CN113186446A - Process for controlling pearlite morphology and carbon-nitrogen compound precipitation of microalloyed medium plate - Google Patents
Process for controlling pearlite morphology and carbon-nitrogen compound precipitation of microalloyed medium plate Download PDFInfo
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- 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
- C22C33/06—Making ferrous alloys by melting using master alloys
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
- C21D2211/009—Pearlite
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Abstract
The invention provides a process for controlling the pearlite morphology and the precipitation of carbon and nitrogen compounds of a microalloyed medium plate, which is based on the temperature control of a heating process, a rolling process and a cooling process, fully combines the precipitation conditions of Nb and V microalloy elements, and fully realizes the solid solution of the Nb and V microalloy elements in the heating process; in the rolling process, a high-temperature and low-temperature pressing system is adopted, dynamic recrystallization is realized in a recrystallization zone, the crystal grains of ferrite and pearlite are refined, and the number of trigeminal crystal boundaries is increased; increasing subboundary in non-recrystallization and providing a large number of nucleation points; the cooling process changes the traditional one-stop cooling mode, adopts a variable cooling speed cooling mode, and creates time conditions for the formation of pearlite and the precipitation of Nb and V carbon nitrogen compounds, so that the form of pearlite is improved, the precipitation amount of Nb and V carbon nitrogen compounds is increased, the overall improvement of the performance of the medium plate is finally realized, and the manufacturing cost of 20-60 yuan/ton steel plate can be saved.
Description
Technical Field
The invention relates to the production field of microalloying medium plates, in particular to a process for controlling the pearlite morphology and the precipitation of carbon nitride of a microalloying medium plate.
Background
The research and development of microalloying technology and niobium microalloyed steel began in the end of the 50 s and the beginning of the 60 s of the 20 th century, when the carbon content was reduced and microalloying elements were added to improve the strength and toughness of the steel on the basis of ordinary mild steel. In the 70 s of the 20 th century, the middle east energy crisis promoted the development of high-strength microalloyed steel represented by petroleum and natural gas long-distance large-caliber pipeline steel and the wide application of controlled rolling technology; the widespread use of accelerated cooling technology (ACC) in high strength sheet and strip steel in the 80 s of the 20 th century has prompted the development of ultra low carbon steel (ULC), interstitial free IF steel and ferritic stainless steel for the automotive industry; in the 90 s of the 20 th century, the development and production of high-technology steel such as a weldable high-strength structural steel thick plate and the like are used, so that niobium becomes a necessary important microalloying element in a thermal mechanical processing (TMCP) technology, an on-line Direct Quenching (DQ) technology and the like, and the application of niobium microalloying in the fields of bake hardening steel, multi-phase steel, TRIP steel, low and medium carbon long sections, non-quenched and tempered steel, stainless steel, alloy structural steel and the like is further widened. To date, microalloying has been extensively used through extensive research and practice.
For the increasing rigors of the survival form of the steel industry at present, technical breakthroughs are sought to reduce the production cost. The reduction of production of iron and steel production enterprises is the constant pursuit of the enterprises and the key of the survival of the enterprises, and under the condition of not increasing the cost, the optimal scheme for reducing the cost is realized by fully utilizing the field condition optimization process.
At present, strengthening mechanisms for strengthening medium plate materials include various strengthening machines such as precipitation strengthening, solid solution strengthening, fine grain strengthening, phase change strengthening and the like. The phase transformation strengthening is the foundation, the room temperature structure of any medium plate is composed of single-phase or multi-phase structures, and different structures are combined to form steel grades with different strength grades. The research on the aspect is mature and widely applied; the fine grain strengthening is a strengthening mode determined based on rolling equipment and a process, a great factor depends on whether the rolling capability of the equipment can realize low-temperature rolling, and the grain refinement is realized by matching with the binding action of micro-alloy elements; the precipitation strengthening and the solid solution strengthening are determined by the types of added alloy elements, and the solid solution strengthening is realized by adding alloy which is smaller than Fe-based atoms, so that the substitution among alloy atoms or the existence of gaps can achieve the solid solution effect; the precipitation strengthening is that alloy element atoms are small and can be precipitated in the subsequent reaction with carbon and nitrogen to produce compounds, and the precipitated compounds have differences of precipitation positions and precipitation sizes.
