CN111041346B - Hot-rolled wire rod for 90 kg-grade welding wire and production method thereof - Google Patents

Hot-rolled wire rod for 90 kg-grade welding wire and production method thereof Download PDF

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CN111041346B
CN111041346B CN201911134864.1A CN201911134864A CN111041346B CN 111041346 B CN111041346 B CN 111041346B CN 201911134864 A CN201911134864 A CN 201911134864A CN 111041346 B CN111041346 B CN 111041346B
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hot
wire rod
temperature
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welding wire
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CN111041346A (en
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杨斌
孔超
张贺佳
贾元海
汪青山
牛志涛
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HBIS Co Ltd Chengde Branch
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HBIS Co Ltd Chengde Branch
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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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Abstract

The invention relates to the technical field of metallurgy, and particularly discloses a hot-rolled wire rod for a 90 kg-grade welding wire and a production method thereof. The hot rolled wire rod comprises the following components: C. the hot-rolled wire rod for the 90 kg-grade welding wire is prepared from Si, Mn, Ni, Mo, Cr, V, Ti, Al, N and Zr, and the balance of Fe and inevitable impurities through the procedures of steelmaking, continuous casting, heating, rolling, spinning and cooling. The invention enables the prepared hot-rolled wire rod to meet the requirements of the wire rod for the welding wire of 90 kg grade by component adjustment and process optimization, obtains ferrite and pearlite structures suitable for drawing, and has good strength and toughness and plasticity of the wire rod, thereby saving the annealing process in the welding wire processing process, and the welded deposited metal has moderate strength, good low-temperature impact power, high production efficiency and wide application prospect.

Description

Hot-rolled wire rod for 90 kg-grade welding wire and production method thereof
Technical Field
The invention relates to the technical field of metallurgy, in particular to a hot-rolled wire rod for a 90 kg-grade welding wire and a production method thereof.
Background
Along with the light weight of mechanical equipment and the rapid development of high-strength steel, the demand on the steel for the high-strength welding wire is also increasing. The high-strength welding wire is a low-carbon alloy steel wire and is formed by hot-rolled wire rods through multi-pass cold drawing, and because the deformation amount in the cold drawing process is large, the hot-rolled wire rods for the welding wire are required to have good mechanical properties so as to meet the requirements on the drawing process, the mechanical properties and the welding quality of the welding wire.
Generally, the higher the strength grade of the welding wire, the more alloy elements are contained in the matrix, especially the more precious metal elements and super-cooled austenite stabilizing elements (such as Ni, Mo, Mn, Cr and the like) are contained, so that the strength of the hot-rolled wire rod is higher, the plasticity is poorer, and the drawing process of the welding wire is more difficult. At present, wire making links of 70 kg-grade and above welding wires generally need to perform recrystallization annealing treatment on hot-rolled wire rods and then perform drawing, and the production process is complex, the processing cost is high, the energy consumption is high, and the production efficiency is low. Moreover, the conventional wire rod for the welding wire is easy to break after being drawn for multiple times, and the performance of products such as low-temperature impact energy, surface shrinkage, elongation after breakage and the like needs to be further improved. The strength of the 90 kg welding wire is far higher than 70 kg, and direct drawing to a finished product is more difficult to realize, so that a hot-rolled wire rod suitable for the 90 kg welding wire is developed, an intermediate annealing process is omitted, one-step drawing forming is realized, and the hot-rolled wire rod has very important significance for improving enterprise competitiveness.
Disclosure of Invention
The invention provides a hot-rolled wire rod for a 90 kg-grade high-strength welding wire and a production method thereof, aiming at the problems that the conventional production process of the hot-rolled wire rod for the 90 kg-grade high-strength welding wire needs to carry out annealing treatment and the low-temperature impact energy, the surface shrinkage and the elongation after fracture of the conventional hot-rolled wire rod for the welding wire need to be further improved.
In order to solve the technical problem, the embodiment of the invention provides the following technical scheme:
a hot-rolled wire rod for a 90 kg-grade welding wire comprises the following components in percentage by weight: 0.06-0.10% of C, 0.45-0.70% of Si, 1.50-1.70% of Mn, 1.50-2.10% of Ni, 0.35-0.53% of Mo, 0.05-0.20% of Cr0.03-0.06% of V, 0.05-0.08% of Ti, 0.035-0.06% of Al, 0.06-0.09% of N, 0.03-0.07% of Zr, less than or equal to 0.01% of P, less than or equal to 0.01% of S, less than or equal to 0.01% of As, less than or equal to 0.01% of Sb, less than or equal to 0.005% of B, less than or equal to 0.01% of Se, less than or equal to 0.01% of Ca, less than or equal to 0.01% of Pb, less than or equal to 0.01% of.
