CN116254448A - Twin induced plasticity high-entropy alloy based on B2 phase and nano ordered phase double precipitation strengthening and preparation method thereof - Google Patents
Twin induced plasticity high-entropy alloy based on B2 phase and nano ordered phase double precipitation strengthening and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a twin induced plasticity high-entropy alloy based on B2 phase and nano ordered phase double precipitation strengthening and a preparation method thereof, wherein the high-entropy alloy comprises the following constituent elements in percentage by atom: 19-21% of Mn, 9-11% of Ni, 5-7% of Si, 5-7% of Al, 0-4% of C and the balance of Fe and unavoidable impurity elements. The high-entropy alloy provided by the application is low in preparation cost, has the advantages of high strength, high plasticity, low density and the like, and has wide application prospects in the fields of aerospace, advanced nuclear energy, biological engineering, advanced equipment manufacturing, national defense industry and the like.
Description
Technical Field
The invention belongs to the technical field of high-entropy alloy, and particularly relates to a twin induced plasticity high-entropy alloy based on B2 phase and nano ordered phase double precipitation strengthening and a preparation method thereof.
Background
High-entropy alloys are a research hotspot in the field of metal materials in recent years. The high entropy alloy in the center region of the phase diagram has a greater potential for element combinations than the conventional alloy in the corner region of the phase diagram, and therefore the available composition space for development is very large. The high-entropy alloy has high thermodynamic stability and good comprehensive mechanical properties, and has wide application prospects in the aspects of high-temperature engines, superconducting devices, low-temperature devices and the like. Currently, single-phase high-entropy alloys with face-centered cubic (FCC) structure are gaining the most attention. Such alloys tend to have excellent plasticity and toughness, but their yield strength is generally low. In order to improve the strength of FCC single-phase high-entropy alloy, the introduction of a precipitated phase by controlling alloy components is an important means. For example, by adding Al element to a CoCrFeMnNi high entropy alloy with an equimolar ratio, B2 and L1 rich in Al and Ni can be produced 2 And L2 1 The precipitated phase is precipitated, thereby leading to remarkable precipitation strengthening effect, and the FCC matrix of the alloy has good plasticity, so that the matching of high strength and high plasticity can be realized. Related researches also show that the addition of the gap elements such as C, N and the like in the high-entropy alloy can generate a remarkable strengthening effect, and the addition of certain specific elements can also lead to the formation of chemical ordered phases with different degrees in the high-entropy alloy, such as chemical short-range ordered phases, chemical long-range ordered phases and the like. The ordered phases are typically nano-sized in size and can act as a barrier to the movement of dislocations during deformation, thereby increasing the strength of the material. In addition, can also be introduced into high-entropy alloyThe TWIP effect, which is similar to that in twinning induced plasticity (TWIP) steel, is achieved by deformation twinning and the interaction of deformation twinning with grain boundaries and precipitation phases to improve the strength and plasticity of the steel. For example, related studies around Fe-Mn-Al-Si systems in recent years have shown that the addition of Si element not only has a remarkable solid solution strengthening effect, but also can reduce the stacking fault energy of the matrix, thereby promoting the TWIP effect, and thus the TWIP effect can be introduced into a high entropy alloy through the addition of Si. The introduction of the strengthening measures can realize higher mechanical properties, but in the current domestic and foreign researches, the high-entropy alloy with three or more strengthening mechanisms is rarely reported, and the research in the aspect is worth further exploration.
In practical engineering application, the requirement of mechanical properties is not satisfied, and the factors such as material cost, preparation process, density and the like need to be comprehensively considered. The traditional high-entropy alloy mainly comprises noble metal elements such as Co, cr, ni and the like, and has large ubiquitous density>8g/cm 3 ) High cost and the like. Therefore, developing a high-entropy alloy having both high strength and high plasticity and low cost and low density is a currently urgent problem to be solved. The alloy has wide application prospect in the fields of energy, traffic, equipment manufacturing and the like.
