Method for improving the mechanical and resistance properties of FeCrAl-based resistance alloys and FeCrAl-based resistance alloys

Abstract

According to the present invention, a method for improving the mechanical and resistance properties of FeCrAl-based resistance alloys and a method for improving the mechanical and resistance properties of FeCrAl-based resistance alloys are provided. A CrAl-based resistance alloy is disclosed. The present invention is a FeCrAl alloy containing alloying elements Ti and By introducing Si and H, a multicomponent structure was developed that is compatible with the BCC matrix of the FeCrAl alloy. The formation of nano-dispersed phases is induced. The chemical composition of the optimized alloy is Fe: 52-59%, Cr:25~29%, Al:11~15%, Ti:2.5~5%, Si:1.5~3% The alloy matrix obtained by the method of the present invention exhibits the characteristics of a BCC structure. , multicomponent nanoparticles with L21 structure are diffusely distributed in the matrix, and the nanoparticles are B It maintains a perfectly matched orientation relationship with the CC matrix, significantly improving the compressive strength of the alloy. , deformability is increased, electrical resistivity is improved, the temperature coefficient of resistivity is reduced, and mechanical and resistance properties are improved. This indicates that performance will be improved across the board.

Description

[Technical Field]

[0001] The present invention relates to the field of metal material manufacturing technology, specifically to the mechanical properties of FeCrAl-based resistance alloys. and a method for improving resistance performance and an FeCrAl-based resistance alloy. [Background technology]

[0002] High resistivity (>100μΩ·cm) and low temperature coefficient of resistivity (TCR) (<100ppm Resistance alloys with Cr / K are used in high precision electronic measurement systems, GPS positioning systems, data storage systems, It plays an important role in many important fields such as storage, thermoelectric equipment and temperature control sensors. Iron-chromium-aluminum (FeCrAl) alloys have high resistivity, high strength, and high-temperature oxidation resistance. It is used as a resistance alloy due to its advantages such as excellent resistance to heat and low cost. are.

[0003] Increasing industrial developments are driving the miniaturization of electronic devices through ever-improving processability and sensitivity. In order to promote the development of integration, high strength, high deformability, high resistivity, and low temperature coefficient of resistivity are required. However, due to the following factors, low-cost resistance alloys are required. Further development and practical application of conventional FeCrAl alloys as resistance materials with their advantages in electrical resistance. First, conventional methods for improving the strength and resistivity of Fe-Cr-Al alloys have been limited. The solution is to increase the Cr and Al content, but if the Cr and Al content is too high, the It is easy to cause stress concentration, which leads to brittle fracture and poor workability. Next, by adjusting the ratio of Fe, Cr, and Al, The temperature coefficient of resistivity can be adjusted, but it can also have both high and low temperature coefficients of resistivity. It is often difficult to do so. Summary of the Invention

[0004] The purpose of this section is to provide an overview of some aspects of embodiments of the present invention and to provide some preferred embodiments. This section and the Abstract and Publications of the specification of this application are intended to provide a brief description of the preferred embodiments. The title should not obscure the purpose of this section, the abstract of the specification, and the title of the invention. In some cases, the details of the present invention may be simplified or omitted, and such simplifications or omissions do not limit the scope of the present invention. It cannot be used to

[0005] In view of the above and / or the drawbacks existing in the prior art, the present invention provides a method for manufacturing a conventional FeCrAl resistance alloy. It is difficult to combine the high resistivity and low temperature coefficient of resistivity of gold, and it is also difficult to achieve high strength and high deformability. The mechanical and resistance performance of FeCrAl-based resistance alloys solves technical issues such as poor synergistic ability A method for improving resistance and an FeCrAl-based resistance alloy are provided.

[0006] One of the objects of the present invention is to provide a material having high strength, high deformability, high resistivity, and low temperature coefficient of resistivity over a wide temperature range. To provide an FeCrAl-based resistance alloy that can achieve the above excellent overall properties. That is the thing.