The hot-rolled wire rod for the 90 kg-grade welding wire provided by the invention reduces the contents of C, Si and Mn elements as much as possible on the premise of ensuring hardenability, and realizes the reduction of strength and the improvement of toughness and plasticity; by adding Ni and Cr elements, the structure strengthening effect is achieved, the welding performance of steel is improved, and the low-temperature impact toughness of the steel is improved; by matching with V, Ti, Al and Zr with stronger refined crystal grains and precipitation strengthening effect, the defect of reduced strength of steel caused by lower content of carbon and silicon elements can be overcome, and the toughness and plasticity of the steel can be further improved; the Mo element is added, so that the hardenability of the steel is improved, the strength of the steel is improved, the toughness of the steel is improved, and the Mo can form special carbide in the steel, so that the hydrogen corrosion resistance of the steel at high temperature and high pressure is improved; the addition of N element can raise the precipitation strengthening effect of V, Ti, Al and Zr, so that under the condition of lower content said elements still have strong precipitation strengthening effect. The components are matched with each other according to a specific proportion, and the requirements on matching of high strength and toughness and plasticity in the production of the hot rolled wire rod for 90 kg-level high-strength welding wires can be well met, so that the prepared hot rolled wire rod can be drawn to a finished product at one time, an intermediate annealing process is omitted, the production process is simplified, and the production cost is saved.
Compared with the prior art, the hot-rolled wire rod prepared by the invention can reach higher strength (the tensile strength is 550-595 MPa, the tensile strength of deposited metal is more than or equal to 930MPa) and plasticity index (the elongation after fracture is more than or equal to 43 percent, and the area shrinkage is more than or equal to 75 percent), has higher low-temperature impact toughness performance (the impact performance at minus 40 ℃ is more than or equal to 130J), has good technological performance, meets the requirement that downstream users want to avoid an annealing process, and has important significance for low-carbon economy, energy conservation and emission reduction.
The action and the proportion of each element are as follows:
c is the most important constituent element in steel and is also the main element for determining the metallographic structure and the performance of the solidified carbon steel. The carbon content is low, the content of ferrite in a metallographic structure can be increased, and therefore the plasticity and the low-temperature impact property of the steel are improved, but the carbon is an element for effectively improving the strength of the steel, the carbon content is high, the tensile strength and the yield strength of the steel can be effectively improved, and in order to take the strength and the plasticity of the pipe into consideration, the content of C is designed to be 0.06-0.10%.
Si is an element which can be dissolved in ferrite to play a role in solid solution strengthening, Si can also improve the proportion of the ferrite in steel, but the yield ratio of the steel is improved due to the excessively high content of Si, but the precipitation of point-shaped carbides is promoted, so that the impact energy of the steel is not good, the solid solution strengthening and the influence on the toughness of Si are comprehensively considered, and the content of Si is designed to be 0.45-0.70%.
Mn, Cr and Ni are undercooled austenite stabilizing elements, and can enable steel to generate a bainite structure under the condition of slow cooling after welding, so that the structure strengthening effect is achieved. In the invention, Mn, Cr and Ni are selectively added, thereby not only compensating the reduction of the strength of the steel caused by lower carbon content, but also improving the toughness and the corrosion resistance of the steel.
V, Ti and Al can form carbonitrides to play a role in precipitation strengthening, and the addition of a proper amount of V, Ti and Al can properly reduce the content of carbon equivalent elements such as C, Mn, Si and the like on the premise of ensuring the strength of the steel, so that the steel has higher toughness and plasticity while maintaining high strength.
Zr is a strong carbide forming element, can effectively remove oxygen and nitrogen in the steelmaking process, simultaneously has the functions of desulfurization and dehydrogenation, can refine austenite grains of steel, and improves the welding performance and the low-temperature impact performance of the steel, but excessively high Zr can reduce the hardenability of the steel, so that the Zr content is controlled to be 0.03-0.07%.
Mo has a solid solution strengthening effect on ferrite, can improve the stability of carbide, promote the precipitation of special carbide and improve the hydrogen corrosion resistance of steel at high temperature and high pressure, and can also obviously improve the hardenability and heat strength of the steel and prevent temper brittleness. However, excessive Mo content increases the overheating sensitivity, Mo is a precious alloy, too high Mo content increases the production cost, and the Mo content in the designed steel is 0.35-0.53%.
N and V in the invention, Ti, Al, Zr affinity are extremely strong, add right amount of N element, can make Ti element precipitate out with the high dispersed TiN priority, not merely can play a role in refining the grain size of the casting blank, the tiny TiN granule that is precipitated can also be regarded as V, Al and precipitating the crystal nucleus of Zr element carbonitride, thus promote V, Al and precipitating of Zr element carbonitride, under the condition of the same content, has improved V, Al and Zr's precipitation amount, therefore, under the condition of lower above-mentioned alloy element content, still can play a higher dual function of refining the grain and precipitating the reinforcement, have reduced the production cost effectively.