Disclosure of Invention
The invention mainly aims at the problem of lack of light high-performance high-entropy alloy meeting application requirements, provides a preparation method of the twin induced plasticity high-entropy alloy based on B2 phase and nano ordered phase double precipitation strengthening through reasonable component design, and develops a low-cost and low-density (7.41 g/cm) alloy with precipitation strengthening, chemical ordered strengthening and twin induced plasticity effects based on the proportion of Ni, al, si, C element content 3 ) The high-entropy alloy solves the technical problems of low cost, low density, high strength and high plasticity of the existing high-entropy alloy.
Specifically, the first part of the invention provides a twin induced plasticity high-entropy alloy based on B2 phase and nano ordered phase double precipitation strengthening, wherein the high-entropy alloy comprises the following constituent elements in percentage by atom: 19-21% of Mn, 9-11% of Ni, 5-7% of Si, 5-7% of Al, 0-4% of C, and the balance of Fe and unavoidable impurity elements. The high-entropy alloy consists of an austenite phase, a B2 phase and a nano ordered phase.
Wherein, the atomic percentage ratio of Ni and Al is 1.3-1.8, so as to ensure that the high-entropy alloy forms a B2 precipitated phase with a body-centered cubic structure after solution quenching; the atomic percentage ratio of Al to C in the high-entropy alloy is 1.3-2.0, so as to ensure that the high-entropy alloy forms a chemical ordered phase after solution quenching; the atomic percentage ratio of Al to Si in the high-entropy alloy is 0.9-1.5, so that the high-entropy alloy has middle-low fault energy and deformation twin crystals generated in a plastic deformation stage.
The second part of the invention provides a preparation method of a twin induced plasticity high entropy alloy based on double precipitation strengthening of a B2 phase and a nano ordered phase, which comprises the following steps:
pure Fe, pure Mn, pure Ni, pure Al, pure Si and pure C with purity not less than 99.9% are adopted as raw materials, the raw materials are proportioned according to the atomic percentage of the high-entropy alloy, and then the prepared raw materials are subjected to vacuum induction smelting to obtain cast ingots;
homogenizing the cast ingot under the protection of argon; cutting into plates, carrying out multi-pass cold rolling, carrying out solution treatment on the cold-rolled sheet, and then carrying out water cooling quenching.
As a further explanation of the present invention, the vacuum induction melting is performed in a vacuum frequency induction melting furnace, repeatedly performed 3 to 5 times, and argon gas is used as a protective atmosphere.
As a further explanation of the present invention, the argon pressure was 0.8X105 Pa, the voltage was 380V, and the frequency of the induced current was 2500Hz.
As a further explanation of the invention, the homogenization treatment is water-cooling quenching after heat preservation for more than 6 hours at 1100 ℃ under the protection of argon.
As a further explanation of the invention, the cold rolling treatment is to cold-roll the homogenized sheet material in a two-roll strip mill for multiple passes, wherein the deformation of each pass is not more than 5%, and the total deformation is about 70%.
As a further explanation of the present invention, the solution treatment is water-cooling quenching after heat preservation of the cold rolled sheet at 950 ℃ for more than 1 hour under the protection of argon.
Compared with the prior art, the invention has the following beneficial technical effects:
the twin induced plasticity high entropy alloy based on the B2 phase and nano ordered phase double precipitation strengthening prepared in the invention has low density (7.41 g/cm) 3 ) The alloy has the advantages of low cost, easy preparation and processing, and simultaneously has low stacking fault energy, dispersed nano ordered phase and B2 precipitation phase, so that the alloy has high strength and high plasticity, and under the optimal component proportion and the optimal solution treatment, the yield strength is 554MPa, the tensile strength is 1019MPa, the uniform elongation is 49 percent, and the elongation after break is 56 percent. The high-entropy alloy has the advantages of low cost, low density, high strength and high plasticity, and can promote the industrial production and application of the high-entropy alloy.
