CN113235013A - Q800 corrosion-resistant steel for mine environment service and preparation method thereof - Google Patents
Q800 corrosion-resistant steel for mine environment service and preparation 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
-
- 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
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
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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
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C21D2211/008—Martensite
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Abstract
The invention discloses Q800 corrosion resistant steel for mine environment service and a preparation method thereof, wherein the Q800 corrosion resistant steel comprises the following components in percentage by mass: 0.16 to 0.19 percent of C, 0.5 to 1.0 percent of Mn0.2 to 0.35 percent of Si, 1.3 to 1.7 percent of Cr1, less than or equal to 0.005 percent of S, less than or equal to 0.008 percent of P, less than or equal to 0.035 percent of Al, 0.02 to 0.03 percent of Nb, 0.015 to 0.025 percent of Ni0.015 to 0.025 percent of Mo0.015 to 0.025 percent of Ti, and the balance of Fe and impurities. The preparation method comprises the following steps: smelting and forging, rolling by adopting a high-temperature slow-speed high-pressure technology, and carrying out on-line quenching and tempering treatment. The steel has yield strength of more than 800MPa, tensile strength of 840-1000 MPa and corrosion rate of 0.10-0.12 mm/a in a typical service mine environment.
Description
Technical Field
The invention relates to the technical field of metal material processing, in particular to novel Q800 corrosion-resistant steel in service in a mine environment and a preparation method thereof.
Background
The high-strength structural steel is a resource-saving product with high technical content and high added value, and the low-alloy high-strength steel has strong adaptability. There is an increasing demand in the market today for steel grades with higher strength grades, such as 800MPa grades. As low-alloy high-strength structural steel, Q800 has the characteristics of high strength, good toughness, good processability and welding performance and the like, belongs to one of steel types widely applied to high-strength steel, and is mainly used in the fields of engineering machinery, coal mine machinery, shipbuilding, steel structures and the like.
Chinese patent with publication number CN109972042A discloses a low-temperature-resistant corrosion-resistant H-shaped steel with yield strength of 800MPa and a preparation method thereof, the yield strength of the obtained H-shaped steel is more than or equal to 800MPa, the tensile strength is 860-940 MPa, the elongation after fracture is more than or equal to 14.0, and the low-temperature impact at-20 ℃ is more than or equal to 50J. The mechanical property is excellent, but the patent does not describe the corrosion resistance of the H-shaped steel in detail, so the H-shaped steel cannot adapt to the service environment under a mine.
Chinese patent publication No. CN104233077A discloses a method for producing high-strength corrosion-resistant steel, and more particularly discloses a method for producing corrosion-resistant steel sheet with high strength, in which the content of Cr added in the component design is 13% to 18%, the component design of the invention is not economical, the cost is very high, and the patent gives no detailed description on which grade of performance the corrosion-resistant steel can finally reach, and it cannot be reasonably speculated according to the prior art and the content disclosed by the patent.
Disclosure of Invention
In view of the problems in the prior art, the inventor of the invention continuously reforms and innovates through long-term exploration and trial and multiple experiments and efforts, and provides Q800 corrosion-resistant steel which is designed to contain Ni and has good mechanical property, welding property and corrosion resistance and is used in a mine environment and a preparation method thereof.
In order to achieve the purpose, the invention adopts the following technical scheme:
the Q800 corrosion-resistant steel for the service of the mine environment comprises the following chemical components in percentage by mass: 0.16 to 0.19 percent of C, 0.5 to 1.0 percent of Mn, 0.2 to 0.35 percent of Si, 1.3 to 1.7 percent of Cr, less than or equal to 0.005 percent of S, less than or equal to 0.008 percent of P, less than or equal to 0.035 percent of Al, 0.02 to 0.03 percent of Nb, 0.015 to 0.025 percent of Ni, 0.015 to 0.025 percent of Mo, 0.02 to 0.03 percent of Ti, and the balance of Fe and other inevitable impurities.
The Q800 corrosion-resistant steel comprises the following chemical components in percentage by mass as a preferable mode: 0.17 to 0.19 percent of C, 0.5 to 0.6 percent of Mn, 0.24 to 0.30 percent of Si, 1.35 to 1.45 percent of Cr, less than or equal to 0.005 percent of S, less than or equal to 0.006 percent of P, less than or equal to 0.035 percent of Al, 0.025 to 0.028 percent of Nb, 0.020 to 0.024 percent of Ni, 0.018 to 0.024 percent of Mo, 0.020 to 0.025 percent of Ti, and the balance of Fe and other inevitable impurities.
As a preferable mode, the Q800 corrosion-resistant steel has the yield strength of more than or equal to 800MPa, the tensile strength of 840-1000 MPa and the corrosion rate of 0.10-0.12 mm/a in service under a typical service mine environment.