The toughness and plasticity of the steel for the high-strength welding wire generally remarkably decreases along with the improvement of the strength, so that 90 kg of the steel for the welding wire is beneficial to subsequent drawing only by ensuring higher toughness and plasticity, thereby ensuring that the wire breakage problem cannot occur after multiple times of drawing. The impurity elements have important influence on the toughness and plasticity of the steel, but because of the numerous impurity elements, how to identify which elements are main elements influencing the toughness and plasticity of the steel is creative. According to the invention, by controlling the elements in a specific content range, the influence of adverse elements on the strength and toughness of the steel is effectively reduced, and the influence of adverse elements on the welding performance of steel is also reduced, so that the strength, toughness and welding performance of the steel for the high-strength welding wire are ensured to the maximum extent. Other adverse elements are further controlled on the basis of the types and the contents of the impurity elements defined by the invention, the improvement effect on the performance of the steel is not large, but the production cost is greatly increased.
The invention also provides a production method of the hot-rolled wire rod for the 90 kg-grade welding wire, which comprises the working procedures of steel making, continuous casting, rolling and cooling; the steelmaking process obtains a continuous casting square billet composed of the components, the continuous casting square billet is subjected to final rolling and then immediately subjected to wire spinning and collection to obtain a hot rolling wire rod, and the hot rolling wire rod is cooled to obtain the hot rolling wire rod for the welding wire; in the cooling procedure, a slow cooling mode is adopted when the temperature is 710-535 ℃, and the cooling speed is less than or equal to 0.05 ℃/s.
In the cooling process, the hot-rolled wire rod is slowly cooled in a temperature range of 710-535 ℃, the cooling speed is controlled to be less than or equal to 0.05 ℃/s, mixed crystal structures such as bainite or martensite and the like in the wire rod structure can be avoided, austenite is fully converted into ferrite and pearlite, the metallographic structure is more ideal, the drawing performance of the wire rod is better, the annealing process can be omitted in the welding wire processing process, and the manufacturing cost is reduced.
Preferably, the cooling speed in the cooling step is controlled in a specific manner as follows: and (3) putting the hot-rolled wire rod with the temperature of more than or equal to 710 ℃ on a roller way of the heat-preservation channel, starting the roller way when the temperature of the hot-rolled wire rod is reduced to 710 ℃, and controlling the running speed of the roller way to ensure that the cooling speed of the hot-rolled wire rod in a temperature interval of 710-535 ℃ is less than or equal to 0.05 ℃/s.
Preferably, the heat preservation channel is divided into 5 temperature zones along the conveying direction of the roller way, the temperature of each temperature zone is sequentially reduced along the conveying direction of the roller way, and the temperature difference between two adjacent temperature zones is the same; the temperature of the first temperature zone is 710-675 ℃, the temperature of the last temperature zone is 570-535 ℃, and the roller way runs in the heat preservation channel at a constant speed.
The preferable cooling mode can realize temperature-controlled cooling of the wire rod at a constant cooling speed in a temperature range of 710-535 ℃, so that martensite or bainite is avoided, austenite is fully converted into ferrite and pearlite suitable for drawing, the transformation time from austenite to ferrite is prolonged, ferrite nucleation and growth are promoted, and the ferrite content ratio is improved.
The temperature control of the heat preservation channel can select the conventional heating mode in the field to carry out temperature-division heating on the heat preservation channel, and the heating mode can be the conventional resistance heating or flame heating mode. The heat preservation passageway is the snakelike heat preservation passageway of length 80 ~ 120 m.
In the cooling process, when the temperature of the hot-rolled wire rod is lower than 535 ℃, special requirements on the cooling speed and the cooling mode are not required, the conventional air cooling, air cooling or water cooling in the field can be selected, and the performance of the prepared hot-rolled wire rod is not obviously influenced.
Preferably, in the continuous casting process, a crystallizer electromagnetic stirring and a solidification end electromagnetic stirring are adopted, wherein 2 electromagnetic stirrers are arranged at the solidification end electromagnetic stirring position and are respectively arranged at 2/5-3/5 of the total length of the liquid core and 1/5 of the total length of the liquid core away from the solidification end.
Preferably, the electromagnetic stirring parameters of the crystallizer are as follows: stirring current is 290-310A, frequency is 7.5-8.5 Hz, and stirring is carried out anticlockwise.
Preferably, the parameters of the electromagnetic stirring at the solidification end are as follows: stirring current is 290-310A, frequency is 7.5-8.5 Hz, and stirring is carried out clockwise.
The electromagnetic stirring is arranged in the crystallizer, so that the full floating of the inclusion can be promoted, the content of the inclusion in steel is reduced, 2 electromagnetic stirrers are arranged at the solidification end, the components of molten steel can be more uniform, each element has no obvious center segregation and no center shrinkage cavity, and the center porosity is less than or equal to 0.5 level.
Preferably, the side length of the continuous casting square billet is 150-165 mm.
The optimized specification of the continuous casting square billet is beneficial to the subsequent rolling procedure, and higher rolling elongation and reducing amount are ensured.
Preferably, the segregation values of C, Mn and Ni elements in the continuous casting billet are both less than or equal to 0.1.
