CN111826590B - Fe23Zr6And Fe2M-Laves phase co-reinforced FeCrAl stainless steel and preparation method thereof - Google Patents
Fe23Zr6And Fe2M-Laves phase co-reinforced FeCrAl stainless steel and preparation method thereof Download PDFInfo
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Abstract
The invention discloses Fe23Zr6And Fe2An M-Laves phase co-strengthened FeCrAl stainless steel consisting of (wt.%): cr 13-15%, Al 4-5%, Mo1.5-3%, Nb0.5-1.5%, Ta 0-1%, Zr0.4-1%, and the balance of Fe and impurities. By increasing the amount of Zr and matching with other alloy components with specific mixture ratio, the preparation method disclosed by the invention can form Fe in the matrix23Zr6And Fe2Two intermetallic compound strengthening phases of M-Laves, wherein Fe23Zr6The phase still exists at 1200 ℃, can effectively inhibit the growth of crystal grains at ultrahigh temperature, remarkably improves the high-temperature structure stability and mechanical property of the alloy, and solves the problems of poor structure stability and rapid coarsening of the crystal grains of FeCrAl at the temperature of more than 1100 ℃ in the prior art, which cause serious performance deterioration.
Description
Technical Field
The invention relates to the field of heat-resistant stainless steel, in particular to Fe23Zr6And Fe2An M-Laves phase co-reinforced FeCrAl stainless steel and a preparation method thereof.
Background
For a long time, the Zr alloy has good corrosion resistance, excellent neutron irradiation resistance, structural integrity and the like under the conventional operating conditions of the light water reactor (350-400 ℃/15MPa of the second generation light water reactor), so that the Zr alloy occupies the monopoly of the cladding material of the light water reactor for a long time. However, 2011 occurrence of nuclear accident in fukushima japan exposed the existing Zr-UO2The fuel system has the defect of poor capability of resisting serious accidents, and the accidents are mainly caused by that the temperature of a reactor core is rapidly increased to 1000-1200 ℃ due to the interruption of cooling water outside the reactor caused by the earthquake, and Zr + H is generated in the temperature range2O→ZrO+H2The reaction up to ↓ and hydrogen implosion occur finally, resulting in the leakage of radioactive substances. Therefore, it is urgently needed to develop a fuel cladding material (namely, ATF cladding material) with accident-resistant and fault-tolerant capabilities to replace the active Zr alloy so as to improve the safety performance of the reactor, and the ATF cladding material is required to meet the performance requirements of the reactor under the conventional operating conditions, and simultaneously have excellent high-temperature steam oxidation resistance and good high-temperature mechanical properties at 1000-1200 ℃.
The FeCrAl ferritic stainless steel has the advantages of excellent high-temperature steam oxidation resistance, corrosion resistance, neutron irradiation resistance and the like, and is the best candidate material for the pressurized water reactor ATF cladding. A great deal of research has been done at home and abroad on the application of FeCrAl series alloy in ATF cladding materials. The research result of national laboratory of Oak Ridge (ORNL) in the United states shows that Fe- (13-15) CrThe (4-5) Al (wt.%) ternary base alloy has excellent high-temperature steam oxidation resistance at an accident temperature of 1200 ℃ and has good neutron irradiation resistance under a normal service condition of 400 ℃. However, the alloy is a single ferrite matrix, and no second phase is precipitated, so that the crystal grains grow rapidly at a high temperature of more than 700 ℃, and the mechanical property of the alloy is seriously reduced. ORNL further investigated carbides (M) in order to improve the high temperature mechanical properties of FeCrAl alloys23C6And M7C3) And intermetallic compound (Fe)2M-Laves phase，hp12-MgZn2Type) precipitation strengthened FeCrAl alloys. The results show that after Mo/Nb co-alloying, the Mo/Nb is due to Fe2The precipitation of the (Mo, Nb) -Laves phase improves the high-temperature structure stability of the alloy obviously, obvious recovery recrystallization does not occur after 800 ℃/24h aging, and the carbide has no obvious effect on the improvement of the structure stability.