The invention adopts the design that Cr contains Ni, and the produced corrosion-resistant steel has good mechanical property, welding property and corrosion resistance, and is suitable for the service of mine environment. The effects of the main components in the Q800 corrosion-resistant steel are shown as follows:
the C element mainly plays a role in strengthening in the steel, and the strength of the steel is improved along with the increase of the C content in a certain range; but Fe formed by C in steel3C is not good for corrosion resistance of steel, so the content of C is limited to 0.16% -0.19%.
Mo and Ti are strong carbide forming elements, and the addition of Mo and Ti in the steel can improve the alloying effect of Cr, so that the Cr element is dissolved in a matrix in a solid manner, and the corrosion resistance of the steel is improved. The Mo element is added into the low-carbon steel, so that the transformation of the proeutectoid ferrite can be delayed, the formation of acicular ferrite and bainite is promoted, and the strength and toughness of the low-alloy steel are improved; the Mo element can improve the solid solubility of the microalloy elements in austenite and delay the precipitation of microalloy carbonitride, so that more microalloy elements can be reserved in steel, and the microalloy elements can not be precipitated from the ferrite structure of the steel at a lower temperature, thereby generating a larger precipitation strengthening effect.
Ni: the Ni element is added into the alloy steel, a passive film of Ni is easily formed on a steel matrix, the corrosion potential of the steel matrix is improved, the corrosion tendency of the steel matrix is reduced, and the stability of the steel matrix is improved. In addition, when the passivation film formed on the steel matrix by Ni is complete, the generation and dissolution of the passivation film are in a dynamic balance state, and when the passivation film is damaged, the generation rate of the passivation film is greater than the dissolution rate of the passivation film at the damaged part, so that a new Ni passivation film is formed on the steel matrix, and the steel matrix is continuously protected from corrosion, namely, the self-repairing capability of the steel matrix is enhanced by the existence of the Ni passivation film.
The invention also provides a preparation method of the Q800 corrosion-resistant steel for the mine environment service, wherein the Q800 corrosion-resistant steel comprises the following chemical components in parts by weight:
a method for preparing Q800 corrosion-resistant steel for service in a mine environment, wherein the Q800 corrosion-resistant steel has the chemical composition of the corrosion-resistant steel, and the preparation method comprises the following steps:
1) selection of an alloy: selecting an alloy according to the mass percentage of the chemical components of the Q800 corrosion-resistant steel;
2) smelting and forging: smelting the selected alloy by using a vacuum smelting induction furnace according to the chemical component requirement of the Q800 corrosion-resistant steel, and forging the smelted alloy into a square billet;
3) rolling: heating and preserving the heat of the forged square billet at 1180-1230 ℃, and then rolling the heated square billet by adopting a high-temperature slow-speed high-pressure technology to obtain a billet;
4) quenching and tempering heat treatment: and carrying out on-line quenching and tempering treatment on the rolled steel billet.
In the invention, the purpose of forging in the step 2) is to reduce the metal internal defects of the corrosion-resistant steel and improve the performance of the corrosion-resistant steel.
In the above preparation method, as a preferred mode, in the rolling step, the high-temperature, slow-speed and large-pressure technology is as follows: rolling is started at 1180-1230 deg.C (e.g., 1190 deg.C, 1200 deg.C, 1210 deg.C, 1220 deg.C), total reduction is 84-90% (e.g., 85%, 86%, 87%, 88%, 89%), and strain rate is 0.2-2.0 s-1(e.g., 0.4 s)-1、0.5s-1、0.8s-1、1.0s-1、1.2s-1、1.5s-1、1.7s-1、1.9s-1) The finishing temperature is controlled to 820 to 870 ℃ (e.g., 830 ℃, 840 ℃, 850 ℃, 860 ℃).
In the above preparation method, as a preferable mode, in the rolling step, the billet is heated and kept at 1180 ℃ to 1230 ℃ (e.g., 1190 ℃, 1200 ℃, 1210 ℃, 1220 ℃) for 120min to 150min (e.g., 130min, 140min, 145 min).
In the above production method, as a preferable mode, in the rolling step, the rolling includes rough rolling and finish rolling.
In the above production method, as a preferable aspect, in the rolling step, the rough rolling reduction ratio in the rough rolling process is 60% to 70% (e.g., 62%, 64%, 65%, 67%, 69%), and the rough rolling deformation ratio is 60% or more (e.g., 70%, 80%, 90%).
In the above production method, in the rolling step, a reduction ratio of the finish rolling is 50% to 60% (e.g., 52%, 54%, 55%, 57%, 59%) and a total deformation ratio of the finish rolling is 50% or more (e.g., 55%, 60%, 65%, 70%, 80%).