Preferably, in the rolling procedure, the heating temperature is 1040-1080 ℃, and the heat preservation time is 20-40 min; the initial rolling temperature is 1010-1050 ℃, and the final rolling temperature is 990-1100 ℃.
The heat preservation time refers to the heat preservation time after the integral temperature of the continuous casting square billet reaches 1040-1080 ℃.
The heating temperature is too high, the heat preservation time is too long, austenite grains are large, and a mixed crystal structure is easily formed after cooling; the heating temperature is too low, the heat preservation time is too short, mixed crystals are formed when the billet enters the first rolling procedure, the existence of the mixed crystals cannot be eliminated in subsequent rolling, and the internal structure deformation of the wire rod with the mixed crystal structure is inconsistent during drawing, so that the drawing performance is reduced.
The preferable initial rolling temperature and final rolling temperature can inhibit austenite grain growth and increase of crystal defects, so that the effective grain boundary area of austenite is increased, ferrite nucleation points are increased, the ferrite amount is increased after phase transformation, grains are finer and more uniform, austenite grains are sufficiently refined, ferrite grains are sufficiently refined, and the plasticity and toughness of the hot-rolled wire rod are improved. And the preferable finishing temperature can also ensure that the temperature of the hot rolled wire rod which is collected immediately after the wire spinning and enters the heat preservation channel is higher than 710 ℃.
Since the steel for a wire of 60 kg or less contains a small amount of supercooled austenite stabilizing alloy elements, the structure of ferrite and pearlite is easily obtained after hot rolling. However, the high-strength steel for welding wires above 60 kg generally contains more super-cooled austenite stabilizing alloy elements, and the structure is difficult to obtain, so that the existing hot-rolled wire rod for welding wires of 90 kg generally is subjected to rough drawing, intermediate annealing and drawing to the finished product specification in the welding wire processing process. According to the invention, specific alloy elements are selected and added, and process conditions such as heating temperature, rolling temperature, cooling speed and the like of a steel blank in the rolling process are matched, so that the prepared hot-rolled wire rod meets the requirement of a wire rod for a welding wire of 90 kg grade, a ferrite + pearlite structure suitable for drawing is obtained, and the strength and toughness and plasticity of the wire rod are good, so that an annealing process can be omitted in the welding wire processing process, the welded deposited metal has moderate strength, good low-temperature impact power and high production efficiency, and the wire rod has a wide application prospect.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is further described in detail with reference to the following embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.
In order to better illustrate the invention, the following examples are given by way of further illustration.
Example 1
The embodiment of the invention provides a hot-rolled wire rod for a 90 kg-grade welding wire, which comprises the following chemical components:
c: 0.06%, Si: 0.70%, Mn: 1.50%, Ni: 2.1%, Mo: 0.35%, Cr: 0.05%, V: 0.06%, Ti: 0.08%, Al: 0.035%, N: 0.09%, Zr: 0.05%, P: 0.01%, S: 0.01%, As: 0.0021%, Sb: 0.001%, B: 0.0035%, Se: 0.01%, Ca: 0.001%, Pb: 0.0015%, Bi: 0.01%, Te: 0.0022%, O: 0.006%, H: 0.000045%, and the balance Fe.
The production method of the hot-rolled wire rod for the 90 kg-grade welding wire comprises the following steps:
step one, taking scrap steel as a raw material, and carrying out electric arc furnace smelting, LF refining and continuous casting treatment to obtain a continuous casting square billet with the specification of 165 x 165 mm; in the continuous casting process, crystallizer electromagnetic stirring and solidification tail end electromagnetic stirring are adopted, wherein 2 electromagnetic stirrers are arranged at the solidification tail end electromagnetic stirring position and are respectively arranged at 2/5 of the total length of the liquid core and 1/10 of the total length of the liquid core away from the solidification tail end; the electromagnetic stirring parameters of the crystallizer are as follows: stirring current 290A, frequency 8.5Hz, anticlockwise stirring, and the parameters of solidification end electromagnetic stirring are as follows: stirring at current 295A and frequency 8.5Hz clockwise;
step two, heating the continuous casting square billet in a ring furnace at 1080 ℃ for 20 min;
rolling the continuous casting square billet, wherein the initial rolling temperature is 1032 ℃, the final rolling temperature is 1005 ℃, and spinning and collecting are carried out immediately after final rolling to obtain a hot rolling disc;
dividing the heat preservation channel into 5 temperature zones along the conveying direction of the roller way, and respectively controlling the temperature, wherein the temperature of each temperature zone is gradually decreased along the conveying direction of the roller way, and the temperature difference between two adjacent temperature zones is the same; the temperature of the first temperature zone is 710-675 ℃, the temperature of the last temperature zone is 570-535 ℃, the temperature of the heat preservation channel is heated to a set temperature, the hot rolled wire rod with the temperature being more than or equal to 710 ℃ is placed on a roller way of the heat preservation channel, the roller way is started when the temperature of the hot rolled wire rod is reduced to 710 ℃, the running speed of the roller way is set to be 1.37m/min, the cooling speed of the hot rolled wire rod is constant to be 0.04 ℃/s in the temperature interval of 710-535 ℃, and the hot rolled wire rod for the 90 kg-grade welding wire is obtained by air cooling to the room temperature below 535 ℃.
