CN116145036A - Hot-rolled wire rod for 2100 MPa-grade or above bridge cable galvanized steel wire and production method thereof - Google Patents
Hot-rolled wire rod for 2100 MPa-grade or above bridge cable galvanized steel wire and production method thereof Download PDFInfo
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- CN116145036A CN116145036A CN202310091571.XA CN202310091571A CN116145036A CN 116145036 A CN116145036 A CN 116145036A CN 202310091571 A CN202310091571 A CN 202310091571A CN 116145036 A CN116145036 A CN 116145036A
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 47
- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 17
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 17
- 238000005096 rolling process Methods 0.000 claims abstract description 60
- 238000001816 cooling Methods 0.000 claims abstract description 43
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 39
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- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 2
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- 238000005246 galvanizing Methods 0.000 description 4
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- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 1
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- -1 CaO compound Chemical class 0.000 description 1
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- 241001062472 Stokellia anisodon Species 0.000 description 1
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- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- CFJRGWXELQQLSA-UHFFFAOYSA-N azanylidyneniobium Chemical compound [Nb]#N CFJRGWXELQQLSA-UHFFFAOYSA-N 0.000 description 1
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
-
- 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
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
-
- 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
- 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
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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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
- C22C38/002—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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
-
- 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
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- 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
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- 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
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- 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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- Materials Engineering (AREA)
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- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to a hot-rolled wire rod for a galvanized steel wire of a bridge cable with 2100MPa grade or more and a production method thereof, wherein the tissue content of sorbite of the wire rod is more than or equal to 95 percent, the pass circle range of the tensile strength is less than or equal to 70MPa according to the coil diameter of 1.1-1.2 meters, the tensile strength is more than 1550MPa, the tensile strength of the galvanized steel wire obtained after drawing and galvanization is more than or equal to 2100MPa, and the torsion detection is carried out according to the GB/T239.1 standard, and the torsion index is more than or equal to 8 times. By adopting a high C and high Si component system and adding a trace of Nb, V and Ti carbonitride forming elements, the hydrogen induced cracking resistance is improved while the strong plasticity is improved. Molten steel is subjected to converter smelting, LF refining, RH vacuum degassing, large round billet continuous casting, intermediate round billet rolling, finishing, round billet rolling control and cooling control and wire rod online water bath toughening treatment. The wire rod adopts a controlled rolling and controlled cooling method in the production process, well matches the on-line water bath cooling speed, expands the specification range of the produced wire rod to phi 11.0 mm-phi 16.5mm, and breaks through the technical bottleneck that salt bath or lead bath toughening heat treatment is adopted in the conventional production of the wire rod of the grade.
Description
Technical Field
The invention belongs to the field of coil steel, and particularly relates to a hot-rolled coil for a high-strength bridge cable steel wire with the pressure of more than or equal to 2100MPa and a production method thereof.
Background
Along with the increasingly severe demands of China on road construction node engineering, china has the characteristics of having multiple ravines, multiple mountains and penetrating terrains of Yangtze river and yellow river, and higher requirements are put forward on bridge construction. The data show that when the strength of the bridge cable wire is increased by 100MPa, the dead weight of the bridge cable wire can be reduced by 10%, the cable diameter is correspondingly reduced, the windward resistance is correspondingly reduced, the influence of wind power and wind direction on the bridge can be reduced, and meanwhile, the safety of the bridge is improved.
With the continuous progress of the technology in iron and steel enterprises and downstream metal product processing industry, the galvanized aluminum steel wires of 1860MPa, 1960MPa, 2000MPa and 2060MPa can be stably produced by adopting domestic wire rods at present. The wire rod for manufacturing the galvanized steel wire adopts a high-C high-Si component system in China, and the toughening treatment generally adopts a Stelmor air cooling process or an online air cooling and offline salt bath or lead bath heat treatment process. Because the cooling rate of the air-cooled wire rod is low, the content of tissue sorbite is below 90%, the fluctuation of the tensile strength of the coil passing ring is about 100MPa, the upper limit of the wire rod production specification can only reach about phi 13.5mm, the produced wire rod can only meet 1860MPa level, and no online batch production case for the wire rod of 2100MPa level is seen in China; the wire rod online air cooling and wire rod offline salt bath (or lead bath) heat treatment process is adopted, the wire rod is required to be air cooled to the room temperature, then the wire rod is continuously fed into a heating furnace in a straight line for re-austenitizing and heating, and is cooled by the salt bath or the lead bath after being discharged, so that the process has high energy consumption, large production waste discharge amount and low production efficiency, and does not accord with the low energy consumption and the green environment-friendly production development trend.
