CN114734009A - Steel wire for ultrahigh-strength card clothing and manufacturing method thereof - Google Patents
Steel wire for ultrahigh-strength card clothing and manufacturing method thereof Download PDFInfo
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- CN114734009A CN114734009A CN202210291434.6A CN202210291434A CN114734009A CN 114734009 A CN114734009 A CN 114734009A CN 202210291434 A CN202210291434 A CN 202210291434A CN 114734009 A CN114734009 A CN 114734009A
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- 238000005554 pickling Methods 0.000 claims abstract 2
- 238000004321 preservation Methods 0.000 claims description 35
- 238000010438 heat treatment Methods 0.000 claims description 16
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- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 claims 3
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- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
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- 229910052719 titanium Inorganic materials 0.000 description 1
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- 210000002268 wool Anatomy 0.000 description 1
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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 ultrahigh strength card clothing and a manufacturing method thereof, wherein the 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 to 0.50 percent, and the balance of Fe and inevitable impurities. The production process of the invention comprises the following steps: continuous casting, cogging, rolling, spinning, stelmor cooling and acid pickling annealing. The properties of the final product are mainly ensured by staged stelmor cooling control and staged spheroidizing annealing process, and the final wire rod satisfies: the tensile strength of the hot-rolled wire rod with the specification of phi 5.5mm exceeds 1350MPa, the surface shrinkage exceeds 30 percent, the grade of a microstructure of the annealed wire rod is less than or equal to 3 according to GB/T18254 evaluation, the hardness is less than or equal to 210HV, and the center segregation is less than or equal to 1.
Description
Technical Field
The invention belongs to the technical field of iron-based special wire rods, and particularly relates to a steel wire rod for ultrahigh-strength card clothing and a manufacturing method thereof.
Background
Card clothing is an important spinning mechanism for carding cotton, wool, chemical fibers and other textile fibers, and the surface is usually needles or teeth, which can be generally divided into two major categories, elastic card clothing and metal card clothing. The card wire is mainly made of high carbon steel, and the failure mode is mainly abrasion and breakage, so the steel for the card wire has high carbon content to meet the requirement of good abrasion resistance. In addition, the drawing of the card wire is required to be performed with a large deformation amount in the manufacturing process of the card wire, and thus the steel for the card wire should have excellent cold drawing property and spheroidizing annealing property.
For a long time, domestic card clothing manufacturers mainly use 80WV steel imported from abroad to manufacture high-performance card wires, the performance of card wires manufactured by adopting the steel tends to be limited, and imported steel has high cost and long supply period, thereby causing great troubles to the domestic card clothing manufacturers; with the progress of the technology, the requirements for steel for card clothing card wire are higher and higher, especially in the aspect of wear resistance, so that the research and development of a novel card clothing card wire alloy steel with higher carbon content and better performance is urgent.
The patent publication No. CN 105838981A discloses a steel for card clothing, which relates to the technical field of metal card clothing processing. The metallic card clothing has high requirements on the strength, hardness and wear resistance of the material, and the composition design is selected to be added into high-carbon steel for microalloying with Nb, V and Ti to form C, N compounds to achieve grain refinement and improve the strength and wear resistance. However, the wire rod prepared by the method has lower carbon content and tensile strength, and cannot meet the requirement of higher wear resistance of the existing steel for card clothing card wire.
The patent publication No. CN 110295316A discloses a textile fluffing elastic card clothing steel wire and a preparation method thereof, in particular to a wire rod of wet type fluffing elastic card clothing steel in the textile field and a production method thereof. The elastic card clothing is designed by optimizing the elements of Mn, Cr and Al in high-carbon steel and optimizing the technological parameters of wire rod preparation, so that the card clothing steel wire rod which has good structure performance, excellent surface quality and excellent internal quality and is suitable for deep drawing is obtained, but the tensile strength of the wire rod prepared by the method can not meet the requirement.