In China, a FeCrAl alloy with Mo, Nb, Ta, Ce, C, N and O as a component disclosed in the patent application with the publication number CN 106995902A, a FeCrAl alloy with Mo, Nb, Zr, Si, Mn, La, Ce and Y as a component disclosed in the patent application with the publication number CN 106987780A, a FeCrAl alloy with Mo, Nb, W, V, Si, Ga, Ce, C, N and O as a component disclosed in the patent application with the publication number CN107058872A and the like belong to the FeCrAl alloy consisting of Fe, Nb, W, V, Si, Ga, Ce, C, N and O and the like2The M-Laves phase reinforced FeCrAl alloy has high-temperature strength and structural stability at 800 ℃, and has excellent high-temperature oxidation resistance at 1000 ℃ under water vapor. The applicant finds that the series of alloys prepared by adopting the components and the technology really disperse and precipitate a large amount of Fe2The M-Laves phase can effectively pin dislocation motion at the temperature of below 1000 ℃ and block grain boundary migration at high temperature, thereby inhibiting grain growth and improving the stability of alloy high-temperature structure; however, when the temperature exceeds 1100 ℃, the Laves phase in the matrix is largely dissolved and is almost completely dissolved at 1200 ℃, and ferrite grains grow rapidly and the alloy is seriously embrittled. For the ATF cladding material, the temperature of the reactor core can be rapidly raised to be more than 1100 ℃ when a loss of coolant accident happens. Therefore, there is a need to develop a composition with improved thermal stabilityHigh intermetallic strengthened FeCrAl alloys are used as candidate ATF cladding materials.
Disclosure of Invention
In order to overcome the defects of the prior art, the invention aims to provide Fe23Zr6And Fe2The FeCrAl stainless steel which is strengthened by the M-Laves phase increases the amount of Zr element, and Fe can be formed by matching each element23Zr6And Fe2Two intermetallic compound strengthening phases of M-Laves, wherein Fe23Zr6The phase still exists at 1200 ℃, the grain growth at ultrahigh temperature can be effectively inhibited, and the high-temperature tissue stability of FeCrAl stainless steel is obviously improved;
the second purpose of the invention is to provide a preparation method of the FeCrAl stainless steel, which is characterized in that the FeCrAl stainless steel is prepared through smelting, homogenization treatment, hot forging, hot rolling and subsequent heat treatment processes, and Fe can be simultaneously precipitated23Zr6And Fe2The M-Laves phase effectively improves the high-temperature structure stability and the mechanical property of the FeCrAl alloy, and solves the problems that the FeCrAl stainless steel has poor structure stability at the temperature of over 1100 ℃ and the mechanical property is seriously deteriorated due to rapid coarsening of crystal grains in the prior art.
One of the purposes of the invention is realized by adopting the following technical scheme:
fe23Zr6And Fe2The M-Laves phase co-reinforced FeCrAl stainless steel comprises the following components in percentage by mass: 13.0-15.0% of Cr, 4.0-5.0% of Al, 1.5-3.0% of Mo, 0.5-1.5% of Nb, 0-1.0% of Ta, 0.4-1.0% of Zr, and the balance of Fe and impurities.
Further, said Fe23Zr6And Fe2The M-Laves phase co-reinforced FeCrAl stainless steel comprises the following components in percentage by mass: 13.0-15.0% of Cr, 4.0-5.0% of Al, 1.5-3.0% of Mo, 0.5-1.5% of Nb, 0-1.0% of Ta, 0.45-1.0% of Zr, and the balance of Fe and impurities.
Preferably, the Fe23Zr6And Fe2An M-Laves phase co-strengthened FeCrAl stainless steel, which is characterized by comprising the following components in percentage by massComprises the following components: 13.4% of Cr, 4.5% of Al, 2.0% of Mo2, 1.0% of Nb, 0.45% of Zr, and the balance of Fe and impurities.
