CN115386807A - Ferrite stainless steel hot-rolled middle plate and preparation method thereof - Google Patents

Ferrite stainless steel hot-rolled middle plate and preparation method thereof Download PDF

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CN115386807A
CN115386807A CN202211147589.9A CN202211147589A CN115386807A CN 115386807 A CN115386807 A CN 115386807A CN 202211147589 A CN202211147589 A CN 202211147589A CN 115386807 A CN115386807 A CN 115386807A
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stainless steel
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ferritic stainless
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CN115386807B (en
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张晶晶
郭保兵
宋岩
邹勇
杨永超
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Shanxi Taigang Stainless Steel Co Ltd
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Shanxi Taigang Stainless Steel Co Ltd
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • 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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C33/00—Making ferrous alloys
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Abstract

The invention belongs to the technical field of stainless steel smelting and hot rolling, and relates to a ferrite stainless steel hot rolling middle plate and a preparation method thereof. The ferrite stainless steel hot rolling middle plate comprises the following components in percentage by weight: c is less than 0.01 percent; n is less than 0.01 percent; si is less than or equal to 0.10 percent; 16.0 to 20.0 percent of Cr; p is less than or equal to 0.025 percent; s is less than or equal to 0.002%; nb10 × (C + N) to 0.25%; 0.04 to 0.08 percent of Al; ti is less than or equal to 0.01 percent; t [ O ] is less than or equal to 0.0015 percent; 0.02 to 0.11 percent of Mn0.02 percent; ni is less than or equal to 0.04 percent; cu is less than or equal to 0.02 percent, and the balance of Fe and inevitable impurities. The invention obtains the ferrite stainless steel hot rolling middle plate with the thickness of 12-25 mm of a steel plate through the innovation of chemical components and a manufacturing process, wherein the room temperature elongation is more than or equal to 30 percent, and the tensile strength is more than 450MPa; the ductile-brittle transition temperature is lower than-10 ℃, and the standard impact power value at 0 ℃ is more than 60J; the 180 ° bend does not produce cracks. The use requirements of industrial fields such as heat exchangers, large equipment flanges, mechanical equipment and the like on the ferrite stainless steel hot rolled steel plate are met.

Description

Ferrite stainless steel hot-rolled middle plate and preparation method thereof
Technical Field
The invention belongs to the technical field of stainless steel smelting and hot rolling, and relates to a ferritic stainless steel hot-rolled middle plate and a preparation method thereof, in particular to a medium-chromium ferritic stainless steel hot-rolled middle plate with high strength, high plasticity and high toughness and a preparation method thereof, which are used in the fields of heat exchangers, flanges, mechanical equipment and the like, wherein the thickness specification of the medium-chromium ferritic stainless steel hot-rolled middle plate is 12-25 mm.
Background
Compared with 304 and 316L, the ferritic stainless steel has the greatest advantages of no Ni, low price, stability, high thermal conductivity, low thermal expansion coefficient, ferromagnetism, immunity to stress corrosion cracking and the like, and is very suitable for industrial fields such as heat exchangers, large equipment flanges, mechanical equipment and the like. The steel grades commonly used are medium chromium ultra low carbon nitrogen ferritic stainless steels (C + N300 ppm) such as 439, 444, 430J 1L. However, the slip direction in the receptor core cubic structure is less, the close arrangement degree of the slip surface is low, dislocation starting of the ferritic stainless steel is difficult in the high-speed strain process, the movement range is small, and the brittleness of the ferritic stainless steel is large; meanwhile, the steel type has obvious size effect, the brittle transition temperature (DBTT) rapidly rises along with the increase of the thickness, when the thickness exceeds 12mm, the room temperature and low temperature toughness of the ferritic stainless steel plate are extremely poor, and the steel is in brittle fracture risk in steel factory production, end user processing and product service. For a steel mill, as the thickness of a ferritic stainless steel plate is increased, a process control window is narrowed, cracks in the hot rolled steel plate easily occur due to improper process routes and parameter configurations, flaw detection is improper, and the strength and the plasticity do not meet the use requirements of users, so that delivery can not be carried out according to the schedule. The problems of stamping cracking, layering, edge breaking and the like easily occur to the terminal user in the using process; in addition, the high brittle transition temperature and poor toughness greatly limit the service environment of the ferritic stainless steel plate and can only be used in areas with the indoor and outdoor temperature higher than 0 ℃ in winter.