In the invention, in order to avoid the core segregation in the rolling process so as to influence the strength and the toughness of the corrosion-resistant steel, the invention adopts a two-stage rolling (namely, rough rolling and finish rolling) method, and the rolling deformation rate of one stage is more than or equal to 60 percent and the total deformation rate of the two stages is more than or equal to 50 percent. Meanwhile, in order to improve the plastic toughness of the corrosion-resistant steel, the tensile strength needs to be increased, and the temperature of the two-stage finish rolling is controlled to be 820-870 ℃.
In the above production method, as a preferable mode, in the rolling step, the overall reduction ratio (i.e., the thickness of the slab before rolling/the thickness of the steel sheet after rolling) is >6 times (e.g., 6.5 times, 7 times, 8 times).
The rolling force required by rolling at high temperature is small, and the temperature of the steel is not reduced too much during the rolling at high temperature, so that the structure control of the steel is facilitated; the slow-speed high-pressure technology utilizes steel structure to be fully refined, and can improve the performance of steel. Meanwhile, because the experimental steel has high strength, the rolling is controlled by adopting a high-temperature, slow-speed and high-pressure technology.
In the above production method, as a preferable mode, step 4) is performed immediately after step 3), that is, in-line quenching after rolling is performed immediately after the rolling step.
In the invention, the subsequent quenching and tempering heat treatment is carried out immediately after the on-line quenching after the rolling, because compared with the modulating heat treatment after the steel is cooled, the process flow can be shortened, and the energy consumption is saved.
In the above production method, as a preferable mode, in the quenching and tempering heat treatment step, the steel obtained in the rolling step is heated to 890 to 910 ℃ (e.g., 895 ℃, 900 ℃, 905 ℃, 909 ℃) and then is kept warm for 60 to 70min (e.g., 65min, 68min) to be austenitized, and then is cooled to room temperature by water, so that the steel can obtain a martensitic structure after quenching, and has high strength.
In the above production method, as a preferable mode, in the quenching and tempering heat treatment step, the tempering is performed by heating the steel obtained after quenching to 590 to 610 ℃ (e.g., 595 ℃, 600 ℃, 605 ℃), maintaining the temperature for 80 to 90min (e.g., 82min, 85min, 87min), and then air-cooling to room temperature.
In the invention, the quenching and tempering heat treatment comprises two parts of on-line quenching and tempering after rolling, and the steel can jump over a ferrite phase transformation area to directly carry out martensite phase transformation due to the higher cooling speed during quenching so as to obtain a martensite structure and have higher strength. However, since the internal stress after quenching is large, although the strength is high, the toughness is poor, so that the tempering heat treatment is adopted after quenching, and the steel structure is subjected to the phase changes of martensite decomposition, carbide formation and transformation, cementite aggregation and spheroidization, alpha phase recovery recrystallization and the like. Upon tempering, sufficient thermal activation causes the lath martensite, which has a very high dislocation density, to rearrange into a net-like and strip-like distribution, transforming into equiaxed crystals, which have a very low dislocation density, with minimal energy and good stability. On the other hand, the precipitated fine grained carbide is separated from the coherent relation with the alpha phase, is aggregated, grown and coarsened, and hinders the recrystallization of the alpha phase, so that the matching of the strength and the plasticity of the steel is optimized, and higher mechanical performance is obtained.
In the above preparation method, as a preferable mode, in the smelting and forging step, the smelting end point temperature is controlled to be 1640-1680 ℃ (e.g., 1650 ℃, 1660 ℃ and 1670 ℃); the finish forging temperature is controlled at 800-850 deg.C (e.g., 810 deg.C, 820 deg.C, 830 deg.C, 840 deg.C).
In the above production method, the thickness of the billet is preferably 60mm to 100mm (for example, 65mm, 70mm, 75mm, 80mm, 85mm, 90mm, 95 mm).
In the invention, the selection of the specification of the blank for preparing the Q800 corrosion-resistant steel is determined according to the performance of a rolling mill and the rolling reduction, and the preparation method can be used for the rolling production of the Q800 corrosion-resistant steel as long as the size of the blank meets the requirements of smelting and rolling conditions.
In the present invention, a billet having a thickness of 100mm is preferable because the overall reduction ratio (i.e., the thickness of the billet before rolling/the thickness of the steel plate after rolling) is more than 6 times.
In the preparation method, as a preferable mode, the Q800 corrosion-resistant steel is a plate with the thickness of 10-16 mm.
Conventional technical knowledge in the art can be used for the details which are not described in the present invention.