Disclosure of Invention
The invention aims to provide a process for controlling the pearlite morphology and the precipitation of carbon and nitrogen compounds of a microalloyed medium plate, which starts from a strengthening mechanism and achieves the aim of increasing the strength of the medium plate by utilizing fine grain strengthening, precipitation strengthening and structure strengthening so as to save the production and manufacturing cost.
The invention relates to a process for controlling the pearlite morphology and the carbon-nitrogen compound precipitation of a microalloyed medium plate, which comprises the following process steps:
(1) designing components: referring to the component requirement range of Q460qk in GB/T33166-2015 hot rolled steel plate and steel strip for automobile axle housing, combining the actual conditions of a medium plate production line, firstly reasonably arranging the proportional relation among elements C, Nb and V, considering that the smelting process needs the condition Al element, the binding capacity of the Al element and N is weaker than that of the Nb and V elements, and the added Nb and V elements are fully combined with N, C; nb, V and C, N can be dissolved at 1250 ℃.
(1) By the solid solubility product formula: lg [% A][%B]n = P-Q/T, solid solution amounts of austenite and ferrite at a specific temperature are measured, then certain microalloy elements are positioned to be the sum of the solid solution amount and the precipitation amount, and the difference of the solid solution amounts in the structure at different temperatures can be positioned to be the precipitation amount. The specific component design is as follows: the steel comprises the following chemical components in percentage by weight: 0.07 to 0.11%, Si: 0.3 to 0.5%, Mn: 1.25-1.60%, S is less than or equal to 0.010%, P is less than or equal to 0.015%, Nb: 0.045-0.055%, V: 0.045-0.060%, Ti: 0.008 to 0.02% of AlS0.025 to 0.045%, and the balance of Fe and inevitable impurities.
(3) Smelting in a converter
Smelting by adopting a 120t top-bottom combined blown converter; the smelting period is 25-35 minutes; the converter smelting main alloy adopts low-carbon ferromanganese, steel grit aluminum, aluminum iron, vanadium iron and ferrocolumbium; the content of P in the converter is controlled to be below 0.015 percent; the tapping temperature of the converter is 1625-1640 ℃.
(4) Refining in LF furnace
A white slag system is adopted, the white slag retention time is more than or equal to 18min, and the alkalinity is controlled to be 5-7; argon blowing is carried out in the whole process, and the tapping temperature is 1570-1585 ℃; and (4) adding 150-200 m of aluminum wire in the later refining stage.
(5) Continuous casting
Continuous casting adopts nitrogen protection pouring; the water cooling system adopts a weak water cooling mechanism; slowly cooling the blank in a slow cooling pit for 48 h; the continuous casting speed is 0.8-1.0 m/min.
(6) Heating: heating in a furnace in a weakly reducing atmosphere; a three-stage heating system: the temperature of the second adding section is 1080-1150 ℃, the temperature of the third adding section is 1200-1220 ℃, the temperature of the soaking section is 1180-1200 ℃, and the soaking time is 10-15 min.
(7) Rolling: a two-stage controlled rolling process is adopted, and the rolling temperature of one stage is 1120-1150 ℃; the intermediate blank temperature-waiting thickness is 2.5-3 times of the thickness of the finished product; the second-stage re-rolling temperature is 920-950 ℃, and the final rolling temperature is 850-880 ℃. The rolling process is carried out for one stage, and the reduction rate is ensured to be more than 15% for two times; the total reduction rate of three times after the second stage is more than or equal to 30 percent. A reasonable rolling reduction schedule is formulated in the rolling process, particularly the pass reduction is controlled well, and the pass reduction is guaranteed to be the key for guaranteeing the refinement of pearlite and improving the existing form of pearlite; meanwhile, the method lays an energy foundation and a nucleation position foundation for the precipitation of microalloy Nb and V carbon nitride.
(8) And (3) cooling: adopting an aerial fog cooling mode, wherein the ratio of the upper water amount to the lower water amount is 1: 1-1: 1.3; the roller speed is 0.6-0.8 m/s. After final rolling, cooling is carried out in a variable cooling speed cooling mode, the first-stage cooling is carried out at a cooling speed of 10-15 ℃/s until the temperature is 700-720 ℃, the third-stage air cooling and the fourth-stage air cooling are carried out, and the fifth-stage cooling is carried out at a speed of 4-5 ℃/s until the temperature is 600-620 ℃. Cooling is carried out at a variable cooling rate, the initial cooling rate is high, the rapid transition from austenite to ferrite and pearlite phase transition region is realized, slow cooling is carried out after the phase transition region reaches the pearlite phase transition region, the form of pearlite and the precipitation amount of microalloy are changed, finally, the supercooling degree is further expanded by the medium cooling rate cooling, the precipitation of the microalloy is further promoted, conditions are created for air cooling precipitation of a subsequent steel plate in the cooling process of a roller way and a cooling bed, and the precipitation time is shortened.
