CN117385260A - Preparation method of Fe50Mn30Co10Cr10 alloy with ultrahigh strength and plastic product - Google Patents
Preparation method of Fe50Mn30Co10Cr10 alloy with ultrahigh strength and plastic product Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 62
- 239000000956 alloy Substances 0.000 title claims abstract description 62
- 238000002360 preparation method Methods 0.000 title claims abstract description 13
- 238000005096 rolling process Methods 0.000 claims abstract description 67
- 230000009467 reduction Effects 0.000 claims abstract description 41
- 238000005098 hot rolling Methods 0.000 claims abstract description 26
- 238000000137 annealing Methods 0.000 claims abstract description 18
- 238000000034 method Methods 0.000 claims abstract description 14
- 230000006698 induction Effects 0.000 claims abstract description 13
- 230000008569 process Effects 0.000 claims abstract description 10
- 238000005554 pickling Methods 0.000 claims abstract description 7
- 238000002844 melting Methods 0.000 claims abstract description 5
- 230000008018 melting Effects 0.000 claims abstract description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 38
- 239000000047 product Substances 0.000 claims description 29
- 238000001816 cooling Methods 0.000 claims description 22
- 229910052742 iron Inorganic materials 0.000 claims description 16
- 239000002994 raw material Substances 0.000 claims description 14
- 238000010438 heat treatment Methods 0.000 claims description 12
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 8
- 238000003723 Smelting Methods 0.000 claims description 8
- 229910052802 copper Inorganic materials 0.000 claims description 8
- 239000010949 copper Substances 0.000 claims description 8
- 239000002184 metal Substances 0.000 claims description 8
- 229910052751 metal Inorganic materials 0.000 claims description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 2
- 238000005266 casting Methods 0.000 claims description 2
- 239000007795 chemical reaction product Substances 0.000 claims description 2
- 239000007789 gas Substances 0.000 claims description 2
- 239000000203 mixture Substances 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 11
- 238000005728 strengthening Methods 0.000 abstract description 6
- 230000009471 action Effects 0.000 abstract description 3
- 230000008859 change Effects 0.000 abstract description 2
- 230000007246 mechanism Effects 0.000 abstract description 2
- 230000000052 comparative effect Effects 0.000 description 5
- 230000009977 dual effect Effects 0.000 description 5
- 230000001276 controlling effect Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 238000010923 batch production Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 230000001960 triggered effect Effects 0.000 description 1
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- 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
- C21D1/26—Methods of annealing
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- 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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- 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
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- 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
- C21D8/0231—Warm rolling
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- 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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Abstract
The invention belongs to the field of high-entropy alloy, and particularly relates to a preparation method of an ultrahigh-strength plastic product Fe50Mn30Co10Cr10 alloy. Firstly, preparing an as-cast slab through vacuum induction melting, then carrying out multi-pass hot rolling with 70% -75% rolling reduction on the as-cast slab, carrying out multi-pass warm rolling with 80% rolling reduction after pickling, and finally carrying out high-temperature short-time annealing at 1050-1150 ℃ to obtain the final annealed plate. The invention suppresses the phase change behavior in the alloy deformation process by controlling the hot rolling and warm rolling temperatures, and improves the rolling plasticity of the material. Meanwhile, grains are refined as much as possible through optimizing an annealing process, certain dislocation density is reserved, and the strong plasticity of the alloy is improved through the comprehensive action of a plurality of strengthening mechanisms. The tensile strength of the prepared Fe50Mn30Co10Cr10 alloy reaches 1050-1280 MPa, the elongation is 35-58%, and the strength-plastic product is 40-73 GPa.
Description
Technical Field
The invention belongs to the field of high-entropy alloy, and particularly relates to a preparation method of an ultrahigh-strength plastic product Fe50Mn30Co10Cr10 alloy.
Background
High entropy alloys generally refer to alloys having 5 or more major elements and between 5 and 35 atomic percent of each element. The high configurational entropy is believed to favor the formation of stable solid solution structures rather than complex intermetallic compounds, and this particular microstructure gives high entropy alloys with excellent properties. Fe of metastable-state dual-phase structure 50 Mn 30 Co 10 Cr 10 The high-entropy alloy is a novel material developed in recent years, the alloy system has low stacking fault energy and unstable phase structure, deformation easily triggers a transformation induced plasticity (TRIP) effect and a twinning induced plasticity (TWIP) effect so as to overcome the strength-ductility balance of a metal material, and the alloy is a novel high-entropy alloy with great development potential. However, fe is now 50 Mn 30 Co 10 Cr 10 The strength of the high-entropy alloy is not outstanding and needs to be further improved. In addition, high-entropy alloys generally have the problems of high work hardening rate and difficult plastic rolling.