The patent information published in China at present is as follows: the patent document with publication number CN 102719643a relates to the rapid placement of hot rolled wire rods into lead or salt tanks for sorbitizing the wire rods, the wire rod cooling medium is lead or salt liquid, which is highly corrosive to equipment and has a certain pollution to the environment, and the produced wire rods are mainly used for manufacturing steel wire ropes and are not practically applied to the production of galvanized steel wires for bridge cables.
The patent document with publication number CN 107587071A relates to steel for bridge cables with the pressure of more than or equal to 2100MPa and a production method, and the composition C of the wire rod: 0.92-0.94%, si:0.70-0.90%, mn:0.45-0.55%, P is less than or equal to 0.01%, S is less than or equal to 0.01%, cr:0.07-0.09%, nb:0.04-0.08%, al:0.16-0.20%, N:0.0040-0.0080%, B:0.0010 to 0.0015%, zr:0.0020 to 0.0050% by weight, which is designed as a high Si component, and a trace amount of Cr is added, and Nb, B and Zr are added. The production process involves longitudinal flame cutting of continuous casting billets, increases production cost, and records wire rod air cooling after spinning for later use.
The patent document with publication number CN107299280A relates to a heat treatment wire rod for a 2000 MPa-level cable wire and a production method thereof, and the wire rod comprises the following components: 0.85% -1.0%, si:0.80-1.50%, mn 0.30-0.80%, P less than or equal to 0.015%, S less than or equal to 0.010%, cr:0.20-0.80%, al:0.010-0.080%, the patent component design is designed as high Si component, and a certain amount of alloy elements such as Mn, cr, al and the like are added. The production process is that the continuous casting blank is rolled into a wire rod, and the wire rod is heated to austenitize again and then is subjected to heat treatment by adopting an off-line salt bath, so that the production cost is high and the production efficiency is low.
Patent document with publication number CN 102936688B describes a wire rod for bridge cable with tensile strength more than or equal to 2000MPa and a production method thereof, wherein the chemical components of the wire rod are C:0.95-1.20%, si:0.10-0.48%, mn:0.60-1.00%, P is less than or equal to 0.025%, S is less than or equal to 0.015%, cr:0.10-0.50%, al:0.05-0.15%, N:0.0100-0.0300%, adopting the design of medium and low Si components, properly adding Mn, cr and Al alloy, and simultaneously adding non-alloy element N. The production process is that the continuous casting blank is rolled into a wire rod, and the wire rod is cooled by air cooling after spinning.
Patent document with publication number of CN 107354380A describes a steel for bridge cable with tensile strength more than or equal to 2300MPa and a production method thereof, wherein the smelting components of molten steel are as follows: 0.92-0.94% of C, si:0.70-1.00%, mn:0.45-0.55%, V:0.16-0.20%, 0.16-0.20% of Al, and trace Cr, B and Zr are added; in addition, the production flow does not involve specific measures such as controlled rolling and controlled cooling of the wire rod, and the cooling process adopts air cooling, and the wire rod is processed in the next step after the air cooling.
Patent document with publication number of CN 107686944A describes a bridge cable steel with tensile strength more than or equal to 2500MPa and a production method thereof, and the related smelting components are as follows: c1.21-1.25%, si:1.10-1.50%, mn:0.20-0.50%, cr 0.07-0.09%, ti:0.06-0.08%, al:0.16-0.20%, and adding trace B, zr. The control rolling process of the wire rod is not disclosed in the literature, and the wire rod is subjected to air cooling.
The patent document with publication number of CN 109468530A describes a hot rolled wire rod for a galvanized steel wire of a large bridge cable with the pressure of more than 2000MPa and a production method thereof, and the related smelting components are C:0.90-1.10%, si:0.20-0.60%, mn:0.30-0.90%, P is less than or equal to 0.010%, S is less than or equal to 0.005%, cr:0.10-0.40%, al:0.010-0.070%, V:0.02-0.15%, cu: less than or equal to 0.05 percent, ca:20-40ppm, N:20-90ppm, the others being Fe and unavoidable residual elements; the content of C in the components of the hot rolled wire rod is further 0.95-1.10%; the Si content is further 0.40-0.60%; the Mn content is further 0.60-0.90%; the Cr content is further 0.30-0.40%; the Al content is further 0.030-0.070 percent; the V content is further 0.05-0.15%; the Ca content is 25-40ppm by weight and the N content is 40-90ppm by weight.
The prior art listed above has small production specification of the wire rod correspondingly manufactured, and is difficult to meet the high-end market demand in strength.