Example 2
The embodiment of the invention provides a hot-rolled wire rod for a 90 kg-grade welding wire, which comprises the following chemical components:
c: 0.10%, Si: 0.45%, Mn: 1.60%, Ni: 1.95%, Mo: 0.53%, Cr: 0.11%, V: 0.03%, Ti: 0.05%, Al: 0.06%, N: 0.06%, Zr: 0.07%, P: 0.0075%, S: 0.0033%, As: 0.01%, Sb: 0.01%, B: 0.0025%, Se: 0.0021%, Ca: 0.01%, Pb: 0.002%, Bi: 0.003%, Te: 0.01%, O: 0.0041%, H: 0.0001%, and the balance Fe.
The production method of the hot-rolled wire rod for the 90 kg-grade welding wire comprises the following steps:
step one, taking scrap steel as a raw material, and carrying out electric arc furnace smelting, LF refining and continuous casting treatment to obtain a continuous casting square billet with the specification of 165 x 165 mm; in the continuous casting process, crystallizer electromagnetic stirring and solidification tail end electromagnetic stirring are adopted, wherein 2 electromagnetic stirrers are arranged at the solidification tail end electromagnetic stirring position and are respectively arranged at 3/5 of the total length of the liquid core and 1/10 of the total length of the liquid core away from the solidification tail end; the electromagnetic stirring parameters of the crystallizer are as follows: stirring current 310A, frequency 7.5Hz, anticlockwise stirring, and the parameters of solidification end electromagnetic stirring are as follows: stirring at a frequency of 7.8Hz and a stirring current of 290A in a clockwise direction;
step two, heating the continuous casting square billet in a ring furnace at 1040 ℃ for 40 min;
step three, rolling the continuous casting square billet, wherein the initial rolling temperature is 1050 ℃, the final rolling temperature is 1000 ℃, and spinning and collecting are carried out immediately after final rolling to obtain a hot rolling disc;
dividing the heat preservation channel into 5 temperature zones along the conveying direction of the roller way, and respectively controlling the temperature, wherein the temperature of each temperature zone is gradually decreased along the conveying direction of the roller way, and the temperature difference between two adjacent temperature zones is the same; the temperature of the first temperature zone is 710-675 ℃, the temperature of the last temperature zone is 570-535 ℃, the temperature of the heat preservation channel is heated to a set temperature, the hot rolled wire rod with the temperature being more than or equal to 710 ℃ is placed on a roller way of the heat preservation channel, the roller way is started when the temperature of the hot rolled wire rod is reduced to 710 ℃, the running speed of the roller way is set to be 1.71m/min, the cooling speed of the hot rolled wire rod is constant to be 0.05 ℃/s in the temperature interval of 710-535 ℃, and the hot rolled wire rod for the 90 kg-grade welding wire is obtained by air cooling to the room temperature below 535 ℃.
Example 3
The embodiment of the invention provides a hot-rolled wire rod for a 90 kg-grade welding wire, which comprises the following chemical components:
c: 0.072%, Si: 0.60%, Mn: 1.70%, Ni: 1.50%, Mo: 0.37%, Cr: 0.07%, V: 0.052%, Ti: 0.05%, Al: 0.046%, N: 0.071%, Zr: 0.033%, P: 0.009%, S: 0.0037%, As: 0.0021%, Sb: 0.0013%, B: 0.0038%, Se: 0.0061%, Ca: 0.0013%, Pb: 0.0014%, Bi: 0.001%, Te: 0.002%, O: 0.0025%, H: 0.00005%; the balance being Fe.
The production method of the hot-rolled wire rod for the 90 kg-grade welding wire comprises the following steps:
step one, taking scrap steel as a raw material, and carrying out electric arc furnace smelting, LF refining and continuous casting treatment to obtain a continuous casting square billet with the specification of 155 x 155 mm; in the continuous casting process, crystallizer electromagnetic stirring and solidification tail end electromagnetic stirring are adopted, wherein 2 electromagnetic stirrers are arranged at the solidification tail end electromagnetic stirring position and are respectively arranged at 1/2 of the total length of the liquid core and 1/10 of the total length of the liquid core away from the solidification tail end; the electromagnetic stirring parameters of the crystallizer are as follows: stirring current 300A, frequency 8.0Hz, anticlockwise stirring, and the parameters of solidification end electromagnetic stirring are as follows: stirring at a frequency of 7.5Hz and a current of 310A in a clockwise manner;
step two, heating the continuous casting square billet in a ring furnace at 1055 ℃ for 30 min;
rolling the continuous casting square billet at the initial rolling temperature of 1021 ℃ and the final rolling temperature of 1010 ℃, and immediately spinning and collecting after final rolling to obtain a hot-rolled disc;
dividing the heat preservation channel into 5 temperature zones along the conveying direction of the roller way, and respectively controlling the temperature, wherein the temperature of each temperature zone is gradually decreased along the conveying direction of the roller way, and the temperature difference between two adjacent temperature zones is the same; the temperature of the first temperature zone is 710-675 ℃, the temperature of the last temperature zone is 570-535 ℃, the temperature of the heat preservation channel is heated to a set temperature, the hot rolled wire rod with the temperature being more than or equal to 710 ℃ is placed on a roller way of the heat preservation channel, the roller way is started when the temperature of the hot rolled wire rod is reduced to 710 ℃, the running speed of the roller way is set to be 1.03m/min, the cooling speed of the hot rolled wire rod is constant to be 0.03 ℃/s in the temperature interval of 710-535 ℃, and the hot rolled wire rod for the welding wire of 90 kg grade is obtained by air cooling to the room temperature below 535 ℃.