(9) And stacking the steel plates after the steel plates are off line, controlling the stacking temperature within 350-400 ℃, unstacking the steel plates after cooling to room temperature, and performing the working procedures of shearing, sampling and spray printing.
The invention provides a process for controlling the pearlite morphology and the precipitation of carbon and nitrogen compounds of a microalloyed medium plate, which is based on the temperature control of a heating process, a rolling process and a cooling process, fully combines the precipitation conditions of Nb and V microalloy elements, and fully realizes the solid solution of the Nb and V microalloy elements in the heating process; in the rolling process, a high-temperature and low-temperature pressing system is adopted, dynamic recrystallization is realized in a recrystallization zone, the crystal grains of ferrite and pearlite are refined, and the number of trigeminal crystal boundaries is increased; increasing subboundary in non-recrystallization and providing a large number of nucleation points; the cooling process changes the traditional one-stop cooling mode, adopts a variable cooling speed cooling mode, and creates time conditions for the formation of pearlite and the precipitation of Nb and V carbon nitrogen compounds, so that the form of pearlite is improved, the precipitation amount of Nb and V carbon nitrogen compounds is increased, the overall improvement of the performance of the medium plate is finally realized, and the manufacturing cost of 20-60 yuan/ton steel plate can be saved.
The invention has the beneficial effects that:
the invention fully utilizes the strengthening mechanism of steel, highlights the functions of precipitation strengthening and structure strengthening, avoids the massive existence of pearlite and improves the existing form of pearlite by controlling the heating, rolling and cooling processes; the precipitation amount of Nb and V carbon nitrogen compounds is increased, the precipitation strengthening effect is enhanced, and the strength of the micro-alloyed medium plate is improved, so that the alloy cost is saved, and the production cost is reduced.
Drawings
FIG. 1 is a comparison of metallographic structures of microalloyed medium plates prepared by a conventional process (a) and a process (b) of the invention under the same composition.
Detailed Description
The present invention is further illustrated by the following specific embodiments.
(1) Actual components: the chemical composition of the steel is as follows:
(2) converter: smelting by adopting a 120t top-bottom combined blown converter, wherein the smelting period is 25-35 minutes; the converter smelting alloy adopts low-carbon ferromanganese, steel grit aluminum, aluminum iron, vanadium iron and ferrocolumbium; the content of P in the converter is controlled to be below 0.015 percent; and (5) slag stopping and tapping. Adding steel grit aluminum during tapping, fully deoxidizing molten steel and primarily alloying, wherein Als: 0.025 to 0.45%. During tapping, 200kg of synthetic slag and lime are added into steel per ton along with steel flow, and the converter is subjected to slag washing, wherein the tapping temperature is 1635 ℃.
(3) Refining in an LF furnace: adding 50kg of steel slag modifying agent per ton of steel, 100kg of refining slag per ton of steel and 400kg of lime in the first batch per ton of steel into molten steel, selecting slag in the refining process, observing, adjusting lime according to slag conditions, adopting a white slag system, keeping the white slag for more than or equal to 18min, and controlling the alkalinity to be 5-7; adding 200m of aluminum wire in the later stage of refining; after the components reach the standard, feeding calcium wires for soft blowing for not less than 8 minutes. The tapping temperature is 1578 ℃.
(4) Continuous casting: the continuous casting adopts conventional covering slag; the whole process is poured under the protection of nitrogen; the water cooling system adopts a weak water cooling mechanism; cutting the continuous casting billets and then putting the cut continuous casting billets into a slow cooling pit for slow cooling for 48 hours; the pulling speed is 0.9 m/min. The blank gauge 220 x 1580 x L (thick x width x length).
(5) Heating: heating in a furnace in a weakly reducing atmosphere; a three-stage heating system: the second heating section is 1100 ℃, the third heating section is 1210 ℃, the soaking section is 1190 ℃ and the soaking time is 13 min.
(6) Rolling: adopting a thermomechanical rolling process, wherein the initial rolling temperature of one stage is 1130 ℃, the thickness of the billet to be rolled is 36mm (the thickness specification of the finished product is 12 mm) of the thickness of the finished product, the initial rolling temperature of the second stage is 930 ℃, and the final rolling temperature is 860 ℃; the rolling process is carried out for one stage, and the reduction rate is ensured to be more than 15% for two times; the total reduction rate of three times after the second stage is more than or equal to 30 percent.
