CN107937796B - Method for improving toughness of super ferrite stainless steel hot rolled plate - Google Patents
Method for improving toughness of super ferrite stainless steel hot rolled plate Download PDFInfo
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- CN107937796B CN107937796B CN201711158036.2A CN201711158036A CN107937796B CN 107937796 B CN107937796 B CN 107937796B CN 201711158036 A CN201711158036 A CN 201711158036A CN 107937796 B CN107937796 B CN 107937796B
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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
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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
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C21D2211/005—Ferrite
Abstract
The invention belongs to the field of ferrite stainless steel manufacturing, aims to solve the problem of cracking of a hot rolled plate strip in the subsequent coiling process in the existing production process, and provides a method for improving the toughness of a super ferrite stainless steel hot rolled plate to smelt molten steel and continuously cast the molten steel into a casting blank, the casting blank is continuously rolled into a hot rolled plate in a hot rolling unit, the hot rolled plate directly enters a continuous heating furnace for heat preservation treatment after passing through the hot rolling unit, and the hot rolled plate is coiled after being rapidly cooled by high-pressure water. The heat preservation treatment of the hot rolled plate by adding the continuous heating furnace eliminates the work hardening and remarkably suppresses the precipitation tendency of brittle phases caused by the work hardening. The waste heat of the hot rolled plate is fully utilized, the heating time is short, the energy consumption is low, and the manufacturing cost is low; the temperature of the hot rolled plate is uniformly controlled along the thickness direction, and the problem of thermal stress caused by overlarge temperature difference between the surface and the core of the plate belt in the reheating process is solved; the retention time of the steel plate in the brittle phase precipitation temperature range is reduced; the processed hot rolled plate has good comprehensive mechanical property, and the hot rolled plate does not need to be subjected to heat treatment before use.
Description
Technical Field
The invention belongs to the technical field of ferrite stainless steel manufacturing, and particularly relates to a method for improving the toughness of a super ferrite stainless steel hot rolled plate.
Background
The super ferritic stainless steel is an iron-chromium alloy which is rich in chromium (26-30%) elements and contains higher molybdenum (2-4%), and the pitting corrosion equivalent PREN (Cr% +3.3 ×% Mo) is more than 35.
For example, the content of the high chromium and the high molybdenum can strongly promote the precipitation of intermetallic compounds such as α ', sigma, chi and Laves in the steel, the precipitation of the intermetallic compounds such as α', sigma, chi and Laves is a brittle phase, the mechanical property of the material can be seriously deteriorated due to the precipitation of the intermetallic compounds along the grain boundary, and meanwhile, the precipitation of the chromium-rich intermetallic compounds can lead the matrix to be poor in chromium, so that the corrosion resistance of the material is reduced.
The production process of the prior ferritic stainless steel hot rolled plate comprises the following steps: smelting molten steel, continuous casting, continuous rolling, high-pressure water rapid cooling and reeling. In order to solve the above problems, the finishing temperature of the steel strip is generally over 900 ℃ in order to avoid the precipitation temperature region of the brittle second phase. The coiling cooling process after hot rolling inevitably passes through the precipitation temperature interval of the brittle second phase, and in order to avoid the long-term retention of the material in the precipitation temperature interval of the brittle second phase, the rapid cooling mode is generally adopted after hot rolling, so that the temperature of the steel plate is rapidly reduced from 900 ℃ to below 400 ℃, and the steel plate rapidly passes through the precipitation temperature interval of the brittle phase, thereby inhibiting the precipitation of the brittle phase.
In the field production process, the finish rolling temperature of hot rolling is difficult to accurately control to be more than 900 ℃, and the difference of dozens of degrees centigrade can have great influence on the performance of the steel plate; the subsequent rapid cooling process can form larger thermal stress in the steel plate, the deformation structure generated in the hot rolling process is difficult to completely eliminate, obvious work hardening is remained, the precipitation tendency of sigma phase along the grain boundary is increased, and the cracking phenomenon of the plate strip in the subsequent coiling process is obviously increased.
Therefore, how to eliminate the work hardening phenomenon, weaken the precipitation tendency of the sigma phase along the grain boundary, avoid cracking in the coiling process of the hot rolled plate, optimize the production process and expand the product supply range is a key technical problem to be solved urgently in the production and manufacturing process of the super ferritic stainless steel.
Disclosure of Invention
Aiming at the defects in the prior art, the invention provides a method for improving the toughness of a super ferrite stainless steel hot rolled plate, and aims to solve the problem of cracking in the process of hot rolling and coiling of the super ferrite stainless steel.