Chinese patent publication No. CN105051234A discloses a hot rolled steel sheet of ferritic stainless steel, a method for manufacturing the same, and a steel strip, which are made to have excellent toughness and corrosion resistance by controlling the components and annealing process. However, the thickness of the ferrite hot rolled steel plate invented by the patent is 5.0-9.0 mm, the ferrite hot rolled steel plate is mainly used for automobile flanges, and the thickness specification of the ferrite hot rolled steel plate can not meet the requirements of domestic industrial manufacturing and use at present. In addition, the manufacturing process of the hot rolled steel plate of the invention of the patent only aims at the ferritic stainless steel rolled plate, and the fact that the toughness and the blanking performance of the ferritic stainless steel hot rolled steel plate manufactured by the manufacturing method of the patent are unqualified when the thickness of the steel plate reaches 9.5 mm and 10mm can be found from the embodiment, which shows that the patent can not control and improve the toughness and the processability of the ferritic stainless steel hot rolled steel plate with more than 10mm. Chinese patent publication No. CN106399833A discloses a middle-chromium molybdenum-free ferritic stainless steel with an extremely low brittle transition temperature and a method for manufacturing the same, in which a ferritic stainless steel sheet having high toughness even in an extremely cold environment is obtained by adding 0.1-0.2% of al, 0.2-0.4% of ni and 0.3-0.5% of cu, and controlling a hot rolling and annealing process, the inventive ferritic stainless steel sheet having a brittle transition temperature of-120 to-100 ℃ and a thickness of 5.5 to 8mm, but the patent does not control and improve the ductile-brittle transition of a ferritic stainless steel sheet of 8mm or more. In addition, as can be seen from the above-mentioned patent embodiments, the production process is to perform coiling after rolling by laminar cooling to 650 ℃, and the hot rolled sheet is a hot rolled sheet as in the hot rolled sheet disclosed in the chinese patent publication No. CN 105051234A. The invention patent publication No. CN102643968A discloses a method for improving the toughness of a medium chromium ferritic stainless steel plate, namely, a warm rolling process is introduced to refine a ferritic stainless steel structure and increase the formation of an intra-grain shear zone and dislocation density so as to reduce the ductile-brittle transition temperature, although a ferritic stainless steel plate with the ductile-brittle transition temperature of-10 ℃ and the thickness of 11mm is obtained in the patent example 3. However, the warm rolling process has a low rolling temperature (the heating temperature is 260-600 ℃), and since the yield strength of the ferritic stainless steel is high, the deformation resistance of the ferritic stainless steel is rapidly increased along with the reduction of the hot rolling temperature, and the multi-pass deformation rolling with the accumulated reduction of 40-80% has extremely low efficiency in industrial mass production and is easy to cause problems of edge and surface cracks and the like.
In summary, the prior art cannot provide a ferritic stainless steel hot-rolled middle plate with a thickness of 12-25 mm and a preparation method thereof.
Disclosure of Invention
The invention aims to provide a ferritic stainless steel hot-rolled middle plate and a preparation method thereof aiming at the defects of the prior art.
Specifically, the ferritic stainless steel hot-rolled middle plate comprises the following components in percentage by weight: c is less than 0.01 percent; n is less than 0.01 percent; si is less than or equal to 0.10 percent; 16.0 to 20.0 percent of Cr; p is less than or equal to 0.025 percent; s is less than or equal to 0.002%; nb10 × (C + N) to 0.25%; 0.04 to 0.08 percent of Al; ti is less than or equal to 0.01 percent; t [ O ] is less than or equal to 0.0015 percent; 0.02 to 0.11 percent of Mn0.02 percent; ni is less than or equal to 0.04 percent; cu is less than or equal to 0.02 percent, and the balance of Fe and inevitable impurities.
The ferrite stainless steel hot rolling middle plate also comprises one or two elements of 0.03-2% of Mo and less than 0.1% of V in percentage by weight.
The thickness of the ferrite stainless steel hot rolling middle plate is 12-25 mm.
On the other hand, the invention also provides a preparation method of the ferrite stainless steel hot rolling middle plate, which sequentially comprises smelting, hot rolling, primary annealing, transverse cutting, acid washing and secondary annealing;
wherein the hot rolling comprises in sequence: a casting blank heating process → a rough rolling process → a finish rolling process → a first water spray cooling process → a hot straightening process → a second water spray cooling process → trimming; wherein the temperature of the heating furnace in the casting blank heating procedure is set to be 1120-1180 ℃, and the heat preservation time is 10 +/-2 min/10mm.
The preparation method of the ferritic stainless steel hot-rolled middle plate comprises the following smelting steps: molten iron pretreatment → converter smelting → VOD refining → LF furnace refining → slab continuous casting to form a billet with the thickness of 200-220 mm, and the isometric crystal proportion of the billet is 60-80%.