Disclosure of Invention
The invention aims to make up the performance deficiency of the existing product, and the coil rod component design adopts a high C and high Si component system from the chemical components and the production process, and simultaneously adds trace Nb, V and Ti carbonitride forming elements, thereby improving the hydrogen induced cracking resistance of the material, and simultaneously adopting a controlled rolling and cooling method in the rolling process, and breaking through the technical bottleneck that the conventional production of the grade coil rod adopts salt bath or lead bath toughening heat treatment. On the basis, trace alloy elements are added, grains are refined in the rolling process, and the rolling and cooling control measures are adopted, so that the online water bath cooling speed is well matched, the specification range of the produced wire rod is enlarged to be phi 11.0 mm-phi 16.5mm, the tensile strength of the galvanized steel wire for the bridge cable produced by adopting the wire rod is more than or equal to 2100MPa, the torsion times are more than or equal to 8 times, and the international blank is filled.
The technical scheme adopted by the invention is as follows: the hot rolled wire rod for galvanized steel wire of 2100MPa level bridge cable has sorbite structure content not less than 95% and pearlite structure in the rest, and has tensile strength not greater than 70MPa, tensile strength not greater than 1550MPa, tensile strength not less than 2100MPa, torsion detection in GB/T239.1 standard, torsion index not less than 8 times, even not less than 12 times, and the tensile strength not less than 1550 MPa.
The specification of the wire rod produced by the method is phi 11.0 mm-phi 16.5mm.
The chemical components of the wire rod comprise high carbon, high silicon, high manganese, trace chromium and trace aluminum, and also comprise elements precipitated as carbide, nitride and carbonitride: one or more of niobium, vanadium and titanium, the interval content of calcium and nitrogen in chemical components is precisely controlled, and the minimum content of phosphorus, sulfur, copper and hydrogen is precisely controlled. The weight percentages of the specific chemical elements are as follows: c:0.80-1.20%, si:0.60-1.50%, mn:0.60-0.90%, cr:0.10-0.70%, al:0.010-0.070%, V:0.02-0.20%, nb:0.005-0.035%, ti:0.005-0.025%, ca:20-40ppm, N:20-90ppm, P is less than or equal to 0.015 percent, S is less than or equal to 0.006 percent, cu: less than or equal to 0.05 percent, H less than or equal to 1.0ppm, and the rest is Fe and unavoidable residual elements.
The action mechanism of the chemical element added to the wire rod for the 2100MPa and above-grade bridge cable is as follows:
carbon (C): carbon is a main strengthening element in steel, and plays a role in gap solid solution strengthening on one hand; on the other hand, the compound formed by the carbide forming element is separated out to play a role of precipitation strengthening. The weight percentage of carbon in the invention is 0.80-1.20%, the dissolution amount of carbon in austenite and the subsequent XDWP water bath cooling strength are fully considered, the stronger the cooling capacity is, the more the precipitation of secondary cementite can be inhibited, and the effect of improving the wire rod strength through solid solution strengthening is achieved.
Silicon (Si): silicon has extremely high solid solution strengthening capability and can remarkably improve the cold work hardening index of steel. In the phase transformation process, si is mainly distributed in ferrite, so that the stability of cementite is improved, spheroidization of cementite sheets in the hot galvanizing process of a cold drawn steel wire is prevented, strength loss in the hot galvanizing process is reduced, and the weight percentage of Si in the invention is 0.60-1.50%.
Manganese (Mn): manganese tends to be distributed in cementite, and when the Si-Mn atom spacing is small, a strong repulsive force exists between Si and Mn atoms, and when the Si content in ferrite is high, mn atoms are repelled into cementite. Manganese is liable to segregate in steel, a low-temperature martensitic structure is liable to be formed during cooling, and in view of the above, the weight percentage of Mn in the present invention is 0.60 to 0.90%.
Chromium (Cr): the chromium addition can improve the stability of cementite, prevent the spheroidization of cementite sheets in the hot galvanizing process of the cold drawn steel wire and reduce the strength loss in the hot galvanizing process. The Cr element is added to refine the lamellar spacing of pearlite, so that the improvement of the plasticity index of the wire rod is facilitated, and the work hardening rate of the material in the wire drawing process is improved. Chromium can reduce the activity of carbon in steel and is also a carbide forming element, so that the diffusion activation energy of carbon in steel can be improved. The weight percentage of carbon in the invention is 0.10-0.70%.
Vanadium (V): vanadium is a carbide forming element, and can play roles in refining grains and precipitation strengthening in the final stage of rolling and in the phase change process. Recent researches show that the vanadium carbide (nitride) phase can capture hydrogen atoms in the matrix to form hydrogen traps, so that the harm of hydrogen in the high-strength steel is avoided, and the weight percentage of vanadium in the invention is 0.02-0.20%.