Example 4
The embodiment of the invention provides a hot-rolled wire rod for a 90 kg-grade welding wire, which comprises the following chemical components:
c: 0.091%, Si: 0.65%, Mn: 1.50%, Ni: 1.99%, Mo: 0.51%, Cr: 0.20%, V: 0.033%, Ti: 0.08%, Al: 0.056%, N: 0.077%, Zr: 0.03%, P: 0.0067%, S: 0.0032%, As: 0.006%, Sb: 0.0017%, B: 0.005%, Se: 0.001%, Ca: 0.0013%, Pb: 0.01%, Bi: 0.001%, Te: 0.0021%, O: 0.0037%, H: 0.000033%, and the balance Fe.
The production method of the hot-rolled wire rod for the 90 kg-grade welding wire comprises the following steps:
step one, taking scrap steel as a raw material, and carrying out electric arc furnace smelting, LF refining and continuous casting treatment to obtain a continuous casting square billet with the specification of 150 x 150 mm; in the continuous casting process, crystallizer electromagnetic stirring and solidification tail end electromagnetic stirring are adopted, wherein 2 electromagnetic stirrers are arranged at the solidification tail end electromagnetic stirring position and are respectively arranged at 3/5 of the total length of the liquid core and 1/10 of the total length of the liquid core away from the solidification tail end; the electromagnetic stirring parameters of the crystallizer are as follows: stirring current 305A, frequency 7.8Hz, anticlockwise stirring, and the parameters of solidification end electromagnetic stirring are as follows: stirring current 305A, frequency 8.3Hz and clockwise stirring;
step two, heating the continuous casting square billet in a ring furnace at 1042 ℃ for 20 min;
step three, rolling the continuous casting square billet, wherein the initial rolling temperature is 1010 ℃, the final rolling temperature is 995 ℃, and immediately spinning and collecting are carried out after final rolling to obtain a hot rolling disc;
dividing the heat preservation channel into 5 temperature zones along the conveying direction of the roller way, and respectively controlling the temperature, wherein the temperature of each temperature zone is gradually decreased along the conveying direction of the roller way, and the temperature difference between two adjacent temperature zones is the same; the temperature of the first temperature zone is 710-675 ℃, the temperature of the last temperature zone is 570-535 ℃, the temperature of the heat preservation channel is heated to a set temperature, the hot rolled wire rod with the temperature being more than or equal to 710 ℃ is placed on a roller way of the heat preservation channel, the roller way is started when the temperature of the hot rolled wire rod is reduced to 710 ℃, the running speed of the roller way is set to be 1.37m/min, the cooling speed of the hot rolled wire rod is constant to be 0.04 ℃/s in the temperature interval of 710-535 ℃, and the hot rolled wire rod for the 90 kg-grade welding wire is obtained by air cooling to the room temperature below 535 ℃.
Example 5
The embodiment of the invention provides a hot-rolled wire rod for a 90 kg-grade welding wire, which comprises the following chemical components:
c: 0.073%, Si: 0.47%, Mn: 1.65%, Ni: 1.89%, Mo: 0.51%, Cr: 0.12%, V: 0.055%, Ti: 0.069%, Al: 0.053%, N: 0.082%, Zr: 0.052%, P: 0.0075%, S: 0.0029%, As: 0.0041%, Sb: 0.0015%, B: 0.0049%, Se: 0.0031%, Ca: 0.0012%, Pb: 0.002%, Bi: 0.002%, Te: 0.0021%, O: 0.0035%, H: 0.000034%, and the balance Fe.
