CN113999962A - High-toughness bainite steel rail and production method thereof - Google Patents
High-toughness bainite steel rail and production method thereof Download PDFInfo
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- CN113999962A CN113999962A CN202111318532.6A CN202111318532A CN113999962A CN 113999962 A CN113999962 A CN 113999962A CN 202111318532 A CN202111318532 A CN 202111318532A CN 113999962 A CN113999962 A CN 113999962A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 204
- 239000010959 steel Substances 0.000 title claims abstract description 204
- 229910001563 bainite Inorganic materials 0.000 title claims abstract description 68
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 24
- 238000010438 heat treatment Methods 0.000 claims abstract description 52
- 238000001816 cooling Methods 0.000 claims abstract description 50
- 238000000034 method Methods 0.000 claims abstract description 39
- 238000005496 tempering Methods 0.000 claims abstract description 32
- 230000008569 process Effects 0.000 claims abstract description 27
- 238000005096 rolling process Methods 0.000 claims abstract description 15
- 238000010521 absorption reaction Methods 0.000 claims abstract description 14
- 229910052720 vanadium Inorganic materials 0.000 claims description 22
- 229910052758 niobium Inorganic materials 0.000 claims description 18
- 229910052759 nickel Inorganic materials 0.000 claims description 17
- 239000012535 impurity Substances 0.000 claims description 14
- 229910052717 sulfur Inorganic materials 0.000 claims description 13
- 229910052748 manganese Inorganic materials 0.000 claims description 7
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 7
- 229910052799 carbon Inorganic materials 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 239000003595 mist Substances 0.000 claims description 6
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- 239000000203 mixture Substances 0.000 claims description 5
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/04—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rails
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D11/00—Process control or regulation for heat treatments
- C21D11/005—Process control or regulation for heat treatments for cooling
-
- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- 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
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- E—FIXED CONSTRUCTIONS
- E01—CONSTRUCTION OF ROADS, RAILWAYS, OR BRIDGES
- E01B—PERMANENT WAY; PERMANENT-WAY TOOLS; MACHINES FOR MAKING RAILWAYS OF ALL KINDS
- E01B5/00—Rails; Guard rails; Distance-keeping means for them
- E01B5/02—Rails
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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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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Architecture (AREA)
- Civil Engineering (AREA)
- Structural Engineering (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
The invention discloses a high-toughness bainite steel rail and a production method thereof, wherein the room-temperature Charpy absorption power of a rail head of the steel rail is more than 100J, and the room-temperature Charpy absorption powers of a rail web and a rail bottom are both more than 90J. Comprises the following steps of online heat treatment: when the temperature of the top surface of the steel rail after finish rolling is at a first preset temperature, respectively cooling the top surface of the steel rail, two upper fillets of the rail head and two side surfaces of the rail head at a preset cooling speed until the temperature of the top surface of the rail is at a second preset temperature, and then air-cooling to room temperature; tempering heat treatment: and placing the steel rail cooled to room temperature in a stable temperature environment for tempering heat treatment, and cooling the steel rail to room temperature after the tempering heat treatment. The high-toughness bainite steel rail obtained by the invention has excellent rail web and rail base room temperature impact toughness, and the bainite steel rail with high toughness on the whole section can be obtained under the condition of not adding a large amount of microalloy elements by controlling the chemical components of the steel rail, an online heat treatment process and a tempering heat treatment process.
Description
Technical Field
The invention relates to the technical field of steel rail production, in particular to a high-toughness bainite steel rail and a production method thereof.
Background
The railway of China is in a high-speed development stage, with the increase of passenger special lines, the existing passenger-cargo mixed transportation line gradually reduces the operation of passenger cars, mainly transports the passenger cars, and simultaneously, the special transportation line for transporting the passenger cars is also developing towards overloading, and the overall trend of the transportation line is developing towards high transportation quantity, heavy axles and high driving density. This trend puts higher demands on the service performance and service life of the steel rail on the line, and the high efficiency and high safety of railway freight can be ensured only by improving the quality and performance of the steel rail.
At present, in order to improve the service performance and service life of a steel rail, a passenger-cargo mixed transportation line and a special freight transportation line at home and abroad mainly adopt a high-performance heat-treated pearlite steel rail, but although the strength and hardness of the steel rail are gradually improved in the conventional heat-treated pearlite steel rail research and development, the toughness of the steel rail is not correspondingly improved, and in a heavy-load line, particularly a small-radius curve section, the contact fatigue, subsequent cracks, stripping and chipping of the steel rail caused by wheel-rail friction, wheel impact and the like become one of the major problems influencing the service life of the steel rail.
