CN111850419A - High-manganese austenitic steel and preparation method thereof - Google Patents
High-manganese austenitic steel and preparation method thereof Download PDFInfo
- Publication number
- CN111850419A CN111850419A CN202010757974.XA CN202010757974A CN111850419A CN 111850419 A CN111850419 A CN 111850419A CN 202010757974 A CN202010757974 A CN 202010757974A CN 111850419 A CN111850419 A CN 111850419A
- Authority
- CN
- China
- Prior art keywords
- austenitic steel
- steel
- manganese austenitic
- alloy
- high manganese
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Images
Classifications
-
- 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
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
-
- 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
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
-
- 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
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides high manganese austenitic steel and a preparation method thereof, and belongs to the technical field of metal materials. The high-manganese austenitic steel provided by the invention comprises the following components in percentage by mass: mn: 25-27%, Al: 8-12%, C: 1.2-1.4%, Nb: 0.05-0.1% and the balance Fe. The invention can reduce the density of steel and improve the austenite by adjusting the dosage of Al, C and MnStability and recovery power, and simultaneously plays a role in solid solution strengthening, and the strength and the wear resistance of the steel are improved; nb element reduces the net carbide in the cast structure, refines austenite grains and improves the yield strength. The results of the examples show that the high manganese austenitic steel provided by the invention has a density of about 6.62g/cm3Compared with pure iron, the alloy has the advantages of 15.13 percent reduction, elastic modulus of more than or equal to 142GPa, yield strength of more than 1020MPa and tensile strength of more than 1150 MPa.
Description
Technical Field
The invention relates to the technical field of metal materials, in particular to high-manganese austenitic steel and a preparation method thereof.
Background
Steel is widely used in various industries, and with the development of science and technology, the requirements of people on the performance of steel are increasingly increased, wherein one of the most concerned focuses at present is the problem of light weight. From the viewpoint of material selection, there are two main approaches to achieving light weight: firstly, light materials are used, such as low-density aluminum and aluminum alloy, magnesium and magnesium alloy, engineering plastics or carbon fiber composite materials and the like, and mainly aluminum alloy is used; and secondly, the high-strength steel is used for replacing common steel to reduce the thickness specification of the steel plate. Due to the factors of high cost, complex process, poor welding performance and the like of the aluminum alloy, the application prospect of the aluminum alloy is restricted; meanwhile, the use requirement cannot be completely met by reducing the thickness of the steel plate. One of the more potential ideas is: the steel plate integrating low density and high strength is developed.
In recent years, a novel system Fe-Mn-Al-C steel has been developed, and has the characteristics of excellent strength and toughness, low density and the like. Light weight Fe-Mn-Al-C steels can be divided into four categories: ferritic steel, ferritic-based dual-phase steel, austenitic-based dual-phase steel, and austenitic steel. Austenitic steels are most promising in terms of properties and processing. The prior art is as follows: influence of solution treatment on the structure and mechanical properties of light-weight high-manganese steel (Lijunpeng, Duxin, Torreya, Zhang Yan)The high manganese steel of 10.31Al-14.85Mn-0.78C-4.93Ni-0.83Cu prepared by Zhang, Zhang Zhongwu, 2018,43(07):109-114, and Metal Heat treatment) has the elastic modulus of 142GPa, the yield strength of 506.91MPa, the tensile strength of 834.50MPa and lower yield strength and tensile strength; and the yield strength and tensile strength of the Fe-Mn-Al-C steel prepared by the research on the tissue properties of the Fe-Mn-Al-C low-density high-strength steel (Zhao super, Song ren Bo, Zhang Lei Feng, Yang Fuqiang, Beijing institute of science and engineering, Beijing university of science and technology, Beijing 100083) are higher, but the density is 6.8g/cm3Still higher, the requirements of social development on novel system Fe-Mn-Al-C steel can not be met gradually.
With the great demand potential of Fe-Mn-Al-C steel in the market, the improvement of the obdurability and the reduction of the density of the Fe-Mn-Al-C steel become one of the key directions of research, development and application.
Disclosure of Invention
The high manganese austenitic steel provided by the invention has low density and high toughness, and can be applied to the fields of automobiles, ocean engineering, metallurgy, chemical engineering, light industry and the like.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides high-manganese austenitic steel which comprises the following components in percentage by mass: mn: 25-27%, Al: 8-12%, C: 1.2-1.4%, Nb: 0.05-0.1% and the balance Fe.
Preferably, the method comprises the following steps of: mn: 26%, Al: 10%, C: 1.4%, Nb: 0.1% and the balance Fe.
Preferably, the method comprises the following steps of: mn: 25%, Al: 10%, C: 1.4%, Nb: 0.05% and the balance Fe.
Preferably, the method comprises the following steps of: mn: 27%, Al: 10%, C: 1.2%, Nb: 0.1% and the balance Fe.