Drawings
FIG. 1 is an Electron Back Scattering Diffraction (EBSD) image and a Transmission Electron Microscope (TEM) image of the high-entropy alloy prepared in examples 1-2 of the present invention;
FIG. 2 is a nano ordered phase TEM image of the high-entropy alloy prepared in examples 1-2 of the present invention;
FIG. 3 is a drawing of a room temperature tensile engineering stress-strain curve and a microstructure Scanning Electron Microscope (SEM) image of the vicinity of a fracture of the high-entropy alloy prepared in examples 1 to 2 of the present invention.
Detailed Description
In order to make the technical solutions and advantages of the embodiments of the present application clearer, the technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings in the embodiments of the present invention. The described embodiments are only some, but not all, embodiments of the invention. The alloy structure and properties of the embodiments of the present application illustrated in the drawings herein may be tailored and designed in a variety of different compositional configurations, and thus the following detailed description of the embodiments of the present application provided in the drawings is not intended to limit the scope of the application as claimed, but is merely representative of selected embodiments of the present application. 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.
The technical scheme of the present application will be explained in connection with specific embodiments.
Example 1
The B2 phase and nano ordered phase based twin precipitation strengthening twin induced plasticity high entropy alloy of the embodiment mainly comprises the following elements in percentage by atom: 58.3% Fe,19.5% Mn,9.8% Ni,6.0% Al,6.4% Si.
The preparation method of the alloy comprises the following steps:
s1, taking pure Fe, pure Mn, pure Ni, pure Al and pure Si with purity not less than 99.9% as raw materials, proportioning according to the atomic percentage of the high-entropy alloy, and then carrying out vacuum induction smelting on the prepared raw materials to obtain an ingot, wherein the argon pressure is 0.8x10 5 Pa, 380V voltage, 2500Hz frequency of induced current;
s2, turning over the cast ingot obtained in the previous step, and adopting the same parameters to carry out remelting, and repeatedly smelting for 3-5 times so as to improve the component uniformity of the finally obtained finished cast ingot;
s3, carrying out homogenizing annealing treatment at 1100 ℃ for more than 6 hours on the finished product ingot under the protection of argon, and then carrying out water cooling quenching.
S4, cutting the plate from the cast ingot, carrying out multi-pass cold rolling on the plate in a double-roller plate and strip mill, wherein the deformation of each pass is not higher than 5%, and the total deformation is about 70%.
S5, carrying out solution treatment on the cold-rolled sheet at 950 ℃ for more than 1h under the protection of argon, and then carrying out water cooling quenching.
The initial structure of the alloy prepared in this example was characterized by EBSD and TEM, and the results are shown in FIG. 1. As can be seen from figure a, the alloy prepared in this example was partially recrystallized and figure B shows that there was a significant B2 phase precipitation at the grain boundaries, with an FCC average grain size of 2.82 μm. Panel c demonstrates the presence of a uniformly distributed B2 phase within the crystal, with an average size of 267nm.
The nano-ordered phase of the alloy prepared in this example was characterized by TEM and the results are shown in figure 2. In FCC
Present in the diffraction pattern obtained by the crystallographic axis
The superlattice point at the location, the central dark field image observed a bright white nano ordered phase with an average size of 1.17nm and a volume fraction of 7.85%.
According to GB/T228.1-2010 section 1 Metal Material tensile test: the room temperature test method measures the mechanical properties of the high-entropy alloy prepared in the embodiment, and the result is shown in figure 3, wherein the yield strength is 450MPa, the tensile strength is 809MPa, the uniform elongation is 40%, and the elongation after break is 46%. The inset shows deformation twins near the fracture, which proves that the alloy prepared in the embodiment has TWIP effect.
Example 2
The B2 phase and nano ordered phase based twin precipitation strengthening twin induced plasticity high entropy alloy of the embodiment mainly comprises the following elements in percentage by atom: 55.7% Fe,19.4% Mn,9.8% Ni,5.7% Al,5.5% Si,3.9% C.