In recent years, in order to solve the problem of contact fatigue of pearlite steel rail, rail production enterprises at home and abroad begin to develop bainite steel rails, which are expected to have high toughness and high contact fatigue resistance of bainite steel, and excellent strong hardness and wear resistance of pearlite steel.
At present, a plurality of steel rail production enterprises at home and abroad already carry out various researches on the bainite steel rail and the production method thereof, the researches comprise the procedures of component design, smelting, rolling, heat treatment, tempering heat treatment and the like of the bainite steel rail, and patent applications are carried out aiming at key technologies in the bainite steel rail, and related main related patent technologies are as follows:
patent CN 104087852A discloses a high-strength bainite steel rail and a production method thereof, and the steel rail comprises the following chemical components by weight percent: c: 0.15% -0.30%, Si: 1.00-1.80%, Mn: 1.50% -2.50%, Cr: 0.20 to 0.60%, Mo: 0.05-0.10 percent, and the balance of Fe and inevitable impurities, and the steel rail head is subjected to accelerated cooling to 220-300 ℃ by adopting an online heat treatment method at a cooling speed of 3.0-5.0 ℃/s when the tread of the steel rail head is naturally cooled to 450-500 ℃, so that the carbide-free bainite, a small amount of martensite and a small amount of residual austenite complex phase steel with excellent wear resistance is obtained. However, the on-line heat treatment method adopted by the heat treatment of the patent is rough, the detailed cooling process of each position of the steel rail is not specified, the performances such as the rail head section hardness and the like of the bainite steel rail for the heavy-duty railway are difficult to obtain, meanwhile, the internal stress of the produced steel rail is not fully eliminated, the full section impact toughness of the steel rail cannot be further optimized, cracks and stripping blocks are easy to generate in the service process, and the service life of the steel rail is influenced.
The patent CN 106435367A 'Bainite steel rail and preparation method thereof' discloses a Bainite steel rail and preparation method thereof, wherein the steel rail comprises, by weight, the content of Bainite ferrite strips in a microstructure of a round angle part on a rail head is more than or equal to 90%, the width of the Bainite ferrite strips is 0.3-0.8 mu m, the content of film-shaped residual austenite is less than or equal to 5%, the width of the film-shaped residual austenite is less than 0.1 mu m, the content of martensite is less than or equal to 5%, and the steel rail has excellent strength and toughness and lower rail bottom center residual stress. However, the bainite steel rail disclosed in the patent adopts a process of direct tempering after on-line heat treatment, the temperature of the steel rail is high when the steel rail starts to be tempered, phase transformation in the rail head of the steel rail may not be completed yet, at this time, the direct tempering heat treatment is started, which easily causes incomplete transformation of bainite in the steel rail finished product, more residual austenite + martensite tissues and negative influence on the full-section impact toughness of the steel rail, and the straightening process of the steel rail after the tempering heat treatment easily causes the reduced residual stress at the rail bottom to be increased again, which has great negative influence on the service safety of the steel rail, and the steel rail has possibility of fracture in the service process.
Patent CN 110468347A discloses a bainite steel rail with high strength and toughness and a manufacturing method thereof, wherein the steel rail comprises the following components in percentage by weight: c: 0.20 to 0.30%, Si: 1.00-1.80%, Mn: 1.80-2.80%, P: less than or equal to 0.025%, S: less than or equal to 0.015 percent, Cr: 0.50 to 1.00%, Mo: 0.40 to 0.70%, Nb: 0.02-0.08%, V:0.05 to 0.10%, Ti: 0.003-0.020%, O is less than or equal to 0.0005%, N: 0.0030-0.0060% and the balance of Fe and inevitable impurities, and the bainite steel rail obtained through the processes of smelting, continuous casting, reheating, rolling and tempering has the tensile strength of more than or equal to 1350MPa, the yield strength of more than or equal to 1150MPa, the elongation after fracture of more than or equal to 14%, the reduction of area of more than or equal to 50%, the normal-temperature impact absorption power of more than or equal to 70J and the hardness of more than or equal to 410 HBW. However, the bainite steel rail disclosed in the patent adopts a hot rolling air cooling after tempering heat treatment process, the obtained bainite steel rail has poor comprehensive mechanical properties, and the performances of abrasion resistance and contact fatigue resistance in the long-term service process are expected to be lower than those of the heat treatment bainite steel rail.