Titanium (Ti): titanium has the functions of refining grains, strengthening precipitation, improving the strength of the wire rod and improving the hydrogen induced cracking resistance. The precipitation temperature of the titanium compound is high, and the type and the particle size of the titanium compound are controlled by controlling the adding time of a titanium wire and the content of titanium and nitrogen in the smelting process, but titanium nitride precipitation with large particles is easily formed by adding too high titanium. Comprehensively, the weight percentage of titanium in the invention is 0.005-0.025%.
Niobium (Nb): the precipitation temperature of the niobium compound is concentrated in the rolling temperature range of the blank, and the rolling and cooling control measures are properly added and applied, so that the method plays a good role in controlling the precipitation size and type of the compound and improving the comprehensive performance of the wire rod. Generally, the role of the different states of niobium is as follows: (1) In order to reduce deformation resistance in actual production, higher heating temperature is generally adopted, the quantity of undissolved niobium is small, and the effect on precipitation strengthening and grain refinement is not great; (2) Niobium in solid solution state interacts with dislocations in austenite, which increases the recrystallization temperature of austenite and prevents austenite grains from recrystallization. (3) The carbon and niobium nitride formed by precipitation are fine and dispersed, and the compound and the niobium in solid solution state inhibit recrystallization and prevent crystal grain growth together, and the dispersion and precipitation play a role in precipitation strengthening at low temperature. Comprehensively considering, the weight percentage of niobium in the invention is 0.005-0.035 percent.
Nitrogen (N): the nitrogen mainly plays a role in ageing strengthening, and forms nitride precipitation with the added trace alloy Nb, V, ti, al, so that the effects of reducing the grain size and strengthening the precipitation are achieved, and the nitrogen content is controlled to be 20ppm-90ppm.
Calcium (Ca): calcium has a denaturation effect on inclusions formed in the steelmaking process, forms a 7Al2O 3-12 CaO compound with low melting point and easy deformation, ensures the castability, improves the plasticity of the wire rod and the subsequent drawing processing performance, and considers the content of Al2O3 in the steelmaking process, wherein the addition amount of Ca is 20-40ppm.
Phosphorus, sulfur, copper, hydrogen (P, S, cu, H): the four elements belong to harmful elements in the wire rod of the invention, and the content of the four elements should be strictly controlled.
The invention also aims to provide a production method of the hot-rolled wire rod for the galvanized steel wires of the bridge cable of 2100MPa grade and above, which comprises the following steps,
(1) Molten steel smelting
Selecting high-grade iron ore to smelt molten iron, controlling the content of harmful elements in the molten iron, performing KR pretreatment on the molten iron, and reducing the content of P, S; adopting a converter to make steel, and controlling the tapping endpoint C to be more than or equal to 0.35%; refining in an LF furnace to deoxidize and remove impurities, wherein the holding time of refined white slag is more than or equal to 15 min; RH controls the high vacuum degree to be more than or equal to 15min, and ensures that the total vacuum time is more than or equal to 20min;
(2) Continuous casting of billets
Adopting a large round blank with the diameter of more than 600mm, carrying out electromagnetic induction heating by a tundish, controlling the superheat degree of each furnace to be less than or equal to 15 ℃ stably, preparing the electromagnetic stirring of a crystallizer and the electromagnetic stirring of a solidification tail end, and carrying out light pressing production on the blank;
(3) Intermediate blank production
The surface of the round billet is peeled off and polished to eliminate surface defects. High-temperature diffusion is carried out after finishing: heating the round billet to 1220 ℃ or above, wherein the total heating time is 13 hours or above, guaranteeing the uniformity of the cross section components of the billet, rolling the billet into an intermediate billet with phi 150-200mm, and fully preserving the heat of the intermediate billet for 48 hours or above in the hydrogen expansion temperature range; the surface hardness is reduced while the hydrogen content in the material is reduced, so that the subsequent finishing treatment is more facilitated. And (3) performing surface finishing after the blank is slowly cooled (for example, covered and slowly cooled) to room temperature, so as to ensure that the surface quality of the blank meets the internal control requirement.
