CN115386807B - 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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CN115386807B
CN115386807B CN202211147589.9A CN202211147589A CN115386807B CN 115386807 B CN115386807 B CN 115386807B CN 202211147589 A CN202211147589 A CN 202211147589A CN 115386807 B CN115386807 B CN 115386807B
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stainless steel
hot
less
rolled
middle plate
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CN115386807A (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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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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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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    • 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
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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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • 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
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    • 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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    • 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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    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • 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
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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-rolled middle plate comprises the following components in percentage by weight: c is less than 0.01%; n is less than 0.01%; si is less than or equal to 0.10 percent; cr 16.0-20.0%; p is less than or equal to 0.025%; s is less than or equal to 0.002%; nb10 x (C+N) to 0.25%; 0.04 to 0.08 percent of Al; ti is less than or equal to 0.01%; t [ O ] is less than or equal to 0.0015%; mn0.02% -0.11%; ni is less than or equal to 0.04 percent; cu is less than or equal to 0.02 percent, and the balance is Fe and unavoidable impurities. The invention obtains the ferrite stainless steel hot-rolled middle plate with the thickness of the steel plate of 12-25 mm through innovation of chemical components and manufacturing process, 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 higher than 60J;180 ° bending does not produce cracks. Meets the use requirements of the industrial fields of heat exchangers, large equipment flanges, mechanical equipment and the like on the ferrite stainless steel hot rolled steel plate.

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, relates to a ferrite stainless steel hot rolling middle plate and a preparation method thereof, and particularly relates to a medium-chromium ferrite stainless steel hot rolling middle plate with high strength, high plasticity and high toughness used in the fields of heat exchangers, flanges, mechanical equipment and the like and a preparation method thereof, wherein the thickness specification of the medium-chromium ferrite stainless steel hot rolling middle plate is 12-25 mm.
Background
Compared with 304 and 316L, the ferritic stainless steel has the greatest advantages of no Ni, lower and stable price, high heat conductivity, low thermal expansion coefficient, ferromagnetism, immunity to stress corrosion cracking and the like, and is very suitable for being used in the industrial fields of heat exchangers, large-scale equipment flanges, mechanical equipment and the like. The commonly used steel types are ferrite stainless steel (C+N is less than or equal to 300 ppm) with medium chromium and ultra-low carbon nitrogen such as 439, 444 and 430J 1L. However, the acceptor has the restriction of small sliding direction and low close-packed degree of sliding surfaces in the acceptor's centered cubic structure, and the ferritic stainless steel is difficult to start in the high-speed strain process and has small movement range, so that the ferritic stainless steel has large brittleness; meanwhile, the steel has obvious size effect, the brittle transition temperature (DBTT) rises rapidly along with the thickness, when the thickness exceeds 12mm, the room temperature and low temperature toughness of the ferrite stainless steel plate are extremely poor, and the steel mill production, end user processing and product service are all at risk of brittle fracture. For steel mills, as the thickness of the ferrite stainless steel plate increases, a process control window is narrowed, a process route and parameter configuration are unsuitable, cracks in the hot rolled steel plate easily occur, flaw detection is unsuitable, and the strength and plasticity do not meet the use requirements of users, so that the hot rolled steel plate cannot be delivered on schedule. The problems of stamping cracking, layering, blanking cracking and the like easily occur in the using process of the terminal user; in addition, the high toughness difference of the brittle transition temperature greatly limits the service environment of the ferrite stainless steel plate, and the ferrite stainless steel plate can only be used in areas with indoor and winter outdoor temperatures higher than 0 ℃.