In the invention, the technical characteristics can be combined arbitrarily to form a new technical scheme under the condition of not conflicting with each other.
The corrosion-resistant steel obtained by the invention is a steel plate with yield strength of more than or equal to 800MPa and tensile strength of 840-1000 MPa, the corrosion rate under the service of a typical service mine environment is 0.10-0.12 mm/a, and the corrosion resistance is improved by more than 1.5 times compared with that of the traditional 800 MPa-level steel.
The steel with excellent mechanical property and corrosion resistance in service in the mine environment is manufactured, the steel loss and equipment failure caused by corrosion can be effectively reduced, and the service life and reliability of equipment for the mine are greatly prolonged and improved. The preparation method based on the existing production process has good cost advantage and can be used for mass production.
Compared with the prior art, the invention has the beneficial effects that:
1. by adopting the design of Cr containing Ni, the produced corrosion-resistant steel has good mechanical property, welding property and corrosion resistance, and is suitable for the service of mine environment.
2. The corrosion-resistant steel manufactured by the method has excellent mechanical property, can effectively reduce steel loss and equipment failure caused by corrosion, and greatly improves the service life and reliability of equipment for mines.
3. The corrosion-resistant steel manufactured by the invention is a preparation method based on the existing production process, so that the corrosion-resistant steel has good cost advantage and can be produced in large quantities.
4. The invention adopts an on-line quenching process, can shorten the process flow and effectively save energy.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this application, illustrate embodiments of the invention and, together with the description, serve to explain the invention and not to limit the invention.
FIG. 1 is a schematic representation of the metallographic structure of a corrosion resistant steel of 16mm thickness prepared in example 1 of the present invention.
FIG. 2 is a macroscopic (FIG. 2a) and microscopic (FIG. 2b) topographical view of a 16mm thick corrosion resistant steel prepared in example 1 of the present invention after corrosion.
FIG. 3 is a macro (FIG. 3a) and micro-topography (FIG. 3b) of conventional 800MPa grade steel after corrosion in example 1 of the present invention.
FIG. 4 is a metallographic structure of a corrosion-resistant steel having a thickness of 16mm prepared in example 2 of the present invention.
FIG. 5 is a macro (FIG. 5a) and micro topography (FIG. 5b) of a 16mm thick corrosion resistant steel prepared in example 2 of the present invention after corrosion.
FIG. 6 is a macro (FIG. 6a) and micro topography (FIG. 6b) of conventional Q800 steel after corrosion in example 2 of the present invention.
FIG. 7 is a metallographic structure of a corrosion-resistant steel having a thickness of 16mm prepared in example 3 of the present invention.
FIG. 8 is a macro (FIG. 8a) and micro topography (FIG. 8b) of a 16mm thick corrosion resistant steel prepared in example 3 of the present invention after corrosion.
FIG. 9 is a macro (FIG. 9a) and micro topography map (FIG. 9b) of conventional Q800 steel after corrosion in example 3 of the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below, and it is obvious that any feature disclosed in the present specification may be replaced by other equivalent or alternative features having similar purposes unless specifically stated otherwise. Unless expressly stated otherwise, each feature is only an example of a generic series of equivalent or similar features. The described embodiments are only some embodiments of the invention, not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Conventional technical knowledge in the art can be used for the details which are not described in the present invention.
Example 1
The Q800 corrosion-resistant steel for mine environment service provided in this example adopts a 350mm twin-roll reversible mill, has a rolling force of 1200KN, and produces Q800 corrosion-resistant steel with a thickness specification of 16mm, and the specific elemental compositions are shown in table 1, and the balance is Fe and inevitable impurities.
TABLE 1 chemical composition of 16mm thick Q800 corrosion resistant steel of example 1
The preparation method of the Q800 corrosion-resistant steel with the chemical composition comprises the following steps:
(1) smelting and forging: smelting the alloy raw material by using a vacuum smelting induction furnace according to the design components in the table 1, and forging the smelted alloy raw material into a square billet with the width of 80mm multiplied by 100mm, so that the internal defects of the metal are reduced, and the performance is improved; wherein the smelting end point temperature is controlled to be 1640-1680 ℃; the final forging temperature is controlled to be 800-850 ℃.
(2) Rolling:
firstly, heating a square billet obtained after forging in the step (1), controlling the heating temperature at 1200 ℃, and preserving heat for 120 min; and then, rolling the heated square billet by adopting a high-temperature slow-speed high-pressure technology to produce a 16mm thin steel plate. Wherein the total pressure reduction rate is 84%.