From the presently published patent, reference is made to strengthening Fe 50 Mn 30 Co 10 Cr 10 The addition of microalloy elements is one of the most common methods of enhancing the strength of the alloy with less patents for high entropy alloys. Patent publication No. CN114622120A reports a TRIP-assisted FeMnCoCrAl three-phase heterogeneous high-entropy alloy and a preparation method thereof, and after a proper amount of Al element is added, the phase transition of FCC (face-centered cubic lattice) to HCP (close-packed hexagonal lattice) is triggered, and a third phase of BCC (body-centered cubic lattice) is introduced, so that certain strength is truly improved, but the elongation rate is improvedAnd also significantly decreased. Patent publication No. CN114855097A also reports a method for improving the strength and low-temperature wear resistance of FeMnCoCr high-entropy alloy, wherein B element is added to FeMnCoCr high-entropy alloy, and as a result, the yield strength and low-temperature wear resistance are improved to different degrees. In addition, by proper processing and manufacturing methods, the grain size of the alloy is further refined, the strength is further improved, but the ultimate tensile strength is only about 800MPa, and obviously, the requirement of ultra-high strength is not met. And at Fe 50 Mn 30 Co 10 Cr 10 There is less exploration in the plastic rolling of high entropy alloys. In conclusion, the prior technical means is to prepare high-strength plastic product Fe with high rolling reduction 50 Mn 30 Co 10 Cr 10 The high entropy alloy has disadvantages.
Disclosure of Invention
Aiming at the problems of low plastic rolling and plastic product in the prior art, the invention aims to provide a preparation method of an Fe50Mn30Co10Cr10 alloy with ultrahigh plastic product, which realizes large reduction rolling and large promotion of the plastic product of Fe50Mn30Co10Cr 10.
The technical scheme of the invention is as follows:
the preparation method of the Fe50Mn30Co10Cr10 alloy with the ultra-high strength and plastic product comprises the following steps:
(1) Vacuum induction melting: high-purity metal of Fe, mn, co, cr with purity more than 99.9wt% is selected as a raw material, and the atomic ratio of each element is as follows: 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr; putting the mixture into a vacuum induction furnace for smelting according to the set components, and casting into an as-cast slab with the thickness of 20mm in a square copper mold;
(2) And (3) hot rolling: carrying out multi-pass hot rolling on an as-cast slab, wherein the hot rolling reduction rate is 70% -75%, the single-pass reduction rate is 20% -30%, the initial rolling temperature is 1100 ℃ -1150 ℃, the final rolling temperature is 1000 ℃ -1020 ℃, and finally, cooling to room temperature by water to obtain a hot rolled plate;
(3) Warm rolling: after pickling a hot rolled plate to remove oxidized iron scales, heating the hot rolled plate to 260-310 ℃ in a resistance box furnace, and then carrying out multi-pass rolling by utilizing a two-roll mill, wherein the rolling reduction is 80%, and the single-pass rolling reduction is 15-30%, so as to obtain a warm rolled plate;
(4) Final annealing: and annealing the warm rolled plate to obtain an end product annealing plate, wherein argon is used as shielding gas in the annealing process.
In the preparation method of the Fe50Mn30Co10Cr10 alloy with the ultra-high strength and plastic product, in the step (2), the hot rolled plate structure is in a FCC and HCP dual-phase structure, wherein the volume ratio of the FCC phase is 80-90%.
In the preparation method of the ultra-high-strength plastic product Fe50Mn30Co10Cr10 alloy, in the step (3), the warm rolling plate structure is of an FCC single-phase structure.
In the step (4), the annealing temperature of the warm rolled plate is 1050-1150 ℃, the heating rate is more than or equal to 30 ℃/s, the heat preservation time is 20-25 s, and the air cooling is carried out.