The patent CN 110951943A discloses a bainite/martensite multiphase steel rail and its heat treatment method, wherein the steel rail alloy system is C-Si-Mn-Cr-Ni-Mo system, and the chemical components comprise, by weight: c:0.15 to 0.30%, Si: 0.70-1.20%, Mn: 1.80-2.50%, Cr: 0.60-1.20%, Ni is less than or equal to 0.70%, Mo: 0.15-0.60% of Nb, less than or equal to 0.06% of Nb, less than or equal to 0.15% of V, less than or equal to 0.004% of Al, less than or equal to 30PPm of RE, less than or equal to 0.025% of P, less than or equal to 0.015% of S, less than or equal to 0.0080% of N, less than or equal to 0.0020% of O, and the balance of Fe and inevitable impurities, wherein the steel rail is subjected to online heat treatment and tempering heat treatment after rolling, so that the obtained bainite steel rail has the tensile strength of more than or equal to 1420MPa, the elongation after fracture of more than or equal to 15%, the reduction of area of more than or equal to 55%, the normal-temperature impact of more than or equal to 110J, the tread hardness of HBW 420-440, the residual stress value of the rail bottom of less than or equal to 250MPa, the hardness distribution of the cross section of the rail head of the steel rail is HRC 43-47, and the high strength and toughness matching is realized. However, the bainite steel rail disclosed in the patent is complex in component system, expensive Nb, RE and other element components are required to be added, the production cost is high, the cooling speeds of two accelerated cooling stages in the online heat treatment process are different, the process is complex, the control is difficult, and the large-scale popularization and use of the steel rail are not facilitated.
In the related patents of the prior bainite steel rail and the production method thereof, most of the bainite steel rails disclosed in the patents have good strength and toughness, but the research on the impact toughness of the whole section of the steel rail is rough, no clear requirements are provided for the impact toughness of the rail web and the rail bottom, the condition that the rail is broken due to cracks and even breakage of the rail web and the rail bottom which possibly occur under the impact of a train is not considered, the obtained bainite steel rail has a certain gap from the application level of an actual heavy-load line, and the chemical composition system and the production process are complex, so that the actual line application of the bainite steel rail is difficult to promote.
Based on this, the prior art still remains to be improved.
Disclosure of Invention
In order to solve the technical problems, the embodiment of the invention provides a high-toughness bainite steel rail and a production method thereof, and aims to solve the technical problem that the bainite steel rail in the prior art cannot meet the practical application.
On one hand, the production method of the high-toughness bainite steel rail disclosed by the embodiment of the invention comprises the following steps:
step one, online heat treatment: when the temperature of the top surface of the steel rail after finish rolling is at a first preset temperature, respectively cooling the top surface of the steel rail, two upper fillets of the rail head and two side surfaces of the rail head at a preset cooling speed, placing the steel rail on a cooling bed until the temperature of the top surface of the rail is at a second preset temperature, and air-cooling the steel rail to room temperature;
step two, tempering heat treatment: and placing the steel rail cooled to the room temperature in a stable temperature environment with a third preset temperature for tempering heat treatment, and cooling the steel rail to the room temperature after the tempering heat treatment.
Further, in the first step, when the top surface of the steel rail, the two upper fillets of the railhead and the two side surfaces of the railhead are respectively cooled at a preset cooling speed, the cooling speed of the two side surfaces of the railhead is controlled to be greater than that of the top surface of the steel rail and the two upper fillets of the railhead.
Further, the predetermined cooling rate is 2.0-5.0 ℃/s.
Further, in the first step, the first predetermined temperature is 680-800 ℃, and the second predetermined temperature is 240-320 ℃;
and/or the presence of a gas in the gas,
in the second step, the third predetermined temperature is 200-350 ℃.
Further, in the second step, the temperature environment is within a range of ± 15 ℃ of the set temperature.
Furthermore, in the steel rail after finish rolling, by weight percentage, 0.15-0.32% of C, 0.50-2.00% of Si, 1.50-3.00% of Mn, 0.40-1.20% of Cr, 0.10-0.60% of Mo, less than or equal to 0.020% of P, less than or equal to 0.015% of S, at least one of Ni, V and Nb, and the balance of Fe and inevitable impurities;
wherein Ni is 0.05 to 0.50% when Ni is contained, V is 0.05 to 0.20% when V is contained, and Nb is 0.001 to 0.020% when Nb is contained.
Or in the steel rail after the finish rolling, by weight percentage, 0.18-0.25% of C, 1.10-1.70% of Si, 1.60-2.40% of Mn, 0.60-1.10% of Cr, 0.25-0.50% of Mo, less than or equal to 0.020% of P, less than or equal to 0.015% of S, at least one of Ni, V and Nb, and the balance of Fe and inevitable impurities.