The invention provides a preparation method of high-manganese austenitic steel, which comprises the following steps:
(1) mixing alloy raw materials and then smelting to obtain an alloy ingot;
(2) carrying out hot rolling on the alloy ingot obtained in the step (1) to obtain an alloy plate;
(3) and (3) sequentially carrying out solid solution treatment and aging treatment on the alloy plate obtained in the step (2) to obtain the high manganese austenitic steel.
Preferably, the smelting temperature in the step (1) is 1700-2000 ℃.
Preferably, the temperature of the hot rolling in the step (2) is 1000 ℃ to 1050 ℃,
preferably, the total deformation amount of the hot rolling in the step (2) is 65% to 70%.
Preferably, the temperature of the solution treatment in the step (3) is 1000-1050 ℃, and the time of the solution treatment is 100-150 minutes.
Preferably, the temperature of the aging treatment in the step (3) is 500-700 ℃, and the time of the aging treatment is 7-9 h.
The invention provides high-manganese austenitic steel which comprises the following components in percentage by mass: mn: 25-27%, Al: 8-12%, C: 1.2-1.4%, Nb: 0.05-0.1% and the balance Fe. According to the invention, Al with higher content is added into the steel, the Al is utilized to reduce the average molar mass of the high-manganese austenitic steel, and the molar volume of the steel is increased, so that the density of the steel is reduced; the content of C element is improved, the stability of austenite in steel and the recovery power of austenite are improved, the austenite phase region is enlarged, and meanwhile, the steel has the function of interstitial solid solution strengthening and can improve the strength and the wear resistance of the steel; the Mn element has the solid solution strengthening effect, the dosage of the Mn element is increased, the austenite phase region can be expanded, the content of residual austenite at room temperature and the stacking fault energy of the alloy are increased, and the Ms point is reduced; a small amount of Nb element can reduce the net carbide in the cast structure, refine austenite grains, strengthen the high manganese steel and greatly improve the yield strength; the elements can also play a synergistic role in reducing the density of the steel. The results of the examples show that the high manganese austenitic steel provided by the invention has a density of about 6.62g/cm3The alloy is reduced by 15.13 percent compared with pure iron, the elastic modulus is more than or equal to 142GPa, the yield strength is more than 1020MPa, and the tensile strength is more than 1150MPa。
Drawings
FIG. 1 is a schematic representation of a tensile specimen cut from a high manganese austenitic steel prepared in examples 1 to 3 of the present invention;
FIG. 2 is a metallographic optical micrograph of a high manganese austenitic steel obtained in example 1 according to the present invention;
FIG. 3 is a metallographic optical micrograph of a high manganese austenitic steel obtained in example 2 according to the invention;
FIG. 4 is a metallographic optical micrograph of a high manganese austenitic steel obtained according to example 3 of the present invention.
Detailed Description
The invention provides high-manganese austenitic steel which comprises the following components in percentage by mass: mn: 25-27%, Al: 8-12%, C: 1.2-1.4%, Nb: 0.05-0.1% and the balance Fe.
According to the mass percentage, the high-manganese austenitic steel provided by the invention comprises 25-27% of Mn, and preferably 26%. According to the invention, the use amount of Mn element is controlled within the above range, so that the solid solution strengthening effect is achieved, the use amount of Mn element is increased from conventional 10-14% to 25-27%, the austenite phase region is enlarged, the content of retained austenite at room temperature and the stacking fault energy of the alloy are increased, and the Ms point is reduced.
According to the mass percentage, the high-manganese austenitic steel provided by the invention comprises 8-12% of Al, preferably 9-11%, and more preferably 10%. The invention controls the dosage of Al element in the range, can reduce the average molar mass of the high manganese austenitic steel, and simultaneously increases the molar volume of the steel, thereby reducing the density of the steel.
According to the mass percentage, the high-manganese austenitic steel provided by the invention comprises 1.2-1.4% of C, and preferably 1.3%. The invention controls the dosage of the C element in the range, improves the stability of austenite in the steel and the recovery power of the austenite, enlarges the austenite phase region, has the function of interstitial solid solution strengthening, and can improve the strength and the wear resistance of the steel.
According to the mass percentage, the high manganese austenitic steel provided by the invention comprises 0.05-0.1% of Nb, and preferably 0.07%. The invention controls the dosage of the Nb element in the range, reduces the net carbide in the cast structure, refines austenite grains, strengthens high manganese steel and greatly improves the yield strength.
The invention limits the dosage of each element in the high manganese austenitic steel, so that the elements play a synergistic effect, and the density of the steel is reduced.
The invention also provides a preparation method of the high-manganese austenitic steel, which comprises the following steps:
(1) mixing alloy raw materials and then smelting to obtain an alloy ingot;
(2) carrying out hot rolling on the alloy ingot obtained in the step (1) to obtain an alloy plate;
(3) and (3) sequentially carrying out solid solution treatment and aging treatment on the alloy plate obtained in the step (2) to obtain the high manganese austenitic steel.