(7) And (3) cooling: adopting an aerial fog cooling mode, wherein the ratio of the upper water amount to the lower water amount is 1: 1.3; the roller speed is 0.8 m/s; the start cooling temperature is 850 ℃, after the final rolling, the cooling adopts a variable cooling speed cooling mode, the first-stage cooling adopts a cooling speed of 10-15 ℃/s to be cooled to 720 ℃, the third-stage air cooling and the fourth-stage air cooling are carried out, and the fifth-stage cooling is carried out at a speed of 4-5 ℃/s to be cooled to 618 ℃.
(8) And stacking the steel plates after the steel plates are off line, controlling the stacking temperature within 350-400 ℃, unstacking the steel plates after cooling to room temperature, and performing the working procedures of shearing, sampling and spray printing.
The properties of the microalloyed medium plate prepared are as follows:
FIG. 1 is a comparison of metallographic structures of microalloyed medium plates prepared by a conventional process (a) and a process (b) of the invention under the same composition. As can be seen from the figure, the precipitation amount of Nb and V carbon-nitrogen compounds in the conventional process is obviously less than that of the invention; the average grain size of ferrite in the conventional process is coarser than that of the invention; the existing form of pearlite is strong in the continuity of pearlite in the conventional process and relatively concentrated, and the pearlite is in small block-shaped dispersed distribution in the invention.
Claims (1)
1. A process for controlling the pearlite morphology and the carbon-nitrogen compound precipitation of a microalloyed medium plate comprises the following process steps:
(1) the steel comprises the following chemical components in percentage by mass: c: 0.07 to 0.11%, Si: 0.3 to 0.5%, Mn: 1.25-1.60%, S is less than or equal to 0.010%, P is less than or equal to 0.015%, Nb: 0.045-0.055%, V: 0.045-0.060%, Ti: 0.008 to 0.02% of AlS0.025 to 0.045%, and the balance of Fe and inevitable impurities;
(2) smelting in a converter: smelting by adopting a top-bottom combined blown converter; the smelting period is 25-35 minutes; the converter smelting main alloy adopts low-carbon ferromanganese, steel grit aluminum, aluminum iron, vanadium iron and ferrocolumbium; the content of P in the converter is controlled to be below 0.015 percent; the tapping temperature of the converter is 1625-1640 ℃;
(3) refining in an LF furnace: a white slag system is adopted, the white slag retention time is more than or equal to 18min, and the alkalinity is controlled to be 5-7; argon blowing is carried out in the whole process, and the tapping temperature is 1570-1585 ℃; adding 150-200 m of aluminum wire in the later stage of refining;
(3) continuous casting: continuous casting adopts nitrogen protection pouring; the water cooling system adopts a weak water cooling mechanism; slowly cooling the blank in a slow cooling pit for 48 h; the continuous casting speed is 0.8-1.0 m/min;
(4) heating: heating in a furnace in a weakly reducing atmosphere; a three-stage heating system: the temperature of the second adding section is 1080-1150 ℃, the temperature of the third adding section is 1200-1220 ℃, the temperature of the soaking section is 1180-1200 ℃, and the soaking time is 10-15 min;
(5) rolling: a two-stage controlled rolling process is adopted, and the rolling temperature of one stage is 1120-1150 ℃; the intermediate blank temperature-waiting thickness is 2.5-3 times of the thickness of the finished product; the second-stage secondary rolling temperature is 920-950 ℃, and the final rolling temperature is 850-880 ℃; the rolling process is carried out for one stage, and the reduction rate is ensured to be more than 15% for two times; the total reduction rate of three times after the second stage is more than or equal to 30 percent;
(6) and (3) cooling: adopting an aerial fog cooling mode, wherein the ratio of the upper water amount to the lower water amount is 1: 1-1: 1.3; the roller speed is 0.6-0.8 m/s; after final rolling, cooling by adopting a variable cooling speed cooling mode, wherein the first-stage cooling is carried out at a cooling speed of 10-15 ℃/s until the temperature is 700-720 ℃, and the third-stage air cooling and the fourth-stage air cooling are carried out, and the fifth-stage cooling is carried out at a speed of 4-5 ℃/s until the temperature is 600-620 ℃; and finally, cooling to room temperature and unstacking.
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