钢铁研究院有限公司 | The production method of ultra-fine extra-high strength wire, wire rod and wire rod |
| CN110629132A (en) * | 2019-09-26 | 2019-12-31 | 江苏省沙钢钢铁研究院有限公司 | Wire rod for ultra-high strength steel cord and method for producing same |
| CN111321352A (en) * | 2020-03-25 | 2020-06-23 | 中国铁道科学研究院集团有限公司 | Strength 2400 MPa-grade prestressed steel strand and production process thereof |
| CN112899566A (en) * | 2020-10-22 | 2021-06-04 | 江苏省沙钢钢铁研究院有限公司 | Wire rod for 5000MPa grade diamond wire and production method thereof |
| CN113088798A (en) * | 2021-03-31 | 2021-07-09 | 江苏省沙钢钢铁研究院有限公司 | High-carbon steel wire rod and production method thereof |
| CN113652610A (en) * | 2021-08-17 | 2021-11-16 | 江苏联峰实业有限公司 | Ultrahigh-strength stranded wire rod for railway bridge and production process |
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