The alloy raw materials are mixed and smelted to obtain the alloy ingot.
The present invention is not particularly limited in the kind of the alloy raw materials, and raw materials capable of providing the above-mentioned alloy elements, which are well known to those skilled in the art, may be used. In the present invention, the alloy raw material is preferably carbon, electrolytic manganese flakes, niobium wires, aluminum blocks and iron blocks, and more preferably carbon, electrolytic manganese flakes, niobium wires, pure aluminum and industrially pure iron. The source of the alloy raw material is not particularly limited in the present invention, and commercially available products known to those skilled in the art may be used. The raw materials are used for preparing the alloy ingot, so that the content of impurities in the alloy ingot can be reduced, and the performance of the high-manganese austenitic steel is improved.
Before the alloy raw materials are mixed, the method preferably further comprises the steps of mixing the electrolytic manganese sheet, the niobium wire, the aluminum block and the iron block with absolute ethyl alcohol respectively, then putting the mixture into an ultrasonic cleaning instrument for cleaning, and taking out and wiping the mixture. The process can remove dust on the surface of the raw material and reduce the content of impurities in the high-manganese austenitic steel.
The smelting equipment is not particularly limited in the present invention, and smelting equipment known to those skilled in the art can be used. In the present invention, the melting equipment is preferably a non-consumable vacuum arc melting furnace.
The invention preferably uses sand paper to polish the inner wall of a water-cooled copper crucible in a non-consumable vacuum arc melting furnace, then uses absolute ethyl alcohol to clean the inner wall, and then puts the mixed alloy raw materials into the water-cooled copper crucible for melting. The process can avoid the influence of other impurities on the inner wall of the water-cooled copper crucible on the performance of the high manganese austenitic steel.
In the present invention, the melting is preferably performed under a protective atmosphere. The invention preferably vacuumizes the non-consumable vacuum arc melting furnace and then fills the protective gas. In the present invention, the degree of vacuum is preferably ≦ 8 × 10-3Pa, more preferably < 8X 10-3Pa. In the present invention, the shielding gas is preferably high-purity helium or high-purity argon, and more preferably high-purity argon. According to the invention, by filling the protective gas, the phenomenon that the performance of the high-manganese austenitic steel is influenced by the reaction of metal elements and impurity elements such as oxygen in the gas in the smelting process can be avoided.
In the invention, the smelting temperature is preferably 1700-2000 ℃, and more preferably 1800 ℃; the number of times of smelting is preferably 3-7 times, and more preferably 5 times. In the present invention, the time for the melting is not particularly limited, and may be set according to the common knowledge in the art. In the present invention, after each melting, it is preferable to further include turning the ingot. The invention can make the components in the steel uniformly distributed through a plurality of times of smelting and turning treatment.
After the alloy ingot is obtained, the alloy ingot is hot-rolled to obtain an alloy plate.
According to the invention, the alloy ingot is preferably heated to a rolling temperature, then is subjected to heat preservation, and then is subjected to hot rolling. In the invention, the heating rate is preferably 5-15 ℃/min, and more preferably 10 ℃/min; the rolling temperature is preferably 1000-1050 ℃; the heat preservation time is preferably 0.5-1 hour. According to the invention, the alloy ingot is heated and insulated, so that the temperature inside and outside the alloy is consistent, and the rolling effect is ensured.
The equipment used in the heating process is not particularly limited in the present invention, and heating equipment known to those skilled in the art may be used. In the present invention, the heating apparatus is preferably a muffle furnace.
The equipment used in the hot rolling process is not particularly limited in the present invention, and hot rolling equipment known to those skilled in the art may be used. In the present invention, the hot rolling apparatus is preferably a two-roll mill.
In the present invention, the hot rolling is preferably a multi-pass rolling deformation. In the invention, the single-pass deformation of the hot rolling is preferably 10-20%, and more preferably 13-17%; the total pass deformation of the hot rolling is preferably 65-70%, and more preferably 66-69%.
According to the invention, preferably, after each pass of rolling, the product of the pass of rolling is heated to the rolling temperature, the temperature is kept for 5 minutes, then the next pass of rolling is carried out, and after the final rolling, the product of the final rolling is heated to the rolling temperature and the temperature is kept for 1 minute. According to the invention, the hot rolling process is limited in the range, so that the coarse grains in the casting state can be crushed, the cracks are obviously healed, the casting defects are eliminated, the as-cast structure is converted into the deformed structure, and the processing performance of the alloy is improved.
After the hot rolling is finished, the present invention preferably cools the hot rolled product to obtain an alloy sheet. In the present invention, the cooling is preferably water cooling; the end temperature of the cooling is preferably room temperature.
