CN116426836A - Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof - Google Patents
Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof Download PDFInfo
- Publication number
- CN116426836A CN116426836A CN202310548099.8A CN202310548099A CN116426836A CN 116426836 A CN116426836 A CN 116426836A CN 202310548099 A CN202310548099 A CN 202310548099A CN 116426836 A CN116426836 A CN 116426836A
- Authority
- CN
- China
- Prior art keywords
- steel
- percent
- light steel
- austenitic
- forging
- 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.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 104
- 239000010959 steel Substances 0.000 title claims abstract description 104
- 238000002360 preparation method Methods 0.000 title abstract description 9
- 238000000034 method Methods 0.000 claims abstract description 21
- 238000010438 heat treatment Methods 0.000 claims abstract description 20
- 239000000126 substance Substances 0.000 claims abstract description 12
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 8
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 238000005242 forging Methods 0.000 claims description 33
- 230000032683 aging Effects 0.000 claims description 17
- 238000005098 hot rolling Methods 0.000 claims description 11
- 239000000463 material Substances 0.000 claims description 11
- 238000003723 Smelting Methods 0.000 claims description 9
- 238000005520 cutting process Methods 0.000 claims description 5
- 238000005096 rolling process Methods 0.000 claims description 5
- 238000005266 casting Methods 0.000 claims description 3
- 230000008569 process Effects 0.000 abstract description 11
- 229910045601 alloy Inorganic materials 0.000 abstract description 6
- 239000000956 alloy Substances 0.000 abstract description 6
- 238000001816 cooling Methods 0.000 description 12
- 238000004321 preservation Methods 0.000 description 12
- 238000001556 precipitation Methods 0.000 description 9
- 229910001566 austenite Inorganic materials 0.000 description 8
- 238000001878 scanning electron micrograph Methods 0.000 description 8
- 238000005728 strengthening Methods 0.000 description 8
- 239000011159 matrix material Substances 0.000 description 7
- 230000006698 induction Effects 0.000 description 6
- 230000001276 controlling effect Effects 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 230000007246 mechanism Effects 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 229910000885 Dual-phase steel Inorganic materials 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 238000003917 TEM image Methods 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000009750 centrifugal casting Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000001550 time effect Effects 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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 discloses Fe-Mn-Al-C-Nb-V austenitic light steel and a preparation method thereof, belonging to the technical field of Fe-Mn-Al-C austenitic light steel. The Fe-Mn-Al-C-Nb-V austenitic light steel comprises the following chemical components in percentage by mass: 0.95 to 1.15 percent of C, 27.00 to 29.00 percent of Mn, 7.00 to 8.50 percent of Al, 0.55 to 0.65 percent of Mo, 0.15 to 1.50 percent of Nb, 0.15 to 1.20 percent of V, and the balance of Fe and unavoidable impurities. The Fe-Mn-Al-C-Nb-V austenitic light steel with excellent mechanical property and high tissue stability is obtained by controlling the content of alloy elements in the Fe-Mn-Al-C-Nb-V austenitic light steel and a heat treatment process.
Description
Technical Field
The invention belongs to the technical field of Fe-Mn-Al-C austenitic light steel, and particularly relates to Fe-Mn-Al-C-Nb-V austenitic light steel and a preparation method thereof.
Background
The current world environmental crisis is becoming more severe, and automobile weight reduction has become one of the focus of attention. Steel is still the most used material for automobile production so far due to the advantages of low price, mature process and stable performance, and Fe-Mn-Al-C austenitic steel is the key point of automobile light weight research work due to low density and excellent mechanical properties.