The invention is realized by the following technical scheme: a method for improving the toughness of a super ferrite stainless steel hot rolled plate comprises the steps of smelting molten steel, continuously casting the molten steel into a casting blank, continuously rolling the casting blank into a hot rolled plate in a hot rolling unit, directly feeding the hot rolled plate into a continuous heating furnace for heat preservation after passing through the hot rolling unit, and coiling after cooling at high pressure water speed.
The method comprises the following specific steps: (1) smelting molten steel by adopting a medium-frequency vacuum induction furnace, and continuously casting the molten steel into a casting blank with the thickness of 200 plus 300 mm; (2) continuously rolling the casting blank into a hot rolled plate with the thickness of 2-10mm in a hot rolling unit, and controlling the hot rolling temperature to be 980 and 1150 ℃; (3) and (3) heat preservation treatment: a continuous heating furnace is arranged behind the hot rolling unit, the hot rolled plate directly enters the continuous heating furnace for heat preservation treatment, the heat preservation temperature is 980-1150 ℃, and the heat preservation time is 10-300 s; (4) and (3) rapidly cooling the hot rolled plate subjected to heat preservation treatment to below 400 ℃ by adopting high-pressure water, wherein the cooling time is less than or equal to 20s, and finally coiling to obtain the super ferrite stainless steel hot rolled coil.
The optimal heat preservation temperature of the super ferrite stainless steel is 1120-1150 ℃, and the optimal heat preservation time is 30-50 s.
The super ferritic stainless steel comprises the following chemical components in percentage by mass: 0.03% of C, 1% of Si, 1% of Mn, 0.04% of P, 25.0-28.0% of Cr, 3.0-4.0% of Mo, 0.42-1.0% of Ti, 0.40-1.0% of Nb, 0.04% of N, 1.0-3.5% of Ni, 0.04% of S and the balance of Fe and impurities.
By adopting the time-delay heat preservation technology, on one hand, the hot rolled plate finishes the recrystallization process, the hot rolled strip structure is converted into equiaxed recrystallized grains, the dislocation density in the steel plate is rapidly reduced, the residual stress is eliminated, and the tendency that harmful second phases are precipitated due to the increase of the dislocation density in the hot rolled process is eliminated. On the other hand, the second phase precipitated in the rolling process is re-dissolved in the heat preservation process, and the harmful effect of the second phase precipitation in the steel is directly eliminated, so that the cracking tendency of the steel plate in the coiling process is greatly reduced. By adopting the scheme, the problem of work hardening generated in the current hot rolling process is solved, the damage of the brittle second phase separated out along the grain boundary to the mechanical property of the steel plate is greatly reduced, and the cracking of the hot rolled plate in the coiling process is avoided.
Compared with the prior art, the invention has the characteristics and beneficial effects that:
the invention is characterized in that a continuous heating furnace is added behind a hot rolling unit to carry out heat preservation treatment on a hot rolled plate, and the aim is to eliminate work hardening generated in the rolling process before the plate strip enters a coiler, so that the reasonable heating temperature is 980-1150 ℃, and the heat preservation time is 10-300 s. The invention can eliminate work hardening and obviously inhibit the precipitation tendency of brittle phases caused by work hardening by adding the continuous heating furnace to carry out heat preservation treatment on the hot rolled plate. The invention fully utilizes the waste heat of the hot rolled plate, has short heating time, low energy consumption and low manufacturing cost; the temperature of the hot rolled plate is uniformly controlled along the thickness direction, and particularly, the problem of thermal stress caused by overlarge temperature difference between the surface of a plate belt and the core part in the reheating process is solved for a thick plate of 5-10 mm; after hot rolling, the steel plate is subjected to heat preservation through a continuous annealing furnace, the temperature is accurately controlled, and the retention time of the hot rolled steel plate in the brittle phase precipitation temperature range is reduced; the processed hot rolled plate has good comprehensive mechanical properties, and the hot rolled plate does not need to be subjected to heat treatment before use.
Drawings
FIG. 1 is a schematic diagram of a specific process of the present invention. FIG. 2 is a fracture morphology graph of an impact test of a hot rolled super ferritic stainless steel plate prepared in example 1; FIG. 3 is an SEM micrograph of a hot rolled super ferritic stainless steel plate prepared according to example 1; FIG. 4 is a fracture morphology diagram of an impact test of a hot rolled super ferritic stainless steel plate prepared by a comparative example; FIG. 5 SEM micrographs of hot rolled super ferritic stainless steel plates prepared by comparative example.