Wherein Ni is 0.25-0.45% in the case of Ni, V is 0.05-0.15% in the case of V, and Nb is 0.002-0.012% in the case of Nb.
Further, the cooling medium in the cooling treatment is one of water mist, compressed air, and a mixture of compressed air and water mist.
On the other hand, the embodiment of the invention also discloses a high-toughness bainite steel rail, wherein the room-temperature Charpy absorption power of a rail head of the steel rail is more than 100J, and the room-temperature Charpy absorption powers of a rail web and a rail bottom of the steel rail are both more than 90J.
Furthermore, the tensile strength of the steel rail is more than 1400MPa, the elongation is more than or equal to 12%, and the hardness of the top surface of the steel rail is 440-475 HBW.
Further, by weight percentage, 0.15-0.32% of C, 0.50-2.00% of Si, 1.50-3.00% of Mn, 0.40-1.20% of Cr, 0.10-0.60% of Mo, less than or equal to 0.020% of P, less than or equal to 0.015% of S, at least one of Ni, V and Nb, and the balance of Fe and inevitable impurities;
wherein Ni is 0.05 to 0.50% when Ni is contained, V is 0.05 to 0.20% when V is contained, and Nb is 0.001 to 0.020% when Nb is contained.
Or 0.18 to 0.25 percent of C, 1.10 to 1.70 percent of Si, 1.60 to 2.40 percent of Mn, 0.60 to 1.10 percent of Cr, 0.25 to 0.50 percent of Mo, less than or equal to 0.020 percent of P, less than or equal to 0.015 percent of S, at least one of Ni, V and Nb, and the balance of Fe and inevitable impurities.
Wherein Ni is 0.25-0.45% in the case of Ni, V is 0.05-0.15% in the case of V, and Nb is 0.002-0.012% in the case of Nb.
By adopting the technical scheme, the invention at least has the following beneficial effects:
the high-toughness bainite steel rail obtained by the invention has excellent rail web and rail bottom room temperature impact toughness, and the bainite steel rail with high toughness on the whole section can be obtained under the condition of not adding a large amount of multiple microalloy elements by controlling the chemical components of the steel rail, an online heat treatment process and a tempering heat treatment process, wherein the rail head room temperature Charpy impact absorption power is more than 100J, and the rail web and rail bottom room temperature Charpy impact absorption power is more than 90J; therefore, the bainite steel rail provided by the invention can effectively reduce the probability of impact contact fatigue damage of a high-strength wheel rail of a heavy-load line, effectively reduce the possibility of rail breakage caused by cracks or fracture of rail waists and rail bottoms under the impact of a train, effectively improve the service performance and service life of the steel rail, and improve the running safety of the train.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, it is obvious that the drawings in the following description are only some embodiments of the present invention, and for those skilled in the art, other drawings can be obtained according to the drawings without creative efforts.
Fig. 1 is a full-section impact toughness measurement position diagram of a steel rail according to an embodiment of the present invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the following embodiments of the present invention are described in further detail with reference to the accompanying drawings.
It should be noted that all expressions using "first" and "second" in the embodiments of the present invention are used for distinguishing two entities with the same name but different names or different parameters, and it should be noted that "first" and "second" are merely for convenience of description and should not be construed as limitations of the embodiments of the present invention, and they are not described in any more detail in the following embodiments.
The endpoints of the ranges and any values disclosed herein are not limited to the precise range or value, and such ranges or values should be understood to encompass values close to those ranges or values. For ranges of values, between the endpoints of each of the ranges and the individual points, and between the individual points may be combined with each other to give one or more new ranges of values, and these ranges of values should be considered as specifically disclosed herein.
Some embodiments of the invention disclose a high-toughness bainite steel rail, wherein the absorption work of the rail head of the steel rail in the summer ratio impact at room temperature is more than 100J, and meanwhile, the steel rail has excellent impact toughness at room temperature of the rail web and the rail base, and the absorption work of the rail web and the rail base in the summer ratio impact at room temperature is more than 90J. The chemical components by weight percentage are as follows: 0.15 to 0.32 percent of C, 0.50 to 2.00 percent of Si, 1.50 to 3.00 percent of Mn, 0.40 to 1.20 percent of Cr, 0.10 to 0.60 percent of Mo, less than or equal to 0.020 percent of P, less than or equal to 0.015 percent of S, at least one of Ni, V and Nb, 0.05 to 0.50 percent of Ni when Ni is contained, 0.05 to 0.20 percent of V when V is contained, 0.001 to 0.020 percent of Nb when Nb is contained, and the balance of Fe and inevitable impurities. The tensile strength of the steel rail is more than 1400MPa, the elongation is more than or equal to 12%, and the hardness of the top surface of the steel rail is 440-475 HBW.