The second purpose of the invention can be achieved by adopting the following technical scheme:
fe23Zr6And Fe2The preparation method of the M-Laves phase co-reinforced FeCrAl stainless steel comprises the following steps:
s1, smelting and casting: proportioning according to the composition of FeCrAl stainless steel, smelting and casting into an alloy ingot;
s2, homogenizing: preserving the heat of the alloy ingot for 0.5-2 h at 1150-1200 ℃, then taking out, and air-cooling to room temperature;
s3, hot forging: placing the alloy ingot obtained in the step S2 in a muffle furnace, heating to 1150-1200 ℃, preserving heat for 10-30 min, taking out, and performing multi-pass hot forging to obtain an alloy bar;
s4, hot rolling: placing the alloy bar in a muffle furnace, heating to 750-850 ℃, preserving heat for 5-15 min, taking out, and performing multi-pass hot rolling to obtain an alloy plate;
s5, aging treatment: and (3) heating the muffle furnace to 800 ℃ of 700-.
Further, the initial forging temperature of the multi-pass hot forging is more than or equal to 1050 ℃, the final forging temperature is more than or equal to 850 ℃, and the total forging amount is 40-50%.
When the multi-pass hot rolling is carried out, the single-pass rolling reduction is more than or equal to 5%, and the total rolling reduction is more than or equal to 60%.
Further, the preparation method further comprises the following steps: before hot forging, the alloy ingot obtained in S2 was descaled and then coated with a layer of Y2O3(ii) a Before hot rolling, the alloy bar is descaled and then coated with a layer of Y2O3。
Preferably, the temperature of the homogenization treatment is 1150 ℃, and the holding time is 0.5 h.
In the aging treatment, the temperature of the muffle furnace is 800 ℃, and the time of the aging treatment is 24 h.
Compared with the prior art, the invention has the beneficial effects that:
1. after the traditional Fe-Cr-Al ternary alloy is added with trace alloying elements such as Mo, Nb and the like to form a Laves phase, the temperature of the alloy is expected to reach 800-1000 ℃, but the Laves phase can be quickly dissolved into a matrix at the temperature of more than 1100 ℃, so that the mechanical property of the alloy is seriously reduced. After a large amount of research, the Zr content in the FeCrAl alloy is increased to be more than 0.4 wt%, and the preparation method is adopted to coordinate with other components in the alloy, so that Fe can be simultaneously precipitated in a matrix after the alloy is subjected to aging treatment at 700-800 DEG C2Nb-Laves phase, Fe2Zr-Laves phase and Fe23Zr6And the phases together strengthen the FeCrAl alloy. In which Fe23Zr6Specific Fe has never been reported in FeCrAl alloys2The M-Laves phase has higher thermal stability, still exists in a matrix more after being subjected to heat treatment at 1200 ℃/1h, can effectively inhibit the growth and coarsening of matrix grains, ensures that the grain size of the alloy subjected to the heat treatment at 1200 ℃ and the ultrahigh temperature is not more than 60 mu M and 120 mu M, is obviously lower than the grain size of FeCrAl alloy under the similar heat treatment process condition in the prior art, and has good high-temperature structure stability and strong mechanical property.
2. The invention carries out the preparation of FeCrAl alloy through smelting, homogenization treatment, hot forging, hot rolling and subsequent heat treatment processes, adds the hot forging process before hot rolling, can lead the alloy to deform more uniformly in different directions, can lead coarse primary precipitated phases in the alloy to be more broken and lead the matrix grains to be further refined, and is beneficial to the Fe in the subsequent heat treatment process23Zr6And Fe2And the precipitation of M-Laves improves the stability and the mechanical property of the alloy high-temperature structure.
Drawings
FIG. 1 TEM bright field image and selected area electron diffraction pattern of FeCrAl stainless steel of example 1 after aging treatment at 800 deg.C/24 h;
FIG. 2 is TEM bright field image and selected area electron diffraction pattern of FeCrAl stainless steel of example 1 after 1000 deg.C/1 h ultrahigh temperature remelting treatment;
FIG. 3 is TEM bright field image and selected area electron diffraction pattern of FeCrAl stainless steel of example 1 after 1200 deg.C/1 h ultrahigh temperature remelting treatment;
FIG. 4 tissue map of OM of FeCrAl stainless steel after ultra-high temperature remelting treatment in example 1;
FIG. 5 is a graph showing OM organization of FeCrAl stainless steel after being subjected to ultra-high temperature remelting treatment;
in the figure: a. ultra-high temperature redissolution treatment at 1100 ℃/1 h; b. and (4) carrying out ultrahigh temperature remelting treatment at 1200 ℃/1 h.