The patent publication No. 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 card clothing and a production method thereof. The elastic card clothing is added with Ni and rare earth elements to meet the requirements of card clothing used in a humid weakly alkaline environment, has the characteristics of high elasticity, strong corrosion resistance and long service life, but the wire rod prepared by the invention is high in manufacturing cost due to the addition of precious alloy and rare earth elements, and is not suitable for the trend of reducing the cost of the market at present.
Disclosure of Invention
The invention aims to solve the technical problem of providing an ultrahigh-strength card clothing steel wire rod and a manufacturing method thereof aiming at the prior art, and the obtained card clothing steel wire rod has the characteristics of high tensile strength and good toughness through chemical composition design and key production process parameter control.
The technical scheme adopted by the invention for solving the problems is as follows: a steel wire for ultrahigh 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 of the total weight of the alloy, and the balance of Fe and inevitable impurities, wherein the total weight of C, Si, Mn and Cr is more than or equal to 1.5 percent, and the total weight of Nb and 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 the steel, the strength of the steel can be obviously improved through solid solution strengthening and precipitation strengthening, the strength is in an obvious increasing trend along with the increase of the content of C, meanwhile, the wire is obviously hardened after cold drawing processing and is beneficial to realizing the strength of a finished steel wire, the ratio of the wire structure sorbite obtained by improving the content of C through Stelmor cooling is high, and therefore, the content of C is controlled to be more than 0.96%.
Si is added as a deoxidizer to steel, reacts with FeO in molten steel to form silicate and is removed, thereby improving the purity of molten steel, and silicate inclusions in a wire rod are easily elongated and deformed in a drawing direction, thereby causing no drawing breakage, and the solid solution strengthening of Si element improves the work hardening rate of steel, remarkably deteriorates the cold workability of steel, and promotes grain boundary segregation of the element P, S, so that the weight percentage of Si is 0.10 to 0.40%.
Mn is added to steel as a strong deoxidizer, which can improve the strength and wear resistance of the steel, but for steel having a high C content, the plasticity of the steel decreases as the Mn content increases. Therefore, the weight percentage of Mn is 0.20-0.60%.
Cr can improve hardenability, strength, hardness and wear resistance of steel, and Cr can refine pearlite lamellar spacing, which is advantageous for improving sorbite ratio, improving drawing performance of wire rod, and suppressing propagation of microcracks, but Cr content is excessive, which easily generates undissolved cementite phase, prolongs the phase transition completion time, easily generates supercooled structures such as troostite, martensite or bainite in hot rolled wire rod or drawn steel wire, has excessively high strength, deteriorates plasticity, and significantly affects drawing workability of steel, so the weight percentage of Cr is 0.20 to 0.40%.
The Nb element can obviously improve the coarsening temperature and the recrystallization temperature of austenitizing, and the size of a sorbite group is reduced while austenite grains are obviously refined. The smaller the sorbite cluster size and the lamella spacing, the higher the wire strength and the better the plasticity. The reason for this is that when the ferrite and the cementite sheet are thin, the phase interface increases, and the resistance to plastic deformation increases under the action of an external force. Further, the ferrite or cementite sheet is thin, which increases the plastic deformability of the steel. The reduction of the size of the pearlite colony shows that the arrangement direction of the pearlite lamella in unit volume is increased, which is beneficial to the reduction of the size of plastic deformation, and reduces the possibility of stress concentration caused by a large amount of local plastic deformation, thereby improving the strength of the wire rod and the plasticity of the wire rod. In addition, Nb element is partially gathered on grain boundaries by trace Nb (C, N) in steel, so that the mobility of the grain boundaries is reduced, and the size of austenite grains of the structure material is abnormally increased in the heating process. In addition, Nb exists in steel as substitutional solute atoms, has a size larger than that of iron atoms, is easy to be deviated and gathered on dislocation lines, generates strong dragging effect on the dislocation lines, delays austenite deformation recrystallization in the rolling process, and refines grains. Therefore, the weight percentage of Nb is 0.01-0.05%.
