CN114774802A - Method for improving mechanical and electrical resistance performance of FeCrAl-based resistance alloy and FeCrAl-based resistance alloy - Google Patents
Method for improving mechanical and electrical resistance performance of FeCrAl-based resistance alloy and FeCrAl-based resistance alloy Download PDFInfo
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Abstract
The invention discloses a method for improving mechanics and resistance performance of FeCrAl-based resistance alloy and FeCrAl-based resistance alloy, which is characterized in that alloy elements Ti and Si are introduced into the FeCrAl alloy to induce and form a multi-component nano disperse phase which is coherent with a BCC matrix of the FeCrAl alloy; the optimized alloy comprises the following chemical compositions: 52-59% of Fe, 25-29% of Cr, 11-15% of Al, 2.5-5% of Ti and 1.5-3% of Si. The alloy matrix obtained by the method of the invention has the BCC structural structure characteristic, and L2 is dispersed and distributed in the matrix1Structured multicomponent nanoparticles, nanoparticlesThe alloy and the BCC matrix keep a completely coherent orientation relation, so that the compression strength of the alloy is obviously improved, the deformability is enhanced, the resistivity is improved, the temperature coefficient of the resistivity is reduced, and the comprehensive improvement of the mechanical and electrical resistance is shown.
Description
Technical Field
The invention belongs to the technical field of metal material preparation, and particularly relates to a method for improving the mechanical and electrical resistance of a FeCrAl-based resistance alloy and the FeCrAl-based resistance alloy.
Background
Resistive alloys with high resistivity (> 100 μ Ω · cm) and Temperature Coefficient of Resistivity (TCR) (<100ppm/K) play a crucial role in many key areas such as high precision electronic measurement systems, GPS positioning systems, data storage, thermoelectric devices, and temperature control sensors. An iron-chromium-aluminum (FeCrAl) -based alloy is used as a resistance alloy because of its advantages of high resistivity, high strength, excellent high-temperature oxidation resistance, low cost, and the like.
With increasing industrial development, a low-cost resistance alloy with high strength, high deformability, high resistivity and low temperature coefficient of resistivity is required to further improve the processability and sensitivity and promote the miniaturization and integration development of electronic devices. However, the following factors limit the further development and practical application of conventional FeCrAl-based alloys, which have the advantage of low cost, as resistive materials. First, the conventional method for improving the strength and resistivity of Fe-Cr-a1 alloy is to increase the Cr and Al contents, but the high Cr and Al contents easily cause stress concentration to aggravate brittle fracture, so that the workability is poor, i.e., the high strength and high deformability are difficult to combine. Secondly, the temperature coefficient of resistivity can be adjusted by adjusting the proportion of Fe, Cr and Al, but the temperature coefficients of high resistivity and low resistivity are difficult to have at the same time.
Disclosure of Invention
This section is for the purpose of summarizing some aspects of embodiments of the invention and to briefly introduce some preferred embodiments. In this section, as well as in the abstract and the title of the invention of this application, simplifications or omissions may be made to avoid obscuring the purpose of the section, the abstract and the title, and such simplifications or omissions are not intended to limit the scope of the invention.
In view of the above and/or the defects existing in the prior art, the invention provides a method for improving the mechanical and electrical resistance of a FeCrAl-based resistance alloy and a FeCrAl-based resistance alloy, and solves the technical problems that the traditional FeCrAl resistance alloy is difficult to combine high resistivity and low resistivity temperature coefficient, and has poor synergistic capability of high strength and high deformability.
One of the objects of the present invention is to provide a FeCrAl-based resistance alloy that can achieve an excellent combination of properties of high strength, high deformability, high resistivity, and low resistivity temperature coefficient over a wide temperature range.
The "wide temperature range" referred to herein in the present invention means a wide temperature range of 673K or less. The high strength refers to the characteristics that the compressive yield strength of the alloy material obtained by the invention is 600-1400 MPa, and the compressive strength is 900-2200 MPa. The term "high deformability" used in the present invention means that the alloy material obtained by the present invention has a characteristic of compressive strain of 10% or more. The high resistivity refers to the characteristic that the alloy material obtained by the invention has the resistivity of 140-230 mu omega cm. The low-resistivity temperature coefficient refers to the characteristic that the alloy material obtained by the invention has the temperature coefficient of resistivity of-200-100 ppm/K.
The invention provides the following technical scheme: a FeCrAl-based resistance alloy comprises the following components in atomic percent: 52-59% of Fe, 25-29% of Cr, 11-15% of Al, 2.5-5% of Ti and 1.5-3% of Si;
wherein the atomic percentage sum of Fe, Cr and Al is more than or equal to 92% and less than or equal to 96%, the atomic percentage sum of Ti and Si is less than or equal to 8% and more than or equal to 4%, and the atomic percentage sum of each component is 100%.