In the rolling process, in order to avoid occurrence of core segregation and influence on the strength and toughness of the corrosion-resistant steel, the embodiment adopts a two-stage rolling method, wherein the reduction rate of one-stage rolling (i.e., rough rolling) is 60%, the deformation rate is not less than 60%, the total deformation rate of the two-stage rolling (i.e., finish rolling or II stage) is not less than 50%, and the overall compression ratio is 6.25 times. In order to improve the ductility and toughness of the corrosion-resistant steel, the tensile strength needs to be increased, so that the temperature of the two-stage finish rolling is controlled to be 820-870 ℃.
In this embodiment, parameters of a partial rolling and cooling control process are shown in table 2 (where the intermediate slab refers to a steel slab obtained after rough rolling), parameters of a salt spray corrosion test are shown in table 3, and performance parameters of the obtained corrosion-resistant steel are shown in table 4.
Table 2 partial controlled rolling and cooling process parameters for Q800 corrosion resistant steel prepared in example 1
(3) Thermal treatment for hardening and tempering
And carrying out on-line quenching and tempering treatment on the rolled steel billet.
And (3) on-line quenching after rolling: and heating the steel obtained in the rolling step to 910 ℃, preserving the heat for 60min for austenitizing, and then cooling the steel to room temperature by water so that the steel can obtain a martensite structure after quenching and has higher strength.
Tempering treatment: and heating the quenched steel to 610 ℃, preserving the heat for 80min, and then cooling the steel to room temperature in air.
TABLE 3 salt spray Corrosion test parameters of Q800 Corrosion-resistant steels obtained after thermal refining treatment in example 1
TABLE 4 Corrosion-resistant Steel Performance parameters of Q800 corrosion-resistant Steel obtained after thermal refining treatment in example 1
In the prior art, conventional Q800 steel has no clear requirement on corrosion resistance, in the embodiment, conventional 800 MPa-grade steel (namely conventional Q800 steel) is used as comparison, a corrosion environment is a simulated mine service environment, and a corrosion rate test is performed according to the specification of a salt spray corrosion experiment in GB/T10125-. The conventional Q800 steel has the following components: 0.15% of C, 1.63% of Mn, 0.39% of Si, 0.25% of Cr, 0.003% of S, 0.012% of P, 0.032% of Al, 0.028% of Nb, 0.18% of Ni, 0.1% of Mo, 0.0012% of Ti, and the balance of Fe and other unavoidable impurities. The corrosion rate of the conventional 800MPa grade steel is 0.1811mm/a, and the corrosion rate of the 16mm thickness Q800 corrosion-resistant steel prepared in the embodiment is 0.1132 mm/a. Compared with the conventional 800 MPa-grade steel, the corrosion resistance of the Q800 corrosion-resistant steel obtained by the embodiment is improved by 1.6 times. The formed products of the corrosion-resistant steel comprise hydraulic supports for coal mines and engineering machinery for mines.
In the embodiment, the metallographic structure and the corrosion morphology of the prepared Q800 corrosion-resistant steel are also determined. Fig. 1 shows the metallographic structure of the Q800 corrosion-resistant steel obtained in this example. Fig. 2 shows the macro (fig. 2a) and micro topography (fig. 2b) of the Q800 corrosion-resistant steel obtained in this example after corrosion. Fig. 3 shows the macro (fig. 3a) and micro-topography (fig. 3b) of conventional Q800 corrosion resistant steel after corrosion.
As is clear from fig. 1, the Q800 corrosion-resistant steel structure produced in this example is martensite.
As can be seen from the analysis and comparison of FIGS. 2 to 3, compared with the conventional 800 MPa-grade steel, the steel has more and compact corroded products, and can form a corrosion product film on the surface of the substrate to hinder the further development of corrosion, so that the corrosion product amount is less, and the corrosion resistance of the steel is stronger.
Example 2
The Q800 corrosion-resistant steel for mine environment service provided in this example adopts a 350mm twin-roll reversible mill, has a rolling force of 1200KN, and produces Q800 corrosion-resistant steel with a thickness specification of 16mm, the specific elemental composition is shown in table 5, and the balance is Fe and unavoidable impurities.
TABLE 5 chemistry of 16mm thick Q800 corrosion resistant steel prepared in example 2
The preparation method of the Q800 corrosion-resistant steel with the chemical composition comprises the following steps:
(1) smelting and forging: according to the design components in the table 5, the alloy raw materials are smelted by using a vacuum smelting induction furnace, and square billets of 80mm (width) x 100mm (thickness) x 100mm (length) are forged after smelting, so that the internal defects of the metal are reduced, and the performance is improved; wherein the smelting end point temperature is controlled to be 1640-1680 ℃; the final forging temperature is controlled to be 800-850 ℃.