In the preparation method of the ultrahigh-strength plastic product Fe50Mn30Co10Cr10 alloy, in the step (4), the annealed plate structure is of an FCC single-phase structure.
In the preparation method of the Fe50Mn30Co10Cr10 alloy with the ultra-high strength and plastic product, in the step (4), the annealed plate is a critical complete recrystallization structure, and the average grain size is 0.8-1.5 mu m.
In the step (4), the annealed plate has good shape, no crack, the tensile strength of 1050-1280 MPa, the elongation of 35-58% and the strength-plastic product of 40-73 GPa.
The design idea of the invention is as follows:
Fe 50 Mn 30 Co 10 Cr 10 the maximum rolling reduction of the high-entropy alloy at room temperature is about 60%, HCP (hot-set control) phase difference in a hot rolled plate is reduced by controlling the hot rolling temperature, meanwhile, the plasticity of the material is improved in a subsequent warm rolling mode, and the phase change behavior in the warm rolling process is strictly controlled, so that the deformed structure is a complete FCC structure. In the subsequent annealing process, high-temperature short-time annealing is adopted to refine grains as much as possible, and certain dislocation density is reserved at the same time, so that the strong plasticity of the alloy is improved through the comprehensive actions of fine grain strengthening, dislocation strengthening and TRIP and TWIP effects.
Compared with the prior art, the invention has the characteristics and beneficial effects that:
(1) The Fe50Mn30Co10Cr10 alloy is easy to crack when being rolled at room temperature to a reduction ratio exceeding 60%, and cannot be prepared into thinner materials. The invention adopts a special warm rolling process, effectively improves the rolling plasticity of the material, and can be used for preparing thin-specification materials with the rolling reduction rate of more than 80 percent.
(2) According to the invention, through the design of hot rolling-warm rolling-annealing integrated process, the deformation of Fe50Mn30Co10Cr10 alloy and the structure, size and phase transformation behavior of a heat treatment structure are effectively regulated, so that an ultrafine FCC single-phase recrystallization structure is obtained, and a structure foundation is provided for improving strength and plasticity.
(3) The Fe50Mn30Co10Cr10 alloy has the strength of 1280MPa at the highest and the plastic product of 73GPa at the highest, and has excellent comprehensive mechanical properties compared with the existing material, wherein the strength of the Fe50Mn30Co10Cr10 alloy is 300MPa and 40GPa at the highest.
(4) The invention has no other noble alloy strengthening elements, adopts the optimized route of the traditional rolling and heat treatment process, has low production cost and is suitable for batch production.
Drawings
FIG. 1 shows a hot rolled sheet structure of Fe50Mn30Co10Cr10 alloy prepared in example 2 of the present invention.
FIG. 2 shows the morphology of a warm rolled plate of Fe50Mn30Co10Cr10 alloy prepared in example 2 of the present invention.
FIG. 3 shows the structure of an annealed Fe50Mn30Co10Cr10 alloy sheet prepared in example 2 of the present invention.
FIG. 4 is a drawing of an annealed sheet of Fe50Mn30Co10Cr10 alloy prepared in example 2 of the present invention. In the figure, the abscissa Engineering strain is engineering strain (%), and the ordinate Engineering stress is engineering stress (MPa).
FIG. 5 shows the morphology of a cold-rolled Fe50Mn30Co10Cr10 alloy sheet prepared in comparative example 1.
FIG. 6 is a structure of an annealed sheet of Fe50Mn30Co10Cr10 alloy prepared in comparative example 1.
Detailed Description
In a specific implementation process, the invention provides a preparation method of an ultrahigh-strength plastic product Fe50Mn30Co10Cr10 alloy, which comprises the following specific procedures: vacuum induction melting is utilized, and the atomic percentages of elements are as follows: and (3) carrying out vacuum induction melting on the components of 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr to obtain an original cast slab, carrying out multi-pass hot rolling with a rolling reduction of 70% -75%, carrying out multi-pass warm rolling with a rolling reduction of 80% after pickling, and finally carrying out high-temperature short-time annealing at 1050-1150 ℃ to obtain the final annealed plate. By controlling parameters such as hot rolling temperature, cooling mode, warm rolling temperature, annealing heating rate, heat preservation time and the like, the single-phase FCC superfine recrystallization structure is obtained, and the strong plastic product of the material is obviously improved.