In some preferred embodiments, the steel rail comprises the following chemical components in percentage by weight: 0.18 to 0.25 percent of C, 1.10 to 1.70 percent of Si, 1.60 to 2.40 percent of Mn, 0.60 to 1.10 percent of Cr, 0.25 to 0.50 percent of Mo, less than or equal to 0.020 percent of P, less than or equal to 0.015 percent of S, at least one of Ni, V and Nb, 0.25 to 0.45 percent of Ni when Ni is contained, 0.05 to 0.15 percent of V when V is contained, 0.02 to 0.12 percent of Nb when Nb is contained, and the balance of Fe and inevitable impurities.
The reasons for limiting the content of the main chemical elements of the steel rail according to the present invention will be described in detail below.
C is the most important and cheapest matrix strengthening element in the bainite steel rail, which ensures that the steel rail obtains good comprehensive mechanical properties. When the content of C is less than 0.15%, the proper strong hardness of the steel rail and the wear resistance and the contact fatigue resistance of the steel rail cannot be ensured under the production process of the invention; when the content of C is more than 0.30 percent, the production process is not beneficial to the formation and growth of bainite ferrite, the strength index of the steel rail is excessive, the toughness and plasticity are too low, the fatigue performance of the steel rail is influenced, and the safe use of the steel rail is adversely influenced; therefore, the carbon content in the present invention is limited to 0.15 to 0.32%.
The main function of Si in bainitic steel is as a solid solution strengthening element, increasing the hardness of the ferrite matrix, improving the strength and hardness of the steel, and simultaneously inhibiting the formation of carbides or cementite. When the Si content is less than 0.50%, the effect of inhibiting formation of carbide and cementite cannot be realized, and a carbide-free bainite structure with high toughness and plasticity cannot be obtained; when the Si content is more than 2.00%, carbide precipitation is excessively suppressed, resulting in excessive retained austenite phase in the structure, and a decrease in the strength of the rail. Therefore, the Si content in the present invention is limited to 0.50 to 2.00%.
Mn can effectively reduce the transformation starting temperature of the bainite structure and mainly plays a role in strengthening phase transformation. When the Mn content is less than 1.50 percent, the bainite structure transformation starting temperature in the steel rail cannot be effectively reduced; when the Mn content is more than 3.00%, a high segregation region is easily generated, so that abnormal structures such as martensite appear, and the welding performance of the steel rail is influenced. Therefore, the Mn content in the present invention is limited to 1.50 to 3.00%.
Cr is an alloy element capable of remarkably improving the hardenability of the bainitic steel; meanwhile, Cr can form carbide with carbon in steel, the carbide distribution in the steel is uniform, the size of the carbide is reduced, and the wear resistance of the steel rail is improved. When the Cr content is less than 0.40%, the carbide proportion formed by the steel is low, and the added alloy elements cannot improve the hardenability enough to obtain a bainite steel rail with proper performance; when the Cr content is more than 1.20 percent, the hardenability of the steel rail is too high, the steel rail is easy to produce harmful martensite structure, and the safe use of the steel rail is adversely affected. Therefore, the Cr content in the present invention is limited to 0.40 to 1.20%.
Mo is an element that can effectively delay pearlite transformation and separate bainite and pearlite transformation C-curves, thereby making the steel susceptible to bainite transformation. When the Mo content is less than 0.10%, the strengthening effect is not obvious; when the content of Mo element is more than 0.60%, transformation efficiency of bainite structure is lowered, and it is difficult to obtain an ideal bainite structure in the accelerated cooling process. Therefore, the Mo content in the present invention is limited to 0.10 to 0.60%.
P and S are impurity elements which cannot be completely removed from the steel rail. P can be segregated at the steel rail structure grain boundary, and the toughness of the steel rail is seriously reduced; s is easy to form MnS inclusions in steel and is harmful to the wear resistance and the contact fatigue resistance of the steel rail. Therefore, the content of P in the invention needs to be controlled below 0.020%; the S content is controlled below 0.015%.
In bainite steel, Ni can improve the hardness of a ferrite matrix and can improve the hardenability of the steel. When the Ni content is less than 0.05%, the effect is small, and the hardness can not be improved; when the Ni content is more than 0.50%, the toughness and plasticity of the ferrite phase in the steel are reduced, resulting in a reduction in the contact fatigue resistance of the steel rail. Therefore, the N content in the present invention is limited to 0.05 to 0.50%.