[0007] Here, the term "wide temperature range" as used in the present invention means a wide temperature range below 673K. "High strength" in the present invention means a compressive yield strength of 600 to 1400 MPa and a crushing strength of 900 The alloy material obtained by the present invention has a strength of 2200 MPa or less. "High deformability" means the alloy material obtained by the present invention that has a compressive strain of 10% or more. In the present invention, "high resistivity" means a material having a resistivity of 140 to 230 μΩ·cm. The term "low temperature coefficient of resistivity" used in the present invention means the alloy material obtained by the present invention. The alloy material obtained by the present invention has a temperature coefficient of resistivity of -200 to 100 ppm / k. means. [Means for solving the problem]

[0008] The present invention provides the following technical solutions: FeCrAl-based resistance alloy contains Fe in atomic percent. :52~59%, Cr:25~29%, Al:11~15%, Ti:2.5~5% and S i Consists of 1.5-3% of ingredients.

[0009] wherein the total atomic percentage of Fe, Cr, and Al is 92% or more and 96% or less; The total atomic percentage of Ti and Si is 8% or less and 4% or more, and the atomic percentage of each component is The total is 100%.

[0010] For example, the atomic percent composition of the alloy in the present invention is 54% Fe, 27% Cr, 13. 5% Al, 4% Ti, 1.5% Si or 55% Fe, 28% Cr, 12% of 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% T The content may be, but is not limited to, 1% i, 2.5% Si, etc.

[0011] Another object of the present invention is to introduce the alloying elements Ti and Si into the FeCrAl alloy. This leads to the formation of multicomponent nano-dispersed phases that are consistent with the BCC matrix of the FeCrAl alloy. The present invention provides a method for improving the mechanical and resistance performance of FeCrAl-based resistance alloys. be.

[0012] Among them, the total atomic percentage of Ti and Si accounts for 4 to 8% of the total.

[0013] Here, the term "BCC matrix" as used in the present invention means a body-centered cubic matrix.

[0014] The "dispersed phase" in the present invention refers to fine dispersed particles formed by precipitation from a supersaturated solid solution. It refers to a solid phase spread over a substrate.

[0015] A preferred embodiment of the method for improving the mechanical and resistance properties of the FeCrAl-based resistance alloy of the present invention where the total atomic percentage of Ti is 2.5 to 5% of the total, and the total atomic percentage of Si is The total atomic percentage of these elements accounts for 1.5 to 3% of the total.

[0016] A preferred embodiment of the method for improving the mechanical and resistance properties of the FeCrAl-based resistance alloy of the present invention Here, the FeCrAl alloy is composed of Fe, Cr and Al, and contains 100 atomic percent of Fe. The total atomic percentage of Cr is 25-29% of the total. The total atomic percentage of Al accounts for 11 to 15% of the total.

[0017] A preferred embodiment of the method for improving the mechanical and resistance properties of the FeCrAl-based resistance alloy of the present invention Here, the raw materials of each component are mixed according to the mixing ratio of each component atom of the alloy, and the alloy is heated in a vacuum or The alloy material is obtained by smelting and casting under inert gas protection conditions.

[0018] "Smelting" in this invention refers to a dry process in which metal materials are put into a heating furnace and melted to produce crude metal. It refers to the metallurgical process, and uses existing equipment such as suspension furnaces, induction furnaces, blast furnaces, reverberatory furnaces, and arc furnaces. It can be implemented.

[0019] A preferred embodiment of the method for improving the mechanical and resistance properties of the FeCrAl-based resistance alloy of the present invention The smelting is carried out under the vacuum conditions, and the degree of vacuum in the furnace is maintained at 1 to 0.0001 Pa. do.

[0020] A preferred embodiment of the method for improving the mechanical and resistance properties of the FeCrAl-based resistance alloy of the present invention Here, the smelting is carried out under the inert gas protection conditions, and the pressure of the inert gas in the furnace is set to 0.0 Maintain pressure between 0.0001 and 5 MPa.

[0021] A preferred embodiment of the method for improving the mechanical and resistance properties of the FeCrAl-based resistance alloy of the present invention In the smelting, the smelting temperature is 1623 to 2473K, and the hKeep warm.

[0022] A preferred embodiment of the method for improving the mechanical and resistance properties of the FeCrAl-based resistance alloy of the present invention Here, each of the component raw materials is a pure metal element particle or ballast with a purity of 99 wt.% or more. The smelting is repeated 3 to 8 times using a molten iron body.