Wherein: 1-intermediate frequency vacuum induction furnace; 2-a continuous casting machine; 3-roughing mill train; 4-finishing mill group; 5-continuous heating furnace; 6-high-pressure water cooling; 7 a coiling machine.
The specific implementation mode is as follows:
the invention is further explained by combining the attached drawings, the specific process schematic diagram of the invention is shown in figure 1, the Charpy impact absorption work of the super ferritic stainless steel is tested by using a sample of 2.5mm × 10mm, 10mm × 55 mm.
Example 1: the chemical composition of the super ferritic stainless steel is shown in table 1. As shown in figure 1, molten steel is smelted by a medium-frequency vacuum induction furnace 1, continuously cast into a continuous casting billet with the thickness of 200mm by a continuous casting machine 2, cooled to 1100 ℃, rolled to the thickness of 5.2mm by a roughing mill group 3 and a finishing mill group 4, kept warm by a continuous heating furnace 5 at the temperature of 1020 ℃, controlled for 180s, cooled by high-pressure water for 6, rapidly cooled to 400 ℃ within 15s, and finally coiled by a coiler 7.
FIG. 2 is a diagram of the appearance of the hot rolled coiled sheet room temperature impact fracture, from which it can be seen that the fracture is mainly a dimple, is a typical ductile fracture, and the impact absorption work is about 30J through testing.
FIG. 3 is an SEM micrograph showing the grains of a hot rolled coil in a distinct band form with distinct second phase precipitates along the grain boundaries.
Table 1 chemical composition (wt.%)
| C | Si | Mn | P | S | Cr | Ni | Mo | Cu | Nb | Ti | N |
| 0.025 | 0.400 | 0.230 | 0.022 | 0.020 | 25.570 | 1.980 | 3.680 | 0.050 | 0.370 | 0.140 | 0.016 |
Example 2: the chemical composition of the super ferritic stainless steel is shown in table 2. As shown in figure 1, molten steel is smelted by a medium-frequency vacuum induction furnace 1, continuously cast into a 295mm continuous casting blank by a continuous casting machine 2, cooled to 980 ℃, rolled to 2mm thick by a roughing mill group 3 and a finishing mill group 4, kept warm by a continuous heating furnace 5 at 1150 ℃, kept warm for 40s, rapidly cooled to 390 ℃ within 10s by high-pressure water cooling 6, and finally coiled by a coiler 7.
The Charpy impact absorption work of the test sample is 28J through detection, and the fracture morphology of the impact test sample mainly comprises a dimple.
Table 2 chemical composition (wt.%)
Example 3: the chemical composition of the super ferritic stainless steel is shown in table 3. As shown in figure 1, molten steel is smelted by a medium-frequency vacuum induction furnace 1, the molten steel is continuously cast into a continuous casting billet with the thickness of 300mm by a continuous casting machine 2, the continuous casting billet is cooled to 1150 ℃, then is rolled to the thickness of 10mm by a roughing mill group 3 and a finishing mill group 4, is subjected to heat preservation by a continuous heating furnace 5, the heat preservation temperature is 980 ℃, the heat preservation time is controlled for 300s, then is rapidly cooled to 390 ℃ within 17s by high-pressure water cooling 6, and finally is coiled by a coiling machine 7.
The Charpy impact absorption work of the test sample is 28J through detection, the fracture morphology of the impact test sample mainly comprises a dimple, and the fracture is a typical ductile fracture.
TABLE 3 chemical composition (wt.%)
Example 4: the chemical composition of the super ferritic stainless steel is shown in table 3. As shown in figure 1, molten steel is smelted by a medium-frequency vacuum induction furnace 1, the molten steel is continuously cast into a continuous casting billet with the thickness of 200mm by a continuous casting machine 2, the continuous casting billet is cooled to 1150 ℃, then is rolled to the thickness of 8mm by a roughing mill group 3 and a finishing mill group 4, is subjected to heat preservation by a continuous heating furnace 5, the heat preservation temperature is 1135 ℃, the heat preservation time is controlled for 50s, then is rapidly cooled to 390 ℃ within 17s, and finally is coiled by a coiling machine 7.
The Charpy impact absorption work of the test sample is 32J through detection, the fracture morphology of the impact test sample mainly comprises a dimple, and the fracture is a typical ductile fracture.