The preparation method of the alloy comprises the following steps:
s1, taking pure Fe, pure Mn, pure Ni, pure Al, pure Si and pure C with purity not less than 99.9% as raw materials, proportioning according to the atomic percentage of the high-entropy alloy, and then carrying out vacuum induction smelting on the prepared raw materials to obtain an ingot, wherein the argon pressure is 0.8x10 5 Pa, 380V voltage, 2500Hz frequency of induced current;
s2, turning over the cast ingot obtained in the previous step, and adopting the same parameters to carry out remelting, and repeatedly smelting for 3-5 times so as to improve the component uniformity of the finally obtained finished cast ingot;
s3, carrying out homogenizing annealing treatment at 1100 ℃ for more than 6 hours on the finished product ingot under the protection of argon, and then carrying out water cooling quenching.
S4, cutting the plate from the cast ingot, carrying out multi-pass cold rolling on the plate in a double-roller plate and strip mill, wherein the deformation of each pass is not higher than 5%, and the total deformation is about 70%.
S5, carrying out solution treatment on the cold-rolled sheet at 950 ℃ for more than 1h under the protection of argon, and then carrying out water cooling quenching.
The initial structure of the alloy prepared in this example was characterized by EBSD and TEM, and the results are shown in FIG. 1. As can be seen from graph d, the alloy prepared in this example was partially recrystallized, and graph e shows that there was a significant B2 phase precipitation at the grain boundaries, with FCC grain sizes of 4.47 μm. Panel f demonstrates the presence of a uniformly distributed B2 phase within the crystal, with an average size of 230nm.
The nano-ordered phase of the alloy prepared in this example was characterized by TEM and the results are shown in figure 2. In FCC [001 ]]The diffraction pattern obtained by the crystal axis exists
The superlattice point at the position, the bright white nano ordered phase is observed by the central dark field image, the average size is 1.03nm, and the volume fraction is 8.6%.
According to GB/T228.1-2010 section 1 Metal Material tensile test: the room temperature test method measures the mechanical properties of the high-entropy alloy prepared in the embodiment, and the result is shown in figure 3, wherein the yield strength is 554MPa, the tensile strength is 1019MPa, the uniform elongation is 49%, and the elongation after fracture is 55%. The inset shows deformation twins near the fracture, which proves that the alloy prepared in the embodiment has TWIP effect.
Finally, it should be noted that the above-mentioned embodiments are merely for illustrating the technical solution of the present invention and not for limiting the same, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that modifications and equivalents may be made to the technical solution of the present invention without departing from the spirit and scope of the technical solution of the present invention.
Claims (9)
1. The twin induced plasticity high-entropy alloy based on B2 phase and nano ordered phase double precipitation strengthening is characterized by comprising the following constituent elements in percentage by atom: 19-21% of Mn, 9-11% of Ni, 5-7% of Si, 5-7% of Al, 0-4% of C, and the balance of Fe and unavoidable impurity elements.
2. The B2-phase and nano-ordered phase dual precipitation strengthening-based twin induced plasticity high-entropy alloy according to claim 1, wherein the high-entropy alloy consists of an austenite phase, a B2 phase and a nano-ordered phase.
3. The B2-phase and nano ordered phase double precipitation strengthening-based twin induced plasticity high-entropy alloy according to claim 1, wherein the ratio of the atomic percentages of Ni and Al in the high-entropy alloy is 1.3-1.8; the atomic percentage ratio of Al to C in the high-entropy alloy is 1.3-2.0; the atomic percentage ratio of Al to Si in the high-entropy alloy is 0.9-1.5.
4. The preparation method of the twin induced plasticity high-entropy alloy based on the double precipitation strengthening of the B2 phase and the nano ordered phase is characterized by comprising the following steps:
adopting pure Fe, pure Mn, pure Ni, pure Al, pure Si and pure C with purity not less than 99.9% as raw materials, preparing the raw materials according to the atomic percentage of the high-entropy alloy as defined in any one of claims 1-3, and then carrying out vacuum induction smelting on the prepared raw materials to obtain an ingot;
homogenizing the cast ingot under the protection of argon; cutting into plates, carrying out multi-pass cold rolling, carrying out solution treatment on the cold-rolled sheet, and then carrying out water cooling quenching.