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 is excellent in toughness and corrosion resistance by controlling the composition and annealing process. However, the thickness of the ferrite hot rolled steel plate invented by the patent is 5.0-9.0 mm, and the ferrite hot rolled steel plate is mainly used for automobile flanges, and the thickness specification of the ferrite hot rolled steel plate cannot meet the requirements of manufacturing and using in the domestic industry at present. Further, the process for producing a hot rolled steel sheet according to the invention of this patent was found to be inferior in toughness and blanking properties only for rolled ferritic stainless steel sheets, and it was found from examples that the toughness and workability of hot rolled ferritic stainless steel sheets of 10mm or more were not controlled and improved when the sheet thicknesses were 9.5 and 10mm. The Chinese patent publication No. CN106399833A discloses a medium chromium molybdenum-free ferritic stainless steel with extremely low brittle transition temperature and a preparation method thereof, namely, a ferritic stainless steel plate with high toughness under 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 hot rolling and annealing processes, wherein the brittle transition temperature of the ferritic stainless steel plate is-120 to-100 ℃ and the thickness is 5.5-8 mm, but the patent does not control and improve the ductile brittle transition of the ferritic stainless steel plate with the thickness of more than 8 mm. In addition, as can be seen from the above-mentioned patent embodiments, the production process is to cool the rolled sheet to 650 ℃ for coiling, and the production process is to use a hot rolled coil similar to the hot rolled steel sheet disclosed in the chinese patent publication No. CN105051234 a. Chinese patent publication No. CN102643968A discloses a method for improving toughness of middle-chromium ferritic stainless steel sheet, that is, refining ferritic stainless steel structure by introducing warm rolling process to increase formation of intragranular shear band and dislocation density to reduce ductile-brittle transition temperature, although ferrite stainless steel sheet with ductile-brittle transition temperature at-10 ℃ and thickness specification of 11mm is obtained in the above patent example 3. However, the warm rolling process is low in rolling temperature (heating temperature is 260-600 ℃), and because 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 rolling reduction of 40-80% is extremely low in efficiency and easy to cause side and surface cracks in industrial mass production.
In view of the above, the prior art has not yet provided a hot rolled ferritic stainless steel middle plate with a thickness of 12-25 mm and a method for manufacturing the same.
Disclosure of Invention
The invention aims at overcoming the defects of the prior art and provides a ferrite stainless steel hot-rolled middle plate and a preparation method thereof.
Specifically, the ferritic stainless steel hot-rolled middle plate comprises the following components in percentage by weight: c is less than 0.01%; n is less than 0.01%; si is less than or equal to 0.10 percent; cr 16.0-20.0%; p is less than or equal to 0.025%; s is less than or equal to 0.002%; nb10 x (C+N) to 0.25%; 0.04 to 0.08 percent of Al; ti is less than or equal to 0.01%; t [ O ] is less than or equal to 0.0015%; mn0.02% -0.11%; ni is less than or equal to 0.04 percent; cu is less than or equal to 0.02 percent, and the balance is Fe and unavoidable impurities.
The ferrite stainless steel hot-rolled middle plate also comprises one or two elements of 0.03-2% of Mo and less than 0.1% of V according to weight percentage.
The thickness of the ferrite stainless steel hot-rolled middle plate is 12-25 mm.
On the other hand, the invention also provides a preparation method of the ferrite stainless steel hot-rolled middle plate, which sequentially comprises smelting, hot rolling, primary annealing, transverse cutting, acid washing and secondary annealing;
wherein, the hot rolling includes in order: casting blank heating process, rough rolling process, finish rolling process, first water spray cooling process, hot straightening process, second water spray cooling process and trimming process; wherein the temperature of a heating furnace in the casting blank heating process is set to be 1120-1180 ℃, and the heat preservation time is 10+/-2 min/10mm.
The preparation method of the ferrite stainless steel hot-rolled middle plate comprises the following steps of: molten iron pretreatment, converter smelting, VOD refining, LF refining, and slab continuous casting to form a billet with the thickness of 200-220 mm, wherein the equiaxial crystal proportion is 60-80%.
In the rough rolling procedure, firstly, rolling for 2 times longitudinally, wherein the total rolling reduction is 10-12%, then, rolling for 4 times transversely, and the total rolling reduction is 30-40%; after descaling by high-pressure water, longitudinal rolling for 6 times, wherein the total rolling reduction is 50-60%; wherein the outlet temperature of rough rolling is 910-950 ℃, and the thickness of rough rolled blank is 45-55 mm.