Fe-Mn-Al-C austenitic steel is one of the most promising steel grades in low-density steels, and in recent years, in order to further improve the mechanical properties of the steel grades, many attempts have been made by researchers to improve the chemical composition and manufacturing process of Fe-Mn-Al-C austenitic steels. In patent number CN202210941998.X, named as ' high-strength high-plasticity light steel and preparation method thereof ', centrifugal casting, sub-rapid solidification and aging treatment are adopted to prepare the light steel, patent number CN202011327942.2, named as ' MIM forming process of Fe-Mn-Al-C steel part ', is proposed to prepare the Fe-Mn-Al-C steel part by utilizing a powder metallurgy method '. However, the Fe-Mn-Al-C steel manufactured by the two methods has complex process, greatly increases cost, and has great difficulty for large-scale industrial production. Patent No. CN202210463745.6 entitled "an aging-strengthened high strength and toughness light steel and a method for producing the same" proposes to produce an aging-strengthened fe—mn—al—c austenite+ferrite dual phase steel by adding Nb and V elements in combination to form (Nb, V) (C, N) and suppressing precipitation of grain boundary carbides. Patent number CN202210463966.3, named as "a dispersion strengthening ultra-high strength high plasticity light steel and a manufacturing method thereof", proposes adding Mo, ni and La elements, and obtaining the Fe-Mn-Al-C austenite plus ferrite dual-phase steel with low magnetism, high strength and high toughness by regulating and controlling precipitation of kappa carbide, improving high temperature ferrite delta and optimizing a processing technology. However, in the Fe-Mn-Al-C dual-phase steel, although the strength is improved due to the generation of high-temperature ferrite delta phase, the toughness is greatly reduced due to the hard and brittle characteristics, and the application occasion of the Fe-Mn-Al-C steel is limited, so that the proportion of the phase is hopefully regulated and reduced. In chinese patent No. CN202210377765.1, entitled "an Fe-Mn-Al-C austenitic light steel and a method for producing the same", it is proposed to cold-roll, anneal and age the Fe-Mn-Al-C austenitic steel, which can improve the strength of the steel, but the strengthening mechanism is not mentioned. At present, the precipitation strengthening of kappa carbide is one of the most main strengthening mechanisms of Fe-Mn-Al-C austenitic steel, the influence of kappa carbide on the mechanical properties of Fe-Mn-Al-C austenitic steel is mainly related to the form size and the distribution position of the steel, the fine intra-grain kappa carbide can obviously improve the strength and the hardness of the material, the coarse inter-grain kappa carbide can cause the reduction of the plasticity and the toughness of the material, and the form and the distribution of the kappa carbide are mainly related to alloy elements in the steel and the treatment process. Aiming at the problem of poor structure stability of the current Fe-Mn-Al-C austenitic steel, the field needs to develop Fe-Mn-Al-C austenitic steel with good performance, low cost and stable structure.
Disclosure of Invention
The invention aims to provide Fe-Mn-Al-C-Nb-V austenitic light steel and a preparation method thereof. In order to realize precipitation strengthening, the invention solves the difficulty in controlling the precipitation mechanism of kappa carbide in Fe-Mn-Al-C austenitic steel, especially the precipitation form position, by controlling the content of alloy elements in Fe-Mn-Al-C-Nb-V austenitic light steel and a heat treatment process, and the obtained Fe-Mn-Al-C-Nb-V austenitic light steel has excellent mechanical property and high tissue stability.
In order to achieve the above purpose, the present invention provides the following technical solutions:
one of the technical schemes of the invention is as follows: provided is Fe-Mn-Al-C-Nb-V austenitic light steel, comprising the following chemical components in percentage by mass: 0.95 to 1.15 percent of C, 27.00 to 29.00 percent of Mn, 7.00 to 8.50 percent of Al, 0.55 to 0.65 percent of Mo, 0.15 to 1.50 percent of Nb, 0.15 to 1.20 percent of V, and the balance of Fe and unavoidable impurities.
The second technical scheme of the invention is as follows: the preparation method of the Fe-Mn-Al-C-Nb-V austenitic light steel comprises the following steps:
feeding according to the designed chemical component content, smelting and casting into steel ingots; heating the steel ingot and forging to obtain a forging material; cutting a plate from the forging material to perform solution treatment or hot rolling treatment; finally, aging treatment is carried out to obtain the Fe-Mn-Al-C-Nb-V austenitic light steel.