In the embodiment of the invention, an Electron Back Scattering Diffraction (EBSD) system of a Zeiss Gemini-300 field emission electron microscope is adopted as an observation material tissue, and a SHIMADZU AGS-X universal stretcher is adopted for measuring mechanical properties.
The present invention will be further described in detail by way of examples and comparative examples. It will be apparent that the described embodiments are only some, but not all, embodiments of the invention. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
Example 1
High-purity metal of Fe, mn, co, cr with purity more than 99.9wt% is selected as a raw material, and the raw material is prepared from the following components in element atomic ratio: the components of 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr are subjected to vacuum induction smelting, and then cast into an as-cast slab with the thickness of 20mm in a square copper mold. And then carrying out multi-pass hot rolling on the cast slab, wherein the hot rolling reduction rate is 75%, the single-pass reduction rate is 20% -30%, the initial rolling temperature is 1100 ℃, the final rolling temperature is 1000 ℃, and finally water cooling is carried out to room temperature. And then, after the hot rolled plate is pickled to remove the oxidized iron sheet, carrying out warm rolling at 280 ℃, wherein the rolling reduction rate is 80%, the single-pass rolling reduction rate is 15-30%, and air cooling to room temperature. Then preserving heat at 1100 ℃ for 20s, heating up at a rate of 35 ℃/s, and then air-cooling to room temperature to obtain the final Fe50Mn30Co10Cr10 alloy annealed plate.
The hot rolled sheet structure in this example is a FCC and HCP dual phase structure, wherein the FCC phase volume fraction is 82%. The warm rolling plate has good shape and no crack, and the warm rolling plate structure is of an FCC single-phase structure. The annealed sheet structure was a critical fully recrystallized structure, which was an FCC single phase, and the average grain size was 1.1 μm. The tensile strength of the annealed plate is 1160MPa, the elongation is 36%, and the strength-plastic product is 41.7GPa.
Example 2
High-purity metal of Fe, mn, co, cr with purity more than 99.9wt% is selected as a raw material, and the raw material is prepared from the following components in element atomic ratio: the components of 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr are subjected to vacuum induction smelting, and then cast into an as-cast slab with the thickness of 20mm in a square copper mold. And then carrying out multi-pass hot rolling on the as-cast slab, wherein the hot rolling reduction rate is 75%, the single-pass reduction rate is 20% -30%, the initial rolling temperature is 1150 ℃, the final rolling temperature is 1020 ℃, and finally, water cooling is carried out to room temperature. And then, after the hot rolled plate is pickled to remove the iron scales, carrying out warm rolling at 300 ℃, wherein the rolling reduction rate is 80%, the single-pass rolling reduction rate is 15-30%, and air cooling to room temperature. Then preserving heat at 1100 ℃ for 20s, heating up at a rate of 35 ℃/s, and then air-cooling to room temperature to obtain the final Fe50Mn30Co10Cr10 alloy annealed plate.
As shown in FIG. 1, the hot rolled plate structure in this example is a FCC and HCP dual phase structure, wherein the volume ratio of FCC phase is 89%. As shown in FIG. 2, the warm rolled plate has good plate shape and no crack, and is organized into an FCC single-phase structure. As shown in FIG. 3, the annealed plate structure was a critical fully recrystallized structure, which was FCC single phase, and the average grain size was 1.4. Mu.m. As shown in fig. 4, it can be seen from the tensile curve that the annealed sheet had a tensile strength of 1280MPa, an elongation of 58% and a strength-to-plastic product of 73GPa.
Example 3
High-purity metal of Fe, mn, co, cr with purity more than 99.9wt% is selected as a raw material, and the raw material is prepared from the following components in element atomic ratio: the components of 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr are subjected to vacuum induction smelting, and then cast into an as-cast slab with the thickness of 20mm in a square copper mold. And then carrying out multi-pass hot rolling on the as-cast slab, wherein the hot rolling reduction rate is 75%, the single-pass reduction rate is 20% -30%, the initial rolling temperature is 1150 ℃, the final rolling temperature is 1020 ℃, and finally, water cooling is carried out to room temperature. And then carrying out hot rolling at 260 ℃ after pickling the hot rolled plate to remove the oxidized iron scales, wherein the rolling reduction rate is 80%, the single-pass rolling reduction rate is 15-30%, and air cooling to room temperature. Then preserving the temperature at 1050 ℃ for 25 seconds, heating up at a rate of 30 ℃/s, and then air-cooling to room temperature to obtain the final Fe50Mn30Co10Cr10 alloy annealed plate.