After the alloy plate is obtained, the alloy plate is sequentially subjected to solid solution treatment and aging treatment to obtain the high manganese austenitic steel.
In the invention, the temperature of the solution treatment is preferably 1000-1050 ℃; the time for the solution treatment is preferably 100 to 150 minutes, and more preferably 120 minutes. The invention can fully dissolve various phases in the alloy through solution treatment, strengthen solid solution, improve toughness and corrosion resistance, eliminate stress and soften, and improve the performance of the alloy.
In the present invention, the heating rate to the solution treatment temperature is not particularly limited, and may be set according to the common knowledge in the art.
After the solution treatment is completed, the present invention preferably further comprises cooling the solution-treated product. In the present invention, the cooling is preferably water cooling; the end temperature of the cooling is preferably room temperature.
In the invention, the temperature of the aging treatment is preferably 500-700 ℃, and more preferably 600 ℃; the time of the aging treatment is preferably 7-9 h, and more preferably 8 h. The invention limits the aging treatment parameters within the range to ensure that Nb is in the range4C3And the hard point compounds are dispersed and precipitated on the austenite matrix so as to improve the hardness, strength and wear resistance of the high-manganese austenitic steel.
The heating rate of heating to the aging treatment temperature in the present invention is not particularly limited, and may be set according to the common knowledge in the art.
After the aging treatment is finished, the invention preferably further comprises cooling treatment of the aging treated product. In the present invention, the cooling is preferably water cooling; the end temperature of the cooling is preferably room temperature.
The equipment required by the solution treatment and the aging treatment is not particularly limited, and the equipment commonly used in the field can be adopted. In the present invention, the equipment required for the solution treatment and the aging treatment is preferably a muffle furnace.
After the cooling treatment is finished, the invention preferably further comprises the step of sequentially polishing and cleaning the cooled product to obtain the high-manganese austenitic steel. The specific operation of the polishing and cleaning is not particularly limited, and the polishing and cleaning process commonly used in the field can be adopted.
The high manganese austenitic steel is prepared by adopting the method of fusion casting, hot rolling, solid solution and aging treatment, more Nb elements can be dissolved into austenite through high-temperature austenitizing quenching in Nb-containing alloy structural steel, and Nb can be dissolved into austenite4C3Or Nb (CN) precipitates to promote precipitation hardening, and dispersion precipitates to promote dispersion strengthening; adopting solid solution and aging treatment to lead Nb to be4C3The hard point compounds are dispersed and precipitated on the austenite matrix so as to improve the wear resistance of the austenite matrix; meanwhile, the preparation process is simple, the cost is low, and the method is suitable for industrial large-scale production.
The technical solution of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. 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.
Example 1
The high-manganese austenitic steel comprises the following components in percentage by mass: mn: 25%, Al: 10%, C: 1.4%, Nb: 0.05% and the balance Fe.
The preparation method of the high manganese austenitic steel comprises the following steps:
(1) soaking 87.492g of industrial pure iron, 34.664g of electrolytic manganese, 13.865g of pure aluminum and 0.069g of niobium wire in an absolute ethyl alcohol beaker, putting the beaker into an ultrasonic cleaning instrument for cleaning, adding 1.941g of carbon, sequentially putting carbon, electrolytic manganese sheets, the niobium wire, an aluminum block and the industrial pure iron into a water-cooled copper crucible of a non-consumable vacuum arc melting furnace, wherein the vacuum degree in the furnace cavity needs to reach 8 multiplied by 10- 3Introducing high-purity argon as a protective gas under Pa, then smelting, turning the ingot after each smelting, and repeatedly smelting and turning the ingot to obtain an alloy ingot with the thickness of 14.7 mm;
(2) heating the alloy cast ingot to 1000 ℃, preserving heat for 0.5 hour, then rolling, wherein the single-pass deformation is 13.6%, placing the alloy cast ingot into a muffle furnace after each pass of rolling, preserving heat for 5 minutes at 1000 ℃, finally rolling the alloy cast ingot into an alloy plate with the thickness of 5mm, wherein the final deformation reaches 66%, reheating to 1000 ℃ after the final pass of rolling, preserving heat for 1 minute, and then rapidly quenching in room-temperature water to obtain the alloy plate;
(3) putting the alloy plate into a muffle furnace heated to 1000 ℃, preserving heat for 120min, carrying out solution treatment, then quickly putting the alloy plate into room-temperature water for quenching treatment, taking out the alloy plate after the alloy plate is completely cooled, putting the alloy plate subjected to solution treatment into the muffle furnace, heating to 600 ℃, preserving heat for 8h, carrying out aging treatment, taking out the alloy plate from the muffle furnace after the aging time is reached, cooling the alloy plate to room temperature by water, and sequentially polishing and cleaning the surface of the treated alloy plate to obtain the high-manganese austenitic steel.