V is a precipitation strengthening element in the pearlite steel, forms carbonitride in the cooling process of the steel rail, can refine the grain size of bainite ferrite, and improves the strong hardness and the toughness and plasticity of the bainite steel. When the content of V is less than 0.05%, the grain refinement and strengthening effects are small, and the performance of the steel rail cannot be effectively improved; when the content of V is more than 0.20%, the capability of improving the strength and the hardness of the steel rail is reduced, and excessive precipitation strengthening effect can cause excessive precipitated phases in steel and have negative effect on the impact toughness of the steel rail. Therefore, the V content in the present invention is limited to 0.05 to 0.20%.
Nb in bainite steel mainly plays a role in increasing the nucleation number and refining the bainite structure in the bainite transformation process. When the Nb content is less than 0.001%, the grain refining effect is not obvious; when the Nb content is more than 0.020%, the content exceeds the limit of the provided fine-grain strengthening effect, and no effect is caused when the Nb content is continuously increased. Therefore, the Nb content in the present invention is limited to 0.001 to 0.020%.
The high-toughness bainite steel rail can be prepared by the following production method which sequentially comprises the following steps: the method comprises the following steps of converter smelting, LF furnace refining, RH vacuum treatment, continuous casting to obtain a steel billet, rolling the steel billet, online heat treatment, processing and tempering heat treatment.
Specifically, in the in-line heat treatment step: when the temperature of the top surface of the steel rail after finish rolling is 680-800 ℃, carrying out accelerated cooling treatment on the top surface of the steel rail, two upper fillets of the rail head and two side surfaces of the rail head at a cooling speed of 2.0-5.0 ℃/s until the temperature of the top surface of the rail is 240-320 ℃, placing the steel rail on a cooling bed, and carrying out air cooling to room temperature; in the tempering heat treatment: and (3) placing the steel rail cooled to the room temperature in a stable temperature environment of 200-350 ℃ for tempering heat treatment for 6-8 hours, and cooling the steel rail to the room temperature after the tempering heat treatment.
In the on-line heat treatment process of the steel rail, the top surface of the steel rail, the two upper fillets of the rail head and the two side surfaces of the rail head adopt different cooling speeds, and the cooling speeds of the two side surfaces of the rail head are greater than those of the two upper fillets of the top surface of the steel rail and the rail head. The cooling medium adopted in the on-line heat treatment process is at least one of water mist, compressed air and a mixture of the compressed air and the water mist. The stable temperature environment obtaining method can be any one of electric heating or coal gas heating, and the stable temperature environment means that the temperature fluctuation is controlled within a preset range, and is preferably controlled within +/-15 ℃ of the specified temperature. If the environmental temperature is unstable in the tempering heat treatment process, the performance of the steel rail is easy to be unstable, particularly the hardness of the section of the steel rail is easy to be abnormal, the stably reduced hardness gradient cannot be obtained, meanwhile, the consistency of the full-length performance of the fixed-length steel rail is easy to be reduced, and the condition that the surface hardness of the full-length steel rail is extremely poor and increased is easy to occur.
Aiming at the online heat treatment process: when the temperature of the tread of the rail head of the steel rail is 680-800 ℃, the steel rail does not start bainite structure phase transformation, accelerated cooling is started at the moment, the surface layer temperature of the rail head of the steel rail can be quickly reduced, the heat of the center part and the web of the rail head is diffused to the surface layer of the rail head, the whole temperature of the steel rail can be reduced by adopting large cooling speed accelerated cooling, when the steel rail reaches the bainite structure phase transformation temperature, the whole cooling of the steel rail can be effectively controlled, high full-section impact toughness of the steel rail is easy to obtain, the cooling speed needs to be controlled between 2.0-5.0 ℃, the steel rail is accelerated cooled to 240-320 ℃ until the surface temperature of the top surface of the steel rail is 240-320 ℃, the bainite transformation of the steel rail is completed at the moment, the accelerated cooling is meaningless, and the accelerated cooling can lead to the generation of a large amount of martensite abnormal structures, so the steel rail at the moment needs to be air-cooled to the room temperature;
aiming at the problem that the cooling speed of two side surfaces of the railhead in the online heat treatment process is greater than the round angles on the top surface of the steel rail and the two sides of the railhead: because the center of the steel rail is close to the rail web of the steel rail, heat conduction is easy to occur between the center and the rail web of the steel rail, in order to control the temperature of the center and the rail web, both sides can be quickly cooled, a better bainite structure is obtained, the accelerated cooling speed of the two side surfaces of the rail head of the steel rail needs to be adjusted in a targeted manner, the center and the rail web of the rail head can be simultaneously covered, and the cooling speed of all the positions needs to be within the range of 2.0-5.0 ℃.