Example 5: the chemical composition of the super ferritic stainless steel is shown in table 2. As shown in figure 1, molten steel is smelted by a medium-frequency vacuum induction furnace 1, continuously cast into a 295mm continuous casting blank by a continuous casting machine 2, cooled to 1100 ℃, rolled to a thickness of 5mm by a roughing mill group 3 and a finishing mill group 4, kept warm by a continuous heating furnace 5 at 1140 ℃, kept warm for 30s, rapidly cooled to 390 ℃ within 10s by high-pressure water cooling 6, and finally coiled by a coiler 7.
The Charpy impact absorption work of the test sample is 32J through detection, the fracture morphology of the impact test sample mainly comprises a dimple, and the fracture is a typical ductile fracture.
Example 6: the chemical composition of the super ferritic stainless steel is shown in table 1. As shown in figure 1, molten steel is smelted by a medium-frequency vacuum induction furnace 1, continuously cast into a continuous casting billet with the thickness of 200mm by a continuous casting machine 2, cooled to 1100 ℃, rolled to the thickness of 10mm by a roughing mill group 3 and a finishing mill group 4, kept warm by a continuous heating furnace 5 at the temperature of 1130 ℃, kept warm for 40s, rapidly cooled to 400 ℃ within 15s by high-pressure water cooling 6, and finally coiled by a coiler 7.
The Charpy impact absorption work of the test sample is 31J through detection, the fracture morphology of the impact test sample mainly comprises a dimple, and the fracture is a typical ductile fracture.
Comparative example: the chemical composition of the super ferritic stainless steel is shown in table 1. Smelting molten steel by using a medium-frequency vacuum induction furnace 1, forming a 200mm continuous casting billet by using a continuous casting machine 2, cooling to 1100 ℃, then rolling to 4.9mm thick by using a roughing mill set 3 and a finishing mill set 4, cooling to 400 ℃ after water cooling, and finally coiling by using a coiling machine 7.
FIG. 4 is a graph showing the appearance of room temperature impact fractures of the hot rolled coil of the comparative example, which shows that cleavage fractures are dominant, and Charpy impact absorption work is about 18J, and impact toughness is poor.
FIG. 5 is an SEM micrograph of a hot rolled coil of a comparative example showing that the sample grains are significantly equiaxed, and white second phase precipitates along the grain boundaries are significantly reduced.
From the above results, it can be seen that the hot rolled coil obtained by the method of the present invention has about 2 times improved toughness, and can significantly reduce the precipitation of harmful second phases along the grain boundaries. The technical problem of cracking of the hot rolled plate in the coiling process is effectively solved.
Claims (2)
1. A method for improving the toughness of a super ferrite stainless steel hot rolled plate comprises the following steps of smelting molten steel and continuously casting the molten steel into a casting blank, and continuously rolling the casting blank into the hot rolled plate in a hot rolling unit, wherein the method comprises the following steps: the hot rolled plate directly enters a continuous heating furnace for heat preservation treatment after passing through a hot rolling unit, and is coiled after being cooled by high-pressure water speed;
the method comprises the following specific steps: (1) smelting molten steel by adopting a medium-frequency vacuum induction furnace, and continuously casting the molten steel into a casting blank with the thickness of 200 plus 300 mm; (2) continuously rolling the casting blank into a hot rolled plate with the thickness of 2-10mm in a hot rolling unit, and controlling the hot rolling temperature to be 980 and 1150 ℃; (3) and (3) heat preservation treatment: a continuous heating furnace is arranged behind the hot rolling unit, the hot rolled plate directly enters the continuous heating furnace for heat preservation treatment, the heat preservation temperature is 980-1150 ℃, and the heat preservation time is 10-300 s; (4) rapidly cooling the hot rolled plate subjected to heat preservation treatment to below 400 ℃ by adopting high-pressure water, wherein the cooling time is less than or equal to 20s, and finally coiling to obtain a super ferrite stainless steel hot rolled coil;
the super ferritic stainless steel comprises the following chemical components in percentage by mass: 0.03% of C, 1% of Si, 1% of Mn, 0.04% of P, 25.0-28.0% of Cr, 3.0-4.0% of Mo, 0.42-1.0% of Ti, 0.40-1.0% of Nb, 0.04% of N, 1.0-3.5% of Ni, 0.04% of S and the balance of Fe and impurities.
2. The method of claim 1, wherein the method comprises the following steps: the heat preservation temperature is 1120-1150 ℃, and the heat preservation time is 30-50 s.
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