The hot rolled sheet structure in this example is a FCC and HCP dual phase structure, wherein the FCC phase volume fraction is 89%. The warm rolling plate has no crack and the structure is FCC single-phase structure. The annealed sheet structure was a critical fully recrystallized structure, and it was an FCC single-phase structure, and the average grain size was 1.4 μm. The tensile strength of the annealed plate is 1094MPa, the elongation is 42%, and the strength-plastic product is 45.9GPa.
Example 4
High-purity metal of Fe, mn, co, cr with purity more than 99.9wt% is selected as a raw material, and the raw material is prepared from the following components in element atomic ratio: the components of 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr are subjected to vacuum induction smelting, and then cast into an as-cast slab with the thickness of 20mm in a square copper mold. And then carrying out multi-pass hot rolling on the as-cast slab, wherein the hot rolling reduction rate is 75%, the single-pass reduction rate is 20% -30%, the initial rolling temperature is 1150 ℃, the final rolling temperature is 1020 ℃, and finally, water cooling is carried out to room temperature. And then carrying out hot rolling at 260 ℃ after pickling the hot rolled plate to remove the oxidized iron scales, wherein the rolling reduction rate is 80%, the single-pass rolling reduction rate is 15-30%, and air cooling to room temperature. And then preserving heat at 1150 ℃ for 20s, heating at a rate of 30 ℃/s, and then air-cooling to room temperature to obtain the final Fe50Mn30Co10Cr10 alloy annealed plate.
The hot rolled sheet structure in this example is a FCC and HCP dual phase structure, wherein the FCC phase volume fraction is 89%. The warm rolled plate has no crack and organizes FCC single-phase structure. The annealed sheet structure was a critical fully recrystallized structure, and it was an FCC single-phase structure, and the average grain size was 1.4 μm. The tensile strength of the annealed plate is 1127MPa, the elongation is 39%, and the strength-plastic product is 43.9GPa.
Example 5
High-purity metal of Fe, mn, co, cr with purity more than 99.9wt% is selected as a raw material, and the raw material is prepared from the following components in element atomic ratio: the components of 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr are subjected to vacuum induction smelting, and then cast into an as-cast slab with the thickness of 20mm in a square copper mold. And then carrying out multi-pass hot rolling on the cast slab, wherein the hot rolling reduction rate is 75%, the single-pass reduction rate is 20% -30%, the initial rolling temperature is 1100 ℃, the final rolling temperature is 1020 ℃, and finally water cooling is carried out to room temperature. And then, after the hot rolled plate is pickled to remove the iron scales, carrying out warm rolling at 300 ℃, wherein the rolling reduction rate is 80%, the single-pass rolling reduction rate is 15-30%, and air cooling to room temperature. Then preserving heat at 1050 ℃ for 20s, heating at a rate of 35 ℃/s, and then air-cooling to room temperature to obtain the final Fe50Mn30Co10Cr10 alloy annealed plate.
The hot rolled sheet structure in this example is a FCC and HCP dual phase structure, wherein the FCC phase volume fraction is 85%. The warm rolling plate has no crack and the structure is FCC single-phase structure. The annealed plate structure was a critical fully recrystallized structure, a single-phase FCC structure, and an average grain size of 0.86 μm. The tensile strength of the annealed plate is 1155MPa, the elongation is 44% and the strength-plastic product is 50.8GPa.
Comparative example 1
High-purity metal of Fe, mn, co, cr with purity more than 99.9wt% is selected as a raw material, and the raw material is prepared from the following components in element atomic ratio: the components of 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr are subjected to vacuum induction smelting, and then cast into an as-cast slab with the thickness of 20mm in a square copper mold. And then carrying out multi-pass hot rolling on the as-cast slab, wherein the hot rolling reduction rate is 75%, the single-pass reduction rate is 20% -30%, the initial rolling temperature is 1150 ℃, the final rolling temperature is 1020 ℃, and finally, water cooling is carried out to room temperature. And then pickling the hot rolled plate to remove the oxidized iron sheet, and rolling at room temperature, wherein the rolling reduction is 60%. And then preserving the temperature at 900 ℃ for 120 seconds, and then air-cooling to room temperature to obtain the final Fe50Mn30Co10Cr10 alloy annealed plate.