Preferably, the temperature of the heating is 1150 ℃ and the time is 3h.
Preferably, the final forging temperature of the forging is not lower than 850 ℃, and the final forging is in a round bar shape.
Preferably, the solution treatment temperature is 1050-1200 ℃ and the time is 1h.
Preferably, the hot rolling treatment is specifically to heat-insulate the plate at 1050 ℃ for 1h, then to perform hot rolling deformation with a total deformation amount of 50%, and the final rolling temperature is not lower than 850 ℃.
Preferably, the aging treatment is carried out at a temperature of 500-600 ℃ for 5 hours.
The beneficial technical effects of the invention are as follows:
by controlling the content of alloy elements in the Fe-Mn-Al-C-Nb-V austenitic light steel and the heat treatment process, the invention can ensure that the generated microalloy carbide generates precipitation strengthening in the Fe-Mn-Al-C-Nb-V austenitic light steel, and simultaneously inhibits the growth of austenite grains and generates fine grain strengthening, thereby improving the mechanical property of the Fe-Mn-Al-C steel.
The shape and the size of the microalloy carbide change less along with the change of the treatment process and the temperature, so that the tissue stability of the light steel is higher.
According to the invention, microalloy carbide is used for replacing kappa carbide, so that the loss of mechanical properties of materials caused by coarsening of a strengthening phase in the use process of low-density steel is effectively avoided, and the difficulty in controlling a precipitation mechanism of kappa carbide in Fe-Mn-Al-C austenitic steel, particularly the control of the precipitation morphology position is solved.
The invention has simple process and great practical value.
Drawings
FIG. 1 is an SEM image of an Fe-Mn-Al-C-Nb-V austenitic light steel prepared in example 1.
FIG. 2 is a TEM image of Fe-Mn-Al-C-Nb-V austenitic light steel prepared in example 1.
FIG. 3 is an EDS diagram of Fe-Mn-Al-C-Nb-V austenitic light steel prepared in example 1.
FIG. 4 is an IPF structure diagram of Fe-Mn-Al-C-Nb-V austenitic light steel obtained at different aging temperatures in example 2, wherein a is a light steel having an aging temperature of 500 ℃, b is a light steel having an aging temperature of 550 ℃, and C is a light steel having an aging temperature of 600 ℃.
FIG. 5 is an SEM image of an Fe-Mn-Al-C-Nb-V austenitic light steel prepared in example 3.
FIG. 6 is an EDS diagram of Fe-Mn-Al-C-Nb-V austenitic light steel prepared in example 3.
FIG. 7 is an SEM image of an Fe-Mn-Al-C austenitic light steel prepared according to example 4.
FIG. 8 is an SEM image of an Fe-Mn-Al-C austenitic light steel prepared according to example 5.
Detailed Description
Various exemplary embodiments of the invention will now be described in detail, which should not be considered as limiting the invention, but rather as more detailed descriptions of certain aspects, features and embodiments of the invention. It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention.
In addition, for numerical ranges in this disclosure, it is understood that each intermediate value between the upper and lower limits of the ranges is also specifically disclosed. Every smaller range between any stated value or stated range, and any other stated value or intermediate value within the stated range, is also encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless otherwise defined, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention.
As used herein, the terms "comprising," "including," "having," "containing," and the like are intended to be inclusive and mean an inclusion, but not limited to.
The invention provides Fe-Mn-Al-C-Nb-V austenitic light steel, which comprises the following chemical components in percentage by mass: 0.95 to 1.15 percent of C, 27.00 to 29.00 percent of Mn, 7.00 to 8.50 percent of Al, 0.55 to 0.65 percent of Mo, 0.15 to 1.50 percent of Nb, 0.15 to 1.20 percent of V, and the balance of Fe and unavoidable impurities.