The V element is a strong carbide generating element, a very stable special carbide is generally formed in the steel wire, and when the carbide is annealed and quenched and heated by the card clothing, the quenching and heating temperature range of the card clothing is widened, the austenite structure is refined, and the fine martensite structure can be obtained after quenching. Meanwhile, the carbides have extremely high hardness, and the card clothing can be dispersedly distributed on a martensite matrix after quenching, 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 during cold-rolling (rolling) of the semi-finished gauge steel wire, so that the addition amount cannot be too large. The weight percentage of V is therefore between 0.05 and 0.5%.
The P element belongs to harmful elements in the card clothing steel, and obviously reduces the plasticity and toughness of the steel, so that the performance is deteriorated. Meanwhile, phosphorus is easy to generate intragranular segregation in the crystallization process, so that the phosphorus content in a local area is higher, the cold brittleness transformation temperature is increased, and cold brittleness is caused. The product needs to meet the requirements of a quenching and tempering process of customers, and P needs to be controlled to be less than or equal to 0.02 percent in order to prevent the phenomena of reduction of the plastic toughness and tempering brittleness of the material.
The S element is also a harmful element in the card clothing steel, and reduces the ductility and toughness of the steel. In the solid state, the solubility of sulphur in iron is very small, but it is present in the steel in the form of FeS. Due to the poor plasticity of FeS, the steel containing more sulfur is more brittle. More seriously, FeS and Fe can form eutectic with low melting point (985 ℃) and are distributed on the grain boundary of austenite. When the steel is heated to about 1200 ℃ for hot press working, eutectic crystals on grain boundaries are melted, and bonding between grains is broken, so that the steel is cracked along the grain boundaries during the working process, i.e., is hot brittle. In addition, sulfide nonmetallic inclusions formed by sulfur segregation can form fibrous structures during rolling, and the mechanical properties of high-strength steel products are reduced. The product needs to be heated at high temperature and rolled under large reduction, so that the S content needs to be strictly controlled to be less than or equal to 0.015 percent.
The manufacturing method of the ultrahigh strength card clothing steel wire rod comprises the following steps:
(1) preparing materials according to design components, smelting by adopting a converter, strictly controlling the tapping temperature to be higher than 1620 ℃ and the end point C% to be higher than 0.15%, preventing peroxidation, then refining by adopting a refining furnace, adopting special synthetic slag for refining to ensure full deoxidation and inclusion removal, simultaneously accurately controlling according to target components, matching RH soft argon blowing after refining is finished, further removing inclusions and ensuring molten steel uniformity;
(2) the continuous casting tundish adopts an induction heating technology to ensure low superheat degree pouring, the drawing speed is 0.5m/min, a displacement mode is adopted under light press, press-down is carried out according to a set press-down amount, proper adjustment is carried out by combining the pressure difference among flows, and the continuous casting billet is ensured to have no obvious crack, central shrinkage cavity and V-shaped segregation under light press by matching with a tail end electromagnetic stirring technology, the continuous carbon bias analysis in the inner and outer arc directions of the intermediate billet is carried out, the carbon bias index is between 0.95 and 1.05, and the tissue and component uniformity of the continuous casting billet is ensured;
(3) the method comprises the following steps of cogging 390mm x 510mm of a large square billet continuous casting blank into an intermediate blank of 155mm x 155mm, heating and diffusing the blank at a high temperature of more than 1200 ℃, ensuring the heating time to be more than 10 hours, effectively solving the problems of material homogeneity and compactness, having good wire rod carbon segregation uniformity, carrying out surface treatment on the intermediate blank to ensure that the surface is free of defects, heating the intermediate blank to more than 1100 ℃, controlling the residual oxygen content in a furnace to be less than 5%, keeping the temperature for 2 hours, discharging the blank from the furnace, 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 be 105m/s, and the wire rod with the diameter of 5.5mm is rolled;