Cutting the obtained high manganese austenitic steel into a tensile sample shown in figure 1 by linear cutting, and performing a tensile test to obtain data related to mechanical properties;
cutting the obtained high manganese austenitic steel into metallographic test samples with the size of 5mm multiplied by 8mm multiplied by 2mm by wire cutting, sealing other non-test surfaces in a metallographic test mosaic machine (XQ-1, Shanghai metallographical mechanical equipment limited), grinding the test surfaces with 150#, 400#, 800#, 1200#, 2000#, 3000# abrasive paper after being taken out, washing surface dirt, polishing, cleaning and drying the surfaces, and carrying out corrosion in a nitric acid alcohol solution environment with the concentration of 10% by taking GB/T10125 one-year 1997 as an experimental basis, thereby obtaining the related data of the metallographic test samples.
As shown in FIG. 2, the austenitic steel prepared in this example consists of fine equiaxed austenite grains with a grain size of 22 μm, and the subsequent aging treatment results in the precipitation of strengthening phases and the mechanical properties are greatly improved.
Example 2
The high-manganese austenitic steel comprises the following components in percentage by mass: mn: 26%, Al: 10%, C: 1.4%, Nb: 0.1% and the balance Fe.
The preparation method of the high manganese austenitic steel comprises the following steps:
(1) soaking 88.046g of industrial pure iron, 36.628g of electrolytic manganese, 14.088g of pure aluminum and 0.141g of niobium wire in an absolute ethyl alcohol beaker, putting the beaker into an ultrasonic cleaning instrument for cleaning, then adding 1.972g of carbon, sequentially putting carbon, electrolytic manganese sheets, the niobium wire, an aluminum block and the industrial pure iron into a water-cooled copper crucible of a non-consumable vacuum arc melting furnace, wherein the vacuum degree in the furnace cavity needs to reach 8 multiplied by 10- 3Introducing high-purity argon as a protective gas under Pa, then smelting, turning the ingot after each smelting, and repeatedly smelting and turning the ingot to obtain an alloy ingot with the thickness of 14.7 mm;
(2) heating the alloy cast ingot to 1000 ℃, preserving heat for 0.5 hour, then rolling, wherein the single-pass deformation is 13.6%, placing the alloy cast ingot into a muffle furnace after each pass of rolling, preserving heat for 5 minutes at 1000 ℃, finally rolling the alloy cast ingot into an alloy plate with the thickness of 5mm, wherein the final deformation reaches 66%, reheating to 1000 ℃ after the final pass of rolling, preserving heat for 1 minute, and then rapidly quenching in room-temperature water to obtain the alloy plate;
(3) putting the alloy plate into a muffle furnace heated to 1000 ℃, preserving heat for 120min, carrying out solution treatment, then quickly putting the alloy plate into room-temperature water for quenching treatment, taking out the alloy plate after the alloy plate is completely cooled, putting the alloy plate subjected to solution treatment into the muffle furnace, heating to 600 ℃, preserving heat for 8h, carrying out aging treatment, taking out the alloy plate from the muffle furnace after the aging time is reached, cooling the alloy plate to room temperature by water, and sequentially polishing and cleaning the surface of the treated alloy plate to obtain the high-manganese austenitic steel.
Cutting the obtained high manganese austenitic steel into a tensile sample shown in figure 1 by linear cutting, and performing a tensile test to obtain data related to mechanical properties;
cutting the obtained high manganese austenitic steel into metallographic test samples with the size of 5mm multiplied by 8mm multiplied by 2mm by wire cutting, sealing other non-test surfaces in a metallographic test mosaic machine (XQ-1, Shanghai metallographical mechanical equipment limited), grinding the test surfaces with 150#, 400#, 800#, 1200#, 2000#, 3000# abrasive paper after being taken out, washing surface dirt, polishing, cleaning and drying the surfaces, and carrying out corrosion in a nitric acid alcohol solution environment with the concentration of 10% by taking GB/T10125 one-year 1997 as an experimental basis, thereby obtaining the related data of the metallographic test samples.
As shown in FIG. 3, the austenitic steel prepared in this example consists of fine equiaxed austenite grains with a grain size of 18 μm, and the subsequent aging treatment results in the precipitation of strengthening phases and a substantial improvement in mechanical properties.
Example 3
The high-manganese austenitic steel comprises the following components in percentage by mass: mn: 27%, Al: 10%, C: 1.2%, Nb: 0.05% and the balance Fe.