According to the preparation method of the ferrite stainless steel hot-rolled middle plate, in the finish rolling process, 7 passes are rolled longitudinally, the reduction of each pass 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.
According to the preparation method of the ferrite stainless steel hot-rolled middle plate, the steel plate is cooled to 550-600 ℃ in the first water spraying and cooling process; and the second water spray cooling procedure 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 to room temperature, and 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 secondary annealed steel plate is 100-300 ℃, the heat preservation time is 8-20 h, and air cooling is performed after heat preservation is finished.
The technical scheme of the invention has the following beneficial effects:
the invention obtains the ferrite stainless steel hot-rolled middle plate with the thickness of the steel plate of 12-25 mm through innovation of chemical components and manufacturing process, 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 higher than 60J;180 ° bending does not produce cracks. Meets the use requirements of the industrial fields of heat exchangers, large equipment flanges, mechanical equipment and the like on the ferrite stainless steel hot rolled steel plate.
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 showing the impact energy absorption versus temperature of a hot rolled sheet of ferritic stainless steel # 2 according to example 1 of the present invention.
FIG. 2 shows the metallographic structure of a hot-rolled sheet of ferritic stainless steel of example 2 according to the invention in example 1.
FIG. 3 is an inner crack observed under an optical microscope in a hot rolled sheet of comparative example 5# ferritic stainless steel in example 2 when the cooling rate after one annealing is 10 ℃/s.
FIG. 4 shows the hot rolled sheet of comparative example 7# ferritic stainless steel in example 2, which has a metallographic structure at a primary annealing temperature of 1020℃and is found to have an abnormal grain growth in comparison with FIG. 2.
Detailed Description
The present invention will be described in detail with reference to the following embodiments for a full understanding of the objects, features, and effects of the present invention. It will be apparent that the described embodiments are only some, but not all, embodiments of the invention. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention. The process of the present invention is carried out by methods or apparatus conventional in the art, except as described below. The following terms have the meanings commonly understood by those skilled in the art unless otherwise indicated.
First, each main condition of the present invention will be described in detail, and in this context, "%" of each element represents "% by mass" or mass%.
On the basis of detailed study of the influence of chemical components, microstructures, manufacturing processes and the like of materials on the mechanical properties of the ferrite stainless steel hot rolled steel plate, the inventor finds that through long-term mass production tracking test, the components and manufacturing processes of the ferrite stainless steel hot rolled steel plate are strictly controlled, the high-strength high-plasticity ferrite stainless steel hot rolled middle plate with the thickness specification of 12-25 mm can be prepared under the existing production equipment conditions of a stainless steel factory, the room temperature (25 ℃) elongation rate of the middle plate is more than or equal to 30%, the tensile strength is more than 450MPa, the 180-DEG bending test of the middle plate is carried out, the problem of bending cracking does not occur, the relation between the bending pressure head diameter D and the steel plate thickness a during the bending test is D=2a, and the excellent plastic workability is demonstrated, and the subsequent processing requirements of users on bending and curling the ferrite stainless steel hot rolled steel plate are met.
Ductile to brittle transition temperature (DBTT) is used for the assessment of material cold brittleness, essentially a reflection of the plastic deformation ability of a material to low temperature and high load rate adaptability, the higher the value, the stronger the brittleness of the material. For a product manufacturing enterprise, the higher the stamping and blanking rate, the higher the production efficiency. However, for ferritic stainless steel middle plates, if the DBTT value is high, this means that the cracking rate of the product is increased at high punching and blanking rates, and the requirement for efficient production cannot be satisfied. The inventor finds that although the manufacturing of the shell stamping and flange blanking of the stainless steel heat exchanger is basically carried out in a workshop with the temperature of more than 0 ℃, the DBTT value of the middle plate of the ferrite stainless steel hot rolling and the data of the user processing cracking rate are compared and judged, and only the DBTT value of the middle plate is controlled below minus 10 ℃ and the standard impact value of the temperature of 0 ℃ is more than 60J, satisfactory processing efficiency and qualification rate data can be obtained, and the service safety of the ferrite stainless steel hot rolling 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 flow and technological parameters need to be innovated.