(2) Rolling:
firstly, heating a square billet obtained after forging in the step (1), controlling the heating temperature at 1200 ℃, and preserving heat for 120 min; and then, rolling the heated square billet by adopting a high-temperature slow-speed high-pressure technology to produce a 16mm thin steel plate. Wherein the total pressure reduction rate is 84%.
In the rolling process, in order to avoid occurrence of core segregation and influence on the strength and toughness of the corrosion-resistant steel, the embodiment adopts a two-stage rolling method, wherein the reduction rate of one-stage rolling (i.e., rough rolling) is 60%, the deformation rate is not less than 60%, the total deformation rate of the two-stage rolling (i.e., finish rolling or II stage) is not less than 50%, and the overall compression ratio is 6.25 times. In order to improve the ductility and toughness of the corrosion-resistant steel, the tensile strength needs to be increased, so that the temperature of the two-stage finish rolling is controlled to be 820-870 ℃.
In this example, the parameters of a part of controlled rolling and controlled cooling processes are shown in table 6 (wherein, the intermediate slab refers to a steel slab obtained after rough rolling), the parameters of a salt spray corrosion test are shown in table 7, and the performance parameters of the obtained corrosion-resistant steel are shown in table 8.
Table 6 controlled rolling and cooling process parameters for Q800 corrosion resistant steel prepared in example 2
(3) Thermal treatment for hardening and tempering
And (3) carrying out on-line quenching and tempering treatment on the rolled steel billet to obtain the final Q800 corrosion-resistant steel.
And (3) on-line quenching after rolling: and heating the steel obtained in the rolling step to 890 ℃, preserving the heat for 70min for austenitizing, and then cooling the steel to room temperature by water so that the steel can obtain a martensite structure after quenching, and has higher strength.
Tempering treatment: and heating the quenched steel to 590 ℃, preserving the heat for 90min, and then cooling the steel to room temperature in air.
TABLE 7 example 2 salt spray Corrosion test parameters for Q800 Corrosion resistant steels after thermal refining and Heat treatment
TABLE 8 Corrosion-resistant Steel Performance parameters of Q800 corrosion-resistant Steel obtained after thermal refining and Heat treatment in example 2
In this example, the corrosion rate of the steel is measured according to the specification of the salt spray corrosion test in GB/T10125-. The conventional Q800 steel in this example had the following composition: 0.088% of C, 1.81% of Mn, 0.19% of Si, 0.22% of Cr, 0.003% of S, 0.014% of P, 0.038% of Al, 0.033% of Nb, 0.18% of Ni, 0.152% of Mo, 0.012% of Ti and the balance of Fe and other unavoidable impurities. Compared with the conventional Q800 steel, the corrosion resistance of the Q800 corrosion-resistant steel prepared by the embodiment is improved by 1.56 times. The formed products of the corrosion-resistant steel comprise hydraulic supports for coal mines and engineering machinery for mines.
In the embodiment, the metallographic structure and the corrosion morphology of the prepared Q800 corrosion-resistant steel are also determined.
Fig. 4 shows the metallographic structure of the Q800 corrosion-resistant steel obtained in this example. Fig. 5 shows the macro (fig. 5a) and micro topography (fig. 5b) of the Q800 corrosion-resistant steel obtained in this example after corrosion. Fig. 6 shows the macro (fig. 6a) and micro-topography (fig. 6b) of conventional Q800 steel after corrosion.
As is clear from fig. 4, the structure of the Q800 corrosion-resistant steel produced in this example is martensite.
As can be seen from the analysis and comparison of fig. 5 to 6, compared with the conventional Q800 steel, the Q800 corrosion-resistant steel prepared in this embodiment has more and dense products after corrosion, and a corrosion product film is formed on the surface of the substrate, which hinders the further development of corrosion, and the amount of the corrosion product is less, so that the corrosion resistance is stronger.
Example 3
The Q800 corrosion-resistant steel for mine environment service provided in this example adopts a 350mm twin-roll reversible mill, has a rolling force of 1200KN, and produces Q800 corrosion-resistant steel with a thickness specification of 16mm, the specific elemental composition is shown in table 9, and the balance is Fe and unavoidable impurities.
TABLE 9 chemistry of 16mm thick Q800 corrosion resistant steel prepared in example 3
The preparation method of the Q800 corrosion-resistant steel with the chemical composition comprises the following steps:
(1) smelting and forging: according to the design components in table 9, the alloy raw material is smelted by using a vacuum smelting induction furnace, and a square billet with the width of 80mm multiplied by 100mm is forged after smelting, so that the internal defects of the metal are reduced, and the performance is improved; wherein the smelting end point temperature is controlled to be 1640-1680 ℃; the final forging temperature is controlled to be 800-850 ℃.