(4) Billet controlled rolling
Reheating the intermediate blank, wherein the heating temperature is 1000-1200 ℃, the total heating time is more than or equal to 3 hours, rolling is controlled after the blank is discharged from a furnace, the initial rolling temperature is 950-1150 ℃, rolling is carried out in rough rolling pass by adopting a large reduction ratio, the accumulated rolling ratio is more than or equal to 4, (the rough rolling is accumulated by 7 rolling mills), and the rough rolling is followed by finish rolling. The initial rolling temperature is 900-970 ℃, and the final rolling temperature is 800-950 ℃;
(5) Wire rod controlled cooling
The wire rod is treated by on-line XDWP water bath toughening heat treatment, and the wire rod is treated according to the following technological parameters:
(5.1) the wire rod laying temperature is 800-950 ℃;
(5.2) performing on-line thermal relaxation after wire rod spinning, wherein the thermal relaxation temperature is 790-940 ℃ and the thermal relaxation time is 10s-60s;
(5.3) cooling the wire rod after on-line thermal relaxation by a water bath, wherein the water bath temperature is 80-100 ℃, and the water bath cooling time is 20-100 s;
(5.4) cooling the wire rod through an XDWP water bath, wherein the water outlet temperature is 500-650 ℃;
(5.5) carrying out heat collection and rolling after the wire rod is discharged, wherein the heat collection temperature is 230-530 ℃, and the heat collection and heat preservation time is 30min-3h, so as to play a role in reducing the hydrogen content and shortening the natural aging.
In the step (2), the tundish is heated by electromagnetic induction in the continuous casting process, the superheat degree of molten steel in each furnace is controlled to be less than or equal to 15 ℃, the crystallizer is stirred by electromagnetic stirring, the solidification tail end is stirred by electromagnetic stirring, and the blank is pressed lightly.
As one of the preferred embodiments of the present application, in step (3), the intermediate billet has a hydrogen diffusion temperature in the range of 200 to 600 ℃.
In the step (5), 2-10 weight percent of sodium chloride process salt is added into XDWP cooling water in the step (5.4), the cooling speed reaches 10-30 ℃/s, the same coil temperature difference of the coil in the step (5.5) is controlled to be less than or equal to 25 ℃, and the coil diameter is 1.1-1.2 meters; the heat collection mode in the step (5.5) is tunnel slow cooling with a heat preservation function.
In step (4), the billet is cooled by setting a cooling water tank (the water pressure of the cooling water is adjusted to achieve the purpose of on-line cooling of the billet) in the rolling process so as to control the temperature of the billet to meet the temperature design requirements of each node of rolling.
Compared with the prior art, the invention has the advantages that:
(1) The chemical components of the wire rod adopt high carbon, high silicon, high manganese, low chromium and low aluminum as basic elements, on the basis, trace amounts of carbonitride forming elements such as niobium, vanadium and titanium are added, so that the strength is improved by refining grains, the effect of resisting hydrogen-induced delayed cracking is improved, the total hydrogen content in the wire rod is reduced from 1.5ppm before to below 1.0ppm at present, and the diffusion peak temperature of hydrogen is improved by about 100 ℃ compared with the wire rod of a traditional component system; ca is added in the smelting process to play a role in modifying inclusions; the precipitation of large-particle TiN is avoided, and the precipitation of fine dispersed nitride is obtained to play a role in precipitation strengthening.
(2) The wire rod production adopts the combination of rolling control and cooling control technology in the patent, breaks through the technical defect that the wire rod adopts off-line lead bath or salt bath only for cooling control and no rolling control when adopting high silicon component design at home and abroad. When the 2100 MPa-level wire rod for the large bridge cable wire is produced in the patent, the production process is different from that in the prior patent in that: the control rolling and cooling process adopted in the production of the wire rod in the patent is a production method. After the blank is discharged from the furnace, rough rolling, finish rolling and wire spinning are carried out, the deformation of each rolling pass is accurately designed, the rough rolling ratio is more than or equal to 4, and the temperature of each node is strictly controlled within the fluctuation range. On the basis, the wire rod is cooled in an online XDWP water bath (quantitative industrial salt is added) after spinning, so that the cooling effect of the large-size wire rod is ensured.
(3) The continuous casting adopts the large round billet with the diameter of more than 600mm to produce, and the round billet is rolled into a round billet with the diameter of 150 mm-200 mm after finishing and high-temperature diffusion. The raw materials in the invention are used for adjusting and optimizing the prior continuous casting bloom to be continuous casting round bloom for rolling production, and the invention has the advantages of greatly improving the difficult problem of poor quality of the bloom corner and improving the uniformity of the cross section composition of the bloom. The surface of the round billet before reheating is peeled off, so that the problems of peeling, missing and peeling and unsatisfactory depth caused by excessive uneven 4 corners of the square billet are avoided; the finished round billet is reheated, so that the problem of high-silicon steel decarburization caused by large radian of the corner of the square billet is avoided.
(4) The wire rod after spinning is subjected to on-line thermal relaxation before entering water. According to different specifications, the thermal relaxation time is 10s-60s, precipitation strengthening of carbide and nitride before phase transformation is carried out, and dislocation density is sufficiently reduced.
(5) After the wire rod is discharged, the heat collection temperature is controlled to be 230-530 ℃, and the heat preservation time is controlled to be 30min-3h. The method has the effects of on-line annealing, eliminating internal stress, shortening natural aging and fully releasing diffusible hydrogen in the wire rod.