The limitation of the components is mainly characterized in that the Ti element content in the casting blank is reduced as much as possible on the premise of ensuring sufficient deoxidation by controlling the components of alloy raw materials and covering slag in the steelmaking process, controlling the parameters of the refining process, controlling the continuous casting process and the like; the oxygen content (T [ O ]) of the finished product is controlled below 15 ppm; the lower the Nb content is on the basis of ensuring the lowest lower limit of 10 x (C+N), the better; the Ni and Cu element contents are not added or reduced as much as possible.
The hot rolled ferritic stainless steel plate with the thickness of less than 12mm can be manufactured by adopting a hot rolled coil manufacturing method, when the thickness reaches or exceeds 12mm, the hot rolled coil is extremely fragile when uncoiling before subsequent annealing due to brittleness of the ferritic stainless steel, cannot be normally manufactured, equipment failure is caused if the hot rolled coil is light, and safety accidents are caused if the hot rolled coil is heavy. The invention provides a manufacturing method of a ferrite stainless steel hot-rolled middle plate with a thickness of 12-25 mm.
The hot rolled ferritic stainless steel middle plate is manufactured through smelting, hot rolling, primary annealing, transverse cutting, acid washing and secondary annealing, and on the basis of the limitation of the components, the hot rolling and primary annealing process parameters are further limited, and the secondary low-temperature annealing is adopted innovatively, so that the middle chromium type hot rolled ferritic stainless steel middle plate with the steel plate thickness of 12-25 mm, high strength, high plasticity and high toughness is finally obtained.
Based on the above findings, the present invention provides a ferritic stainless steel hot-rolled middle plate and a manufacturing method thereof, wherein the ferritic stainless steel hot-rolled middle plate comprises, by weight: c is less than 0.01%; n is less than 0.01%; si is less than or equal to 0.10 percent; cr 16.0-20.0%; p is less than or equal to 0.025%; s is less than or equal to 0.002%; nb10 x (C+N) to 0.25%; 0.04 to 0.08 percent of Al; ti is less than or equal to 0.01%; t [ O ] is less than or equal to 0.0015%; mn0.02% -0.11%; ni is less than or equal to 0.04 percent; cu is less than or equal to 0.02 percent, and the balance is Fe and unavoidable impurities.
The actions of the elements and preferred ranges of the contents thereof in the hot rolled sheet of ferritic stainless steel according to the present invention are described in detail below.
C and N are harmful elements in the ferritic stainless steel, and the plasticity, toughness and corrosion resistance of the middle plate of 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 below 0.01 percent, the lower limit is preferably 0.008 percent, and the lower limit of the content of C and N is 0.001 percent due to the limitations of equipment capacity and smelting cost.
Si is an effective element as a deoxidizer, but solid solution in the matrix will reduce the toughness of the material. Si is usually introduced into steel-making molten iron, and from the viewpoint of improving the workability and toughness of the material, the lower the content thereof, the more reduced the content thereof, and the refining cost increases, so that the upper limit may be set to 0.10% and Si may not be contained.
Cr is a key element for ensuring corrosion resistance of a plate in the ferritic stainless steel, and the content thereof is controlled to be 16.0% -20.0% in view of corrosion resistance, workability and cost.
P is an impurity element in ferritic stainless steel, and tends to be easily aggregated at grain boundaries to cause intergranular embrittlement, and the lower the content, the better the content, and therefore the upper limit is controlled to 0.025%, preferably 0.020% or less.
S is an impurity element in ferritic stainless steel, and is extremely likely to form MnS inclusions with Mn element in the matrix, and the lower the content is, the better the corrosion resistance is, so that the upper limit is controlled to 0.002%, preferably 0.0015% or less.