Aiming at the tempering heat treatment process: the temperature of the heat preservation of the tempering heat treatment of the bainite steel rail is 200-350 ℃, and the tempered bainite steel rail can obtain higher strength and toughness and comprehensive mechanical property at the temperature; if the tempering temperature is lower than 200 ℃, the tempering effect of the steel rail is not obvious, and excellent full-section toughness is difficult to obtain, and if the tempering temperature is higher than 350 ℃, the toughness and plasticity of the steel rail are obviously reduced; the tempering heat treatment time of the bainite steel rail is 6-8 hours, if the time is too short, the steel rail is not tempered sufficiently, the impact toughness fluctuation of the rail web and the rail bottom of the steel rail is large, the internal residual stress is not sufficiently eliminated, when the treatment time is more than 8 hours, carbide in the steel rail is separated out, and the extension of the steel rail tempering time has no significant meaning.
The complete production process of the production method of the bainite steel rail with excellent rail top surface can be as follows: smelting low-sulfur vanadium-containing molten steel by a converter or an electric furnace, performing LF refining, RH or VD vacuum treatment, protecting and continuously casting blooms, heating a billet heating furnace, descaling with high-pressure water before billet rolling, rolling by a universal mill, performing on-line steel rail heat treatment, cooling with air at room temperature by a stepping cooling bed, performing horizontal and vertical composite straightening, inspecting the specification of a steel rail, processing a processing line, tempering heat treatment, inspecting the surface and warehousing.
The present invention will be described in detail below by way of examples, but the scope of the present invention is not limited thereto.
Examples 1 to 3 and comparative examples 1 to 3 correspond to steel rails having the following chemical compositions, which are listed in table 1, and the following numbers 1 to 3.
TABLE 1
Examples 1 to 3 comparative examples 1 to 3 the heat treatment process parameters are shown in table 2, and the difference between the smelting process and the rolling process between the examples and comparative examples is negligible.
TABLE 2
The full-face impact toughness and tensile properties and the rail top surface hardness of examples 1 to 3 and comparative examples 1 to 3 are shown in Table 3. In the invention, a U2 notch test scheme in GB/T229-2007 method for testing Charpy pendulum impact of metal materials is adopted, the sampling position is shown in figure 1, the side surface of the sample is open, and the rail head, the rail web and the rail bottom are respectively used for testing the room-temperature Charpy impact absorption work of 4 samples.
TABLE 3
Compared with the comparative example, the embodiment of the invention has obvious influence on the final performance of the rolled steel rail due to different online heat treatment and tempering heat treatment modes of the rolled steel rail under the same chemical components and smelting process, the head room-temperature Charpy impact absorption power of the steel rail obtained by adopting the method of the invention is more than 100J, the waist and bottom room-temperature Charpy impact absorption powers of the steel rail are more than 90J, and the steel rail has excellent full-section impact toughness; in the comparative example, the impact toughness at full fracture surface was not satisfactory.
It should be particularly noted that the various components or steps in the above embodiments can be mutually intersected, replaced, added or deleted, and therefore, the combination formed by the reasonable permutation and combination conversion shall also belong to the protection scope of the present invention, and the protection scope of the present invention shall not be limited to the embodiments.
The above is an exemplary embodiment of the present disclosure, and the order of disclosure of the above embodiment of the present disclosure is only for description and does not represent the merits of the embodiment. It should be noted that the discussion of any embodiment above is exemplary only, and is not intended to intimate that the scope of the disclosure, including the claims, of embodiments of the invention is limited to those examples, and that various changes and modifications may be made without departing from the scope, as defined in the claims. The functions, steps and/or actions of the method claims in accordance with the disclosed embodiments described herein need not be performed in any particular order. Furthermore, although elements of the disclosed embodiments of the invention may be described or claimed in the singular, the plural is contemplated unless limitation to the singular is explicitly stated.
Those of ordinary skill in the art will understand that: the discussion of any embodiment above is meant to be exemplary only, and is not intended to intimate that the scope of the disclosure, including the claims, of embodiments of the invention is limited to these examples; within the idea of an embodiment of the invention, also technical features in the above embodiment or in different embodiments may be combined and there are many other variations of the different aspects of an embodiment of the invention as described above, which are not provided in detail for the sake of brevity. Therefore, any omissions, modifications, substitutions, improvements, and the like that may be made without departing from the spirit and principles of the embodiments of the present invention are intended to be included within the scope of the embodiments of the present invention.