The invention also provides a preparation method of the Fe-Mn-Al-C-Nb-V austenitic light steel, which comprises the following steps:
(1) Smelting: feeding according to the design requirements of the composition components of the steel, smelting and casting into a steel ingot with one end of which has the diameter of 100mm and the other end of which has the diameter of 150mm and the height of 400mm in a vacuum induction furnace;
(2) Forging: heating the steel ingot to 1150 ℃, preserving heat for 3 hours, forging, wherein the final forging temperature is not lower than 850 ℃, and finally forging into a round bar with the diameter of about 40 mm;
(3) The treatment process comprises the following steps: carrying out one of the steps A or B on the forged round bar obtained in the step (2)
A. Solid solution: placing the forged round bar obtained in the previous step into a heat treatment furnace with the temperature of 1050-1200 ℃ for heat preservation for 1h, and then cooling to room temperature;
B. and (3) hot rolling: cutting a steel plate with the thickness of 30mm multiplied by 20mm multiplied by 80mm from the forged round bar obtained in the previous step, placing the steel plate into a heat treatment furnace with the temperature of 1050 ℃ for heat preservation for 1h, then carrying out hot rolling deformation with the total deformation amount of 50%, wherein the final rolling temperature is not lower than 850 ℃, and cooling the steel plate after hot rolling to room temperature;
(4) Aging: and (3) preserving heat of the plate obtained in the step (3) for 5 hours at 500-600 ℃, and then air-cooling to room temperature to obtain the Fe-Mn-Al-C-Nb-V austenitic light steel.
The Fe-Mn-Al-C-Nb-V austenitic light steel prepared by the preparation process consists of an austenitic matrix and carbides which are dispersed in the matrix, wherein the size of the carbides is 0.05-0.4 mu m.
Example 1
Smelting by using a vacuum induction furnace and pouring to obtain the cast ingot, wherein the cast ingot comprises the following chemical components in percentage by weight: c1.05, mn 27.92, al 7.33, mo 0.62, nb 0.16, V0.16. Heating the cast ingot to 1150 ℃, preserving heat for 3 hours, forging, wherein the final forging temperature is not lower than 850 ℃, and finally forging into round bars with the diameter of about 40 mm. Cutting a steel plate with the thickness of 30mm multiplied by 20mm multiplied by 80mm from a forged bar, placing the steel plate into a heat treatment furnace with the temperature of 1050 ℃ for heat preservation for 1h, then carrying out hot rolling deformation with the total deformation amount of 50 percent, wherein the final rolling temperature is not lower than 850 ℃, cooling the hot rolled steel plate to room temperature by water, and then carrying out air cooling on the steel plate to room temperature after heat preservation for 5h at 550 ℃ to obtain the Fe-Mn-Al-C-Nb-V austenitic light steel. The microstructure of the aged steel is observed, the mechanical property of the aged steel is measured, the SEM image is shown in figure 1, the TEM image is shown in figure 2, and the EDS is shown in figure 3. As can be seen from FIGS. 1 to 3, the matrix structure was single-phase austenite, the average grain size was 16.4.+ -. 7.4. Mu.m, and the (Nb, V) C precipitate phase was present in the structure at 106.6.+ -. 49.7 nm. The measured mechanical properties are: the yield strength is 669MPa, the tensile strength is 1001MPa, and the elongation is 49%.