In the rough rolling procedure, the ferrite stainless steel hot rolling middle plate is longitudinally rolled for 2 times, the total rolling reduction is 10-12%, and then the ferrite stainless steel hot rolling middle plate is transversely rolled for 4 times, and the total rolling reduction is 30-40%; descaling by high-pressure water, and longitudinally rolling for 6 times, wherein the total reduction is 50-60%; wherein the outlet temperature of the rough rolling is 910-950 ℃, and the thickness of the rough rolling blank is 45-55 mm.
In the finish rolling process, the ferrite stainless steel hot-rolled middle plate is longitudinally rolled for 7 times, the reduction of each time is 8-20%, the finish rolling outlet temperature is not less than 800 ℃, and the thickness of a hot-rolled steel plate after finish rolling is 12-25 mm.
In the preparation method of the ferrite stainless steel hot-rolled middle plate, the steel plate is cooled to 550-600 ℃ in the first water spray cooling process; and the second water spray cooling process cools the steel plate to room temperature.
According to the preparation method of the ferrite stainless steel hot-rolled middle plate, the temperature of the steel plate subjected to primary annealing is 880-940 ℃, the heat preservation time is 1.2-1.5 min/mm, and after the heat preservation is finished, water is uniformly sprayed in the width direction to cool the steel plate to room temperature, wherein the cooling speed is 3-5 ℃/s.
According to the preparation method of the ferrite stainless steel hot-rolled middle plate, the temperature of the steel plate subjected to secondary annealing is 100-300 ℃, the heat preservation time is 8-20 hours, and air cooling is performed after the heat preservation is finished.
The technical scheme of the invention has the following beneficial effects:
through the innovation of chemical components and a manufacturing process, the ferrite stainless steel hot-rolled middle plate with the thickness of 12-25 mm is obtained, the room-temperature elongation is more than or equal to 30%, and the tensile strength is more than 450MPa; the ductile-brittle transition temperature is lower than minus 10 ℃, and the standard impact power value at 0 ℃ is larger than 60J; the 180 ° bend does not produce cracks. The use requirements of industrial fields such as heat exchangers, large equipment flanges, mechanical equipment and the like on the ferritic stainless steel hot rolled steel plate are met.
Drawings
Various other advantages and benefits will become apparent to those of ordinary skill in the art upon reading the following detailed description of the preferred embodiments. The drawings are only for purposes of illustrating the preferred embodiments and are not to be construed as limiting the invention.
FIG. 1 is a graph of impact absorption energy vs. temperature for a ferritic stainless steel hot rolled middle plate of example 2 of the present invention in example 1.
FIG. 2 shows the metallographic structure of the plate in example 1 of the invention # 2 ferritic stainless steel hot rolled.
FIG. 3 is an internal crack observed under an optical microscope of a hot rolled middle plate of a ferritic stainless steel of comparative example No. 5 in example 2, when a cooling rate after primary annealing is 10 ℃/s.
FIG. 4 is a metallographic structure of a hot rolled middle plate of ferritic stainless steel of comparative example 7# in example 2, in which abnormal grain growth was observed when the primary annealing temperature was 1020 ℃.
Detailed Description
The invention will be described in detail with reference to the following detailed description for fully understanding the objects, features and effects of the invention. It is to be understood that the described embodiments are merely a few embodiments of the invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments of the present invention without making any creative effort, shall fall within the protection scope of the present invention. The process of the present invention employs conventional methods or apparatus in the art, except as described below. The following noun terms have meanings commonly understood by those skilled in the art unless otherwise specified.
First, each main condition of the present invention will be explained in detail, and in this context, "%" of each element content represents "% by mass" or mass%.
On the basis of studying the influence of chemical components, microstructures, manufacturing processes and the like of materials on the mechanical properties of the ferritic stainless steel hot rolled steel plate in detail, the inventor finds that a high-strength and high-plasticity ferritic stainless steel hot rolled middle plate with the thickness of 12-25 mm can be prepared under the existing production equipment conditions of a stainless steel factory by strictly controlling the components and the manufacturing processes of the ferritic stainless steel hot rolled steel plate, the room-temperature (25 ℃) elongation of the middle plate is more than or equal to 30%, the tensile strength of the middle plate is more than 450MPa, the problem of bending cracking can not occur when the middle plate is subjected to a 180-degree bending test, the relation between the bending pressure head diameter D and the steel plate thickness a in the bending test is D =2a, the excellent plastic processability is shown, and the subsequent processing requirements of bending and curling the ferritic stainless steel hot rolled steel plate by a user are met.