Claims (10)
1. A production method of a high-toughness bainite steel rail is characterized by comprising the following steps:
step one, online heat treatment: when the temperature of the top surface of the steel rail after finish rolling is at a first preset temperature, respectively cooling the top surface of the steel rail, two upper fillets of the rail head and two side surfaces of the rail head at a preset cooling speed, placing the steel rail on a cooling bed until the temperature of the top surface of the rail is at a second preset temperature, and air-cooling the steel rail to room temperature;
step two, tempering heat treatment: and placing the steel rail cooled to the room temperature in a stable temperature environment with a third preset temperature for tempering heat treatment, and cooling the steel rail to the room temperature after the tempering heat treatment.
2. The method according to claim 1, wherein in the first step, when the top surface of the rail, the rounded corners of the head, and the two sides of the head are respectively cooled at a predetermined cooling rate, the cooling rate of the two sides of the head is controlled to be greater than the cooling rate of the top surface of the rail and the rounded corners of the head.
3. The production method according to claim 1 or 2, wherein the predetermined cooling rate is 2.0 to 5.0 ℃/s.
4. The method as claimed in claim 1, wherein in the first step, the first predetermined temperature is 680-800 ℃, and the second predetermined temperature is 240-320 ℃;
and/or the presence of a gas in the gas,
in the second step, the third predetermined temperature is 200-350 ℃.
5. The production method according to claim 1, wherein in the second step, the temperature environment is within ± 15 ℃ of the set temperature.
6. The production method according to claim 1, wherein the steel rail after finish rolling comprises, by weight, 0.15 to 0.32% of C, 0.50 to 2.00% of Si, 1.50 to 3.00% of Mn, 0.40 to 1.20% of Cr, 0.10 to 0.60% of Mo, less than or equal to 0.020% of P, less than or equal to 0.015% of S, at least one of Ni, V and Nb, and the balance of Fe and unavoidable impurities;
wherein Ni is 0.05-0.50% when Ni is contained, V is 0.05-0.20% when V is contained, and Nb is 0.001-0.020% when Nb is contained;
alternatively, the first and second electrodes may be,
in the steel rail after finish rolling, by weight percentage, 0.18-0.25% of C, 1.10-1.70% of Si, 1.60-2.40% of Mn, 0.60-1.10% of Cr, 0.25-0.50% of Mo, less than or equal to 0.020% of P, less than or equal to 0.015% of S, at least one of Ni, V and Nb, and the balance of Fe and inevitable impurities;
wherein Ni is 0.25-0.45% in the case of Ni, V is 0.05-0.15% in the case of V, and Nb is 0.002-0.012% in the case of Nb.
7. The method of claim 1, wherein the cooling medium in the cooling process is one of water mist, compressed air, and a mixture of compressed air and water mist.
8. A high-toughness bainite steel rail is characterized in that the absorption work of the steel rail head in summer impact at room temperature is more than 100J, and the absorption work of the rail web and the rail bottom in summer impact at room temperature is more than 90J.
9. The high-toughness bainite steel rail according to claim 8 has tensile strength of 1400MPa, elongation not lower than 12% and rail top hardness of 440-475 HBW.
10. The high-toughness bainitic steel rail according to claim 8, wherein the steel rail contains, in weight%, 0.15 to 0.32% of C, 0.50 to 2.00% of Si, 1.50 to 3.00% of Mn, 0.40 to 1.20% of Cr, 0.10 to 0.60% of Mo, 0.020% or less of P, 0.015% or less of S, at least one of Ni, V and Nb, and the balance of Fe and unavoidable impurities;
wherein Ni is 0.05-0.50% when Ni is contained, V is 0.05-0.20% when V is contained, and Nb is 0.001-0.020% when Nb is contained;
alternatively, the first and second electrodes may be,
0.18 to 0.25 percent of C, 1.10 to 1.70 percent of Si, 1.60 to 2.40 percent of Mn, 0.60 to 1.10 percent of Cr, 0.25 to 0.50 percent of Mo, less than or equal to 0.020 percent of P, less than or equal to 0.015 percent of S, at least one of Ni, V and Nb, and the balance of Fe and inevitable impurities;
wherein Ni is 0.25-0.45% in the case of Ni, V is 0.05-0.15% in the case of V, and Nb is 0.002-0.012% in the case of Nb.
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