(6) The water bath cooling medium is water and a certain amount of industrial salt mixture is used as the cooling medium, the cooling speed of the wire rod is improved by 5-10 ℃/s, and the tensile strength of the wire rod is improved by 20MPa under the condition of the same components while the precipitation of high-carbon steel network cementite is inhibited.
(7) The sorbite tissue content is up to more than 95 percent (the rest is pearlite tissue). The pass range of the tensile strength is less than or equal to 70MPa (the coil diameter of the coil rod is 1.1-1.2 m), and no abnormal structures such as bainite, martensite and the like exist.
(8) The tensile strength of the wire rod is above 1500MPa, after drawing and galvanization, the tensile strength of the galvanized steel wire is more than or equal to 2100MPa, torsion detection is carried out according to GB/T239.1 standard, the torsion times are more than or equal to 8 times, and other indexes all meet standard requirements.
Drawings
FIG. 1 is a photograph of a metallographic microstructure of XDWP water bath toughening heat treatment of example 1 of the present invention;
FIG. 2 is an SEM photograph of the XDWP water bath patenting heat treatment of example 2 of the present invention.
Detailed Description
The invention is described in further detail below in connection with the following examples, which are exemplary and intended to illustrate the invention, but are not to be construed as limiting the invention.
And should not be taken as limiting the scope of the invention.
Example 1
The production brand of the steelmaking branch factory is XCQ2100LS1, molten steel is smelted by a converter, LF refining and RH vacuum degassing, the high vacuum degree is controlled for 15min, and the total vacuum time is ensured to be 20min; the smelting chemical components in percentage by weight are as follows:
c:0.80-1.20%, si:0.60-1.50%, mn:0.60-0.90%, cr:0.10-0.70%, al:0.010-0.070%, V:0.02-0.20%, nb:0.005-0.035%, ti:0.005-0.025%, ca:20-40ppm, N:20-90ppm, P is less than or equal to 0.015 percent, S is less than or equal to 0.006 percent, cu: less than or equal to 0.05 percent, H less than or equal to 1.0ppm, and the rest is Fe and unavoidable residual elements.
The superheat degree of molten steel is 15 ℃, the continuous casting adopts the large round billet shape production with phi 600mm, the billet is produced by adopting the light pressing and hot charging process, the round billet surface is finished and then subjected to high-temperature diffusion treatment, round steel (intermediate billet) with the intermediate billet size of phi 200mm is rolled at the furnace heating temperature of 1250 ℃ for 14 hours, the rolled billet is subjected to pit cooling, the surface of the billet is subjected to finishing treatment at normal temperature, and then is subjected to secondary heating in a heating furnace, the heating temperature of 1200 ℃ and the heat preservation time of 3.0 hours, the billet is subjected to controlled rolling production after being discharged from the furnace, and the temperature of each node of rolling is as follows: the initial rolling temperature of the blank is 950-1150 ℃, the rolling ratio of the blank in the rough rolling stage is more than or equal to 4, the temperature of the blank entering a finishing mill is 900-970 ℃, the final rolling temperature is 800-950 ℃, the spinning temperature is 800-950 ℃, and the rolling specification of the wire rod is phi 15.0mm.
Wire rods are rolled into a specified specification through high-speed wires and then are threaded, and online XDWP water bath toughening treatment is carried out according to the following technological parameters: the wire rod spinning temperature is 800-950 ℃; the wire rod is subjected to on-line thermal relaxation after spinning, the thermal relaxation temperature is 790-940 ℃, and the thermal relaxation time is 10-30 s; after the wire rod is thermally relaxed on line, cooling the wire rod by a water bath, wherein the temperature of the water bath is 80-100 ℃, the cooling time of the water bath is 20-100 s, and 6 wt% of NaCl industrial salt is added into the water bath; the temperature of water discharged from the wire rod after the wire rod is cooled by XDWP water bath is 500-650 ℃. The heat collection temperature after the wire rod is discharged is 330-530 ℃, and the tunnel slow cooling heat preservation time is controlled to be 3 hours.
The tensile strength Rm of the wire rod produced by the water bath toughening treatment is more than or equal to 1500MPa, the area shrinkage Z is more than or equal to 30%, the diameter through ring range of 1.2 meters is less than or equal to 70MPa, the sorbite content of a metallographic structure is more than or equal to 95%, and the balance is pearlite. The specification of the drawn steel wire is phi 7.0mm, the tensile strength Rm of the galvanized steel wire is more than or equal to 2150MPa, and the torsion times of the galvanized steel wire are more than or equal to 8 times.