Example 2
Smelting by using a vacuum induction furnace and pouring to obtain the cast ingot, wherein the cast ingot comprises the following chemical components in percentage by weight: c1.05, mn 27.92, al 7.33, mo 0.62, nb 0.16, V0.16. Heating the cast ingot to 1150 ℃, preserving heat for 3 hours, forging, wherein the final forging temperature is not lower than 850 ℃, and finally forging into round bars with the diameter of about 40 mm. Placing the forging bar into a heat treatment furnace at 1050 ℃ for heat preservation for 1h, then performing water quenching, and then performing air cooling to room temperature after heat preservation for 5h at 500, 550 and 600 ℃ respectively to obtain Fe-Mn-Al-C-Nb-V austenitic light steel with different time-effect temperatures. The microstructure of the aged steel is observed, and the mechanical properties of the aged steel are measured, and the IPF structure diagram of the obtained Fe-Mn-Al-C-Nb-V austenitic light steel is shown in fig. 4, wherein a is light steel with an aging temperature of 500 ℃, b is light steel with an aging temperature of 550 ℃, and C is light steel with an aging temperature of 600 ℃. As can be seen from FIG. 4, the matrix structure of the test steel after aging is single-phase austenite, and the average grain sizes of the test steel after aging treatment at 500, 550 and 600 ℃ are 28.4+/-14.5 microns, 30.5+/-13.4 microns and 29.5+/-17.0 microns respectively, so that the microstructure is little in change with time and temperature, and the performance difference is small, thus indicating that the structure stability is good. The mechanical properties are shown in Table 1.
TABLE 1 mechanical Properties of light Steel obtained at different time-effective temperatures
| Aging temperature/. Degree.C | Yield strength/MPa | Tensile strength/MPa | Elongation/% |
| 500 | 568 | 941 | 54.1 |
| 550 | 561 | 940 | 52.4 |
| 600 | 562 | 940 | 55.1 |
Example 3
Smelting by using a vacuum induction furnace and pouring to obtain the cast ingot, wherein the cast ingot comprises the following chemical components in percentage by weight: c1.11, mn 27.36, al 8.06, mo 0.60, nb 1.48 and V1.05, heating the cast ingot to 1150 ℃, preserving heat for 3 hours, forging, and finally forging into round bars with the diameters of about 40mm, wherein the final forging temperature is not lower than 850 ℃. Placing the forged bar into a heat treatment furnace with 1200 ℃ for heat preservation for 1h, then cooling the forged bar to room temperature by water, and then performing air cooling aging treatment after heat preservation for 5h at 600 ℃ to obtain the Fe-Mn-Al-C-Nb-V austenitic light steel. The microstructure of the aged steel is observed, the mechanical property of the aged steel is measured, the SEM image is shown in figure 5, and the EDS image is shown in figure 6. As can be seen from FIGS. 5 to 6, the matrix structure was single-phase austenite, the average grain size was 42.2.+ -. 13.4. Mu.m, and the (Mo, nb, V) C precipitate phase was present in the structure at 100 to 400 nm. The measured mechanical properties are: yield strength 836MPa, tensile strength 1010MPa, elongation 33.7%.
Example 4
Smelting by using a vacuum induction furnace and pouring to obtain the cast ingot, wherein the cast ingot comprises the following chemical components in percentage by weight: c1.05, mn 27.67, al 7.29 and Mo 0.64, heating the cast ingot to 1150 ℃, preserving heat for 3 hours, forging, wherein the final forging temperature is not lower than 850 ℃, and finally forging into round bars with the diameters of about 40 mm. Cutting a steel plate with the thickness of 30mm multiplied by 20mm multiplied by 80mm from a forged bar, placing the steel plate into a heat treatment furnace with the temperature of 1050 ℃ for heat preservation for 1h, then carrying out hot rolling deformation with the total deformation amount of 50 percent, wherein the final rolling temperature is not lower than 850 ℃, cooling the hot rolled steel plate to room temperature by water, and then carrying out air cooling to room temperature after the steel plate is subjected to heat preservation for 5h at 550 ℃ to obtain the Fe-Mn-Al-C austenitic light steel. The microstructure of the aged steel was observed and the mechanical properties of the aged steel were measured, and SEM images thereof are shown in fig. 7. As is clear from FIG. 7, the matrix structure was single-phase austenite, the average grain size was 35.6.+ -. 11.8. Mu.m, and no micro-alloy carbide precipitated phase was present in the structure. The measured mechanical properties are: the yield strength is 615MPa, the tensile strength is 966MPa, and the elongation is 54.0%.