For example, the alloy of the present invention may be, but is not limited to, 54% Fe, 27% Cr, 13.5% Al, 4% Ti, 1.5% Si; or 55% Fe, 28% Cr, 12% Al, 3% Ti, 2% Si; or 52% Fe, 29% Cr, 14% Al, 2% Ti, 3% Si; or 59% Fe, 26% Cr, 11% Al, 2.5% Ti, 1.5% Si; or 56% Fe, 25% Cr, 13% Al, 3.5% Ti, 2.5% Si, etc.
The invention also aims to provide a method for improving the mechanical and electrical resistance performance of FeCrAl-based resistance alloy, which is characterized in that alloy elements Ti and Si are introduced into FeCrAl alloy to induce and form multi-component nano disperse phase which is coherent with BCC matrix of the FeCrAl alloy;
wherein the sum of atomic percentages of Ti and Si accounts for 4-8% of the total.
As used herein, the term "BCC matrix" refers to a body centered cubic matrix.
The term "dispersed phase" as used herein refers to a fine, dispersed solid phase precipitated from a supersaturated solid solution.
As a preferred scheme of the method for improving the mechanical and electrical resistance performance of the FeCrAl-based resistance alloy, the method comprises the following steps: the sum of atomic percentages of Ti accounts for 2.5-5% of the total;
the sum of the atomic percentages of Si accounts for 1.5-3% of the total.
As a preferred scheme of the method for improving the mechanical and electrical resistance performance of the FeCrAl-based resistance alloy, the method comprises the following steps: the FeCrAl alloy consists of Fe, Cr and Al, wherein the sum of the atomic percentages of Fe accounts for 52-59% of the total, the sum of the atomic percentages of Cr accounts for 25-29% of the total, and the sum of the atomic percentages of Al accounts for 11-15% of the total.
As a preferred scheme of the method for improving the mechanical and electrical resistance performance of the FeCrAl-based resistance alloy, the method comprises the following steps: the raw materials of each component are proportioned according to the atomic proportion of each component of the alloy, and the alloy material is obtained by smelting and casting under the protection of vacuum or inert gas.
The term "smelting" as used herein refers to a pyrometallurgical process in which a metal material is put into a heating furnace to produce a crude metal, and may be carried out using existing equipment such as a suspension furnace, an induction furnace, a blast furnace, a reverberatory furnace, and an electric arc furnace.
As a preferred scheme of the method for improving the mechanical and electrical resistance performance of the FeCrAl-based resistance alloy, the method comprises the following steps: the smelting is carried out under the vacuum condition, and the vacuum degree in the furnace is maintained to be 1-0.0001 Pa.
As a preferred scheme of the method for improving the mechanical and electrical resistance performance of the FeCrAl-based resistance alloy, the method comprises the following steps: the smelting is carried out under the protection of inert gas, and the pressure of the inert gas in the furnace is maintained to be 0.000001-5 MPa.
As a preferred scheme of the method for improving the mechanical and electrical resistance performance of the FeCrAl-based resistance alloy, the method comprises the following steps: and smelting at 1623-2473K, and keeping the temperature for 0.01-1 h.
As a preferred scheme of the method for improving the mechanical and electrical resistance performance of the FeCrAl-based resistance alloy, the method comprises the following steps: the raw materials of each component are pure metal element particles or blocks with the purity higher than 99 wt.%, and are repeatedly smelted for 3-8 times.
As a preferred scheme of the method for improving the mechanical and electrical resistance performance of the FeCrAl-based resistance alloy, the method comprises the following steps: the obtained alloy material has the compressive yield strength of 600-1400 MPa, the compressive strength of 900-2200 MPa and the compressive strain of more than 10%; the resistivity of the alloy is 140-230 mu omega cm in a wide temperature range below 673K; the temperature coefficient of resistivity is-200 to 100 ppm/K.
Compared with the prior art, the invention has the following beneficial effects:
the invention provides a new method, namely, a multicomponent nano disperse phase which is coherent with a BCC matrix is formed by introducing a proper amount of alloy elements Ti and Si. The multicomponent L21The nano-particle phase obviously improves the compressive strength of the alloy, enhances the deformability, improves the resistivity, reduces the temperature coefficient of the resistivity and shows comprehensive improvement of the mechanical and electrical resistance properties. The method provided by the invention has simple preparation process, does not need to carry out fussy heat treatment, and can obtain excellent performance in a casting state. The method is expected to provide a new method for solving the problems that the traditional FeCrAl resistance alloy is difficult to have both high resistivity and low resistivity temperature coefficient, and has poor synergistic capability of high strength and high deformability.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings required to be used in the description of the embodiments are briefly introduced below, and it is obvious that the drawings in the description below are only some embodiments of the present invention, and it is obvious for those skilled in the art that other drawings can be obtained according to the drawings without inventive labor. Wherein:
FIG. 1 is an XRD spectrum of FeCrAl-based resistance alloy obtained in example 1 of the present invention.