Example 2
The production brand of the steelmaking branch factory is XCQ2200LS1, molten steel is smelted by a converter, LF refining and RH vacuum degassing, the high vacuum degree is controlled for 17min, and the total vacuum time is ensured to be 25min; the smelting chemical components in percentage by weight are as follows:
c:0.85-0.99%, si:0.95-1.25%, mn:0.60-0.90%, cr:0.25-0.35%, al:0.015-0.035%, V:0.04-0.10%, nb:0.005-0.025%, ti:0.005-0.015%, ca:20-40ppm, N:20-90ppm, P is less than or equal to 0.015 percent, S is less than or equal to 0.006 percent, cu: less than or equal to 0.05 percent, H less than or equal to 1.0ppm, and the rest is Fe and unavoidable residual elements.
The superheat degree of molten steel is 10-15 ℃, the continuous casting adopts a large round billet shape with phi 600mm, a light pressing process is adopted, the furnace heating temperature is 1220 ℃, the heat preservation time is 15 hours, round steel with the intermediate billet size of phi 150mm is rolled, the rolled billet is subjected to pit cooling, the surface of the billet is subjected to finishing treatment at normal temperature, the billet is then heated in a heating furnace for the second time, the heating temperature is 1180 ℃, the heat preservation time is 3.5 hours, the billet is subjected to controlled rolling production after being discharged from the furnace, and the temperature of each node of rolling is as follows: the rough temperature of the blank is 1100-1120 ℃, the temperature of the entering finishing mill is 950-970 ℃, the final rolling temperature is 900-950 ℃, the spinning temperature is 900-950 ℃, and the rolling specification of the wire rod is phi 14.0mm.
Wire rods are rolled into a specified specification through high-speed wires and then are threaded, and online XDWP water bath toughening treatment is carried out according to the following technological parameters: the wire rod spinning temperature is 900-950 ℃; after wire rod spinning, on-line thermal relaxation is carried out, wherein the thermal relaxation temperature is 890-940 ℃, and the thermal relaxation time is 50s; cooling the wire rod after on-line thermal relaxation by a water bath, wherein the temperature of the water bath is 80-100 ℃, the cooling time of the water bath is 20-100 s, and 10 wt% of NaCl industrial salt is added into the water bath; the temperature of water discharged from the wire rod after the wire rod is cooled by XDWP water bath is 550-650 ℃. The heat collection temperature after the wire rod is discharged is 350-530 ℃, and the tunnel slow cooling heat preservation time is 2 hours.
The tensile strength Rm of the wire rod produced by the water bath toughening treatment is more than or equal to 1550MPa, the area shrinkage Z is more than or equal to 29%, the pass limit is less than or equal to 50MPa, and the sorbite content of a metallographic structure is more than or equal to 95%. The specification of the drawn steel wire is phi 6.2mm, the tensile strength Rm of the galvanized steel wire is more than or equal to 2250MPa, and the torsion times of the galvanized steel wire are more than or equal to 8 times.
In addition to the above embodiments, the present invention also includes other embodiments, and all technical solutions that are formed by equivalent transformation or equivalent substitution should fall within the protection scope of the claims of the present invention.
Claims (10)
1. A2100 MPa grade and above bridge cable zinc-coated steel wire uses hot rolling wire rod, its characterized in that: the content of the sorbite tissue of the wire rod is more than or equal to 95%, the rest is pearlite tissue, the total circle limit of the tensile strength is less than or equal to 70MPa according to the circle diameter of the wire rod of 1.1-1.2 m, the tensile strength of the wire rod is more than 1550MPa, the tensile strength of the galvanized steel wire obtained after drawing and galvanization is more than or equal to 2100MPa, torsion detection is carried out according to the GB/T239.1 standard, and the torsion index is more than or equal to 8 times.
2. A wire rod as defined in claim 1, wherein: the production specification of the wire rod is phi 11.0 mm-phi 16.5mm.
3. A wire rod as defined in claim 1, wherein: the wire rod chemistry comprises carbon, silicon, manganese, chromium, aluminum, and also contains elements that precipitate as carbides, nitrides, carbonitrides: one or more of niobium, vanadium and titanium, the interval content of calcium and nitrogen in chemical components is precisely controlled, and the minimum content of phosphorus, sulfur, copper and hydrogen is precisely controlled.
4. A wire rod according to claim 3, wherein: the weight percentages of the chemical elements of the wire rod are as follows: c:0.80-1.20%, si:0.60-1.50%, mn:0.60-0.90%, cr:0.10-0.70%, al:0.010-0.070%, V:0.02-0.20%, nb:0.005-0.035%, ti:0.005-0.025%, ca:20-40ppm, N:20-90ppm, P is less than or equal to 0.015 percent, S is less than or equal to 0.006 percent, cu: less than or equal to 0.05 percent, H less than or equal to 1.0ppm, and the rest is Fe and unavoidable residual elements.