Detailed Description
The present invention is further described with reference to the accompanying drawings and the detailed description, and it should be noted that, in the case of no conflict, any combination between the embodiments or technical features described below may form a new embodiment.
Fe23Zr6And Fe2The M-Laves phase co-reinforced FeCrAl stainless steel comprises the following components in percentage by mass: 13.0-15.0% of Cr, 4.0-5.0% of Al, 1.5-3.0% of Mo, 0.5-1.5% of Nb, 0-1.0% of Ta, 0.4-1.0% of Zr, and the balance of Fe and impurities.
As a further preferred embodiment, Fe23Zr6And Fe2The M-Laves phase co-reinforced FeCrAl stainless steel comprises the following components in percentage by mass: 13.0-15.0% of Cr, 4.0-5.0% of Al, 1.5-3.0% of Mo, 0.5-1.5% of Nb, 0-1.0% of Ta, 0.45-1.0% of Zr, and the balance of Fe and impurities.
The existing Fe- (13-15) Cr- (4-5) Al (wt.%) ternary alloy has excellent corrosion resistance, high-temperature steam oxidation resistance and neutron irradiation resistance, but the high-temperature mechanical property of the ternary alloy is insufficient at the temperature of over 800 ℃ due to no second phase precipitation, after a certain amount of Mo, Nb and other trace alloying elements are added to form a Laves phase, the use temperature of the ternary alloy is expected to reach 800-1000 ℃, meanwhile, the precipitation of the Laves phase does not consume Al and Cr in a matrix, and the high-temperature steam oxidation resistance and the corrosion resistance of the ternary alloy can be ensured. However, the Laves phase dissolves rapidly into the matrix above 1100 ℃, resulting in severe degradation of the mechanical properties of the alloy. Therefore, an intermetallic compound with higher thermal stability needs to be introduced into the FeCrAl alloy to improve the structural stability and the mechanical property of the alloy under accident conditions (1000-1200 ℃).
Through changing the components and the process of FeCrAl alloy, the applicant of the invention finds that Fe can be obtained by combining proper process when the Zr content in the alloy is more than 0.4 wt.% in cooperation with other alloy elements2Nb、Fe2Zr-Laves phase and Fe23Zr6Co-strengthening FeCrAl alloy with Fe23Zr6It has never been reported in FeCrAl alloy that the alloy still exists in a matrix after heat treatment at 1200 ℃/1h, and the coarsening of crystal grains is effectively inhibited. Thus, Fe of the present invention23Zr6And Fe2The M-Laves phase co-reinforced FeCrAl stainless steel is expected to become a novel ATF cladding material.
In the FeCrAl alloy of the invention:
1) the element Cr is a main element for providing corrosion resistance, and the Tammann law indicates that when Cr is added into Fe to form a solid solution, the electrode potential of the Cr changes abruptly (n/8 law) along with the increase of Cr content, namely the atomic percent (at.%) of Cr reaches 12.5 percent and 25%. multidot.; however, since the sigma- (FeCr) and alpha' -Cr phases are easily induced by too high Cr content to deteriorate the mechanical properties of the alloy, the Cr content in the present invention is 13.0 to 15.0 wt.% in view of the corrosion resistance and mechanical properties of the alloy.
2) The element Al is the main element for ensuring the excellent high-temperature steam oxidation resistance of the alloy, because Al can form compact and continuous Al on the surface of the alloy2O3The higher the Al content, the better the oxidation resistance of the alloy, but too high Al content can seriously degrade the processability of FeCrAl alloy. Therefore, the Al content in the present invention is 3.0 to 5.0 wt.%.
3) The element Mo can improve the high-temperature strength of the material by solid-solution strengthening and also can improve the pitting corrosion resistance of the alloy, but Mo is also an element which promotes the precipitation of the sigma phase. Therefore, in the present invention, the Mo content is set to 1.5 to 3.0 wt.%.
4) The elements Nb and Ta are both Fe2An M-Laves phase forming element, which may be present below 1100 ℃,especially Fe2A Ta-Laves phase; however, too high Nb and Ta contents promote a large amount of Laves phase to precipitate and aggregate, which brings inconvenience to alloy processing. Therefore, in the present invention, the contents of Nb and Ta are set to 0.5 to 1.5 wt.% and 0 to 1.0 wt.%, respectively.