[0023] A preferred embodiment of the method for improving the mechanical and resistance properties of the FeCrAl-based resistance alloy of the present invention The obtained alloy material has a compressive yield strength of 600 to 1400 MPa and a crushing strength of The alloy has a wide range of temperatures below 673K, with a temperature of 900 to 2200 MPa and a compressive strain of 10% or more. The resistivity in the low temperature range is 140 to 230 μΩ·cm, and the temperature coefficient of resistivity is -200 to It has the characteristics of 100 ppm / k.

[0024] Compared with the prior art, the present invention has the following beneficial effects: The present invention uses appropriate amounts of alloying elements, Ti and Si, to form a BCC matrix. The present invention provides a novel method for inducing the formation of a multi-component nano-dispersed phase that is consistent with the The L21 nanoparticle phase significantly improves the compressive strength of the alloy, enhancing its deformability and increasing its resistivity. The present invention improves the mechanical and resistance properties of the material by increasing the temperature coefficient of resistivity and decreasing the temperature coefficient of resistivity. The method provided by the present invention has a simple manufacturing process, does not require complicated heat treatment, and can produce a cast-like product. This allows for superior performance in high resistance conditions compared to conventional FeCrAl resistor alloys. It is difficult to combine low modulus and low temperature coefficient of resistivity, and the synergistic ability of high strength and high deformability is poor. It is expected to provide new ways to solve these problems. [Brief explanation of the drawings]

[0025] In order to more clearly explain the technical solutions of the embodiments of this utility model, the following description of the embodiments will be The drawings that must be used are briefly explained below. These are merely some examples of utility models, and a person skilled in the art can easily understand them without any creative work. It is obvious that other drawings can be derived based on these drawings. [Figure 1] FIG. 1 is a diagram showing an XRD spectrum of an FeCrAl-based resistance alloy obtained in Example 1 of the present invention. [Figure 2] 1 is a diagram showing an EBSD phase distribution map and an inverse polarity diagram (IPF) of an FeCrAl-based resistance alloy obtained in Example 1 of the present invention. FIG. [Figure 3] FIG. 1 is a view showing a scanning electron microscope morphology of the microstructure of the FeCrAl-based resistance alloy obtained in Example 1 of the present invention. [Figure 4]1 is a diagram showing a high-angle annular dark-field image (HAADF) and a selected area electron diffraction spectrum in a transmission electron microscope of the FeCrAl-based resistance alloy obtained in Example 1 of the present invention. FIG. [Figure 5] FIG. 1 is a diagram showing an HAADF image of the FeCrAl-based resistance alloy obtained in Example 1 of the present invention under a transmission electron microscope and the corresponding energy spectrum distribution. [Figure 6] FIG. 1 is a diagram showing the resistivity-temperature curve of the FeCrAl-based resistance alloy obtained in Example 1 of the present invention. [Figure 7] 1 is a stress-strain diagram at room temperature during compression of an FeCrAl-based resistance alloy obtained in Example 1 of the present invention. FIG. [Figure 8] FIG. 2 is a stress-strain diagram of the FeCrAl-based resistance alloy obtained in Example 1 of the present invention during compression at 673 K. [Figure 9] FIG. 2 is a scanning electron microscope morphology diagram of the microstructure of the FeCrAl-based resistance alloy obtained in Example 2 of the present invention. [Figure 10] FIG. 2 is a graph showing the resistivity-temperature curve of the FeCrAl-based resistance alloy obtained in Example 2 of the present invention. [Figure 11] FIG. 2 is a scanning electron microscope morphology diagram of the microstructure of the FeCrAl-based resistance alloy obtained in Example 3 of the present invention. [Figure 12] FIG. 1 is a diagram showing the resistivity-temperature curve of the FeCrAl-based resistance alloy obtained in Example 3 of the present invention. [Figure 13] FIG. 2 is a stress-strain diagram of the FeCrAl-based resistance alloy obtained in Example 3 of the present invention during compression at room temperature. [Figure 14] FIG. 2 is a scanning electron microscope morphology diagram of the microstructure of the alloy obtained in Comparative Example 1 of the present invention. [Figure 15] FIG. 2 is a graph showing the resistivity-temperature curve of an alloy obtained according to Comparative Example 1 of the present invention. [Figure 16] FIG. 2 is a stress-strain diagram of the alloy obtained in Comparative Example 1 of the present invention during compression at room temperature. [Figure 17]FIG. 2 is a scanning electron microscope morphology diagram of the microstructure of the alloy obtained in Comparative Example 2 of the present invention. [Figure 18] FIG. 1 is a graph showing the resistivity-temperature curve of an alloy obtained by Comparative Example 2 of the present invention. [Figure 19] FIG. 2 is a stress-strain diagram of the alloy obtained in Comparative Example 2 of the present invention during compression at room temperature. [Figure 20] FIG. 2 shows the XRD spectrum of the alloy material provided by Comparative Example 3 of the present invention. [Figure 21] FIG. 1 shows an EBSD phase distribution diagram and an inverse polarity diagram (IPF) of an alloy material provided by Comparative Example 3 of the present invention. [Figure 22] FIG. 2 is a scanning electron microscope morphology diagram of the microstructure of the alloy material provided by Comparative Example 3 of the present invention. [Figure 23] FIG. 2 is a diagram showing a scanning electron microscope backscattered electron image of an alloy material provided by Comparative Example 3 of the present invention and the corresponding energy spectrum distribution. [Figure 24] FIG. 10 is a diagram showing the resistivity-temperature curve of an alloy material provided by Comparative Example 3 of the present invention. [Figure 25] FIG. 2 is a stress-strain diagram of an alloy material provided by Comparative Example 3 of the present invention in a compression process at room temperature. [Figure 26] FIG. 2 is a scanning electron microscope morphology diagram of the microstructure of the alloy material provided by Comparative Example 4 of the present invention. [Figure 27] FIG. 10 is a diagram showing the resistivity-temperature curve of an alloy material provided by Comparative Example 4 of the present invention. [Figure 28] FIG. 2 is a stress-strain diagram of an alloy material provided by Comparative Example 4 of the present invention in a compression process at room temperature. DETAILED DESCRIPTION OF THE INVENTION