FIG. 2 is an EBSD phase distribution diagram and an inverse polarity diagram (IPF) of FeCrAl-based resistance alloy obtained in example 1 of the present invention.
FIG. 3 is a scanning electron microscope topography of the microstructure of the FeCrAl-based resistance alloy obtained in example 1 of the present invention.
FIG. 4 shows a high angle annular dark field image (HAADF) and a selected area electron diffraction spectrum of the FeCrAl-based resistance alloy obtained in example 1 of the present invention under a transmission electron microscope.
FIG. 5 is an HAADF image of FeCrAl-based resistance alloy obtained in example 1 of the present invention under a transmission electron microscope and a corresponding energy spectrum plane distribution image.
FIG. 6 is a resistivity-temperature graph of FeCrAl-based resistance alloy obtained in example 1 of the present invention.
FIG. 7 is a graph of compressive engineering stress-strain at room temperature for FeCrAl-based resistance alloy obtained in example 1 of the present invention.
FIG. 8 is a graph of compressive engineering stress-strain at 673K for FeCrAl-based resistance alloy obtained in example 1 of the present invention.
FIG. 9 is a scanning electron microscope topography of the microstructure of FeCrAl-based resistance alloy obtained in example 2 of the present invention.
FIG. 10 is a graph of resistivity versus temperature for FeCrAl-based resistance alloys obtained in example 2 of the present invention.
FIG. 11 is a scanning electron microscope morphology image of the microstructure of the FeCrAl-based resistance alloy obtained in example 3 of the present invention.
FIG. 12 is a graph of resistivity versus temperature for FeCrAl-based resistance alloys obtained in example 3 of the present invention.
FIG. 13 is a graph of room temperature compressive engineering stress-strain for FeCrAl-based resistance alloy obtained in example 3 of the present invention.
FIG. 14 is a scanning electron micrograph of the microstructure of the alloy obtained in comparative example 1 of the present invention.
FIG. 15 is a graph of resistivity versus temperature for the alloy of comparative example 1 of the present invention.
FIG. 16 is a graph of room temperature compressive engineering stress versus strain for the alloy obtained in comparative example 1 of the present invention.
FIG. 17 is a SEM image of the microstructure of the alloy obtained in comparative example 2 of the present invention.
FIG. 18 is a graph of resistivity versus temperature for the alloy of comparative example 2 of the present invention.
FIG. 19 is a graph of room temperature compressive engineering stress versus strain for the alloy of comparative example 2 of the present invention.
FIG. 20 is an XRD spectrum of the alloy material provided by comparative example 3 of the present invention.
FIG. 21 is an EBSD phase distribution diagram and an Inverse Pole Figure (IPF) of the alloy material provided by comparative example 3 of the present invention.
FIG. 22 is a SEM image of the microstructure of the alloy material provided by comparative example 3 of the present invention.
Fig. 23 is a scanning electron microscope backscattered electron image and a corresponding energy spectrum plane distribution image of the alloy material provided by comparative example 3 of the present invention.
FIG. 24 is a resistivity-temperature plot of the alloy material provided in comparative example 3 of the present invention.
FIG. 25 is a graph of compressive engineering stress-strain at room temperature for the alloy material provided in comparative example 3 of the present invention.
FIG. 26 is a SEM image of the microstructure of the alloy material provided by comparative example 4 of the present invention.
FIG. 27 is a resistivity-temperature plot of the alloy material provided by comparative example 4 of the present invention.
FIG. 28 is a graph of compressive engineering stress-strain at room temperature for the alloy material provided in comparative example 4 of the present invention.
Detailed Description
In order to make the aforementioned objects, features and advantages of the present invention more comprehensible, specific embodiments thereof are described in detail below with reference to examples of the specification.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, but the present invention may be practiced in other ways than those specifically described and will be readily apparent to those of ordinary skill in the art without departing from the spirit of the present invention, and therefore the present invention is not limited to the specific embodiments disclosed below.
Furthermore, the references herein to "one embodiment" or "an embodiment" refer to a particular feature, structure, or characteristic that may be included in at least one implementation of the present invention. The appearances of the phrase "in one embodiment" in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments mutually exclusive of other embodiments.