The preparation method of the high manganese austenitic steel comprises the following steps:
(1) get worker88.633g of pure iron, 38.786g of electrolytic manganese, 13.3652g of pure aluminum and 0.144g of niobium wire are immersed in an absolute ethyl alcohol beaker, the beaker is put into an ultrasonic cleaner for cleaning, 1.724g of carbon is added, the carbon, the electrolytic manganese sheet, the niobium wire, the aluminum block and the industrial pure iron are sequentially put into a water-cooled copper crucible of a non-consumable vacuum arc melting furnace, and the vacuum degree in the furnace cavity needs to reach 8 multiplied by 10-3Introducing high-purity argon as a protective gas under Pa, then smelting, turning the ingot after each smelting, and repeatedly smelting and turning the ingot to obtain an alloy ingot with the thickness of 14.7 mm;
(2) heating the alloy cast ingot to 1000 ℃, preserving heat for 0.5 hour, then rolling, wherein the single-pass deformation is 13.6%, placing the alloy cast ingot into a muffle furnace after each pass of rolling, preserving heat for 5 minutes at 1000 ℃, finally rolling the alloy cast ingot into an alloy plate with the thickness of 5mm, wherein the final deformation reaches 66%, reheating to 1000 ℃ after the final pass of rolling, preserving heat for 1 minute, and then rapidly quenching in room-temperature water to obtain the alloy plate;
(3) putting the alloy plate into a muffle furnace heated to 1000 ℃, preserving heat for 120min, carrying out solution treatment, then quickly putting the alloy plate into room-temperature water for quenching treatment, taking out the alloy plate after the alloy plate is completely cooled, putting the alloy plate subjected to solution treatment into the muffle furnace, heating to 600 ℃, preserving heat for 8h, carrying out aging treatment, taking out the alloy plate from the muffle furnace after the aging time is reached, cooling the alloy plate to room temperature by water, and sequentially polishing and cleaning the surface of the treated alloy plate to obtain the high-manganese austenitic steel.
Cutting the obtained high manganese austenitic steel into a tensile sample shown in figure 1 by linear cutting, and performing a tensile test to obtain data related to mechanical properties;
cutting the obtained high manganese austenitic steel into metallographic test samples with the size of 5mm multiplied by 8mm multiplied by 2mm by wire cutting, sealing other non-test surfaces in a metallographic test mosaic machine (XQ-1, Shanghai metallographical mechanical equipment limited), grinding the test surfaces with 150#, 400#, 800#, 1200#, 2000#, 3000# abrasive paper after being taken out, washing surface dirt, polishing, cleaning and drying the surfaces, and carrying out corrosion in a nitric acid alcohol solution environment with the concentration of 10% by taking GB/T10125 one-year 1997 as an experimental basis, thereby obtaining the related data of the metallographic test samples.
As shown in FIG. 3, the austenitic steel prepared in this example consists of fine equiaxed austenite grains with a grain size of 20 μm, and the subsequent aging treatment results in the precipitation of strengthening phases and a substantial improvement in mechanical properties.
Comparative example 1
10.31Al-14.85Mn-0.78C-4.93Ni-0.83Cu high manganese steel prepared in Lijunpeng, Duxin, Jutsu, Zhang Zhongwu, 2018,43(07):109-114, heat treatment of metals).
Comparative example 2
Fe-10.4Mn-9.7Al-0.7C steel prepared in research on texture properties of Fe-Mn-Al-C low-density high-strength steel (Zhao super, Song ren Bo, Zhang Lei Feng, Yang Fuqiang, Beijing institute of science and engineering, Beijing technology university, Beijing 100083).
TABLE 1 results of the Performance test of the high manganese austenitic steels obtained in examples 1 to 3 and comparative examples 1 to 2
As can be seen from Table 1, the high manganese austenitic steel prepared by the invention has the elastic modulus of more than or equal to 142GPa, the yield strength of more than 1020MPa and the tensile strength of more than 1150MPa, the performance of the high manganese austenitic steel is higher than that of the high manganese austenitic steel prepared by the prior art (comparative example 1 and comparative example 2), and the density of the high manganese austenitic steel prepared by the invention is less than or equal to 6.62g/cm3Comparative example 2 the high manganese austenitic steel prepared has a density of 6.8g/cm3It can be seen that the high manganese austenitic steel prepared by the method has lower density and wider application prospect.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (10)
1. A high manganese austenitic steel comprises the following components by mass percent: mn: 25-27%, Al: 8-12%, C: 1.2-1.4%, Nb: 0.05-0.1% and the balance Fe.
2. The high manganese austenitic steel of claim 1, comprising, in mass percent: mn: 26%, Al: 10%, C: 1.4%, Nb: 0.1% and the balance Fe.
3. The high manganese austenitic steel of claim 1, comprising, in mass percent: mn: 25%, Al: 10%, C: 1.4%, Nb: 0.05% and the balance Fe.
4. The high manganese austenitic steel of claim 1, comprising, in mass percent: mn: 27%, Al: 10%, C: 1.2%, Nb: 0.1% and the balance Fe.