The production method of the hot-rolled wire rod for the 90 kg-grade welding wire comprises the following steps:
step one, taking scrap steel as a raw material, and carrying out electric arc furnace smelting, LF refining and continuous casting treatment to obtain a continuous casting square billet with the specification of 165 x 165 mm; in the continuous casting process, crystallizer electromagnetic stirring and solidification tail end electromagnetic stirring are adopted, wherein 2 electromagnetic stirrers are arranged at the solidification tail end electromagnetic stirring position and are respectively arranged at 2/5 positions of the total length of the liquid core and 1/10 positions away from the solidification tail end and the total length of the liquid core; the electromagnetic stirring parameters of the crystallizer are as follows: stirring current 300A, frequency 8.0Hz, anticlockwise stirring, and the parameters of solidification end electromagnetic stirring are as follows: stirring at a frequency of 8.5Hz and a current of 300A clockwise;
step two, heating the continuous casting square billet in a ring furnace at 1060 ℃ for 27 min;
rolling the continuous casting square billet at the initial rolling temperature of 1040 ℃ and the final rolling temperature of 990 ℃, and immediately spinning and collecting after final rolling to obtain a hot rolling disc;
dividing the heat preservation channel into 5 temperature zones along the conveying direction of the roller way, and respectively controlling the temperature, wherein the temperature of each temperature zone is gradually decreased along the conveying direction of the roller way, and the temperature difference between two adjacent temperature zones is the same; the temperature of the first temperature zone is 710-675 ℃, the temperature of the last temperature zone is 570-535 ℃, the temperature of the heat preservation channel is heated to a set temperature, the hot rolled wire rod with the temperature being more than or equal to 710 ℃ is placed on a roller way of the heat preservation channel, the roller way is started when the temperature of the hot rolled wire rod is reduced to 710 ℃, the running speed of the roller way is set to be 1.03m/min, the cooling speed of the hot rolled wire rod is constant to be 0.03 ℃/s in the temperature interval of 710-535 ℃, and the hot rolled wire rod for the welding wire of 90 kg grade is obtained by air cooling to the room temperature below 535 ℃.
Comparative example 1
The comparative example provides a hot-rolled wire rod for a 90 kg-grade welding wire, and the chemical components and the preparation method of the hot-rolled wire rod are the same as those in example 5, except that the temperature of the first temperature zone of a heat-preservation channel in the cooling process is 615-580 ℃, the temperature of the last temperature zone is 470-435 ℃, namely the cooling speed of the hot-rolled wire rod in the temperature interval of 615-435 ℃ is controlled to be constant at 0.03 ℃/s.
Comparative example 2
This comparative example provides a hot rolled wire rod for a 90 kg-grade welding wire, whose chemical composition and preparation method are the same as those of example 5, except that in the continuous casting process, a crystallizer was provided for electromagnetic stirring and solidification end stirring, and an electromagnetic stirrer was provided at the solidification end at 1/3 which is the full length of the liquid core from the solidification end.
Comparative example 3
This comparative example provides a hot rolling wire rod for 90 kg level welding wire, its chemical composition is:
c: 0.073%, Si: 0.47%, Mn: 1.65%, Ni: 1.89%, Mo: 0.51%, Cr: 0.12%, V: 0.055%, Ti: 0.069%, Al: 0.053%, N: 0.082%, Zr: 0.052%, P: 0.018%, S: 0.0029%, As: 0.0041%, Sb: 0.0015%, B: 0.0049%, Se: 0.0031%, Ca: 0.0012%, Pb: 0.002%, Bi: 0.002%, Te: 0.0021%, O: 0.0035%, H: 0.000034%, and the balance Fe.
The preparation method of the hot-rolled wire rod for the 90 kg-grade welding wire is the same as that of the hot-rolled wire rod in the embodiment 5, and the details are not repeated.
The insulation channels in examples 1-5 and comparative examples 1-3 were serpentine insulation channels having a length of 100 m.
The quality of the continuously cast billets of examples 1 to 5 and comparative examples 1 to 3 was examined, and the results are shown in Table 1. The segregation condition is characterized by the concentration distribution condition of three elements of C, Mn and Ni in a continuous casting billet, the segregation value is equal to the area high concentration of each element-the area lowest concentration/average concentration, and the segregation value of each element is required to be less than or equal to 0.1 in actual production.
TABLE 1
Figure BDA0002279320140000131
The hot rolled mechanical properties of the hot rolled wire rods prepared in examples 1 to 5 and comparative examples 1 to 3, the tensile strength of the deposited metal, and the impact energy at-40 ℃ are shown in Table 2.
TABLE 2
Figure BDA0002279320140000141
The method has the advantages that through the optimization of components and processes, the prepared hot-rolled wire rod can meet the performance requirements of a wire rod for a welding wire of 90 kg grade, has higher strength and impact toughness, low production cost and high production efficiency, can effectively improve the market competitiveness of domestic enterprises, and has wide application prospect.
The above description is only for the purpose of illustrating the preferred embodiments of the present invention and is not to be construed as limiting the invention, and any modifications, equivalents or improvements made within the spirit and principle of the present invention should be included in the scope of the present invention.