Example 1
According to the chemical formula Fe55Cr28Al12Ti3Si2(atomic percent) batching, wherein the raw materials use blocks corresponding to all pure elements; suspension smelting is adopted, smelting is carried out under the inert gas protective atmosphere, and the smelting is carried out repeatedly for 4 times; and (3) pumping the vacuum degree to 0.001 Pa during smelting, then filling argon gas until the air pressure is slightly positive, keeping the smelting temperature at 1873K for 5min, and casting into a cuboid shape to obtain the FeCrAl-based resistance alloy of the embodiment 1.
As can be seen from FIGS. 1 and 2, the main phase of the FeCrAl-based resistance alloy obtained in example 1 is a BCC solid solution structure. As can be seen from FIG. 3, there are dispersed nanoparticles in the FeCrAl-based resistance alloy obtained in example 1. As can be seen from FIG. 4, the nano-dispersed particles in the FeCrAl-based resistance alloy obtained in example 1 exhibited L21Structure and is completely coherent with the BCC matrix, the particle size is 45 +/-11 nm, and the area percentage is 33% +/-4%. As can be seen from FIG. 5, the FeCrAl-based resistance alloy obtained in example 1 has L2 dispersed therein1The nano phase of the structure is simultaneously enriched with Al, Ti and Si elements and barren Fe and Cr elements. As can be seen from FIG. 6, the room temperature resistivity of the FeCrAl-based resistance alloy obtained in example 1 can be as high as-183 μ Ω. cm, and still be maintained at-181 μ Ω. cm when the temperature is raised to 673K. The temperature coefficient of resistivity in the temperature range of room temperature to 673K is as low as-35 +/-10 ppm/K. As can be seen from FIG. 7, the FeCrAl-based resistance alloy obtained in example 1 has a compressive yield strength of about 1096MPa, a compressive strength of about 1694MPa and a compressive strain of about 20% at room temperature. As can be seen from FIG. 8, the FeCrAl-based resistance alloy obtained in example 1 has a compressive yield strength of about 1055MPa, a compressive strength of up to 1980MPa, and a compressive strain of up to 35% at 673K.
Example 2
According to the chemical formula Fe55Cr28Al12Ti3Si2(atomic percentage) burdening, wherein the raw material uses blocks corresponding to each pure element; suspension smelting is adopted, smelting is carried out under the inert gas protective atmosphere, and the smelting is carried out repeatedly for 4 times; and (3) pumping the vacuum degree to 0.001 Pa during smelting, then filling argon gas to slightly positive pressure, keeping the smelting temperature at 1873K, keeping the temperature for 5min, casting the alloy into a cuboid shape, raising the temperature of the alloy from room temperature to 673K at the temperature raising rate of 4K/min, and then rapidly quenching to obtain the FeCrAl-based resistance alloy of the embodiment 2.
As can be seen from FIGS. 9 and 10, L2 in FeCrAl-based resistance alloy obtained in example 21The structured nano dispersed phase still exists stably at the temperature of 673K, and the temperature coefficient of low resistivity (-46ppm/K) in the temperature range of room temperature to 673K is determined.
Example 3
According to the chemical formula Fe54Cr27Al13.5Ti4Si1.5(atomic percentage) burdening, wherein the raw material uses blocks corresponding to each pure element; arc melting is adopted, melting is carried out under the inert gas protective atmosphere, and the melting is repeated for 4 times; during smelting, the vacuum degree is pumped to 0.001 Pa, then argon is injected until the pressure is slightly positive, and the smelting temperature is 1873K, thus obtaining the FeCrAl-based resistance alloy of the embodiment 3.
As can be seen from FIG. 11, the FeCrAl-based resistance alloy obtained in example 3 has dispersed nanoparticles. As can be seen from FIG. 12, the room temperature resistivity of the FeCrAl-based resistance alloy obtained in example 3 can reach 184 μ Ω. cm, and still maintains 180 μ Ω. cm when the temperature is raised to 673K. The temperature coefficient of resistivity in the temperature range of room temperature to 673K is as low as-58 ppm/K. As can be seen from FIG. 13, the FeCrAl-based resistance alloy obtained in example 3 has a compressive yield strength of about 1243MPa, a compressive strength of about 1823MPa, and a compressive strain of about 17%.
Comparative example 1
According to the chemical formula Fe58Cr22Al15Ti1Si4(atomic percentage) burdening, wherein the raw material uses blocks corresponding to each pure element; arc melting is adopted, the melting is carried out under the inert gas protective atmosphere, and the steps are repeatedSmelting for 4 times; during smelting, the vacuum degree is pumped to 0.001 Pa, then argon is injected until the pressure is slightly positive, and the smelting temperature is 1873K, thus obtaining the alloy in the comparative example 1.