(2) Rolling:
firstly, heating a square billet obtained after forging in the step (1), controlling the heating temperature at 1200 ℃, and preserving heat for 120 min; and then, rolling the heated square billet by adopting a high-temperature slow-speed high-pressure technology to produce a 16mm thin steel plate. Wherein the total pressure reduction rate is 84%.
In the rolling process, in order to avoid occurrence of core segregation and influence on the strength and toughness of the corrosion-resistant steel, the embodiment adopts a two-stage rolling method, wherein the reduction rate of one-stage rolling (i.e., rough rolling) is 60%, the deformation rate is not less than 60%, the total deformation rate of the two-stage rolling (i.e., finish rolling or II stage) is not less than 50%, and the overall compression ratio is 6.25 times. In order to improve the ductility and toughness of the corrosion-resistant steel, the tensile strength needs to be increased, so that the temperature of the two-stage finish rolling is controlled to be 820-870 ℃.
In this embodiment, the parameters of a part of controlled rolling and controlled cooling processes are shown in table 10 (wherein, the intermediate slab refers to a steel slab obtained after rough rolling), the parameters of a salt spray corrosion test are shown in table 11, and the performance parameters of the obtained corrosion-resistant steel are shown in table 12.
TABLE 10 controlled Rolling and Cooling Process parameters for Q800 Corrosion resistant Steel prepared in example 3
(3) Thermal treatment for hardening and tempering
And (3) carrying out on-line quenching and tempering treatment on the rolled steel billet to obtain the final Q800 corrosion-resistant steel.
And (3) on-line quenching after rolling: and heating the steel obtained in the rolling step to 900 ℃, preserving heat for 65min for austenitizing, and then cooling the steel to room temperature by water so that the steel can obtain a martensite structure after quenching and has higher strength.
Tempering treatment: and heating the quenched steel to 600 ℃, preserving the heat for 85min, and then cooling the steel to room temperature in air.
TABLE 11 salt spray Corrosion test parameters of Q800 Corrosion-resistant steels obtained after thermal refining treatment in example 3
TABLE 12 Corrosion-resistant Steel Performance parameters of Q800 corrosion-resistant Steel obtained after thermal refining treatment in example 3
In this example, the corrosion rate of the steel is measured according to the specification of the salt spray corrosion test in GB/T10125-. The conventional Q800 steel in this example had the following composition: 0.093% of C, 1.9% of Mn, 0.2% of Si, 0.25% of Cr, 0.003% of S, 0.018% of P, 0.039% of Al, 0.033% of Nb, 0.2% of Ni, 0.25% of Mo, 0.008% of Ti and the balance of Fe and other inevitable impurities. Compared with the conventional Q800 steel, the corrosion resistance of the Q800 corrosion-resistant steel prepared by the embodiment is improved by 1.53 times. The formed products of the corrosion-resistant steel comprise hydraulic supports for coal mines and engineering machinery for mines.
In the embodiment, the metallographic structure and the corrosion morphology of the prepared Q800 corrosion-resistant steel are also determined.
Fig. 7 shows the metallographic structure of the Q800 corrosion-resistant steel obtained in this example. Fig. 8 shows the macro (fig. 8a) and micro topography (fig. 8b) of the Q800 corrosion-resistant steel obtained in this example after corrosion. Fig. 9 shows the macro (fig. 9a) and micro-topography (fig. 9b) of conventional Q800 steel after corrosion.
As is clear from fig. 7, the structure of the Q800 corrosion-resistant steel produced in this example was martensite.
As can be seen from the analysis and comparison of fig. 8 to 9, compared with the conventional Q800 steel, the Q800 corrosion-resistant steel prepared in this embodiment has more and dense products after corrosion, and a corrosion product film is formed on the surface of the substrate, which hinders the further development of corrosion, and the amount of the corrosion product is less, so that the corrosion resistance is stronger.
The method can be realized by upper and lower limit values and interval values of intervals of process parameters (such as temperature, time and the like), and embodiments are not listed.
Finally, it should be noted that the above embodiments are only used for illustrating the technical solutions of the present invention and are not limited. Although the present invention has been described in detail with reference to the embodiments, it will be understood by those skilled in the art that various changes may be made and equivalents may be substituted without departing from the spirit and scope of the invention as defined in the appended claims.
Claims (10)
1. A Q800 corrosion resistant steel used for mine environment service is characterized in that,
the corrosion-resistant steel comprises the following chemical components in percentage by mass: 0.16 to 0.19 percent of C, 0.5 to 1.0 percent of Mn, 0.2 to 0.35 percent of Si, 1.3 to 1.7 percent of Cr, less than or equal to 0.005 percent of S, less than or equal to 0.008 percent of P, less than or equal to 0.035 percent of Al, 0.02 to 0.03 percent of Nb, 0.015 to 0.025 percent of Ni, 0.015 to 0.025 percent of Mo, 0.02 to 0.03 percent of Ti, and the balance of Fe and other inevitable impurities.