(4) spinning, wherein the spinning temperature is 850 ℃ and 950 ℃;
(5) the stelmor cooling line is used for air cooling, the transformation of sorbite is realized in the air cooling process, the opening degree of a fan is adjusted on line to ensure that the cooling rate is more than 20 ℃/s between the spinning temperature of 900 ℃ and 700 ℃, and the wire rod is rapidly cooled to inhibit the precipitation of the reticular cementite; when the temperature is 700-650 ℃, the cooling rate is ensured to be more than 15 ℃ per second, 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, generally maintained for 10-12s, the sufficient phase transformation of the sorbite is ensured, the low-temperature phase transformation below 550 ℃ is avoided to generate low-temperature tissues such as troostite, bainite and the like, the sorbite proportion is improved, and the tensile property of the wire rod is improved. In practical application, the opening degree of No. 1-7 fans on a stelmor cooling line is adjusted, and all fans behind No. 7 fans are closed: setting the roller speed to be 0.85-0.95m/s, 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%, number 6: 20-40%, No. 7: 20 to 40 percent;
(6) after acid washing, hot rolled wire rods are loaded into a bell-type furnace for spheroidizing annealing, hydrogen protection is adopted in the whole process, the hot rolled wire rods are loaded into the furnace and are rapidly heated to 650 ℃ for the first time along with the furnace for heat preservation, and the heat preservation is carried out for 0.5-1 h; after the first heat preservation, rapidly heating the wire rod to 790 ℃ for heat preservation, and preserving the heat for 0.5-1 h; 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 4-5 h; after the third heat preservation, rapidly cooling the wire rod to 700 ℃ for heat preservation for 0.5-1 h; and after the fourth heat preservation, controlling the wire rod to be rapidly cooled to 650 ℃ for heat preservation, preserving the heat for 3-4h, finally, controlling the cooling and discharging, and ensuring that the microstructure after spheroidizing annealing is granular pearlite, the structure grade is less than or equal to 3 grade, and the hardness is less than or equal to 210 HV. The temperature rise stage is set to ensure that the temperature is uniform, the temperature rises rapidly to 790 to start spheroidization in a two-phase region, the temperature is maintained at 780 to obtain dispersed carbide particles, the temperature is reduced to 700 to obtain fine spherical carbide, and the temperature is maintained at 650 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 tensile strength of the obtained phi 5.5mm hot rolled wire rod is between 1350-1450MPa, the surface shrinkage is 30-40%, the wire rod after spheroidizing annealing does not exceed 1 grade according to GB/T18254 evaluation, the microstructure grade is less than or equal to 3 grade, the hardness is less than or equal to 210HV, and the deep drawing of a user can be met.
Drawings
FIG. 1 is a schematic representation of the sorbite structure of the wire of the invention;
FIG. 2 is a schematic, low power view of the wire of the present invention;
FIG. 3 is a schematic view showing a spheroidized structure of the card clothing steel wire rod according to the present invention.
Detailed Description
The present invention will be further described with reference to the following examples.
Smelting by adopting a 120t converter, controlling the tapping temperature to 1650 ℃, controlling the end point C% to 0.18%, then refining by adopting a refining furnace, wherein the refining adopts low-alkalinity synthetic slag to ensure full deoxidation and inclusion removal, meanwhile, the refining is accurately controlled according to target components, and after the refining is finished, RH soft argon blowing is matched to further remove the inclusion and ensure the molten steel uniformity; and then, the molten steel is transferred to continuous casting, the drawing speed is 0.5m/min, the total reduction is 12mm under light pressure, the tail end is electromagnetically stirred for 1.5HZ/300A, and the continuous casting blank with the cross section size of 390mm x 510mm is cast.