Nb is an element for fixing C and N in ferritic stainless steel, and the addition of Nb can inhibit the grain boundary precipitation of chromium carbonitride phase and prevent the occurrence of intergranular corrosion, but excessive addition of Nb can cause solid solution strengthening and result in rod-like Fe 2 Nb ravigs phase formation increases material brittleness, and thus the Nb content is controlled to 10× (c+n) to 0.25%, where Nb, C, and N are each the content. As the C and N contents vary, the Nb content is preferably controlled to 10X (C+N) from the viewpoint of improving toughness.
Al is added as a deoxidizing element, the lower limit of the content is controlled to be 0.04% in order to ensure deoxidizing effect, but excessive addition of Al is extremely unfavorable for plasticity and toughness, al-Mg spinel inclusions are easily formed in molten steel, micro cracks are easily generated at interfaces of heterogeneous phases and matrixes in the rolling process, stress concentration is caused, and the cracks are rapidly expanded under a lower stress level, so that 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 like Nb, but TiN is formed in a liquid state before casting of stainless steel and is a square hard particle, and when the ferritic stainless steel is plastically deformed, stress concentration is extremely likely to occur at corners thereof, and the TiN becomes a crack source, causing brittle fracture. As the thickness of the ferrite stainless steel hot rolled steel plate increases, the reduction of casting blank is reduced, the breaking capacity of a hard phase is reduced, and the influence of TiN is more obvious. Therefore, for a middle plate of ferrite stainless steel with the thickness of 12-25 mm, the Ti content control is particularly important, the Ti content is extremely low limited through the control of alloy raw materials and casting powder components in the steelmaking process, the control of refining process parameters, the control of continuous casting process and the like, and when the Ti content in the ferrite stainless steel is less than 0.01%, square TiN phase formation is basically not observed in the matrix. Therefore, the upper limit of the Ti content is controlled to 0.01% or Ti may not be contained.
O is an element which is detrimental to both corrosion resistance and toughness of ferritic stainless steel, and is often present in the steel in the form of oxide inclusions, and is as low as possible, so the upper limit of the total oxygen content (T [ O ]) in the steel is set to 0.0015%.
Mn is an unavoidable element in molten iron in stainless steel smelting, but is disadvantageous in terms of plasticity and toughness of ferritic stainless steel, and therefore, setting the upper limit to 0.11% and controlling too low will bring about an increase in steel-making cost, and thus controlling the Mn content to 0.02 to 0.11%.
Ni and Cu are beneficial to plasticity and corrosion resistance of ferrite stainless steel, but a large amount of 12-25 mm thick ferrite stainless steel middle plates are used for manufacturing magnesium alloy smelting and casting equipment, and the solubility of Ni and Cu in the magnesium alloy is extremely small, so that Mg is formed with magnesium 2 Ni and Mg 2 Cu intermetallic compounds, which allow concentrations below 10mg/kg, otherwise greatly reduce the corrosion resistance of magnesium alloys. Therefore, the Ni and Cu content in the raw materials of the apparatus must be strictly controlled so as to control the migration amount of Ni and Cu elements into the magnesium alloy melt in the stainless steel melting and casting apparatus at high temperature. The laboratory simulates actual working conditions, carries out soaking tests of the ferrite stainless steel middle plates with different Ni and Cu contents in magnesium alloy melt, and has the test temperature of 660 ℃ and soaking time of 8 hours. The test results show that the migration amounts of Ni and Cu are lower than 10mg/kg for steel plates 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 Ni content in 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%, or Cu may not be contained.
Mo is an element for improving the corrosion resistance of ferritic stainless steel, and when the content reaches 0.03%, the effect of improving the corrosion resistance is exhibited, so that the lower limit is set to 0.03%, and excessive addition reduces the workability of ferritic stainless steel, so that the Mo content is controlled to 0.03% to 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%.
According to the hot-rolled ferritic stainless steel middle plate, through the synergistic effect of elements with specific contents, the room-temperature elongation of the hot-rolled ferritic stainless steel middle plate with the thickness of 12-25 mm is more than or equal to 30%, 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 higher than 60J;180 ° bending does not produce cracks.