Example 5
Smelting by using a vacuum induction furnace and pouring to obtain the cast ingot, wherein the cast ingot comprises the following chemical components in percentage by weight: c1.05, mn 27.67, al 7.29, mo 0.64. Heating the cast ingot to 1150 ℃, preserving heat for 3 hours, forging, wherein the final forging temperature is not lower than 850 ℃, and finally forging into round bars with the diameter of about 40 mm. Placing the forging bar into a heat treatment furnace at 1050 ℃ for heat preservation for 1h, then cooling to room temperature by water, and then cooling to room temperature by air after heat preservation for 5h at 550 ℃ to obtain the Fe-Mn-Al-C austenitic light steel. The microstructure of the aged steel was observed and the mechanical properties of the aged steel were measured, and SEM images thereof were shown in fig. 8. As is clear from FIG. 8, the matrix structure was single-phase austenite, the average grain size was 52.5.+ -. 18.3. Mu.m, and no micro-alloy carbide precipitated phase was present in the structure. The measured mechanical properties are: yield strength 524MPa, tensile strength 879MPa and elongation 63.7%.
The above embodiments are only illustrative of the preferred embodiments of the present invention and are not intended to limit the scope of the present invention, and various modifications and improvements made by those skilled in the art to the technical solutions of the present invention should fall within the protection scope defined by the claims of the present invention without departing from the design spirit of the present invention.
Claims (7)
1. An Fe-Mn-Al-C-Nb-V austenitic light steel is characterized by comprising the following chemical components in percentage by mass: 0.95 to 1.15 percent of C, 27.00 to 29.00 percent of Mn, 7.00 to 8.50 percent of Al, 0.55 to 0.65 percent of Mo, 0.15 to 1.50 percent of Nb, 0.15 to 1.20 percent of V, and the balance of Fe and unavoidable impurities.
2. A method of producing the Fe-Mn-Al-C-Nb-V austenitic light steel of claim 1, comprising the steps of:
feeding according to the designed chemical component content, smelting and casting into steel ingots; heating the steel ingot and forging to obtain a forging material; cutting a plate from the forging material to perform solution treatment or hot rolling treatment; finally, aging treatment is carried out to obtain the Fe-Mn-Al-C-Nb-V austenitic light steel.
3. The method of claim 2, wherein the heating is performed at 1150 ℃ for 3 hours.
4. The method according to claim 2, wherein the final forging temperature of the forging is not lower than 850 ℃, and the final forging is performed in a round bar shape.
5. The method according to claim 2, wherein the solution treatment temperature is 1050 to 1200 ℃ for 1 hour.
6. The method according to claim 2, wherein the hot rolling treatment is specifically to heat-insulate the sheet material at 1050 ℃ for 1 hour, and then to perform hot rolling deformation with a total deformation amount of 50%, and the final rolling temperature is not lower than 850 ℃.
7. The method according to claim 2, wherein the aging treatment is carried out at a temperature of 500 to 600 ℃ for a period of 5 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310548099.8A CN116426836B (en) | 2023-05-16 | 2023-05-16 | Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310548099.8A CN116426836B (en) | 2023-05-16 | 2023-05-16 | Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN116426836A true CN116426836A (en) | 2023-07-14 |
| CN116426836B CN116426836B (en) | 2024-01-05 |
Family
ID=87083357
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202310548099.8A Active CN116426836B (en) | 2023-05-16 | 2023-05-16 | Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN116426836B (en) |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111850419A (en) * | 2020-07-31 | 2020-10-30 | 燕山大学 | High-manganese austenitic steel and preparation method thereof |
| CN114752866A (en) * | 2022-04-24 | 2022-07-15 | 燕山大学 | Corrosion-resistant low-temperature-impact-resistant austenitic light steel and preparation method and application thereof |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6693217B2 (en) * | 2015-04-02 | 2020-05-13 | 日本製鉄株式会社 | High Mn steel for cryogenic temperatures |