5. The preparation method of the twin induced plasticity high entropy alloy based on the B2 phase and nano ordered phase double precipitation strengthening of the invention as claimed in claim 4 is characterized in that the vacuum induction smelting is carried out in a vacuum frequency induction smelting furnace, repeated 3-5 times is carried out, and argon is adopted as a protective atmosphere.
6. The method for preparing the twin induced plasticity high entropy alloy based on the double precipitation strengthening of the B2 phase and the nano ordered phase as claimed in claim 4, wherein the argon pressure is 0.8X10 5 Pa, the voltage is 380V, and the frequency of the induced current is 2500Hz.
7. The preparation method of the twin induced plasticity high entropy alloy based on the double precipitation strengthening of the B2 phase and the nano ordered phase, which is disclosed in claim 4, is characterized in that the homogenization treatment is water cooling quenching after heat preservation of more than 6h at 1100 ℃ under the protection of argon.
8. The method for preparing the twin induced plasticity high entropy alloy based on the B2 phase and nano ordered phase double precipitation strengthening as claimed in claim 4, wherein the cold rolling treatment is that the homogenized sheet material is subjected to multi-pass cold rolling in a double-roller strip mill, the deformation of each pass is not higher than 5%, and the total deformation is 70%.
9. The method for preparing the twin induced plasticity high entropy alloy based on the double precipitation strengthening of the B2 phase and the nano ordered phase according to claim 4, wherein the solution treatment is water cooling quenching after the cold rolled sheet is kept at 950 ℃ for more than 1h under the protection of argon.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101812575A (en) * | 2010-04-12 | 2010-08-25 | 中国石油天然气集团公司 | Alloy tube containing 13 to 19 percent of manganese and preparation method thereof |
| KR20110115651A (en) * | 2010-04-16 | 2011-10-24 | 현대제철 주식회사 | Light and high ductility aluminum contained twip steel and manufacturing method therof |
| US20120199253A1 (en) * | 2009-10-14 | 2012-08-09 | Japan Science And Technology Agency | Fe-based shape memory alloy and its production method |
| RU2615738C1 (en) * | 2016-02-08 | 2017-04-10 | Федеральное государственное автономное образовательное учреждение высшего образования "Белгородский государственный национальный исследовательский университет" (НИУ "БелГУ") | HIGH-STRENGTH STEELS OF Fe-Mn-Al-C SYSTEM WITH TWIP AND TRIP EFFECTS |
| US20190300978A1 (en) * | 2016-05-24 | 2019-10-03 | Arcelormittal | Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts |
| CN115044830A (en) * | 2022-06-07 | 2022-09-13 | 西北工业大学 | Light TWIP steel based on twinning induced plasticity and ordered reinforcement and preparation method thereof |
-
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- 2023-02-14 CN CN202310112395.3A patent/CN116254448B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20120199253A1 (en) * | 2009-10-14 | 2012-08-09 | Japan Science And Technology Agency | Fe-based shape memory alloy and its production method |
| CN101812575A (en) * | 2010-04-12 | 2010-08-25 | 中国石油天然气集团公司 | Alloy tube containing 13 to 19 percent of manganese and preparation method thereof |
| KR20110115651A (en) * | 2010-04-16 | 2011-10-24 | 현대제철 주식회사 | Light and high ductility aluminum contained twip steel and manufacturing method therof |
| RU2615738C1 (en) * | 2016-02-08 | 2017-04-10 | Федеральное государственное автономное образовательное учреждение высшего образования "Белгородский государственный национальный исследовательский университет" (НИУ "БелГУ") | HIGH-STRENGTH STEELS OF Fe-Mn-Al-C SYSTEM WITH TWIP AND TRIP EFFECTS |
| US20190300978A1 (en) * | 2016-05-24 | 2019-10-03 | Arcelormittal | Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts |
| CN115044830A (en) * | 2022-06-07 | 2022-09-13 | 西北工业大学 | Light TWIP steel based on twinning induced plasticity and ordered reinforcement and preparation method thereof |
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