It can be seen from fig. 14 that the alloy obtained in comparative example 1 has evidence of the presence of nanoparticles. It can be seen from FIG. 15 that the room temperature resistivity of the alloy obtained in comparative example 1 was about 204. mu. Ω. cm. The temperature coefficient of resistivity over the temperature range of room temperature to 673K is about-159 ppm/K. It can be seen from FIG. 16 that the alloy obtained in comparative example 1 has a compressive yield strength of about 850MPa, a compressive strength of about 1878MPa and a compressive strain of about 30%.
Comparative example 2
According to the chemical formula Fe56Cr25Al14Ti2Si3(atomic percentage) burdening, wherein the raw material uses blocks corresponding to each pure element; arc melting is adopted, melting is carried out under the inert gas protective atmosphere, and the melting is repeated for 4 times; during smelting, the vacuum degree is pumped to 0.001 Pa, then argon is injected until the pressure is slightly positive, and the smelting temperature is 1873K, thus obtaining the alloy in the comparative example 2.
The presence of dispersed nanoparticles in the alloy obtained in comparative example 2 can be seen in fig. 17. It can be seen from FIG. 18 that the room temperature resistivity of the alloy obtained in comparative example 2 was about 197. mu. Ω. cm. The temperature coefficient of resistivity over the temperature range of room temperature to 673K is about-171 ppm/K. It can be seen from FIG. 19 that the alloy obtained in comparative example 2 has a compressive yield strength of about 980MPa, a compressive strength of about 2026MPa and a compressive strain of about 30%.
Comparative example 3
According to the chemical formula Fe55Cr28Al12Ti3Si2(atomic percentage) burdening, wherein the raw material uses blocks corresponding to each pure element; suspension smelting is adopted, smelting is carried out under the inert gas protective atmosphere, and the smelting is carried out repeatedly for 4 times; during smelting, after the vacuum degree is pumped to 0.001 Pa, argon is filled until the air pressure is slightly positive, the smelting temperature is 1873K, the temperature is kept for 5min, and the mixture is cast into a cuboid shape; and then carrying out high-temperature homogenization treatment under the argon protection atmosphere (the argon pressure is 10Pa), the temperature is 1573K, and after 3 hours of homogenization treatment, carrying out oil quenching to obtain the alloy of the comparative example 3.
It can be seen from FIGS. 20 and 21 that the alloy obtained in comparative example 3 exhibits a single-phase BCC structure. Figures 22 and 23 further demonstrate that the alloy obtained in comparative example 3 does not have dispersed nanoparticles. As can be seen from FIG. 24, the temperature coefficient of resistivity of the alloy obtained in comparative example 3 was-163. + -.10 ppm/K in the temperature range from room temperature to 673K. As can be seen from FIG. 25, the alloy obtained in comparative example 3 has a compressive yield strength of about 1191MPa, a compressive strength of only 1254MPa and a compressive strain of only 8%.
Comparative example 4
According to the chemical formula Fe55Cr29Al16(atomic percent) batching, wherein the raw materials use blocks corresponding to all pure elements; adopting electric arc melting, melting under the inert gas protective atmosphere, and repeatedly melting for 4 times; during smelting, the vacuum degree is pumped to 0.001 Pa, then argon is injected until the pressure is slightly positive, and the smelting temperature is 1873K, thus obtaining the alloy of the comparative example 4.
As can be seen from FIG. 26, the alloy obtained in comparative example 4 has a single-phase BCC structure. As can be seen from FIG. 27, the temperature coefficient of resistivity of the alloy obtained in comparative example 4 was about-146 ppm/K in the temperature range from room temperature to 673K. As can be seen from fig. 28, the compressive yield strength of the alloy obtained in comparative example 4 is much lower than that of examples 1 or 2.
Comparative example 5
According to the disclosure of the published Metallurgical transactions A [ T.Naohara, A.Inoue, T.Minemura, T.Masumoto, K.Kumada, Metallurgical transactions A13 (1982) 337-343-]Of conventional Fe65Cr20Al15、Fe60Cr20Al20、Fe50Cr30Al20The room temperature resistivity of the alloy is 156 mu omega cm,180 mu omega cm and 186 mu omega cm respectively; the temperature coefficients of resistivity in the range of room temperature to 673K were-17 ppm/K, -73ppm/K and-85 ppm/K, respectively. I.e., temperature coefficients of high resistivity and low resistivity are difficult to achieve.
Comparing examples 1, 2 and 3, it can be seen that: the multi-component L2 completely compatible with BCC matrix and existing in the alloy optimized by the method provided by the invention1The nano dispersed phase can stably exist under 673K, and the optimized alloy has excellent medium-temperature mechanical property and simultaneously keeps high resistivity and resistivity-temperature stability within 673K.