The ductile-brittle transition temperature (DBTT) is used for evaluating the cold brittleness of a material, the essence is the reflection of the plastic deformability of the material on the adaptability of low temperature and high loading rate, and the higher the value is, the stronger the brittleness of the material is represented. For product manufacturing enterprises, the higher the stamping and blanking rates, the higher the production efficiency. However, for the ferritic stainless steel plate, if the DBTT value is higher, the cracking rate of the product is increased under high punching and blanking speed, and the requirement of high-efficiency production cannot be met. The inventor finds that although the manufacturing of stainless steel heat exchanger shell stamping and flange blanking is basically carried out in a workshop with the temperature of above 0 ℃, satisfactory machining efficiency and qualification rate data can be obtained only by comparing and judging the DBTT value of the middle plate of the ferritic stainless steel hot rolled steel and the machining cracking rate data of a user, and controlling the DBTT value of the middle plate to be below-10 ℃ and the standard impact value of 0 ℃ to be more than 60J, and the service safety of the ferritic stainless steel hot rolled steel plate in a low-temperature environment is ensured.
In order to meet the above requirements, the composition range of the 12-25 mm middle plate needs to be further limited from the manufacturing point of view, and the manufacturing process and process parameters need to be innovated.
The limitation of the components is mainly embodied in that the Ti element content in the casting blank is reduced as much as possible on the premise of ensuring full deoxidation through alloy raw materials and casting powder component control, refining process parameter control, continuous casting process control and the like in the steelmaking process; the oxygen content (TO) of the finished product is controlled below 15 ppm; the lower the Nb content is, the better the lower the minimum lower limit of 10 (C + N) is guaranteed; the content of Ni and Cu elements is not added or reduced as much as possible.
The ferritic stainless steel hot rolled steel plate with the thickness of less than 12mm can be manufactured by a hot rolled plate manufacturing method, when the thickness reaches or exceeds 12mm, the brittleness of the ferritic stainless steel causes that a hot rolled coil is easy to brittle break when being uncoiled before subsequent annealing, normal production cannot be realized, equipment failure is caused if the thickness is light, and safety accidents are caused if the thickness is heavy. Therefore, the invention provides a method for manufacturing a ferritic stainless steel hot-rolled middle plate with the thickness of 12-25 mm.
The ferritic stainless steel hot-rolled middle plate is manufactured by smelting, hot rolling, primary annealing, transverse cutting, acid washing and secondary annealing, and on the basis of the limitation of the components, the parameters of the hot rolling and primary annealing process are further limited and secondary low-temperature annealing is innovatively adopted, so that the medium-chromium ferritic stainless steel hot-rolled middle plate with the thickness of 12-25 mm and high strength, high plasticity and high toughness is finally obtained.
Based on the above knowledge, the invention provides a ferritic stainless steel hot rolling middle plate and a manufacturing method thereof, wherein the ferritic stainless steel hot rolling middle plate comprises the following components in percentage by weight: c is less than 0.01 percent; n is less than 0.01 percent; si is less than or equal to 0.10 percent; 16.0 to 20.0 percent of Cr; p is less than or equal to 0.025 percent; s is less than or equal to 0.002%; nb10 × (C + N) to 0.25%; 0.04 to 0.08 percent of Al; ti is less than or equal to 0.01 percent; t [ O ] is less than or equal to 0.0015 percent; 0.02 to 0.11 percent of Mn; ni is less than or equal to 0.04 percent; cu is less than or equal to 0.02 percent, and the balance of Fe and inevitable impurities.
The effects of the elements and the preferable ranges of the contents thereof in the ferritic stainless steel hot rolled middle plate of the present invention will be described in detail below.
C and N are harmful elements in the ferritic stainless steel, and the plasticity, toughness and corrosion resistance of the plate in the ferritic stainless steel are reduced along with the increase of the content of C and N, so that the upper limit of the content of C and N is controlled to be less than 0.01%, the lower limit is better, the upper limit is preferably 0.008%, the lower limit is limited by equipment capacity and smelting cost, and the lower limit is 0.001%.
Si is an effective element as a deoxidizer, but is dissolved in the matrix to lower the toughness of the material. Since Si is usually carried in steel-making water, from the viewpoint of improving workability and toughness of the material, the lower the Si content, the better the Si content, and the more the refining cost increases by an excessive decrease, the upper limit is set to 0.10%, and Si may not be contained.
Cr is a key element for ensuring the corrosion resistance of the ferritic stainless steel medium plate, and the content of Cr is controlled to be 16.0-20.0% in comprehensive consideration of the corrosion resistance, the processability and the cost.
P is an impurity element in ferritic stainless steel, and easily segregates at grain boundaries to cause intergranular embrittlement, and the upper limit thereof is preferably set to 0.025%, preferably 0.020% or less, because the smaller the content thereof is.