Heating and diffusing the continuous casting billet at high temperature of about 1250 ℃, ensuring the heating time to be more than 10 hours, then cogging into an intermediate billet with the thickness of 155mm and 155mm, carrying out surface treatment on the intermediate billet to ensure that surface defects are completely removed, heating the continuous casting billet to be more than 1100 ℃, controlling the residual oxygen content in a furnace to be below 5%, keeping the temperature for 2 hours, discharging the continuous casting billet out of the furnace, and 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 be 105m/s, and the spinning temperature is controlled to be 900 ℃; after rolling, the wire rod is cooled by a stelmor cooling line, in order to realize balanced cooling rate on a cooling roller way, the air volume of a No. 1-7 fan on the cooling line is required to be adjusted according to seasonal environment temperature, the initial roller way speed is 0.9m/s and is increased by 0.03m/s, the environment temperature is 20 ℃, and the opening degree of the No. 1-7 fan is set: no. 1: 80%, No. 2: 70%, number 3: 30%, No. 4: 30%, No. 5: 30%, number 6: 20%, No. 7: 20 percent; the cooling rate between 900 ℃ and 3# is ensured to be more than 20 ℃/S, the cooling rate is properly reduced after a 4# fan, the phase change temperature of the wire rod is controlled to be more than 600 ℃, so that the sorbite is fully subjected to phase change, and the wire rod forms a uniform sorbite tissue after passing through the air-cooled roller way. And (4) aging the test sample after the wire rod is off-line, and detecting the mechanical property and the structure of the wire rod. After acid washing, hot rolled wire rods are loaded into a bell-type furnace for spheroidizing annealing, hydrogen protection is adopted in the whole process, the hot rolled wire rods are loaded into the furnace and are rapidly heated to 650 ℃ for the first time along with the furnace for heat preservation, and the heat preservation is carried out for 0.5 h; after the first heat preservation, rapidly heating the wire rod to 790 ℃ for heat preservation, and preserving the heat for 0.5 h; 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, rapidly cooling the wire rod to 700 ℃ for heat preservation, and preserving the heat for 0.5 h; and after the fourth heat preservation, controlling the wire rod to be rapidly cooled to 650 ℃ for heat preservation, preserving the heat for 3 hours, controlling the temperature and discharging from the furnace, and finally detecting the structure, the surface hardness and the center segregation of the wire rod.
The chemical components of the embodiment 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 |
Example hot rolled wire rod test results:
| sample numbering | Tensile strength Mpa | The flour shrinks% |
| Sample 1 | 1411 | 39 |
| Sample 2 | 1389 | 35 |
| Sample 3 | 1378 | 34 |
| Sample 4 | 1430 | 35 |
| Sample 5 | 1411 | 39 |
Example post-anneal test results:
| sample numbering | Tissue of | Hardness HBW | Center segregation/order |
| 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 |
Although preferred embodiments of the present invention have been described in detail hereinabove, it should be clearly understood that modifications and variations of the present invention are possible to those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (10)
1. A steel wire for ultrahigh 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 inevitable impurities.
2. The steel wire rod for ultra-high strength card clothing according to claim 1, characterized in that: the content of C, Si, Mn and Cr in the steel for the card clothing meets the condition that the content of C + Si + Mn + Cr is more than or equal to 1.5 percent, and the content of Nb and V meets the condition that the content of Nb + V is more than or equal to 0.1 percent.
3. The steel wire rod for ultra-high strength card clothing according to claim 1, characterized in that: the card clothing uses steel as specification
The hot rolled wire rod has tensile strength of 1350 and 1450MPa and surface shrinkage of 30-40%.
4. The steel wire rod for ultra-high strength card clothing according to claim 1, characterized in that: the metallographic structure of the card clothing after spheroidizing annealing is a granular pearlite structure, the structure level is less than or equal to 3, the hardness is less than or equal to 210HV, and the center segregation is not more than 1.