2. The Q800 corrosion resistant steel of claim 1,
the corrosion-resistant steel comprises the following chemical components in percentage by mass: 0.17 to 0.19 percent of C, 0.5 to 0.6 percent of Mn, 0.24 to 0.30 percent of Si, 1.35 to 1.45 percent of Cr, less than or equal to 0.005 percent of S, less than or equal to 0.006 percent of P, less than or equal to 0.035 percent of Al, 0.025 to 0.028 percent of Nb, 0.020 to 0.024 percent of Ni, 0.018 to 0.024 percent of Mo, 0.020 to 0.025 percent of Ti, and the balance of Fe and other inevitable impurities.
3. The Q800 corrosion resistant steel of claim 1 or 2,
the yield strength of the corrosion-resistant steel is more than or equal to 800MPa, the tensile strength is 840-1000 MPa, and the corrosion rate of the corrosion-resistant steel in service under a typical service mine environment is 0.10-0.12 mm/a.
4. A method for producing Q800 corrosion-resistant steel according to any one of claims 1 to 3,
the preparation method comprises the following steps:
1) selection of an alloy: selecting an alloy according to the chemical composition in mass percent of the Q800 corrosion resistant steel of any one of claims 1-3;
2) smelting and forging: the chemical composition requirement of the Q800 corrosion-resistant steel according to any one of claims 1-3, wherein the selected alloy is smelted by using a vacuum smelting induction furnace, and the smelted alloy is forged into a square billet;
3) rolling: heating and preserving the heat of the forged square billet at 1180-1230 ℃, and then rolling the heated square billet by adopting a high-temperature slow-speed high-pressure technology to obtain a billet;
4) quenching and tempering heat treatment: and carrying out on-line quenching and tempering treatment on the rolled steel billet.
5. The production method according to claim 4,
in the rolling step, the high-temperature slow-speed large-reduction technology comprises the following steps: rolling at 1180-1230 ℃ with total rolling reduction rate of 84-90% and strain rate of 0.2-2.0 s-1Controlling the finish rolling temperature to be 820-870 ℃;
preferably, the square billet is heated and insulated at 1180-1230 ℃ for 120-150 min.
6. The production method according to any one of claims 4 to 5,
the rolling comprises rough rolling and finish rolling;
preferably, in the rough rolling process, the rough rolling reduction rate is 60-70%, and the rough rolling deformation rate is more than or equal to 60%;
preferably, in the finish rolling process, the finish rolling reduction rate is 50-60%, and the total finish rolling deformation rate is more than or equal to 50%;
preferably, in the rolling step, the overall reduction ratio is >6 times.
7. The production method according to any one of claims 4 to 6,
and immediately after the rolling step, carrying out on-line quenching after rolling in the quenching and tempering heat treatment step.
8. The production method according to any one of claims 4 to 7,
in the step of quenching and tempering heat treatment, the on-line quenching after rolling is to heat the steel obtained in the step of rolling to 890-910 ℃, preserve heat for 60-70 min to austenitize, and then cool the steel to room temperature;
preferably, in the step of quenching and tempering heat treatment, the tempering treatment is to heat the steel obtained after quenching to 590-610 ℃, preserve heat for 80-90 min, and then air-cool the steel to room temperature.
9. The production method according to any one of claims 4 to 8,
in the smelting and forging steps, the smelting end point temperature is controlled to be 1640-1680 ℃, and the finish forging temperature is controlled to be 800-850 ℃;
preferably, the thickness of the square billet is 60 mm-100 mm.
10. The production method according to any one of claims 4 to 9,
the Q800 corrosion-resistant steel is a plate with the thickness of 10-16 mm.
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| CN104662193A (en) * | 2012-09-19 | 2015-05-27 | 杰富意钢铁株式会社 | Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance |
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| CN112639146A (en) * | 2018-08-31 | 2021-04-09 | 杰富意钢铁株式会社 | High-strength steel sheet and method for producing same |
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| JPS5822323A (en) * | 1981-07-31 | 1983-02-09 | Agency Of Ind Science & Technol | Manufacture for corrosion resisting steel |
| CN104662193A (en) * | 2012-09-19 | 2015-05-27 | 杰富意钢铁株式会社 | Wear-resistant steel plate having excellent low-temperature toughness and corrosion wear resistance |
| CN112639146A (en) * | 2018-08-31 | 2021-04-09 | 杰富意钢铁株式会社 | High-strength steel sheet and method for producing same |
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Application publication date: 20210810 |