S is an impurity element in ferritic stainless steel, and forms MnS inclusions with Mn elements in the matrix, which deteriorates corrosion resistance, and the lower the content, the better the corrosion resistance, so the upper limit is controlled to 0.002%, preferably 0.0015% or less.
Nb is an element for fixing C and N in the ferritic stainless steel, and can inhibit grain boundary precipitation of a chromium carbonitride phase and prevent intergranular corrosion from occurring, but excessive addition of Nb can cause solid solution strengthening and lead to rod-shaped Fe 2 The formation of the Nb laves phase increases the brittleness of the material, and therefore the Nb content is controlled to 10 × (C + N) to 0.25%, where Nb, C and N are each content. As the contents of C and N vary, the amount of Nb added is preferably controlled to 10 (C + N) from the viewpoint of improving toughness.
Al is added as a deoxidizing element, the lower limit of the content of Al is controlled to be 0.04% in order to ensure the deoxidizing effect, but the excessive addition of Al is extremely unfavorable for plasticity and toughness, al-Mg spinel type inclusions are easily formed in molten steel, micro cracks are easily generated at the interface of heterogeneous phases and a matrix in the rolling process, stress concentration is caused, the cracks are rapidly expanded at a lower stress level, and the low-temperature toughness of the ferritic stainless steel is further deteriorated. Therefore, the upper limit is controlled to 0.08%, preferably 0.06% or less.
Ti is an element for fixing C and N in ferritic stainless steel, as in Nb, but TiN is formed in a liquid state before stainless steel casting, is a square hard particle, and when ferritic stainless steel is plastically deformed, stress concentration is easily formed at the corner, which becomes a crack source, and causes brittle fracture. With the increase of the thickness of the ferritic stainless steel hot rolled steel plate, the reduction of the casting blank is reduced, the crushing capability of the hard phase is reduced, and the influence of TiN is more obvious. Therefore, for a 12-25 mm ferritic stainless steel medium plate, ti content control is particularly important, the Ti content is extremely low limited through alloy raw material and casting powder component control, refining process parameter control, continuous casting process control and the like in a steelmaking process, and when the Ti content in the ferritic stainless steel is less than 0.01 percent, the formation of a square TiN phase in a matrix is basically not observed. Therefore, the upper limit of the Ti content may be controlled to 0.01% or not.
O is an element which is unfavorable for both corrosion resistance and toughness of ferritic stainless steel, and is often present in the steel in the form of oxide inclusions as low as possible, so that the upper limit of the total oxygen amount (TO) in the steel is set to 0.0015%.
Mn is an inevitable element in stainless steel-making water, but is disadvantageous in terms of plasticity and toughness of ferritic stainless steel, so that the upper limit is set to 0.11%, and excessively low control causes an increase in steel-making cost, and therefore, the Mn content is controlled to 0.02 to 0.11%.
Ni and Cu are beneficial to the plasticity and corrosion resistance of the ferritic stainless steel, but the ferritic stainless steel middle plate with the thickness of 12-25 mm is largely used for manufacturing magnesium alloy smelting and casting equipment, the solubility of Ni and Cu in magnesium alloy is extremely small, and the Ni and the Cu often form Mg with magnesium 2 Ni and Mg 2 Cu intermetallic compounds, which allow a concentration lower than 10mg/kg, otherwise greatly reduce the corrosion resistance of the magnesium alloy. Therefore, the Ni and Cu contents in the raw materials of the equipment must be strictly controlled, so that the migration amounts of Ni and Cu elements in stainless steel smelting and casting equipment at high temperature to the magnesium alloy melt are controlled. The laboratoryAnd simulating the actual working condition, and performing a soaking test of the ferritic stainless steel middle plates with different Ni and Cu contents in the magnesium alloy melt at the test temperature of 660 ℃ for 8 hours. The test result shows that the migration quantities of Ni and Cu are both lower than 10mg/kg for the steel plate with Ni less than or equal to 0.04% and Cu less than or equal to 0.02%. In view of the above experimental results, the upper limit of the Ni content of the present invention is controlled to 0.04%, and Ni may not be contained. The upper limit of the Cu content is controlled to 0.02%, and Cu may not be contained.
Mo is an element for improving the corrosion resistance of ferritic stainless steel, and the effect of improving the corrosion resistance is exhibited when the content reaches 0.03%, so that the lower limit is set to 0.03%, and excessive addition of Mo lowers the workability of ferritic stainless steel, so that the content of Mo is controlled to 0.03% -0.2%.
V can be an element for fixing carbon and nitrogen in ferritic stainless steel, but is expensive and excessive addition is disadvantageous in workability, so the upper limit is controlled to 0.1%.
In the ferritic stainless steel hot rolling middle plate, the room temperature elongation of the ferritic stainless steel hot rolling middle plate with the thickness of 12-25 mm is more than or equal to 30% and the tensile strength is more than 450MPa through the synergistic effect of the elements with specific contents; the ductile-brittle transition temperature is lower than minus 10 ℃, and the standard impact power value at 0 ℃ is larger than 60J; the 180 ° bend did not crack.
The ferritic stainless steel hot-rolled middle plate is prepared by sequentially performing smelting, hot rolling, primary annealing, transverse cutting, acid pickling and secondary annealing, wherein the hot rolling process comprises 7 steps of heating a casting blank, rough rolling, finish rolling, then spraying water to cool the casting blank to 550-600 ℃, carrying out hot straightening, spraying water again to cool the casting blank to room temperature, and cutting edges.
The ferritic stainless steel casting blank structure consists of columnar crystal areas and equiaxed crystal areas, the original columnar crystals are in an as-cast state {001} < uvw > orientation, coarse alpha-oriented grains are formed in subsequent hot rolling, the orientation annealing recrystallization rate is extremely low, and the coarse alpha-oriented grains are easily left in a finished plate to cause brittle cleavage fracture. The thickness of a smelted casting blank is controlled to be 200-220 mm, the thickness of a finished product of the ferrite stainless steel hot rolling medium plate is 12-25 mm, the thicker the finished product is, the smaller the rolling reduction is, the lower the hot rolling strain energy storage is, the smaller the recrystallization driving force is, and the more developed the alpha orientation in the finished product is. Therefore, from the viewpoint of improving the toughness of finished products, the isometric crystal proportion of the casting blank is controlled to be more than 60%, the higher the isometric crystal proportion is, the better the isometric crystal proportion is, but the improvement of the isometric crystal proportion can increase the electromagnetic stirring energy consumption and reduce the production efficiency, and in addition, when the isometric crystal proportion reaches 80%, the effect basically reaches saturation. Considering the factors, the isometric crystal proportion of the casting blank is controlled to be 60-80%.
The research result of the inventor in a laboratory shows that the grain refinement is beneficial to the ferrite stainless steel hot rolling middle plate to obtain the excellent performance of high strength and high toughness. Therefore, the idea of selecting the technological parameters of the hot rolling procedure is low-temperature heating and low-temperature hot rolling, and sufficient recrystallization driving energy is provided for the annealing of finished products. The heating temperature of the casting blank before hot rolling and rough rolling is controlled to be 1120-1180 ℃, the heat preservation time is 10 +/-2 min/10mm, the strength of the material is increased along with the temperature drop in the hot rolling process when the heating temperature is too low, and the material exceeds the load of a rolling mill, so that the smooth rolling cannot be realized; the temperature is too high, the crystal grains grow seriously and the hot rolling fission problem is easy to appear by overburning.
The matching and the reduction control of transverse and longitudinal rolling passes in the hot rolling rough rolling process not only ensure the order width of a customer, but also reduce the anisotropy of the performance of a finished product most importantly, so that the transverse and longitudinal impact toughness all meet the design requirement; the outlet temperature of the finish rolling is controlled to be above 800 ℃, and the water is sprayed to cool to 550-600 ℃ after the finish rolling, so as to prevent brittle sigma phase and Fe 2 Separating out an Nb phase; then the unevenness of the middle plate is controlled by hot straightening. The temperature of the hot rolled plate after hot straightening is about 500 ℃, and the hot rolled plate is sprayed with water again to be cooled to room temperature so as to prevent the low-temperature brittleness at 475 ℃ of the ferritic stainless steel.
The temperature of the primary annealing steel plate is controlled to be 880-940 ℃, the temperature is too low, recrystallization cannot be finished, the tissue of a finished product is in a strip shape, and the brittle alpha-oriented crystal grains are taken as the main material; if the temperature is too high, crystal grains are easy to grow, the strength of a finished product is reduced, and the ductile-brittle transition temperature is increased. In addition, in order to ensure the plate shape after primary annealing, water is uniformly sprayed along the width direction of the hot rolled plate to cool the hot rolled plate to room temperature, and the cooling speed needs to be controlled at 3-5 ℃/s. When the cooling speed is lower than 3 ℃/s, brittle sigma phase and Fe are precipitated in the cooling process 2 A Nb phase; the cooling speed is higher than 5 ℃/s, and the ferritic stainless steel hot rolled plate is a thick medium plate and is cooledHowever, excessive temperature difference of the cross section of the hot rolled plate is easily caused by excessive speed, the residual stress is increased rapidly, and when the residual stress exceeds the tensile strength of a matrix, microcracks are formed inside the hot rolled plate, as shown in fig. 3, and the flaw detection of a finished product is not successful.