5. A method of producing the high manganese austenitic steel of any of claims 1 to 4, comprising the steps of:
(1) mixing alloy raw materials and then smelting to obtain an alloy ingot;
(2) carrying out hot rolling on the alloy ingot obtained in the step (1) to obtain an alloy plate;
(3) and (3) sequentially carrying out solid solution treatment and aging treatment on the alloy plate obtained in the step (2) to obtain the high manganese austenitic steel.
6. The preparation method according to claim 5, wherein the temperature of the smelting in the step (1) is 1700-2000 ℃.
7. The production method according to claim 5, wherein the temperature of the hot rolling in the step (2) is 1000 ℃ to 1050 ℃.
8. The production method according to claim 5 or 7, wherein the total deformation amount of the hot rolling in the step (2) is 65% to 70%.
9. The production method according to claim 5, wherein the temperature of the solution treatment in the step (3) is 1000 to 1050 ℃ and the time of the solution treatment is 100 to 150 minutes.
10. The preparation method according to claim 5, wherein the temperature of the aging treatment in the step (3) is 500-700 ℃, and the time of the aging treatment is 7-9 h.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010757974.XA CN111850419A (en) | 2020-07-31 | 2020-07-31 | High-manganese austenitic steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010757974.XA CN111850419A (en) | 2020-07-31 | 2020-07-31 | High-manganese austenitic steel and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN111850419A true CN111850419A (en) | 2020-10-30 |
Family
ID=72953442
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010757974.XA Pending CN111850419A (en) | 2020-07-31 | 2020-07-31 | High-manganese austenitic steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111850419A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113737104A (en) * | 2021-09-07 | 2021-12-03 | 燕山大学 | High-aluminum weathering steel and preparation method thereof |
| CN114703429A (en) * | 2022-04-12 | 2022-07-05 | 燕山大学 | Fe-Mn-Al-C series austenitic light steel and preparation method thereof |
| CN114774806A (en) * | 2022-04-25 | 2022-07-22 | 燕山大学 | High-strength and high-toughness light steel plate and preparation method and application thereof |
| CN114807772A (en) * | 2022-04-29 | 2022-07-29 | 燕山大学 | Aging-strengthened high-strength high-toughness light steel and manufacturing method thereof |
| CN114892084A (en) * | 2022-04-29 | 2022-08-12 | 燕山大学 | High-strength austenitic light steel with high impact toughness and manufacturing method thereof |
| CN116426836A (en) * | 2023-05-16 | 2023-07-14 | 燕山大学 | Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006176843A (en) * | 2004-12-22 | 2006-07-06 | Nippon Steel Corp | High-strength and low-density steel sheet superior in ductility and manufacturing method therefor |
| CN101432456A (en) * | 2006-12-27 | 2009-05-13 | Posco公司 | High manganese high strength steel sheets with excellent crashworthiness, and method for manufacturing of it |
| WO2009084792A1 (en) * | 2007-12-28 | 2009-07-09 | Posco | High manganese steel having high strength and excellent delayed fracture resistance and manufacturing method thereof |
| CN103328120A (en) * | 2011-01-11 | 2013-09-25 | 蒂森克虏伯钢铁欧洲股份公司 | Method for producing a hot-rolled flat steel product |
| CN106244927A (en) * | 2016-09-30 | 2016-12-21 | 北京理工大学 | A kind of low-density unimach and preparation method thereof |
| CN107937834A (en) * | 2016-10-12 | 2018-04-20 | 现代自动车株式会社 | Potassium steel |
| US10480053B2 (en) * | 2014-11-27 | 2019-11-19 | Korea Institute Of Machinery And Materials | Austenitic light-weight high-strength steel with excellent properties of welds, and method of manufacturing the same |
| CN110607480A (en) * | 2019-08-02 | 2019-12-24 | 华北理工大学 | Nb-containing high-strength high-toughness low-density steel for automobile and preparation method thereof |
-
2020
- 2020-07-31 CN CN202010757974.XA patent/CN111850419A/en active Pending
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006176843A (en) * | 2004-12-22 | 2006-07-06 | Nippon Steel Corp | High-strength and low-density steel sheet superior in ductility and manufacturing method therefor |
| JP4464811B2 (en) * | 2004-12-22 | 2010-05-19 | 新日本製鐵株式会社 | Manufacturing method of high strength and low specific gravity steel sheet with excellent ductility |
| CN101432456A (en) * | 2006-12-27 | 2009-05-13 | Posco公司 | High manganese high strength steel sheets with excellent crashworthiness, and method for manufacturing of it |
| WO2009084792A1 (en) * | 2007-12-28 | 2009-07-09 | Posco | High manganese steel having high strength and excellent delayed fracture resistance and manufacturing method thereof |