5. A wire rod as defined in claim 1, wherein: torsion detection is carried out according to GB/T239.1 standard, and the torsion index is more than or equal to 8 times.
6. A method for producing hot-rolled wire rods for 2100 MPa-grade or above bridge cable galvanized steel wires is characterized by comprising the following steps: comprises the following steps of the method,
(1) Molten steel smelting
Comprises molten iron pretreatment, converter steelmaking, LF refining and RH vacuum degassing, wherein the molten iron is subjected to KR pretreatment, and the P, S content is reduced; adopting a converter to make steel, and controlling the tapping endpoint C to be more than or equal to 0.35%; refining in an LF furnace to deoxidize and remove impurities, wherein the holding time of refined white slag is more than or equal to 15 min; RH controls the high vacuum degree to be more than or equal to 15min, and ensures the total vacuum time to be more than or equal to 20min;
(2) Continuous casting of billets
Adopting a large round blank with the diameter of more than 600mm, carrying out electromagnetic induction heating by a tundish, controlling the superheat degree of each furnace to be less than or equal to 15 ℃ stably, preparing the electromagnetic stirring of a crystallizer and the electromagnetic stirring of a solidification tail end, and carrying out light pressing production on the blank;
(3) Intermediate blank production
Peeling and grinding the surface of the round billet to eliminate surface defects, and performing high-temperature diffusion after finishing: the round billet heating temperature is above 1220 ℃, the total heating time is above 13 hours, the uniformity of the components of the cross section of the billet is ensured, and the billet is rolled into the billet
The intermediate blank is fully insulated for more than 48 hours in the hydrogen expansion temperature range;
(4) Billet controlled rolling
Reheating the intermediate blank, wherein the heating temperature is 1000-1200 ℃, the total heating time is more than or equal to 3 hours, rolling is controlled after the blank is discharged from a furnace, the initial rolling temperature is 950-1150 ℃, rolling is carried out by adopting a large reduction ratio in the rough rolling stage, finish rolling is carried out after rough rolling, the initial rolling temperature is 900-970 ℃, and the final rolling temperature is 800-950 ℃;
(5) Wire rod online toughening control cooling
The wire rod is processed according to the following technological parameters:
(5.1) the wire rod laying temperature is 800-950 ℃;
(5.2) performing on-line thermal relaxation after wire rod spinning, wherein the thermal relaxation temperature is 790-940 ℃ and the thermal relaxation time is 10s-60s;
(5.3) cooling the wire rod after on-line thermal relaxation by a water bath, wherein the water bath temperature is 80-100 ℃, and the water bath cooling time is 20-100 s;
(5.4) cooling the wire rod through an XDWP water bath, wherein the water outlet temperature is 500-650 ℃;
and (5.5) carrying out heat collection and coiling after the wire rod is discharged, wherein the heat collection temperature is 230-530 ℃, and the heat collection and heat preservation time is 30min-3h.
7. The method according to claim 6, wherein: in the step (2), the tundish is heated by electromagnetic induction in the continuous casting process, the superheat degree of molten steel in each furnace is controlled to be less than or equal to 15 ℃, the crystallizer is stirred by electromagnetic stirring, the solidification tail end is stirred by electromagnetic stirring, and the blank is pressed down lightly.
8. The method according to claim 6, wherein: in the step (3), the hydrogen diffusion temperature of the intermediate billet is in the range of 200-600 ℃.
9. The method according to claim 6, wherein: in the step (5), 2-10 weight percent of sodium chloride process salt is added into the XDWP cooling water in the step (5.4), the corresponding water bath cooling speed is 10-30 ℃/s, the same coil temperature difference of the coil in the step (5.5) is controlled to be less than or equal to 25 ℃, and the coil diameter is 1.1-1.2 meters; the heat collection and insulation mode in the step (5.5) is tunnel slow cooling with an insulation function.
10. The method according to claim 6, wherein: in the step (4), the blank is cooled by arranging a cooling water tank in the rolling process so as to control the temperature of the blank to be in accordance with the temperature design of each node of rolling; in the step (4), the 7-pass rolling ratio of rough rolling is more than or equal to 4.
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| CN118653094B (en) * | 2024-08-19 | 2024-11-19 | 江苏永钢集团有限公司 | Cold heading steel wire rod for 15.9-grade non-quenched and tempered bolt and manufacturing method thereof |
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| CN118653094B (en) * | 2024-08-19 | 2024-11-19 | 江苏永钢集团有限公司 | Cold heading steel wire rod for 15.9-grade non-quenched and tempered bolt and manufacturing method thereof |
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