Comparing example 1 with comparative examples 1 and 2, it is understood that the resistivity temperature stability of the alloy obtained when the contents of the introduced Ti and Si elements are out of the range of the present invention is significantly inferior to that of example 1.
Comparing example 1 with comparative example 3, it is clear that multicomponent L2 which is completely coherent with the BCC matrix and is provided by the process of the present invention is not present1The alloy of the nano dispersed phase, i.e., the alloy of comparative example 3, is inferior in compressive strength, compressive strain and temperature stability of resistivity to those of example 1. Comparing example 1 with comparative example 4, it is known that the alloy without introducing Ti and Si elements has a compressive yield strength much lower than that of the alloy optimized according to the present invention, and has poor temperature stability of resistivity. Namely, the invention is induced by introducing proper amount of alloy elements Ti and Si to form multi-component nano dispersed phase multi-component L2 which is coherent with a Body Centered Cubic (BCC) matrix1The nano dispersed phase can effectively improve the deformability and the resistivity-temperature stability within 673K. Comparing example 1 with comparative example 5, it can be seen that the alloy obtained by the method of the present invention has both high resistivity and low resistivity temperature coefficient.
The invention provides a method for improving the mechanics and the resistance performance of FeCrAl-based resistance alloy, namely, a multi-component nano disperse phase which is coherent with a BCC matrix is formed by introducing a proper amount of alloy elements Ti and Si. Has the following characteristics: firstly, proper amount of alloy elements Ti and Si are introduced to induce and form multi-component nano dispersed phase which is completely coherent with BCC matrix. The coherent multi-component nano disperse phase maintains high strength and simultaneously improves the work hardening capacity so as to improve the compressive strength and the compressive strain. Secondly, the presence of the multicomponent coherent nanodispersed phase reduces the temperature coefficient of resistivity. Moreover, the difference between the atomic radius of the added alloy elements Ti and Si and the atomic radius of the added alloy elements Fe and Cr is larger, larger lattice distortion is generated, the solid solution strengthening effect and the lattice scattering effect in the alloy are effectively improved, and the strength and the resistivity are further improved. In addition, compared with the traditional FeCrAl alloy, the alloy does not contain rare metal elements and can be developed into environment-friendly resistance alloy. The technical measures provided by the invention can realize excellent comprehensive characteristics of high strength, high deformability, high resistivity and low resistivity temperature coefficient in a wide temperature range.
It should be noted that the above-mentioned embodiments are only for illustrating the technical solutions of the present invention and not for limiting, 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 or equivalent substitutions may be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention, which should be covered by the claims of the present invention.
Claims (10)
1. An FeCrAl-based resistance alloy, which is characterized in that: the composition comprises the following components in atomic percentage: 52-59% of Fe, 25-29% of Cr, 11-15% of Al, 2.5-5% of Ti and 1.5-3% of Si;
wherein the atomic percentage sum of Fe, Cr and Al is more than or equal to 92 percent and less than or equal to 96 percent, the atomic percentage sum of Ti and Si is less than or equal to 8 percent and more than or equal to 4 percent, and the atomic percentage sum of all the components is 100 percent.
2. A method for improving the mechanical and electrical resistance performance of FeCrAl-based resistance alloy is characterized by comprising the following steps: introducing alloy elements Ti and Si into the FeCrAl alloy to induce and form a multi-component nano disperse phase which is coherent with a BCC matrix of the FeCrAl alloy;
wherein the sum of atomic percentages of Ti and Si accounts for 4-8% of the total.
3. A method for enhancing the mechanical and electrical resistance properties of a FeCrAl-based resistance alloy as claimed in claim 2, wherein: the sum of atomic percentages of Ti accounts for 2.5-5% of the total;
the sum of the atomic percentages of the Si accounts for 1.5-3% of the total.
4. A method for enhancing the mechanical and electrical resistance properties of a FeCrAl-based resistance alloy according to claim 2 or 3, wherein: the FeCrAl alloy consists of Fe, Cr and Al, wherein the sum of the atomic percentages of Fe accounts for 52-59% of the total, the sum of the atomic percentages of Cr accounts for 25-29% of the total, and the sum of the atomic percentages of Al accounts for 11-15% of the total.
5. A method for enhancing the mechanical and electrical resistance properties of a FeCrAl-based resistance alloy as defined in claim 4 wherein: the raw materials of each component are proportioned according to the atomic proportion of each component of the alloy and are smelted under the protection of vacuum or inert gas to obtain the alloy material.
6. A method for enhancing the mechanical and electrical resistance properties of a FeCrAl-based resistance alloy as defined in claim 5 wherein: the smelting is carried out under the vacuum condition, and the vacuum degree in the furnace is maintained to be 1-0.0001 Pa.