As shown in FIG. 5, in this comparative example, the cold-rolled sheet of Fe50Mn30Co10Cr10 alloy with 60% reduction rate had obvious large-size cracks, the cold-rolled structure was a FCC+HCP dual-phase structure, and the FCC content was 45%. As shown in FIG. 6, HCP phase of about 2%z was present in the annealed plate structure, and the average grain size was 2.2. Mu.m. The tensile strength of the annealed plate is 815MPa, the elongation is 34%, the product of strength and elongation is 27.7GPa, and the mechanical property of the annealed plate is obviously lower than that of the material in the invention.
The implementation result shows that the invention suppresses the phase transformation behavior in the alloy deformation process by controlling the hot rolling and warm rolling temperatures, and improves the rolling plasticity of the material. Meanwhile, grains are refined as much as possible through optimizing an annealing process, certain dislocation density is reserved, and the strong plasticity of the alloy is improved through the comprehensive action of a plurality of strengthening mechanisms.
Claims (7)
1. The preparation method of the Fe50Mn30Co10Cr10 alloy with the ultra-high strength and plastic product is characterized by comprising the following steps of:
(1) Vacuum induction melting: high-purity metal of Fe, mn, co, cr with purity more than 99.9wt% is selected as a raw material, and the atomic ratio of each element is as follows: 50% of Fe, 30% of Mn, 10% of Co and 10% of Cr; putting the mixture into a vacuum induction furnace for smelting according to the set components, and casting into an as-cast slab with the thickness of 20mm in a square copper mold;
(2) And (3) hot rolling: carrying out multi-pass hot rolling on an as-cast slab, wherein the hot rolling reduction rate is 70% -75%, the single-pass reduction rate is 20% -30%, the initial rolling temperature is 1100 ℃ -1150 ℃, the final rolling temperature is 1000 ℃ -1020 ℃, and finally, cooling to room temperature by water to obtain a hot rolled plate;
(3) Warm rolling: after pickling a hot rolled plate to remove oxidized iron scales, heating the hot rolled plate to 260-310 ℃ in a resistance box furnace, and then carrying out multi-pass rolling by utilizing a two-roll mill, wherein the rolling reduction is 80%, and the single-pass rolling reduction is 15-30%, so as to obtain a warm rolled plate;
(4) Final annealing: and annealing the warm rolled plate to obtain an end product annealing plate, wherein argon is used as shielding gas in the annealing process.
2. The method for producing an ultra-high-strength plastic-product Fe50Mn30Co10Cr10 alloy according to claim 1, wherein in the step (2), the hot rolled plate structure has a dual-phase structure of FCC and HCP, wherein the volume ratio of the FCC phase is 80% to 90%.
3. The method for producing an ultra-high-strength plastic-product Fe50Mn30Co10Cr10 alloy according to claim 1, wherein in the step (3), the warm rolled plate structure is of an FCC single-phase structure.
4. The method for preparing the ultra-high-strength plastic product Fe50Mn30Co10Cr10 alloy according to claim 1, wherein in the step (4), the annealing temperature of the warm rolled plate is 1050-1150 ℃, the heating rate is more than or equal to 30 ℃/s, the heat preservation time is 20-25 s, and the air cooling is performed.
5. The method for producing an ultrahigh-strength plastic-product Fe50Mn30Co10Cr10 alloy according to claim 1, wherein in the step (4), the annealed plate structures are all FCC single-phase structures.
6. The method for producing an ultrahigh-strength plastic-product Fe50Mn30Co10Cr10 alloy according to claim 1, wherein in the step (4), the annealed sheet has a critical fully recrystallized structure and has an average grain size of 0.8 to 1.5. Mu.m.
7. The method for producing an ultrahigh-strength plastic-product Fe50Mn30Co10Cr10 alloy according to claim 1, wherein in the step (4), the annealed plate has a good shape, no cracks, a tensile strength of 1050-1280 MPa, an elongation of 35-58% and a plastic-product of 40-73 GPa.
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