5) The element Zr is not only a Laves phase forming element, but also Fe23Z6Forming elements, the applicant's findings indicate that only Fe is formed in FeCrAl alloys when the Zr content is below 0.3 wt.%2Nb、Fe2The Laves phase in the form of Zr and the like can precipitate Fe when the Zr content is higher than 0.4 wt%23Z6And (4) phase(s). Therefore, in the invention, the Zr content is set to be 0.4-1.0 wt.%, which is beneficial to Fe23Z6And (4) separating out a phase.
Fe23Zr6And Fe2The preparation method of the M-Laves phase co-reinforced FeCrAl stainless steel comprises the following steps:
s1, smelting and casting: proportioning according to the composition of FeCrAl stainless steel, smelting and casting to form an alloy ingot;
s2, homogenizing: preserving the heat of the alloy ingot obtained in the step S1 at 1150-1200 ℃ for 0.5-2 h, taking out, and air-cooling to room temperature;
s3, hot forging: descaling the alloy ingot obtained in S2, and coating a layer of Y2O3Then placing the alloy bar into a muffle furnace, heating to 1150-1200 ℃, preserving heat for 10-30 min, taking out, and performing multi-pass hot forging to obtain an alloy bar; the initial forging temperature of the multi-pass hot forging is more than or equal to 1050 ℃, the final forging temperature is more than or equal to 850 ℃, and the total forging amount is 40-50%;
s4, hot rolling: descaling the alloy bar obtained in S3, and coating a layer of Y2O3Then placing the alloy plate in a muffle furnace, heating to 750-850 ℃, preserving heat for 5-15 min, taking out and carrying out multi-pass hot rolling to obtain an alloy plate; when multi-pass hot rolling is carried out, the single-pass rolling reduction is more than or equal to 5 percent, and the total rolling reduction is more than or equal to 60 percent;
s5, aging treatment: and (3) heating the muffle furnace to 800 ℃ of 700-.
Example 1
FeCrAl stainless steel with Fe as component78.65Al4.5Cr13.4Mo2.0Nb1.0Zr0.45(wt.%), prepared by the following method:
(1) preparing raw materials according to the proportion of the alloy components by using high-purity metal as a raw material, smelting the alloy by using an induction smelting furnace, and casting the molten metal into a cylindrical crucible after the molten metal is uniformly smelted to obtain a cylindrical ingot with the diameter of 40mm and the length of 60 mm;
(2) carrying out homogenization treatment on the cast ingot obtained in the step (1) at 1150 ℃ for 0.5h in a muffle furnace to eliminate segregation tissues in the alloy, taking out a sample after reaching the heat preservation time, and air-cooling to room temperature;
(3) carrying out hot forging on the ingot obtained in the step (2), taking out an oxide layer on the surface of the alloy ingot before the hot forging, and coating a layer of Y2O3Placing the sample in a muffle furnace, heating to 1150 ℃, preserving heat for 10min to enable the internal and external temperatures of the sample to be consistent, taking out the sample to perform multi-pass hot forging, wherein the initial forging temperature is not lower than 1050 ℃ and the final forging temperature is not lower than 850 ℃ in the hot forging process; the total forging amount of the hot forging is 50 percent, and a bar with the diameter of 20mm is finally obtained;
and (4): hot rolling the bar obtained in the step (3), removing surface scale and coating Y before hot rolling2O3Placing the sample in a muffle furnace, heating to 800 ℃, preserving the temperature for 10min to make the internal and external temperatures of the sample consistent, taking out the sample, and carrying out multi-pass hot rolling, wherein the single-pass reduction is not less than 5%, the total reduction is 65%, and finally obtaining a plate with the thickness of 7 mm;
and (5): and (3) after the temperature of the muffle furnace rises to 800 ℃, putting the alloy plate obtained in the step (4) into the muffle furnace for aging treatment for 24 hours, taking out the plate, and cooling the plate to room temperature in the air to obtain the FeCrAl stainless steel of the embodiment.