7. A method for enhancing the mechanical and electrical resistance properties of a FeCrAl-based resistance alloy as defined in claim 5, wherein: the smelting is carried out under the protection of inert gas, and the pressure of the inert gas in the furnace is maintained to be 0.000001-5 MPa.
8. A method for improving the mechanical and electrical resistance properties of a FeCrAl-based resistance alloy according to any one of claims 5 to 7, wherein: and smelting at 1623-2473K, and keeping the temperature for 0.01-1 h.
9. A method for enhancing the mechanical and electrical resistance properties of a FeCrAl-based resistance alloy as defined in claim 8, wherein: the raw materials of each component are pure metal element particles or blocks with the purity higher than 99 wt.%, and are repeatedly smelted for 3-8 times.
10. A method for enhancing the mechanical and electrical resistance properties of a FeCrAl-based resistance alloy as defined in any one of claims 2, 3, 5-7, and 9, wherein: the obtained alloy material has the compressive yield strength of 600-1400 MPa, the compressive strength of 900-2200 MPa and the compressive strain of more than 10%; the resistivity of the alloy is 140-230 mu omega cm in a wide temperature range below 673K; the temperature coefficient of resistivity is-200 to 100 ppm/K.
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| JP2023524857A JP2024517528A (en) | 2022-04-07 | 2022-11-25 | Method for improving the mechanical and resistance properties of FeCrAl-based resistance alloys and FeCrAl-based resistance alloys |
| PCT/CN2022/134252 WO2023193451A1 (en) | 2022-04-07 | 2022-11-25 | Method for improving mechanical and resistive performances of fecral-based resistive alloy, and fecral-based resistive alloy |
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| WO2023193451A1 (en) * | 2022-04-07 | 2023-10-12 | 中南大学 | Method for improving mechanical and resistive performances of fecral-based resistive alloy, and fecral-based resistive alloy |
| CN117026103A (en) * | 2023-08-08 | 2023-11-10 | 中南大学 | Multi-component soft magnetic alloy with high strength, high resistance and low resistance temperature coefficient, and preparation method and application thereof |
| CN117026103B (en) * | 2023-08-08 | 2024-10-29 | 中南大学 | Multi-component soft magnetic alloy with high strength, high resistance and low resistance temperature coefficient, and preparation method and application thereof |
Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6168757B1 (en) * | 1995-11-15 | 2001-01-02 | Alphatech, Inc. | Material formulation for galvanizing equipment submerged in molten aluminum and aluminum/zinc melts |
| US20020051727A1 (en) * | 2000-09-04 | 2002-05-02 | Roger Berglund | FeCrAI alloy |
| JP2006219728A (en) * | 2005-02-10 | 2006-08-24 | Tohoku Univ | Ferro-alloy for resistor having high resistance |
| DE102010006800A1 (en) * | 2010-02-04 | 2011-03-17 | Daimler Ag | Aluminum-containing iron alloy, useful for powder metallurgical manufacture of automobile components, comprises specified range of aluminum, chromium, nickel, elements e.g. niobium, nitrogen, molybdenum or iron, and unavoidable traces |
| CN107217197A (en) * | 2017-05-27 | 2017-09-29 | 中国核动力研究设计院 | A kind of advanced Reactor fuel element cladding FeCrAl base alloy materials and preparation method thereof |
| US20190193131A1 (en) * | 2016-06-24 | 2019-06-27 | Sandvik Materials Technology Deutschland Gmbh | A Method For Forming A Hollow Of A Ferritic FeCrAl Alloy Into A Tube |
| CN110004367A (en) * | 2018-11-27 | 2019-07-12 | 中国科学院金属研究所 | A kind of preparation method of oxide dispersion intensifying FeCrAl alloy pipe |
| US20190264307A1 (en) * | 2018-02-23 | 2019-08-29 | Ut-Battelle, Llc | CORROSION AND CREEP RESISTANT HIGH Cr FeCrAl ALLOYS |
| CN110863153A (en) * | 2019-12-05 | 2020-03-06 | 中国核动力研究设计院 | Preparation method of FeCrAl-based ODS alloy material for advanced nuclear fuel element cladding |
| WO2020067480A1 (en) * | 2018-09-28 | 2020-04-02 | 日本製鉄株式会社 | Composite particle group, negative electrode active material particle group, negative electrode, battery, and composite particles with exposed convex parts contained in composite particle group |
| CN112322957A (en) * | 2020-11-10 | 2021-02-05 | 中南大学 | Corrosion-resistant high-strength-and-toughness Fe-rich multi-component alloy and preparation method thereof |
| CN113564493A (en) * | 2021-08-10 | 2021-10-29 | 成都大学 | High-entropy alloy reinforced FeCrAl alloy cladding material and preparation process thereof |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09213464A (en) * | 1996-02-01 | 1997-08-15 | Daido Steel Co Ltd | Heating element for tube heater |
| DE19928842C2 (en) * | 1999-06-24 | 2001-07-12 | Krupp Vdm Gmbh | Ferritic alloy |
| CN104975238A (en) * | 2014-04-10 | 2015-10-14 | 常熟市电热合金材料厂有限公司 | Fe-Cr-Al electrothermal alloy |
| JP6562188B1 (en) * | 2018-01-30 | 2019-08-21 | Ｊｆｅスチール株式会社 | Method for producing Fe-Cr alloy |
| CN114774802B (en) * | 2022-04-07 | 2022-11-25 | 中南大学 | Method for improving mechanical and electrical resistance performance of FeCrAl-based resistance alloy and FeCrAl-based resistance alloy |
-
2022
- 2022-04-07 CN CN202210363946.9A patent/CN114774802B/en active Active
- 2022-11-25 WO PCT/CN2022/134252 patent/WO2023193451A1/en active Application Filing
- 2022-11-25 JP JP2023524857A patent/JP2024517528A/en active Pending
Patent Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6168757B1 (en) * | 1995-11-15 | 2001-01-02 | Alphatech, Inc. | Material formulation for galvanizing equipment submerged in molten aluminum and aluminum/zinc melts |
| US20020051727A1 (en) * | 2000-09-04 | 2002-05-02 | Roger Berglund | FeCrAI alloy |
| JP2006219728A (en) * | 2005-02-10 | 2006-08-24 | Tohoku Univ | Ferro-alloy for resistor having high resistance |
| DE102010006800A1 (en) * | 2010-02-04 | 2011-03-17 | Daimler Ag | Aluminum-containing iron alloy, useful for powder metallurgical manufacture of automobile components, comprises specified range of aluminum, chromium, nickel, elements e.g. niobium, nitrogen, molybdenum or iron, and unavoidable traces |
| US20190193131A1 (en) * | 2016-06-24 | 2019-06-27 | Sandvik Materials Technology Deutschland Gmbh | A Method For Forming A Hollow Of A Ferritic FeCrAl Alloy Into A Tube |
| CN107217197A (en) * | 2017-05-27 | 2017-09-29 | 中国核动力研究设计院 | A kind of advanced Reactor fuel element cladding FeCrAl base alloy materials and preparation method thereof |
| US20190264307A1 (en) * | 2018-02-23 | 2019-08-29 | Ut-Battelle, Llc | CORROSION AND CREEP RESISTANT HIGH Cr FeCrAl ALLOYS |
| WO2020067480A1 (en) * | 2018-09-28 | 2020-04-02 | 日本製鉄株式会社 | Composite particle group, negative electrode active material particle group, negative electrode, battery, and composite particles with exposed convex parts contained in composite particle group |
| CN110004367A (en) * | 2018-11-27 | 2019-07-12 | 中国科学院金属研究所 | A kind of preparation method of oxide dispersion intensifying FeCrAl alloy pipe |
| CN110863153A (en) * | 2019-12-05 | 2020-03-06 | 中国核动力研究设计院 | Preparation method of FeCrAl-based ODS alloy material for advanced nuclear fuel element cladding |
| CN112322957A (en) * | 2020-11-10 | 2021-02-05 | 中南大学 | Corrosion-resistant high-strength-and-toughness Fe-rich multi-component alloy and preparation method thereof |
| CN113564493A (en) * | 2021-08-10 | 2021-10-29 | 成都大学 | High-entropy alloy reinforced FeCrAl alloy cladding material and preparation process thereof |
Non-Patent Citations (1)
| Title |
|---|
| 杜国维，曹慧泉，蔡家敏，马如璋: "热循环过程铁铬铝合金中α＇相沉淀", 《北京科技大学学报》 * |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2023193451A1 (en) * | 2022-04-07 | 2023-10-12 | 中南大学 | Method for improving mechanical and resistive performances of fecral-based resistive alloy, and fecral-based resistive alloy |
| CN117026103A (en) * | 2023-08-08 | 2023-11-10 | 中南大学 | Multi-component soft magnetic alloy with high strength, high resistance and low resistance temperature coefficient, and preparation method and application thereof |
| CN117026103B (en) * | 2023-08-08 | 2024-10-29 | 中南大学 | Multi-component soft magnetic alloy with high strength, high resistance and low resistance temperature coefficient, and preparation method and application thereof |
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| WO2023193451A1 (en) | 2023-10-12 |
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