5. A method for manufacturing the ultra high strength steel wire rod for card clothing according to claim 1, wherein: the method comprises the following steps:
(1) preparing materials according to design components, smelting by adopting a converter, then refining by adopting a refining furnace, accurately controlling according to target components, and matching with RH soft argon blowing after refining is finished to ensure the component uniformity of molten steel;
(2) the continuous casting adopts the technology of combining low drawing speed, soft reduction and electromagnetic stirring, so that the tissue and component uniformity of the continuous casting billet is ensured;
(3) continuously casting a bloom into a heating furnace for high-temperature diffusion, 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 material homogeneity and compactness and ensuring wire rod segregation and uniform tissue;
(4) spinning, wherein the spinning temperature is 850 ℃ and 950 ℃;
(5) the transformation of the sorbite is realized in the air cooling process of the Stalmo cooling line, and the full transformation of the sorbite is ensured by adopting a process combining strong cooling and slow cooling;
(6) and (3) pickling the hot-rolled wire rod, then loading the pickled hot-rolled wire rod into a bell-type furnace, heating to 780-790 ℃ under the protection of hydrogen for spheroidizing annealing to obtain a good spheroidized structure so as to facilitate subsequent processing.
6. The method for manufacturing an ultra high strength steel wire rod for card clothing according to claim 5, wherein: in the step (1), the tapping temperature is strictly controlled to be higher than 1620 ℃ and the end point C% is higher than 0.15%.
7. The method of claim 5, wherein the steel wire rod for ultra-high strength card clothing comprises: and (3) adopting an induction heating technology for the continuous casting tundish in the step (2) to ensure low superheat degree pouring, wherein the drawing speed is 0.5m/min, adopting a displacement mode under soft reduction, carrying out reduction according to a set reduction, carrying out proper adjustment by combining the pressure difference among flows, and ensuring that the carbon bias index of the continuous casting billet is between 0.95 and 1.05 by matching with a tail end electromagnetic stirring technology.
8. The method of claim 5, wherein the steel wire rod for ultra-high strength card clothing comprises: in the step (3), firstly, 390mm x 510mm of a bloom continuous casting blank is cogging into an intermediate blank of 155mm x 155mm, the blank is heated and diffused at a high temperature of more than 1200 ℃, the heating time is ensured to be more than 10 hours, then the intermediate blank is heated to be more than 1100 ℃, the residual oxygen content in the furnace is controlled to be less than 5 percent, the furnace is taken out after heat preservation for 2 hours, and the rolling is carried out after high-pressure water descaling: the initial rolling temperature is 1000 ℃, the rolling process is divided into 39 passes of rolling, the rolling speed is set to be 105m/s, and the wire rod with the diameter of 5.5mm is rolled.
9. The method of claim 5, wherein the steel wire rod for ultra-high strength card clothing comprises: the stelmor cooling in the step (5) adopts a staged cooling mode, and the opening degree of a fan is adjusted on line in the first stage to ensure that the cooling rate is more than 20 ℃/s between 900 ℃ and 700 ℃; the second stage keeps the temperature at 700-650 ℃ and the cooling rate is more than 15 DEG/s; the third stage is maintained at 600-650 deg.c for 10-20 sec, and the isothermal process is prolonged through controlling the temperature.
10. The method for manufacturing an ultra high strength steel wire rod for card clothing according to claim 5, wherein: the spheroidizing annealing process in the step (6) adopts a staged heat preservation mode, firstly, the hot rolled wire rod is charged into a furnace and is rapidly heated to 650 ℃ along with the furnace for the first time for heat preservation, and the heat preservation is carried out for 0.5 to 1 hour; after the first heat preservation, rapidly heating the wire rod to 790 ℃ for heat preservation, and preserving the heat for 0.5-1 h; 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 4-5 h; after the third heat preservation, rapidly cooling the wire rod to 700 ℃ for heat preservation, and preserving the heat for 0.5-1 h; and after the fourth heat preservation, controlling the wire rod to be quickly cooled to 650 ℃ for heat preservation, preserving the heat for 3-4h, and finally, controlling the temperature and discharging from the furnace.
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