Claims (10)

1. A hot-rolled wire rod for a 90 kg-grade welding wire is characterized by comprising the following components in percentage by weight: 0.06-0.10% of C, 0.45-0.70% of Si, 1.50-1.70% of Mn, 1.50-2.10% of Ni, 0.35-0.53% of Mo, 0.05-0.20% of Cr, 0.03-0.06% of V, 0.05-0.08% of Ti, 0.035-0.06% of Al, 0.06-0.09% of N, 0.03-0.07% of Zr, less than or equal to 0.01% of P, less than or equal to 0.01% of S, less than or equal to 0.01% of As, less than or equal to 0.01% of Sb, less than or equal to 0.005% of B, less than or equal to 0.01% of Se, less than or equal to 0.01% of Ca, less than or equal to 0.01% of Pb, less than or equal to 0.01%;
the production method of the hot-rolled wire rod for the 90 kg-grade welding wire comprises the working procedures of steel making, rolling and cooling; the steelmaking process obtains a continuous casting square billet composed of the components, the continuous casting square billet is subjected to final rolling and then immediately subjected to wire spinning and collection to obtain a hot rolling wire rod, and the hot rolling wire rod is cooled to obtain the hot rolling wire rod for the welding wire; in the cooling procedure, when the temperature of the hot-rolled wire rod is 710-535 ℃, a slow cooling mode is adopted, and the cooling speed is less than or equal to 0.05 ℃/s; in the continuous casting process, crystallizer electromagnetic stirring and solidification tail end electromagnetic stirring are adopted, wherein 2 electromagnetic stirrers are arranged at the solidification tail end electromagnetic stirring and are respectively arranged at 2/5-3/5 of the total length of the liquid core and 1/10 of the total length of the liquid core away from the solidification tail end.
2. The hot-rolled wire rod for a 90 kg-grade welding wire according to claim 1, wherein the microstructure is ferrite and pearlite, the tensile strength is 550 to 595MPa, the elongation after fracture is not less than 43%, the surface shrinkage is not less than 75%, the tensile strength of the deposited metal is not less than 930MPa, and the-40 ℃ impact performance of the deposited metal is not less than 130J.
3. The method for producing a hot-rolled wire rod for a 90 kg-grade welding wire according to claim 1 or 2, wherein the production method comprises the steps of steel making, continuous casting, rolling and cooling; the steelmaking process obtains a continuous casting square billet composed of the components, the continuous casting square billet is subjected to final rolling and then immediately subjected to wire spinning and collection to obtain a hot rolling wire rod, and the hot rolling wire rod is cooled to obtain the hot rolling wire rod for the welding wire; in the cooling procedure, when the temperature of the hot-rolled wire rod is 710-535 ℃, a slow cooling mode is adopted, and the cooling speed is less than or equal to 0.05 ℃/s.
4. The method for producing a hot-rolled wire rod for a welding wire of 90 kg grade according to claim 3, wherein the cooling speed is controlled by the following specific method: and (3) putting the hot-rolled wire rod with the temperature of more than or equal to 710 ℃ on a roller way of the heat-preservation channel, starting the roller way when the temperature of the hot-rolled wire rod is reduced to 710 ℃, and controlling the running speed of the roller way to ensure that the cooling speed of the hot-rolled wire rod in a temperature interval of 710-535 ℃ is less than or equal to 0.05 ℃/s.
5. The method for producing a hot-rolled wire rod for a welding wire of 90 kg grade according to claim 4, wherein the heat-insulating passage is divided into 5 temperature zones along the roller conveying direction and temperature control is performed respectively, and the temperature of each temperature zone is gradually decreased along the roller conveying direction, and the temperature difference between two adjacent temperature zones is the same; the temperature of the first temperature zone is 710-675 ℃, the temperature of the last temperature zone is 570-535 ℃, and the roller way runs in the heat preservation channel at a constant speed.
6. The method for producing a hot-rolled wire rod for a 90 kg-grade welding wire according to claim 3, wherein in the continuous casting step, a crystallizer is used for electromagnetic stirring and solidification end electromagnetic stirring is used, wherein 2 electromagnetic stirrers are arranged at the solidification end electromagnetic stirring position, and are respectively arranged at 2/5-3/5 of the total length of the liquid core and at 1/10 of the total length of the liquid core away from the solidification end.
7. The method for producing a hot-rolled wire rod for a welding wire of 90 kg grade according to claim 6, wherein the parameters of the electromagnetic stirring of the crystallizer are as follows: stirring current is 290-310A, frequency is 7.5-8.5 Hz, and stirring is carried out anticlockwise.
8. The method for producing a hot rolled wire rod for a 90 kg grade welding wire according to claim 7, wherein the parameters of the solidification end electromagnetic stirring are as follows: stirring current is 290-310A, frequency is 7.5-8.5 Hz, and stirring is carried out clockwise.
9. The production method of the hot-rolled wire rod for the 90 kg-grade welding wire according to claim 8, wherein the side length of the continuous casting billet is 150-165 mm; and/or the segregation values of C, Mn and Ni elements in the continuous casting billet are respectively less than or equal to 0.1.
10. The production method of the hot-rolled wire rod for the 90 kg-grade welding wire according to claim 3, wherein in the rolling process, the heating temperature is 1040-1080 ℃, and the heat preservation time is 20-40 min; the initial rolling temperature is 1010-1050 ℃, and the final rolling temperature is 990-1010 ℃.
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