The hot-rolled middle plate of the ferritic stainless steel is prepared by smelting, hot rolling, primary annealing, transverse cutting, pickling and secondary annealing in sequence, wherein the hot rolling process comprises 7 steps of casting blank heating, rough rolling, finish rolling, water spray cooling to 550-600 ℃, hot straightening, water spray cooling to room temperature again and trimming.
The ferrite stainless steel casting blank structure consists of a columnar crystal area and an equiaxed crystal area, wherein the original columnar crystal is in an as-cast {001} < uvw > orientation, and coarse alpha-oriented grains are formed in subsequent hot rolling, and the orientation annealing recrystallization rate is extremely low, so that the ferrite stainless steel casting blank structure is easy to leave in a finished plate to cause brittle cleavage and fracture. The thickness of a smelting casting blank is controlled to be 200-220 mm, the thickness of a finished product of the hot-rolled plate of the ferrite stainless steel is 12-25 mm, the thicker the finished product is, the smaller the rolling reduction is, the lower the hot-rolled strain energy storage is, the smaller the recrystallization driving force is, and the more developed the alpha orientation is in the finished product. Therefore, from the viewpoint of improving the toughness of the finished product, the higher the equiaxed crystal proportion of the casting blank is, the better, but the improvement of the equiaxed crystal proportion increases the electromagnetic stirring energy consumption and reduces the production efficiency, and in addition, the effect is basically saturated when the equiaxed crystal proportion reaches 80%. The above factors are considered, and the equiaxial crystal proportion of the casting blank is controlled to be 60% -80%.
The laboratory research results of the inventor show that grain refinement is helpful for obtaining excellent properties of high strength and high toughness of the hot rolled middle plate of the ferritic stainless steel. 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 annealing the finished product. The heating temperature of a 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 a material is increased along with temperature reduction in the process of hot rolling at the too low heating temperature to exceed the load of a rolling mill, and smooth rolling cannot be realized; the temperature is too high, the grains are seriously grown and are easy to overburn, and the problem of hot rolling fission is easy to occur.
In the hot rolling rough rolling process, matching of transverse and longitudinal rolling passes and control of rolling reduction ensure the ordering width of customers, and most importantly, the anisotropy of the finished product performance is reduced, so that the transverse and longitudinal impact toughness meets the design requirement; the outlet temperature of the finish rolling is controlled to be above 800 ℃, and the finish rolling is cooled to 550-600 ℃ by spraying water after finishing rolling, so as to prevent brittle sigma phase and Fe 2 Precipitation of Nb phase; the hot straightening is then performed to control the unevenness of the slab. The hot rolled sheet temperature after hot straightening was about 500 c and again water spray cooled to room temperature to prevent 475 c low temperature brittleness of the ferritic stainless steel.
The temperature of the primary annealed steel plate is controlled between 880 and 940 ℃, the temperature is too low, recrystallization cannot be completed, and the finished product tissue is in a strip shape and mainly comprises brittle alpha oriented grains; and when the temperature is too high, crystal grains are easy to grow up, the strength of the finished product is reduced, and the ductile-brittle transition temperature is increased. In addition, in order to ensure the shape of the plate after primary annealing, water is uniformly sprayed along the width direction of the hot rolled plate to cool to room temperature, and the cooling speed is controlled to be 3-5 ℃/s. When the cooling speed is lower than 3 ℃ per second, brittle sigma phase and Fe are precipitated in the cooling process 2 A Nb phase; the cooling speed is higher than 5 ℃/s, and as the ferrite stainless steel hot rolled plate is a thick middle plate, the excessive cooling speed easily causes excessive temperature difference of the cross section of the hot rolled plate, the residual stress is rapidly increased, and when the residual stress exceeds the tensile strength of a matrix, microcracks are formed in the hot rolled middle plate, as shown in fig. 3, so that the finished product flaw detection is not suitable.