| CN103328120A (en) * | 2011-01-11 | 2013-09-25 | 蒂森克虏伯钢铁欧洲股份公司 | Method for producing a hot-rolled flat steel product |
| US10480053B2 (en) * | 2014-11-27 | 2019-11-19 | Korea Institute Of Machinery And Materials | Austenitic light-weight high-strength steel with excellent properties of welds, and method of manufacturing the same |
| CN106244927A (en) * | 2016-09-30 | 2016-12-21 | 北京理工大学 | A kind of low-density unimach and preparation method thereof |
| CN107937834A (en) * | 2016-10-12 | 2018-04-20 | 现代自动车株式会社 | Potassium steel |
| CN110607480A (en) * | 2019-08-02 | 2019-12-24 | 华北理工大学 | Nb-containing high-strength high-toughness low-density steel for automobile and preparation method thereof |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113737104A (en) * | 2021-09-07 | 2021-12-03 | 燕山大学 | High-aluminum weathering steel and preparation method thereof |
| CN114703429A (en) * | 2022-04-12 | 2022-07-05 | 燕山大学 | Fe-Mn-Al-C series austenitic light steel and preparation method thereof |
| CN114703429B (en) * | 2022-04-12 | 2022-09-23 | 燕山大学 | Fe-Mn-Al-C series austenitic light steel and preparation method thereof |
| CN114774806A (en) * | 2022-04-25 | 2022-07-22 | 燕山大学 | High-strength and high-toughness light steel plate and preparation method and application thereof |
| CN114807772A (en) * | 2022-04-29 | 2022-07-29 | 燕山大学 | Aging-strengthened high-strength high-toughness light steel and manufacturing method thereof |
| CN114892084A (en) * | 2022-04-29 | 2022-08-12 | 燕山大学 | High-strength austenitic light steel with high impact toughness and manufacturing method thereof |
| CN114892084B (en) * | 2022-04-29 | 2023-02-24 | 燕山大学 | High-strength austenitic light steel with high impact toughness and manufacturing method thereof |
| CN116426836A (en) * | 2023-05-16 | 2023-07-14 | 燕山大学 | Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof |
| CN116426836B (en) * | 2023-05-16 | 2024-01-05 | 燕山大学 | Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111850419A (en) | High-manganese austenitic steel and preparation method thereof | |
| JP6574307B2 (en) | High toughness seamless steel pipe and manufacturing method thereof | |
| CN106756614B (en) | The thick easily welding F690 steel plates of 210mm that resistance to marine atmosphere, seawater splash corrode | |
| EP4257717A1 (en) | High-entropy austenitic stainless steel, and preparation method therefor | |
| CN112011745A (en) | Fe-Mn-Si-based shape memory alloy powder, preparation method and application thereof, 3D printing method and shape memory alloy | |
| CN111961893B (en) | High-strength high-plasticity high-entropy alloy and preparation method thereof | |
| CN101956134A (en) | High-strength high-plasticity copper-containing high-carbon TWIP steel and preparation process thereof | |
| CN110791717B (en) | High-quality hypoeutectoid alloy tool steel wire rod and production method thereof | |
| CN113106316B (en) | High-strength and high-toughness CrMnFeNi dual-phase high-entropy alloy and preparation method thereof | |
| CN110549033A (en) | weather-resistant bridge steel Q690qE matched gas shielded welding wire and preparation method thereof | |
| CN108441613A (en) | A kind of anti-white point control method of age-hardening plastic mould steel | |
| CN114622120A (en) | TRIP-assisted AlFeMnCoCr three-phase heterogeneous high-entropy alloy and preparation method thereof | |
| CN108374125A (en) | A kind of high-strength weather-proof steel alloy for mechanical equipment manufacture | |
| CN102586686B (en) | Clean corrosion-resistant steel for ocean engineering and manufacturing method thereof | |
| CN116555672A (en) | High-strength and high-toughness medium manganese steel plate and preparation method thereof | |
| CN111676409A (en) | Preparation method of low-density low-cost Fe-Mn-Al-C intermediate entropy alloy | |
| JPS62270721A (en) | Production of high-mn austenitic stainless steel for cryogenic service | |
| CN115976420A (en) | Low-cost 400 MPa-level spiral steel bar and preparation method thereof | |
| CN112853224B (en) | High-strength high-plasticity low-carbon medium-manganese TRIP steel and preparation method thereof | |
| CN101748328A (en) | Ship structure steel plate capable of being welded with high liner energy and method for producing same | |
| WO2020038019A1 (en) | Fe-mn-cr-ni series medium entropy stainless steel and preparation method therefor | |
| CN113355497B (en) | Low-activation steel plate and preparation process thereof | |
| CN102644025B (en) | High-strength and high-toughness steel plate and preparation method thereof | |
| CN116479335B (en) | Hot-rolled austenitic stainless steel for hydrogen storage valve and manufacturing method thereof | |
| CN113737105B (en) | Rare earth-containing weathering resistant steel and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination |