CN113430467B - Thin 1400 MPa-grade bainite steel and manufacturing method thereof - Google Patents
Thin 1400 MPa-grade bainite steel and manufacturing method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0637—Accessories therefor
- B22D11/0697—Accessories therefor for casting in a protected atmosphere
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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
- C21D2211/001—Austenite
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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
- C21D2211/002—Bainite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention belongs to the technical field of steel production, and discloses thin 1400 MPa-grade bainite steel and a manufacturing method thereof. The molten steel comprises the following chemical components in percentage by mass: c: 0.20-0.25%; si: 0.80-1.50%; mn: 1.20-1.70%; cr: 0.10-0.20%; nb: 0.02-0.04%; al: less than or equal to 0.003 percent; p: less than or equal to 0.020%; s: less than or equal to 0.004 percent. The invention adopts medium and low temperature coiling to obtain the microstructure of the steel strip, which comprises bainite and 4 to 7 percent of residual austenite. The thickness of the steel coil of the 1400 MPa-level bainite steel is 0.8-1.8 mm. The steel belt has excellent mechanical property, wherein the tensile strength grade is more than or equal to 1400MPa, and the elongation after fracture is more than or equal to 13%. The method solves the problem that the traditional hot rolling process is difficult to produce thin ultrahigh-strength products.
Description
Technical Field
The invention belongs to the technical field of steel production, and particularly relates to thin 1400 MPa-level bainite steel and a manufacturing method thereof.
Background
With the increasing prominence of the world energy and environmental protection problems and requirements, light weight is very important in the industries of automobiles, agricultural machinery, equipment manufacturing and the like. Reducing the thickness of a steel sheet by increasing the strength of the steel sheet is an important means for achieving weight reduction. The application proportion of the ultra-high strength steel plate with the tensile strength of 1400MPa is larger and larger, but the thin ultra-high strength steel needs to depend on hot rolling and subsequent cold rolling to ensure the thinner thickness of the steel, and cold rolling and subsequent annealing to ensure the performance of the steel. The difficulty of producing the ultrahigh-strength steel plate by directly utilizing a hot rolling production line is high.
Patent document 201310241442.0 discloses "a hot-rolled martensitic steel and a method for producing the same", which is added with a large amount of Mn, Ti, and Cr elements and thus has a high alloy cost. The coiling temperature of the method is controlled to be 150-200 ℃, and high requirements on a coiler are put forward due to the high strength and low coiling temperature. The method does not give any explanation on the specification of the limit thickness, and the thickness in the embodiment is 4.0-6.0 mm.
Patent document 201110154249.4 discloses a carbon-silicon-manganese Q & P steel and a method for manufacturing the same, which adds a large amount of C and is not favorable for a subsequent welding process.
Patent document 201310121568.4 discloses "a 700MPa grade high strength hot rolled Q & P steel and a method for producing the same", in which addition of a large amount of Si is disadvantageous in controlling the surface quality of a steel strip, addition of a large amount of Al is disadvantageous in casting, addition of a large amount of Mn and Ti is disadvantageous, and the alloy cost is high. The method needs two-stage cooling after hot rolling, and the air cooling is carried out for 5-10 seconds at a high temperature between the two-stage cooling. The method is difficult to produce the thin steel strip, the thickness range of the steel strip is 3.0-12.0 mm, and the thickness of the steel strip is more than 2 mm.
It can be seen that the above prior art method has at least the following disadvantages:
(a) the Si content in the molten steel is too high, which is not beneficial to the surface quality control of the steel strip;
(b) the Al content in the molten steel is too high, which is not beneficial to casting;
(c) the addition of other alloys in the molten steel is excessive, and the alloy cost is high;
(d) the cooling after hot rolling is multi-section cooling, and high-temperature air cooling is needed for several seconds between cooling sections, so that thin steel strips are not produced;
(e) the coiling temperature is too low, and the requirement on a coiler is high;
(f) after hot rolling, heat treatment is matched to achieve ultrahigh strength.
Therefore, the present invention aims to provide a method for manufacturing a thin gauge 1400MPa grade bainitic steel, which overcomes the above technical drawbacks of the prior art.
Disclosure of Invention
In order to achieve the purpose of the invention, the invention adopts the following technical scheme.
According to a first aspect of the present invention there is provided a method of manufacturing 1400MPa thin gauge bainite steel, said method including the steps of:
(1) smelting to obtain molten steel, wherein the molten steel is prepared from the following chemical components in percentage by mass:
C：0.20～0.25％；
Si：0.80～1.50％；
Mn：1.20～1.70％；
Cr：0.10～0.20％；
Nb：0.02～0.04％；
P：≤0.020％；
Al：≤0.003％；
S：≤0.004％；
the balance of Fe and inevitable impurities;
(2) carrying out strip continuous casting on the molten steel obtained in the step (1) by using a double-roll casting process under the protection of inert gas to obtain a cast strip, wherein the casting speed of the strip continuous casting is 20-60 m/min, and the thickness of the obtained cast strip is 1.5-2.0 mm;
(3) hot rolling the cast strip obtained in the step (2) into a thin strip for one time, wherein the hot rolling reduction rate is 10-40%, and the hot rolling outlet temperature is 820-900 ℃;
(4) and (4) cooling the steel strip obtained in the step (3) to 450-500 ℃ through an aerial fog cooling system, and air-cooling to room temperature after coiling, wherein the coiling temperature is 350-400 ℃.
According to the method for manufacturing the thin 1400MPa bainite steel, the step (1) is preferably deoxidized by Si without adding Al.
According to the method for manufacturing the thin 1400MPa bainite steel, the casting temperature of the molten steel in the step (2) is 1500-1600 ℃.
According to the method for manufacturing the thin 1400MPa bainite steel, the casting speed of the strip casting in the step (2) is preferably 42-60 m/min
According to the method for manufacturing the 1400 MPa-level bainite steel with thin specification, in the step (3), the hot rolling outlet temperature of the steel strip is preferably 838-900 ℃.
According to the method for manufacturing the 1400 MPa-grade bainite steel with the thin specification, preferably, the steel strip is further subjected to air cooling for 2-3 seconds after the hot rolling in the step (3) and before the gas mist cooling in the step (4) so as to refine the bainite ferrite lath bundle in the microstructure.
According to a second aspect of the invention there is provided a thin gauge 1400MPa grade bainite steel manufactured using the method described above.
According to the 1400 MPa-level bainite steel with thin specification, the thickness of a finished steel coil is preferably 0.8-1.8 mm.
According to the thin 1400MPa bainite steel, the tensile strength of the thin 1400MPa bainite steel is preferably not less than 1400MPa, and the elongation after fracture is not less than 13%.
According to the thin 1400MPa grade bainite steel, the microstructure of the thin 1400MPa grade bainite steel preferably comprises bainite + 4-7% of residual austenite.
Advantageous technical effects
Compared with the prior art, the invention has the technical advantages and beneficial technical effects that:
(1) the content of Si in the bainite steel is only 0.8-1.5%, the content is obviously lower than that in the prior art, 4-7% of residual austenite can be stably obtained by matching with the technical route of the bainite steel, and the bainite steel has high strength and high elongation after fracture; meanwhile, the acid-washing surface quality of the steel strip is good due to the low Si content of the invention, and the subsequent welding process is easier.
(2) The invention deoxidizes Si without adding Al, thereby eliminating the defect that Al is easy to block a water gap and ensuring that 5 furnaces can be continuously cast during normal production.
(3) The added Mn and Cr are low, the Nb content is only 0.02-0.04%, the alloy cost is low, and the bainite ferrite lath bundle can be stably obtained by matching with the technical route of the invention, so that the bainite steel has the strength of more than or equal to 1400 MPa.
(4) The air cooling section is arranged after hot rolling and before the cooling section, the quantity of sub-crystals in austenite grains can be increased by matching with the whole process route of the invention, bainite ferrite lath bundles are further refined, and the thin steel strip is easy to produce, so that the bainite steel strip has high strength of more than or equal to 1400MPa, high elongation and thickness controlled within 0.8-1.8 mm.
(5) The invention only carries out hot rolling with 10-40% of reduction in one pass, and the hot rolling temperature is 820-900 ℃, so that the invention can easily obtain a 0.8-1.8 mm bainite high-strength steel thin strip which meets the requirements of thin specification and high strength.
(6) The coiling temperature of the method is 350-400 ℃, which is obviously higher than that of the prior art, so that the method has lower requirement on a coiling machine, and the defects of poor coiling shapes such as coil collapse and the like are not easy to occur during coiling.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings of the embodiments will be briefly described below. It is to be expressly understood that the drawings in the following description are directed to only some embodiments of the invention and are not intended as a definition of the limits of the invention.
FIG. 1 is a flow chart of a manufacturing process for manufacturing 1400MPa grade bainite steel with thin gauge according to an embodiment of the present invention.
Fig. 2 is a metallographic structure diagram of ultra-high strength steel produced according to example 1 of the present invention.
Fig. 3 is a metallographic structure diagram of ultra-high strength steel produced according to example 2 of the present invention.
Fig. 4 is a metallographic structure diagram of ultra-high strength steel produced according to example 3 of the present invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions of the embodiments of the present invention will be clearly and completely described below. It is to be understood that the embodiments described are only a few embodiments of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the described embodiments of the invention without any inventive step, are within the scope of protection of the invention.
Unless defined otherwise, technical or scientific terms used herein shall have the ordinary meaning as understood by one of ordinary skill in the art to which this invention belongs.
Example 1
(1) Smelting molten steel: the molten steel with qualified components is obtained by electric furnace steelmaking, VD vacuum furnace degassing and LF furnace refining, and the molten steel comprises the following components in percentage by weight: c: 0.233%; si: 1.2 percent; mn: 1.48 percent; cr: 0.18%, Nb: 0.034%; al: 0.0020 percent; p: 0.010%; s: 0.0020 percent; the balance of iron and inevitable impurity elements.
(2) Strip continuous casting: and continuously casting the qualified molten steel by using a twin-roll casting and rolling process, wherein the casting temperature of the molten steel is 1560 ℃, the casting and rolling speed is 42m/min, and the molten steel is subjected to thin-strip continuous casting under the protection of inert gas, wherein the thickness of a cast strip is 1.85 mm.
(3) Hot rolling: the cast strip is hot-rolled into a hot-rolled thin strip with the thickness of 1.50mm by one pass with the rolling reduction of 18.9 percent, the hot-rolled outlet temperature is 866 ℃, the strip steel temperature after aerial fog cooling is 465 ℃ and the coiling temperature is 387 ℃.
The high-strength steel produced according to the components and the process has the following mechanical properties: the yield strength is 1134MPa, the tensile strength is 1487MPa, the elongation is 15 percent, and the residual austenite content is 6 percent.
The metallurgical structure of the thin gauge 1400MPa grade bainite steel obtained according to the above examples is shown in FIG. 2.
Example 2
(1) Smelting molten steel: the molten steel with qualified components is obtained by electric furnace steelmaking, VD vacuum furnace degassing and LF furnace refining, and the molten steel comprises the following components in percentage by weight: c: 0.217%; si: 0.95 percent; mn: 1.62 percent; cr: 0.20%, Nb: 0.032%; al: 0.0025 percent; p: 0.012%; s: 0.0017%; the balance of iron and inevitable impurity elements.
(2) Strip continuous casting: and continuously casting the qualified molten steel by using a twin-roll casting and rolling process, wherein the casting temperature of the molten steel is 1530 ℃, the casting and rolling speed is 57m/min, and the molten steel is subjected to thin-strip continuous casting under the protection of inert gas, wherein the thickness of a cast strip is 1.6 mm.
(3) Hot rolling: the cast strip is hot-rolled into a hot-rolled thin strip with the thickness of 1.20mm by one pass at the reduction of 25 percent, the hot-rolling outlet temperature is 838 ℃, the temperature of the strip steel after aerial fog cooling is 465 ℃, and the coiling temperature is 395 ℃.
The high-strength steel produced according to the components and the process has the following mechanical properties: the yield strength is 1075MPa, the tensile strength is 1436MPa, the elongation is 14 percent, and the content of residual austenite is 4 percent.
The metallurgical structure of the thin gauge 1400MPa grade bainite steel obtained according to the above examples is shown in FIG. 3.
Example 3
(1) Smelting molten steel: the molten steel with qualified components is obtained by electric furnace steelmaking, VD vacuum furnace degassing and LF furnace refining, and the molten steel comprises the following components in percentage by weight: c: 0.225 percent; si: 1.3 percent; mn: 1.66 percent; cr: 0.14%, Nb: 0.037%; al: 0.0021%; p: 0.0130 percent; s: 0.0021%; the balance of iron and inevitable impurity elements.
(2) Strip continuous casting: and continuously casting the qualified molten steel by using a twin-roll casting and rolling process, wherein the casting temperature of the molten steel is 1570 ℃, the casting and rolling speed is 55m/min, and the molten steel is subjected to thin-strip continuous casting under the protection of inert gas, wherein the thickness of a cast strip is 1.5 mm.
(3) Hot rolling: the cast strip is hot-rolled into a hot-rolled thin strip with the thickness of 0.90mm by one pass with the reduction of 40 percent, the hot-rolling outlet temperature is 841 ℃, the strip temperature after aerial fog cooling is 482 ℃ and the coiling temperature is 410 ℃.
The high-strength steel produced according to the components and the process has the following mechanical properties: the yield strength is 1044MPa, the tensile strength is 1438MPa, the elongation is 13 percent, and the content of residual austenite is 4 percent.
The metallurgical structure of the thin gauge 1400MPa grade bainite steel obtained according to the above examples is shown in FIG. 4.
While the foregoing is directed to embodiments of the present invention, it is noted that various modifications and adaptations may be made by those skilled in the art without departing from the principles of the invention and should be considered as within the scope of the invention.
Claims (10)
1. A method of manufacturing thin gauge 1400MPa grade bainitic steel, comprising the steps of:
(1) smelting to obtain molten steel, wherein the molten steel is prepared from the following chemical components in percentage by mass:
C：0.20～0.25％；
Si：0.80～1.30％；
Mn：1.20～1.70％；
Cr：0.10～0.20％；
Nb：0.02～0.04％；
P：≤0.020％；
Al：≤0.003％；
S：≤0.004％；
the balance of Fe and inevitable impurities;
(2) carrying out strip continuous casting on the molten steel obtained in the step (1) by using a double-roll casting process under the protection of inert gas to obtain a cast strip, wherein the casting speed of the strip continuous casting is 20-60 m/min, and the thickness of the obtained cast strip is 1.5-2.0 mm;
(3) hot rolling the cast strip obtained in the step (2) into a thin strip for one time, wherein the hot rolling reduction rate is 10-40%, and the hot rolling outlet temperature is 820-900 ℃;
(4) cooling the steel strip obtained in the step (3) to 450-500 ℃ by an aerial fog cooling system, air-cooling to room temperature after coiling, wherein the coiling temperature is 350-400 ℃,
and (3) after the hot rolling in the step (3) and before the gas spray cooling in the step (4), air cooling for 2-3 seconds is further carried out on the steel strip so as to refine the bainite ferrite lath bundle in the microstructure.
2. The method of claim 1, wherein: in the step (1), Si is deoxidized, and Al is not added.
3. The method of claim 1, wherein: in the step (2), the casting temperature of the molten steel is 1500-1600 ℃.
4. The method of claim 1, wherein: in the step (2), the casting and rolling speed of the strip continuous casting is 42-60 m/min.
5. The method of claim 1, wherein: in the step (3), the hot rolling outlet temperature of the steel strip is 838-900 ℃.
6. The method of claim 5, wherein: in the step (3), the hot rolling outlet temperature of the steel strip is 838-866 ℃.
7. A thin 1400MPa grade bainite steel is characterized in that: the thin gauge 1400MPa grade bainitic steel is manufactured using the method according to any one of claims 1-6.
8. A thin gauge 1400MPa grade bainite steel according to claim 7, characterised in that: the thickness of the finished steel coil of the thin 1400MPa grade bainite steel is 0.8-1.8 mm.
9. A thin gauge 1400MPa grade bainite steel according to claim 7, characterised in that: the tensile strength of the thin 1400MPa grade bainite steel is more than or equal to 1400MPa, and the elongation after fracture is more than or equal to 13%.
10. A thin gauge 1400MPa grade bainitic steel according to any one of claims 7-9, characterized in that: the microstructure of the thin 1400MPa grade bainite steel comprises bainite and 4-7% of residual austenite.
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| CN115478203A (en) * | 2022-09-27 | 2022-12-16 | 张家港中美超薄带科技有限公司 | Method for producing hot-rolled thin strip steel based on thin strip casting and rolling and ultrahigh-strength part |
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| CN103429766B (en) * | 2011-05-30 | 2015-08-05 | 塔塔钢铁有限公司 | There is the bainitic steel of high strength and high-elongation and manufacture the method for described bainitic steel |
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