The secondary annealing is to put the steel plate after pickling into a low-temperature furnace for secondary annealing, and the laboratory research results show that as the thickness of the hot-rolled ferritic stainless steel medium plate is 12-25 mm, a large amount of residual annealing stress still exists in the medium plate even if the cooling speed after primary annealing is limited to 3-5 ℃/s, and the impact toughness and plasticity of the hot-rolled ferritic stainless steel medium plate are greatly reduced. The temperature of the secondary annealed 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 effect of eliminating residual stress is not obvious, the heat preservation time is required to be greatly prolonged, and the production efficiency is influenced; the temperature is higher than 300 ℃, the shape of the hot rolled plate is affected, and the surface of the steel plate is easy to cause oxidative discoloration.
Examples
The invention is further illustrated by means of the following examples, which are not intended to limit the scope of the invention. The experimental methods without specific conditions noted in the following examples follow conventional methods and conditions.
Example 1
The steels with different compositions shown in Table 1 are prepared into a ferrite stainless steel hot-rolled middle plate with the thickness of 12mm through smelting, hot rolling, transverse cutting, primary annealing, acid washing and secondary annealing. The equiaxed crystal proportion of the casting blank is controlled to be 60-80%, the heating temperature of the casting blank before hot rolling is 1120-1180 ℃, the heat preservation is carried out for 10+/-2 min/10mm, then rough rolling and finish rolling are carried out, the outlet temperature of rough rolling is 910-950 ℃, the outlet temperature of finish rolling is more than or equal to 800 ℃, water spray cooling is carried out to 550-600 ℃, hot straightening is carried out, the temperature after hot straightening is about 500 ℃, water spray cooling is carried out to room temperature, and then edge cutting and transverse cutting are carried out.
Then the hot-rolled middle plate is kept at 880-940 ℃ for 1.2-1.5 min/mm, and then cooled to room temperature at a speed of 3-5 ℃/s. And (3) carrying out secondary annealing after pickling, preserving the temperature of the steel plate at 100-300 ℃ for 8-20 h, and then carrying out air cooling.
Table 1 shows 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 tensile test of metallic materials section 1 according to GB/T228.1: the results of evaluation of tensile strength, elongation, bending property and impact property of the invention examples and comparative examples in Table 1 were shown in room temperature test method, GB/T232 bending test method for metallic materials and GB/T229 Charpy pendulum impact test method for metallic materials.
Table 2 results of evaluating the properties of ferritic stainless steels of examples and comparative examples of the present invention
As is clear from tables 1 and 2, the hot rolled ferritic stainless steel sheet of the present invention has excellent strength, elongation and toughness, and fig. 1 and 2 are impact absorption energy-temperature diagram and metallographic structure, respectively, of the hot rolled ferritic stainless steel sheet of example 2# of the present invention; while deviating from the comparative examples of the present invention, some of the strength and toughness were unacceptable.
Example 2
Table 1 the inventive example 3# steel was selected and the steel composed of this composition was subjected to smelting, hot rolling, transverse cutting, primary annealing, pickling and secondary annealing to prepare a hot rolled intermediate sheet of ferritic stainless steel having a thickness of 12 to 25mm. Tensile strength, elongation, bending property and impact property were evaluated in the same manner as in example 1. The test conditions and the evaluation results are shown in tables 3 and 4, respectively.
TABLE 3 conditions for producing ferritic stainless steels of examples and comparative examples of the present invention
Table 4 results of evaluation of the properties of ferritic stainless steels of examples and comparative examples of the present invention
As can be seen from Table 4, the hot-rolled sheet of the ferritic stainless steel No. 1-3 prepared by the preparation method of the invention has good strength, plasticity and toughness; in the comparative examples deviating from the present invention, some disqualification of strength, plasticity and toughness, comparative example 4 in Table 4, the equiaxed crystal ratio and finish rolling outlet temperature were lower, resulting in lower elongation and insufficient toughness of the hot rolled intermediate plate; in comparative example 5, the cooling rate after primary annealing reaches 10 ℃/s, and micro cracks are formed in the middle plate due to the excessive thermal stress of the cross section of the middle plate, as shown in fig. 3, the strength and the elongation are extremely low, and the middle plate is bent and cracked; in comparative example 6, the secondary annealing time is insufficient, the residual stress is not completely eliminated, the tensile strength and the elongation value of the finished product of the hot rolled plate are low, and the toughness is poor. The primary annealing temperature of the hot-rolled middle plate in comparative example 7 is too high, so that the grains grow abnormally, the performance of the hot-rolled finished product is obviously inferior to that of the hot-rolled finished product in the embodiment of the invention, and the metallographic structure is shown in figure 4.