The secondary annealing is to put the acid-washed steel plate into a low-temperature furnace for secondary annealing, and the laboratory research result shows that because the thickness of the ferrite stainless steel hot-rolled middle plate is 12-25 mm, even if the cooling speed after the primary annealing is limited to 3-5 ℃/s, a large amount of residual annealing stress still exists in the middle plate, and the impact toughness and the plasticity of the ferrite stainless steel hot-rolled middle plate are greatly reduced. The temperature of the secondary annealing steel plate is limited to 100-300 ℃, the heat preservation time is 8-20 h, and then the steel plate is taken out for air cooling. The temperature is lower than 100 ℃, the residual stress eliminating effect is not obvious, the heat preservation time needs to be greatly prolonged, and the production efficiency is influenced; the temperature is higher than 300 ℃, the shape of a hot rolled plate is affected, and the surface of the steel plate is easily oxidized and discolored.
Examples
The invention is further illustrated by the following examples, which are not intended to limit the scope of the invention. Experimental procedures without specifying specific conditions were carried out in the following examples, according to conventional methods and conditions.
Example 1
Steels with different compositions shown in the table 1 were subjected to smelting, hot rolling, cross cutting, primary annealing, pickling, and secondary annealing to prepare a ferrite stainless steel hot-rolled middle plate with a thickness of 12 mm. Controlling the isometric crystal proportion of the casting blank to be 60-80%, heating the casting blank at 1120-1180 ℃ before hot rolling, preserving heat for 10 +/-2 min/10mm, then carrying out rough rolling and finish rolling, wherein the outlet temperature of the rough rolling is 910-950 ℃, the outlet temperature of the finish rolling is not less than 800 ℃, spraying water, cooling to 550-600 ℃, then carrying out hot straightening, the temperature after the hot straightening is about 500 ℃, spraying water, cooling to room temperature, and then cutting edges and transversely cutting.
Then, the hot-rolled middle plate is kept at 880-940 ℃ for 1.2-1.5 min/mm, and then is cooled to room temperature at the speed of 3-5 ℃/s. After acid washing, secondary annealing is carried out, the temperature of the steel plate is 100-300 ℃, the temperature is kept for 8-20 h, and then air cooling is carried out.
Table 1 shows the chemical compositions of seven examples and three comparative examples of the ferritic stainless steel hot rolled middle plate of the present invention; table 2 shows the results of the tensile test of metallic materials according to GB/T228.1 part 1: the results of evaluation of tensile strength, elongation, bending properties and impact properties of the inventive examples and comparative examples in Table 1 are shown in Room temperature test method, GB/T232 bending test method for Metal materials, and GB/T229 impact test method for Charpy pendulum for Metal materials.
Figure BDA0003852288420000111
TABLE 2 evaluation results of the properties of ferritic stainless steels of the inventive and comparative examples
Figure BDA0003852288420000121
As is clear from tables 1 and 2, the ferritic stainless steel hot rolling middle plate with the composition of the present invention has good strength, elongation and toughness, and fig. 1 and 2 are a graph of impact absorption energy versus temperature and a metallographic structure of the ferritic stainless steel hot rolling middle plate of example 2# of the present invention, respectively; however, the comparative examples of the present invention failed to satisfy the requirements of strength and toughness.
Example 2
Table 1, the steel of the invention example 3 is selected, and the ferritic stainless steel hot-rolled middle plate with the thickness of 12-25 mm is prepared from the steel with the composition through smelting, hot rolling, transverse cutting, primary annealing, acid washing and secondary annealing. Tensile strength, elongation, bending properties and impact properties were evaluated in the same manner as in example 1. The test conditions and the evaluation results are shown in table 3 and table 4, respectively.
TABLE 3 production conditions of ferritic stainless steels of inventive and comparative examples
Figure BDA0003852288420000122
Figure BDA0003852288420000131
TABLE 4 evaluation results of ferritic stainless steels of the inventive and comparative examples
Figure BDA0003852288420000132
As can be seen from Table 4, the 1-3 # ferritic stainless steel hot-rolled middle plate prepared by the preparation method of the invention has good strength, plasticity and toughness; in the comparative example deviating from the present invention, some of the strength, plasticity and toughness were not qualified, and in comparative example 4 in table 4, the equiaxed crystal ratio and the finish rolling outlet temperature were too low, resulting in too low elongation and insufficient toughness of the hot rolled middle plate; in comparative example 5, the cooling rate after the primary annealing reached 10 ℃/s, and microcracks were formed inside the middle plate due to excessive thermal stress of the cross section of the middle plate, as shown in fig. 3, the strength and elongation were extremely low, and the bending cracks; comparative example 6 has insufficient secondary annealing time, residual stress is not completely eliminated, and the hot rolled sheet product has low tensile strength and elongation values and poor toughness. Comparative example 7 the hot rolled middle plate has an excessively high primary annealing temperature, resulting in abnormal growth of crystal grains, and the hot rolled product performance is significantly inferior to that of the inventive example, and the metallographic structure is shown in fig. 4.
The present invention has been disclosed in the foregoing in terms of preferred embodiments, but it will be understood by those skilled in the art that these embodiments are merely illustrative of the present invention and should not be construed as limiting the scope of the present invention. It should be noted that all changes and substitutions that are equivalent to these embodiments are deemed to be within the scope of the claims of the present invention. Therefore, the protection scope of the present invention should be subject to the scope defined in the claims.

Claims (10)

1. A ferrite stainless steel hot rolling middle plate is characterized by comprising the following components in percentage by weight: c is less than 0.01 percent; n is less than 0.01 percent; si is less than or equal to 0.10 percent; 16.0 to 20.0 percent of Cr; p is less than or equal to 0.025 percent; s is less than or equal to 0.002%; nb10 × (C + N) to 0.25%; 0.04 to 0.08 percent of Al; ti is less than or equal to 0.01 percent; t [ O ] is less than or equal to 0.0015 percent; 0.02 to 0.11 percent of Mn0.02 percent; ni is less than or equal to 0.04 percent; cu is less than or equal to 0.02 percent, and the balance of Fe and inevitable impurities.
2. The ferritic stainless steel hot rolled middle plate according to claim 1, further comprising one or two elements of Mo 0.03 to 2% and V < 0.1% in weight percentage.
3. The ferritic stainless steel hot rolled mid-sheet according to claim 1 or 2, characterized in that the thickness of the ferritic stainless steel hot rolled mid-sheet is 12-25 mm.
4. A method for the preparation of a ferritic stainless steel hot rolled middle plate according to any of claims 1-3 comprising in sequence smelting, hot rolling, primary annealing, cross cutting, pickling and secondary annealing, characterized in that the hot rolling comprises in sequence: a casting blank heating procedure → a rough rolling procedure → a finish rolling procedure → a first water spray cooling procedure → a hot straightening procedure → a second water spray cooling procedure → an edge cutting; wherein the temperature of the heating furnace in the casting blank heating procedure is set to be 1120-1180 ℃, and the heat preservation time is 10 +/-2 min/10mm.
5. The method of making a ferritic stainless steel hot rolled mid-plate as claimed in claim 4 wherein the smelting comprises: molten iron pretreatment → converter smelting → VOD refining → LF furnace refining → slab continuous casting to obtain billet with thickness of 200-220 mm, and the isometric crystal proportion is 60-80%.
6. The method for preparing the ferritic stainless steel hot-rolled middle plate as claimed in claim 4, wherein in the rough rolling process, the longitudinal rolling is performed for 2 passes, the total rolling reduction is 10-12%, the transverse rolling is performed for 4 passes, and the total rolling reduction is 30-40%; descaling by high-pressure water, and longitudinally rolling for 6 times, wherein the total reduction is 50-60%; wherein the outlet temperature of the rough rolling is 910-950 ℃, and the thickness of the rough rolling blank is 45-55 mm.
7. The method for preparing the ferritic stainless steel hot-rolled middle plate as claimed in claim 4, wherein the finish rolling process comprises 7 passes of rolling in a longitudinal direction, a reduction of 8 to 20% per pass, a finish rolling exit temperature of not less than 800 ℃, and a thickness of the hot-rolled steel plate after the finish rolling is 12 to 25mm.
8. The method for preparing a ferritic stainless steel hot-rolled middle plate according to claim 4, wherein the first water spray cooling process cools a steel plate to 550 to 600 ℃; and the second water spray cooling process cools the steel plate to room temperature.
9. The preparation method of the ferritic stainless steel hot-rolled middle plate as claimed in claim 4, wherein the temperature of the steel plate subjected to primary annealing is 880-940 ℃, the heat preservation time is 1.2-1.5 min/mm, and after the heat preservation is finished, the steel plate is uniformly cooled to room temperature by water spraying along the width direction at a cooling speed of 3-5 ℃/s.
10. The method for preparing the ferritic stainless steel hot-rolled middle plate as claimed in claim 4, wherein the temperature of the secondarily annealed steel plate is 100 to 300 ℃, the holding time is 8 to 20 hours, and the steel plate is air-cooled after the holding is finished.
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