Comparative example 1
FeCrAl stainless steel with Fe as component78.83Al4.6Cr13.5Mo2.0Nb1.0Zr0.07(wt.%), the comparative example FeCrAl stainless steel was made in the same way as example 1,and will not be described in detail herein.
Test example
(1) TEM tissue characterization was performed on FeCrAl stainless steel of example 1, and the obtained TEM bright field image and the corresponding selected area electron diffraction pattern are shown in FIG. 1.
As can be seen from FIG. 1, Fe having a size of less than 400nm is diffused and precipitated in the FeCrAl stainless steel matrix of example 123Z6And Fe2Nb、Fe2Zr-Laves phase, and there is little difference in the composition of the three intermetallic compounds at this time.
(2) The FeCrAl stainless steels of example 1 and comparative example 1 were subjected to ultra high temperature remelting treatment at different temperatures for 1h to simulate the texture change of the clad material under the conditions of loss of coolant accident and OM and TEM texture characterization of the alloys in different heat treatment states, the results are shown in fig. 2-5.
FIG. 2 is a TEM bright field image and a corresponding selected area electron diffraction pattern of FeCrAl stainless steel of example 1 after 1000 deg.C/1 h ultrahigh temperature remelting treatment. As can be seen from FIG. 2, only Fe remains in the alloy23Z6And Fe2Nb-Laves phase, Fe2Complete dissolution of Zr-Laves occurs, indicating Fe23Z6And Fe2Nb to Fe2Zr has higher thermal stability. At this time, the point composition analysis result showed Fe23Zr6Significant Zr enrichment occurs while Nb is depleted.
FIG. 3 is a TEM bright field image and a corresponding selected area electron diffraction pattern of FeCrAl stainless steel of example 1 after 1200 deg.C/1 h ultrahigh temperature remelting treatment. As can be seen from FIG. 3, only Fe remains in the FeCrAl alloy23Z6Phase of Fe2Nb and Fe2Complete dissolution of Zr-Laves occurs, indicating Fe23Z6Specific to Fe2M-Laves has higher thermal stability. At this time, the point composition analysis result showed Fe23Z6Only Zr in the alloy is enriched, and Nb is completely dissolved back into the matrix, thereby causing Fe2And (4) re-dissolving the Nb-Laves phase.
FIG. 4 is a graph of OM structure of FeCrAl stainless steel of example 1 after 1100 deg.C/1 h (a), 1200 deg.C/1 h (b) ultra-high temperature remelting treatment. As can be seen from FIG. 4, the FeCrAl stainless steel of example 1 has a grain size of 59 μm and 108 μm after ultra-high temperature heat treatment at 1100 deg.C/1 h and 1200 deg.C/1 h, respectively.
FIG. 5 is a OM structural diagram of FeCrAl stainless steel of comparative example 1 after 1100 deg.C/1 h (a), 1200 deg.C/1 h (b) ultra-high temperature remelting treatment. As can be seen from FIG. 5, the FeCrAl stainless steel has a grain size of 131 μm and 309 μm after being subjected to ultra-high temperature heat treatment at 1100 ℃/1h and 1200 ℃/1h, respectively. Comparing fig. 4 and 5, it can be seen that the grain size of the FeCrAl stainless steel of the present application after ultra-high temperature heat treatment is significantly lower than that of comparative example 1, coarsening of the grain size at ultra-high temperature is greatly inhibited, and the high temperature stability of the alloy is significantly improved.
Comparative example 2
An FeCrAl alloy for nuclear fuel cladding, the composition and preparation method of the alloy are the same as those described in example 1 of patent application publication No. CN 109652628A.
As can be seen from the grain size detection and the results recorded in the table, the FeCrAl alloy of the comparative example has the grain size of more than 70 μm after recrystallization annealing at 900 ℃/10min, and has the grain size of more than 300 μm after recrystallization annealing at 1100 ℃/10min, which is far larger than the grain size (59 μm) of the alloy in the embodiment 1 of the invention under the same heat treatment condition. Thus, it is shown that Fe of the present invention23Z6And Fe2FeCrAl alloys co-strengthened with M-Laves phase due to high thermal stability of Fe23Z6The high-temperature structure stability of the alloy is obviously improved, and coarsening of the grain size is obviously inhibited, so that the alloy is expected to become a light water reactor ATF cladding material.
The above embodiments are only preferred embodiments of the present invention, and the scope of the present invention is not limited thereto, and any insubstantial changes and substitutions made by those skilled in the art based on the present invention are within the scope of the present invention claimed in the present invention.
Claims (9)
1. Fe23Zr6And Fe2An M-Laves phase co-strengthened FeCrAl stainless steel, which is characterized in thatThe composition comprises the following components in percentage by mass: 13.0-15.0% of Cr13.0-5.0% of Al4.0%, 1.5-3.0% of Mo0.5-1.5% of Nb0.5-1.5%, 0-1.0% of Ta, 0.4-1.0% of Zr, and the balance of Fe and impurities;
said Fe23Zr6And Fe2The preparation method of the M-Laves phase co-reinforced FeCrAl stainless steel comprises the following steps:
s1, smelting and casting: proportioning according to the composition of FeCrAl stainless steel, smelting and casting into an alloy ingot;
s2, homogenizing treatment: preserving the heat of the alloy ingot for 0.5-2 h at 1150-1200 ℃, then taking out, and air-cooling to room temperature;
s3, hot forging: placing the alloy ingot obtained in the step S2 in a muffle furnace, heating to 1150-1200 ℃, preserving heat for 10-30 min, taking out, and performing multi-pass hot forging to obtain an alloy bar;
s4, hot rolling: placing the alloy bar in a muffle furnace, heating to 750-850 ℃, preserving heat for 5-15 min, taking out, and performing multi-pass hot rolling to obtain an alloy plate;
s5, aging treatment: and (3) heating the muffle furnace to 800 ℃ of 700-.
2. Fe of claim 123Zr6And Fe2The M-Laves phase co-reinforced FeCrAl stainless steel is characterized by comprising the following components in percentage by mass: 13.0-15.0% of Cr, 4.0-5.0% of Al, 1.5-3.0% of Mo, 0.5-1.5% of Nb, 0-1.0% of Ta, 0.45-1.0% of Zr, and the balance of Fe and impurities.
3. Fe of claim 123Zr6And Fe2The M-Laves phase co-reinforced FeCrAl stainless steel is characterized by comprising the following components in percentage by mass: 13.4% of Cr, 4.5% of Al, 2.0% of Mo, 1.0% of Nb1.45% of Zr, and the balance of Fe and impurities.
4. A method according to any one of claims 1 to 3Fe of item (i)23Zr6And Fe2The preparation method of the M-Laves phase co-reinforced FeCrAl stainless steel is characterized by comprising the following steps of:
s1, smelting and casting: proportioning according to the composition of FeCrAl stainless steel, smelting and casting into an alloy ingot;
s2, homogenizing: preserving the heat of the alloy ingot for 0.5-2 h at 1150-1200 ℃, then taking out, and air-cooling to room temperature;
s3, hot forging: placing the alloy ingot obtained in the step S2 in a muffle furnace, heating to 1150-1200 ℃, preserving heat for 10-30 min, taking out, and performing multi-pass hot forging to obtain an alloy bar;
s4, hot rolling: placing the alloy bar in a muffle furnace, heating to 750-850 ℃, preserving heat for 5-15 min, taking out, and performing multi-pass hot rolling to obtain an alloy plate;
s5, aging treatment: and (3) heating the muffle furnace to 800 ℃ of 700-.
5. The preparation method according to claim 4, wherein the multi-pass hot forging has a forging start temperature of 1050 ℃ or higher, a forging finish temperature of 850 ℃ or higher, and a total forging amount of 40-50%.
6. The preparation method according to claim 4, wherein during the multi-pass hot rolling, the single-pass rolling reduction is not less than 5%, and the total rolling reduction is not less than 60%.
7. The method of claim 4, further comprising: descaling the alloy ingot obtained in S2 before hot forging, and then coating a layer of Y2O3(ii) a Before hot rolling, the alloy bar is descaled and then coated with a layer of Y2O3。
8. The method according to claim 4, wherein the homogenization treatment temperature is 1150 ℃ and the holding time is 0.5 h.
9. The preparation method according to claim 4, wherein in the aging treatment, the muffle furnace temperature is 800 ℃ and the aging treatment time is 24 h.
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