The present invention has been disclosed above 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 equivalent to those of the embodiments are considered to be covered by the scope of the claims of the present invention. The scope of the invention should, therefore, be determined with reference to the appended claims.

Claims (9)

1. The hot-rolled ferritic stainless steel middle plate is characterized by comprising the following components in percentage by weight: c is less than 0.01%; n is less than 0.01%; si is less than or equal to 0.10 percent; cr 16.0-20.0%; p is less than or equal to 0.025%; s is less than or equal to 0.002%; nb10× (C+N) to 0.25%; 0.04% -0.08% of Al; ti 0.002% -0.01%; t [ O ] is less than or equal to 0.0015%; mn0.02% -0.11%; ni 0.02% -0.04%; 0.01% -0.02% of Cu, and the balance of Fe and unavoidable impurities;
the thickness of the ferrite stainless steel hot-rolled middle plate is 12-25 mm, the room temperature elongation is more than or equal to 30%, the tensile strength is more than 450MPa, the ductile-brittle transition temperature is lower than-10 ℃, the standard impact power value at 0 ℃ is more than 60J, and no crack is generated when the ferrite stainless steel hot-rolled middle plate is bent at 180 degrees.
2. The ferritic stainless steel hot-rolled middle plate according to claim 1, further comprising one or two elements of Mo 0.03% -2% and V < 0.1% in weight percent.
3. The method for manufacturing a hot rolled ferritic stainless steel medium plate according to any one of claims 1 to 2, comprising in order smelting, hot rolling, primary annealing, transverse cutting, pickling and secondary annealing, characterized in that the hot rolling comprises in order: casting blank heating process, rough rolling process, finish rolling process, first water spray cooling process, hot straightening process, second water spray cooling process and trimming process; the temperature of a heating furnace in the casting blank heating process is set to be 1120-1180 ℃, and the heat preservation time is 10+/-2 min/10mm.
4. A method for producing a hot rolled ferritic stainless steel middle plate according to claim 3, wherein the smelting comprises: molten iron pretreatment, converter smelting, VOD refining, LF refining, and slab continuous casting to form a billet with the thickness of 200-220 mm, wherein the equiaxial crystal proportion is 60-80%.
5. The method for manufacturing a hot rolled ferritic stainless steel middle plate according to claim 3, wherein in the rough rolling step, the longitudinal rolling is performed for 2 times, the total rolling reduction is 10-12%, the transverse rolling is performed for 4 times, and the total rolling reduction is 30-40%; after descaling by high-pressure water, longitudinal rolling is performed for 6 times, and the total rolling reduction is 50-60%; wherein the rough rolling outlet temperature is 910-950 ℃, and the thickness of the rough rolled blank is 45-55 mm.
6. The method for manufacturing a hot rolled ferritic stainless steel strip according to claim 3, wherein in the finish rolling step, 7 passes are rolled in the longitudinal direction, the reduction per pass is 8-20%, the finish rolling outlet temperature is not less than 800 ℃, and the thickness of the hot rolled steel strip after finish rolling is 12-25 mm.
7. The method for manufacturing a hot rolled ferritic stainless steel middle plate according to claim 3, wherein the first water spray cooling process cools the steel plate to 550-600 ℃; and the second water spray cooling procedure cools the steel plate to room temperature.
8. The method for manufacturing a hot rolled ferritic stainless steel middle plate according to claim 3, 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, water is uniformly sprayed in the width direction to cool the steel plate to room temperature, and the cooling speed is 3-5 ℃/s.
9. The method for manufacturing a hot rolled ferritic stainless steel middle plate according to claim 3, wherein the temperature of the steel plate subjected to secondary annealing is 100-300 ℃, the heat preservation time is 8-20 h, and air cooling is performed after the heat preservation is finished.
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