[0026] In order to make the above objects, features and advantages of the present invention more clearly comprehensible, the following detailed description is The specific embodiments of the present invention will be described in detail in combination with the examples in the book.

[0027] In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention. The invention may be implemented in other ways different from those described here. Similar extensions can be made without violating the contents of the present invention. It is not intended to be limited by the specific embodiments disclosed.

[0028] Next, "one embodiment" or "embodiment" as used herein refers to at least one implementation of the present invention. "a" refers to a particular feature, structure, or characteristic that may be included in a "In an embodiment" does not all refer to the same embodiment, and may be mutually exclusive with other embodiments. Nor does it refer to any particular single or alternative embodiment. Example 1

[0029] The raw materials are bulk materials corresponding to each pure element, and the chemical formula is Fe 55 Cr 28 Al 12 Ti3 Formulated according to Si2 (atomic percentage). Melted using suspension smelting under an inert gas protective atmosphere. The melting process is repeated four times. After the vacuum level is reduced to 0.001 Pa, Argon gas was added until the temperature became slightly positive, and the melting temperature was 1873K, and the melting temperature was 5 min. The temperature was maintained and the mixture was poured into a rectangular parallelepiped shape, that is, the FeCrAl-based resistance alloy of Example 1 was obtained. It was.

[0030] As can be seen from FIGS. 1 and 2, the main components of the FeCrAl-based resistance alloy obtained in Example 1 The Fe phase has a BCC solid solution structure. CrAl-based resistance alloys have dispersed nanoparticles. As can be seen in Figure 4, The nano-dispersed particles in the FeCrAl-based resistance alloy obtained in Example 1 have an L21 structure. The grain size is 45 ± 11 nm, and the area percentage is 33% ± 4%. The nano-structure of L21 dispersed in the FeCrAl-based resistance alloy obtained by 1 is the same. If so, the alloy is rich in Al, Ti, and Si elements and deficient in Fe and Cr elements. As can be seen, the FeCrAl-based resistance alloy obtained in Example 1 has a room temperature resistivity of about 1. 83 μΩ·cm, and when heated to 673 K, it remains at ~181 μΩ·cm The temperature coefficient of resistivity in the temperature range from room temperature to 673 K is -35 As can be seen from FIG. 7, the FeC obtained in Example 1 The rAl-based resistance alloy has a compressive yield strength of approximately 1096 MPa and a crushing strength of approximately 1694 MPa at room temperature. MPa, and the compressive strain is about 20%. The compressive yield strength of FeCrAl-based resistance alloys at 673 K is approximately 1055 MPa. , the crushing strength is high at 1980 MPa and the compressive strain is high at 35%. Example 2

[0031] The raw materials are bulk materials corresponding to each pure element, and the chemical formula is Fe 55 Cr 28 Al 12 Ti3 Formulated according to Si2 (atomic percentage). Melted using suspension smelting under an inert gas protective atmosphere. The melting process is repeated four times. After the vacuum level is reduced to 0.001 Pa, Argon gas was added until the temperature was slightly positive, and the melting temperature was 1873 K. The alloy was heated from room temperature to 673 K at a rate of 4 K / min. After heating to 1000K and rapid quenching, the FeCrAl-based resistance alloy of Example 2 was obtained. was made.

[0032] As can be seen from FIGS. 9 and 10, in the FeCrAl-based resistance alloy obtained in Example 2, The nano-dispersed phase with L21 structure remains stable at 673 K and is stable from room temperature to 673 K. Determine the low temperature coefficient of resistivity (-46 ppm / K) in the temperature range up to 1000 K. Example 3

[0033] The raw materials are bulk materials corresponding to each pure element, and the chemical formula is Fe 54 Cr 27 Al 13.5 T i4Si 1.5 (atomic percentage) and arc smelting in an inert gas protective atmosphere. The melting process is repeated four times under vacuum. The vacuum level during melting is reduced to 0.001 Pa. After that, argon gas was filled until the pressure became slightly positive, and the smelting temperature was 1873 K. That is, the FeCrAl-based resistance alloy of Example 3 was obtained.

[0034] As can be seen from FIG. 11, the FeCrAl-based resistance alloy obtained in Example 3 contains nano- As can be seen from FIG. 12, the FeCr particles obtained in Example 3 are dispersed. Al-based resistance alloys have a high room temperature resistivity of 184 μΩ·cm. In the temperature range from room temperature to 673 K, the resistivity remains at ~180 μΩ·cm. The temperature coefficient of resistivity in the example is low at -58 ppm / K. The FeCrAl-based resistance alloy obtained by the method 3 has a compressive yield strength of about 1243 MPa and a crushing strength of about 1000 MPa. The strength is approximately 1823 MPa and the compressive strain is approximately 17%. Comparative Example 1

[0035] The raw materials are bulk materials corresponding to each pure element, and the chemical formula is Fe 58 Cr 22 Al 15 Ti1 Formulated according to Si4 (atomic percentage). Produced by arc smelting under an inert gas protective atmosphere. The melting process is repeated four times. After the vacuum level is reduced to 0.001 Pa, Argon gas was filled until the pressure was slightly positive, and the smelting temperature was 1873K, i.e. Thus, the alloy in Comparative Example 1 was obtained.

[0036] As can be seen from FIG. 14, there is no indication of the presence of nanoparticles in the alloy obtained by Comparative Example 1. As can be seen from FIG. 15, the alloy obtained in Comparative Example 1 has a room temperature resistivity of about 2. 04 μΩ·cm. Temperature coefficient of resistivity in the temperature range from room temperature to 673 K. As can be seen from FIG. 16, the value obtained by Comparative Example 1 is about -159 ppm / K. The alloy has a compressive yield strength of approximately 850 MPa, a crushing strength of approximately 1878 MPa, and a compressive strain of approximately It is 30%. Comparative Example 2

[0037] The raw materials are bulk materials corresponding to each pure element, and the chemical formula is Fe 56 Cr 25 Al 14 Ti2 Formulated according to Si3 (atomic percentage). , arc smelted under inert gas protective atmosphere. The melting process is repeated four times. After the vacuum level is reduced to 0.001 Pa, Argon gas was charged until the pressure was slightly positive, and the smelting temperature was 1873 K, i.e. Thus, the alloy in Comparative Example 2 was obtained.

[0038] As can be seen from FIG. 17, the alloy obtained by Comparative Example 2 has dispersed nanoparticles. As can be seen from FIG. 18, the alloy obtained in Comparative Example 2 has a room temperature resistivity of about 19. The temperature coefficient of resistivity in the temperature range from room temperature to 673 K is 7 μΩ·cm. As can be seen from FIG. 19, the composite obtained by Comparative Example 2 is about −171 ppm / K. Gold has a compressive yield strength of approximately 980 MPa, a crushing strength of approximately 2026 MPa, and a compressive strain of approximately 30 %. Comparative Example 3

[0039] The raw materials are bulk materials corresponding to each pure element, and the chemical formula is Fe 55 Cr 28 Al 12 Ti3 Formulated according to Si2 (atomic percentage). Melted under inert gas protective atmosphere using suspension smelting. The melting process is repeated four times. After the vacuum level is reduced to 0.001 Pa, Argon gas was added until the temperature became slightly positive, and the smelting temperature was 1873 K and 5 min The temperature is kept constant and the mixture is cast into a rectangular parallelepiped shape. Next, the mixture is poured into an argon gas protective atmosphere (argon gas pressure After high-temperature homogenization at 1573 K and 10 Pa, the sample was homogenized for 3 hours. Oil quenching was carried out, that is, the alloy of Comparative Example 3 was obtained.

[0040] As can be seen from Figures 20 and 21, the alloy obtained by Comparative Example 3 has a single-phase BCC structure. 22 and 23 show the nanoparticles dispersed in the alloy obtained by Comparative Example 3. As can be seen from Figure 24, the absence of particles was confirmed. The alloy has a temperature coefficient of resistivity of -163°C in the temperature range from room temperature to 673 K. 25, the composite obtained by Comparative Example 3 is ±10 ppm / K. Gold has a compressive yield strength of about 1191 MPa, a crushing strength of only 1254 MPa, and a compressive strain of Only 8%. Comparative Example 4

[0041] The raw materials are bulk materials corresponding to each pure element, and the chemical formula is Fe 55 Cr 29 Al 16 (atom The alloy is mixed according to the percentage. It is melted by arc melting under an inert gas protective atmosphere and melted four times. Repeated smelting. After the vacuum level during smelting was reduced to 0.001 Pa, the pressure was slightly reduced. Argon gas was filled until the temperature became positive, and the smelting temperature was 1873K, i.e., The alloy was obtained.

[0042] As can be seen from Figure 26, the alloy obtained by Comparative Example 4 has a single-phase BCC structure. As can be seen from Figure 27, the alloy obtained in Comparative Example 4 was The temperature coefficient of resistivity in the temperature range is about -146 ppm / K. As can be seen, the alloy obtained in Comparative Example 4 has a compressive yield strength that is greater than that of Examples 1 and 2. It was quite low. Comparative Example 5

[0043] Published literature Metallurgical transactions A [T. Nao hara, A. Inoue, T. Minemura, T. Masumoto, K. K. umada,Metallurgical transactions A 13 (1 982) 337-343], the conventional Fe 65 Cr 20 Al 15 , Fe 60 Cr20 Al 20 , Fe 50 Cr 30 Al 20 The room temperature resistivity of the alloy is 156 μ Ω·cm, 180 μΩ·cm and 186 μΩ·cm from room temperature to 673 K The temperature coefficients of resistivity in the range of -17 ppm / K and -73 ppm / K, respectively. and -85 ppm / K. In other words, it has both high resistivity and low temperature coefficient of resistivity. It is difficult to do so.

[0044] Comparing Examples 1, 2 and 3, it can be seen that the alloys optimized by the method provided by the present invention have The multicomponent L21 nanodispersed phase, perfectly matched with the underlying BCC matrix, is stable at 673 K. The optimized alloy maintains its excellent intermediate temperature mechanical performance while maintaining high resistivity. It can be seen that the resistivity-temperature stability is maintained within 673 K.

[0045] Comparing Example 1 with Comparative Examples 1 and 2, it is clear that the contents of the introduced Ti and Si elements are higher than those of the present invention. The alloys obtained outside the range were clearly inferior in temperature stability of resistivity to that of Example 1. We can see that.

[0046] Comparing Example 1 and Comparative Example 3, the BCC matrix provided by the method of the present invention The alloy without the multi-component L21 nano-dispersed phase, i.e., the alloy of Comparative Example 3, is It can be seen that the crushing strength, compressive strain and resistivity temperature stability are all inferior to those of Example 1. Comparing Example 1 and Comparative Example 4, the compressive yield strength of the alloy without the introduction of Ti and Si elements was is much lower than the yield strength of the alloy obtained after optimization of the present invention, and the temperature stability of the resistivity is That is, in the present invention, the alloying elements Ti and Si are introduced in appropriate amounts. By inserting the nano-particles into the matrix, a multi-component nano-dispersed phase is formed that is aligned with the body-centered cubic (BCC) matrix. The formation of a multicomponent L21 nanodisperse phase is induced, which is deformable and resistivity-temperature stable within 673 K. Comparing Example 1 with Comparative Example 5, the method of the present invention can effectively improve the properties. It can be seen that the alloy obtained by the method combines high resistivity with a low temperature coefficient of resistivity.

[0047] The present invention uses appropriate amounts of alloying elements, Ti and Si, to form a BCC matrix. Mechanics and resistance of FeCrAl-based resistance alloys induced by the formation of multicomponent nanodispersed phases consistent with the This provides a method for improving performance. It has the following features: First, the alloying elements Ti and S are The introduction of an appropriate amount of i induces the formation of a multicomponent nano-dispersed phase that is perfectly matched with the BCC matrix. The coherent multi-component nano-dispersed phase improves the work hardening ability while maintaining high strength. Next, the nano-components that are aligned with each other are used to improve the crushing strength and compressive strain. The presence of dispersed phases reduces the temperature coefficient of resistivity. The atomic radius of Si is significantly different from that of Fe and Cr, resulting in large lattice distortion. This effectively improves the solid solution strengthening effect and lattice scattering effect in the alloy, thereby increasing the strength. In addition, the alloy contains fewer rare metals than conventional FeCrAl alloys. By not including any elements, it can be developed into an environmentally friendly resistance alloy. By using the technological means provided by Ming, we can achieve high strength, high deformability, high resistivity, and low resistivity over a wide temperature range. It is possible to achieve excellent overall characteristics, including a temperature coefficient.

[0048] It should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, and are not intended to be limiting. Although the present invention has been described in detail with reference to preferred embodiments, those skilled in the art will appreciate that , modifying the technical solution of the present invention without departing from the spirit and scope of the technical solution of the present invention. and the like, all of which are to be included within the scope of the present invention. It should be understood that this is the case.

Claims

1. An FeCrAl-based resistance alloy, In atomic percentage, Fe: 55%, Cr: 28%, Al: 12%, Ti: 3% and Si: 2% It consists of ingredients, The alloying elements Ti and Si and the BCC matrix of the FeCrAl alloy form a co-lattice structure. A multi-component nano-dispersed phase is formed, and the nano-dispersed particles exhibit an L21 structure. An FeCrAl-based resistance alloy characterized by:

2. 1. A method for improving the mechanical and resistive performance of an FeCrAl-based resistive alloy, comprising: By introducing alloying elements Ti and Si into the FeCrAl alloy, Inducing the formation of a multicomponent nanodispersed phase that is consistent with the BCC matrix of the alloy; The total atomic percentage of Ti and Si accounts for 5% of the total, and the atomic percentage of Ti is The total atomic percentage of Si accounts for 3% of the total, and the total atomic percentage of Si accounts for 2% of the total. The FeCrAl alloy is composed of Fe, Cr, and Al, and the total atomic percentage of Fe is The total atomic percentage of Cr is 28% of the total, and the total atomic percentage of Al is 28%. The total accounts for 12% of the total, The raw materials for each component are mixed according to the atomic ratio of each component of the alloy, and the alloy is then stored in a vacuum or inert gas. The alloy material is obtained by smelting under protective conditions, and each of the component raw materials is pure gold with a purity of 99 wt. % or more. Repeated smelting 3 to 8 times using metal element particles or bulk bodies, The smelting is carried out under the vacuum conditions, and the degree of vacuum in the furnace is maintained at 1 to 0.0001 Pa. Smelting is carried out under gas protection conditions, and the pressure of the inert gas inside the furnace is maintained at 0.000001 to 5 MPa. The smelting temperature is 1623 to 2473K, and the temperature is maintained for 0.01 to 1 hour. The obtained alloy material has a compressive yield strength of 600 to 1400 MPa and a crushing strength of 900 to 2000 MPa. The alloy has a resistance of 200 MPa and a compressive strain of 10% or more, and has a wide temperature range of 673 K or less. The resistivity is 140 to 230 μΩ cm, and the temperature coefficient of resistivity is -200 to 100 ppm / k property, A method for improving the mechanical and resistance performance of an FeCrAl-based resistance alloy, comprising:

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