| CN106244927B (en) * | 2016-09-30 | 2018-04-03 | 北京理工大学 | A kind of low-density unimach and preparation method thereof |
| WO2020085861A1 (en) * | 2018-10-25 | 2020-04-30 | 주식회사 포스코 | Cryogenic austenitic high-manganese steel having excellent shape, and manufacturing method therefor |
| CN112877606B (en) * | 2021-01-12 | 2022-03-08 | 钢铁研究总院 | Ultrahigh-strength full-austenite low-density steel and preparation method thereof |
| CN113088826B (en) * | 2021-02-25 | 2022-07-29 | 钢铁研究总院有限公司 | Microalloyed high-strength-toughness low-density steel and preparation method thereof |
| CN115323278A (en) * | 2022-06-29 | 2022-11-11 | 钢铁研究总院有限公司 | Low-density steel with yield of 700MPa and heat treatment method thereof |
-
2023
- 2023-05-16 CN CN202310548099.8A patent/CN116426836B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111850419A (en) * | 2020-07-31 | 2020-10-30 | 燕山大学 | High-manganese austenitic steel and preparation method thereof |
| CN114752866A (en) * | 2022-04-24 | 2022-07-15 | 燕山大学 | Corrosion-resistant low-temperature-impact-resistant austenitic light steel and preparation method and application thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN116426836B (en) | 2024-01-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110066964B (en) | Ultrahigh-strength medium manganese steel and warm rolling preparation method thereof | |
| CN110172641B (en) | Fine-grain high-toughness hot-work die steel and preparation method thereof | |
| CN110129678B (en) | Economical fine-grain high-toughness hot-work die steel and preparation method thereof | |
| CN109136652B (en) | Nickel-based alloy large-section bar for nuclear power key equipment and manufacturing method thereof | |
| CN106756567B (en) | A kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa% | |
| CN107779746B (en) | Ultra-fine grain alloy steel with ultrahigh strength, high toughness, corrosion resistance, oxidation resistance and preparation method thereof | |
| CN102864379B (en) | Fe-Cr-Co-W-Mo martensitic heat resistant steel and method for manufacturing same | |
| CN108220807A (en) | A kind of low-density high alumina superelevation carbon bearing steel and preparation method thereof | |
| CN114622133B (en) | Heat-resistant steel for ultra-supercritical steam turbine rotor forging and preparation method thereof | |
| CN114703429B (en) | Fe-Mn-Al-C series austenitic light steel and preparation method thereof | |
| CN112695256A (en) | Ferrite martensite steel ladle shell material and preparation method thereof | |
| CN115522126B (en) | Medium manganese steel with good wear resistance and production method thereof | |
| CN114480806A (en) | Manufacturing method of thick TiC particle enhanced martensite wear-resistant steel plate | |
| CN114231765A (en) | Preparation method and application of high-temperature alloy bar | |
| CN114959494A (en) | 1400 MPa-grade additive manufacturing ultralow-temperature stainless steel and preparation method thereof | |
| CN108624820B (en) | Automobile high-strength ductile steel with strength-elongation product of more than 45 GPa% and preparation method thereof | |
| CN110004368B (en) | Processing method for improving intergranular corrosion resistance of alloy with FCC crystal structure | |
| CN116426836B (en) | Fe-Mn-Al-C-Nb-V austenitic light steel and preparation method thereof | |
| CN108715976B (en) | Ti-Zr-C particle reinforced wear-resistant steel and preparation method thereof | |
| CN110791706A (en) | Austenitic coarse-grain structural steel for cold forging and preparation method of wire rod of austenitic coarse-grain structural steel | |
| CN114480984B (en) | Ti alloyed low-density high-strength steel and preparation method thereof | |
| CN102605249A (en) | Manganese and boron series low-carbon microalloy high-strength non-quenched and tempered steel and production method thereof | |
| CN112501504B (en) | BCA 2-grade container ship crack arrest steel plate and manufacturing method thereof | |
| CN110218935B (en) | Hot-work die steel with three-dimensional isotropic performance and preparation method thereof | |
| WO2020155197A1 (en) | Gradient ultra-fine grained low-carbon micro-alloy steel and preparation method therefor |
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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |