CN116607085B - Amorphous alloy strip with high resistivity and preparation method thereof - Google Patents
Amorphous alloy strip with high resistivity and preparation method thereof Download PDFInfo
- Publication number
- CN116607085B CN116607085B CN202310590815.9A CN202310590815A CN116607085B CN 116607085 B CN116607085 B CN 116607085B CN 202310590815 A CN202310590815 A CN 202310590815A CN 116607085 B CN116607085 B CN 116607085B
- Authority
- CN
- China
- Prior art keywords
- amorphous alloy
- alloy strip
- derived
- strip
- amorphous
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/02—Amorphous alloys with iron as the major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0611—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by a single casting wheel, e.g. for casting amorphous metal strips or wires
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/003—Making ferrous alloys making amorphous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- H—ELECTRICITY
- H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
- H05B—ELECTRIC HEATING; ELECTRIC LIGHT SOURCES NOT OTHERWISE PROVIDED FOR; CIRCUIT ARRANGEMENTS FOR ELECTRIC LIGHT SOURCES, IN GENERAL
- H05B3/00—Ohmic-resistance heating
- H05B3/10—Heating elements characterised by the composition or nature of the materials or by the arrangement of the conductor
- H05B3/12—Heating elements characterised by the composition or nature of the materials or by the arrangement of the conductor characterised by the composition or nature of the conductive material
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C2200/00—Crystalline structure
- C22C2200/02—Amorphous
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Soft Magnetic Materials (AREA)
Abstract
The invention discloses a high-resistivity amorphous alloy strip, which has a chemical formula of Fe aPbCrcBdSieCuhNifMog, wherein a, B, c, d, e, f, g, h is an atomic percentage, a is 65-77,8-B is 5-10, d is 3-6, e is 0-2, f is 0-5, g is 1-5, h is 0-2, and a+b+c+d+e+f+g+h=100, wherein Fe represents an iron element, P represents a phosphorus element, cr represents a boron element, si represents a silicon element, ni represents a nickel element, mo represents a molybdenum element and Cu represents a copper element. The amorphous alloy strip provided by the invention has higher glass transition temperature, ensures the application of the amorphous alloy strip in the field of low-temperature heating, has high resistivity, high strength and high hardness, and can meet the use requirements in different environments.
Description
Technical Field
The invention relates to the technical field of materials, in particular to an amorphous alloy strip with high resistivity and a preparation method thereof.
Background
The amorphous alloy is usually prepared by a rapid solidification method, and has no special structural defects of crystalline alloy such as grain boundary, dislocation and the like because atoms are not rearranged and grown and nucleated under extremely cold conditions, and is characterized by long-range disorder and short-range order on a macroscopic structure, and has excellent performances in soft magnetic performance, strength, hardness and corrosion resistance because the internal atomic arrangement and distribution mode is very similar to glass, also called metallic glass, belongs to metastable phase and can be transformed into crystalline state under external stimulus (factors such as pressure, temperature and the like).
With the rapid development of electric heating devices, the performance requirements on electric heating materials are also higher and higher, and the use of low-iron amorphous alloy strips as electric heating materials (the atomic percentage of Fe is lower than 60%) has been studied in the prior art. The iron-based amorphous alloy has higher resistivity and higher electrothermal conversion efficiency on one hand, thereby being beneficial to the rapid temperature rise of the heating element and improving the electrothermal conversion rate, and on the other hand, the thickness of the iron-based amorphous alloy is extremely thin and is only between 20 and 30 mu m, the width can be cut according to the corresponding size of practical application, the occupied space is small, the heating area is large, the heating efficiency is high, and the electrothermal conversion efficiency is also beneficial to being improved. However, iron-based amorphous materials have a great brittleness, which increases the resistance to a wide range of applications, and therefore, amorphous alloy strips need to have better processing flexibility, on the one hand, amorphous alloy strips with a thickness ranging from 20 μm to 30 μm can be obtained, and on the other hand, the amorphous alloy strips are not easy to break, and the method can be applied to equipment in different low-temperature electric heating fields. Because the amorphous alloy strip is electrically heated in different environments, the requirements of different application environments on the amorphous strip are different, for example, the amorphous alloy strip is used as a heating element of an outdoor heating belt, when the amorphous alloy strip is applied to the snow melting and ice melting of an outdoor highway, on one hand, the outdoor impact is large, cracks or fractures can be caused, the service life is reduced, and on the other hand, the outdoor environment is severe, the corrosion of the strip can be caused, so that the service performance of the amorphous alloy strip is influenced, and therefore, the amorphous strip still needs to be good in strength, hardness and corrosion resistance.
Although the amorphous alloy strip has more excellent performance than the traditional electric heating materials such as tungsten wire and nickel chrome wire, the technical problems still exist, namely, firstly, the resistivity of the amorphous alloy strip is low, the electric heat conversion rate is not facilitated, secondly, the relation between the processing flexibility, the hardness and the strength of the amorphous alloy strip is balanced, when the processing flexibility of the prepared amorphous alloy strip is better, the hardness and the strength of the amorphous alloy strip are reduced, the amorphous alloy strip is easy to break in the using process, and when the hardness and the strength of the prepared amorphous alloy strip are better, the processing flexibility of the amorphous alloy strip is reduced, the breakage of the amorphous alloy strip is also likely to be caused, thirdly, the corrosion resistance of the amorphous alloy strip can be improved, so that the amorphous alloy strip is beneficial to being applied to different environments, and fourthly, the temperature application range of the amorphous alloy strip can be improved, and the glass transition temperature of the low-iron amorphous alloy in the prior art is lower, so that the low-iron amorphous alloy strip can be suitable for the field of low-temperature heating of the amorphous alloy strip which is lower than 200 ℃.
Disclosure of Invention
Aiming at the problems in the prior art, the invention discloses an amorphous alloy strip with high resistivity and a preparation method thereof, and the amorphous alloy strip has good strength and hardness on the basis of good processing flexibility, can be suitable for the low-temperature heating field with wider temperature range of 50-300 ℃, and has higher resistivity and electrothermal conversion rate.
The invention is realized by the following technical scheme:
The chemical formula of the amorphous alloy strip with high resistivity is Fe aPbCrcBdSieCuhNifMog, wherein a, B, c, d, e, f, g, h is atomic percent, a is 65-77,8-B is 5-10, d is 3-6, e is 0-2, f is 0-5, g is 1-5, h is 0-2, and a+b+c+e+f+g+h=100, wherein Fe represents iron element, P represents phosphorus element, cr represents boron element, si represents silicon element, ni represents nickel element, mo represents molybdenum element and Cu represents copper element.
According to the design, the amorphous alloy strip is used as an electric heating material, so that the resistivity of the amorphous alloy strip is improved, the cost is reduced, the atomic percentage of Fe in the amorphous alloy strip is increased, and the Fe is increased to 65-77%. On the basis, in order to further improve the amorphous capability and processing flexibility of the amorphous alloy strip on the basis of obtaining higher resistance, the amorphous capability and processing flexibility of the amorphous alloy strip are further enhanced by the P-B-Si-Cu system in an amorphous alloy strip system, meanwhile, the amorphous alloy strip is further doped with Cr on the basis of stably doping the high resistivity of the amorphous alloy strip after the P-B-Si-Cu system, element segregation is reduced, the amorphous capability of the amorphous alloy strip, the processing flexibility of the amorphous strip and the strength and hardness of the amorphous strip are further stabilized and improved, and finally the amorphous alloy strip is doped with Cr, so that the corrosion resistance of the amorphous alloy strip is improved.
As a further scheme, the chemical formula of the amorphous alloy strip is Fe aPbCrcBdSieCuhNifMog, wherein a, b, c, d, e, f, g, h is atomic percent, a is more than or equal to 68 and less than or equal to 88,10 and less than or equal to 13, c is more than or equal to 5 and less than or equal to 10, d is more than or equal to 3 and less than or equal to 6, e is more than or equal to 0 and less than or equal to 2, f+g is more than 4.5 and less than or equal to 8, h is more than 0 and less than or equal to 2, and a+b+c+d+e+f+g+h=100. The amorphous alloy strip obtained in the range has better resistivity and also has better strength and hardness.
As a further scheme, the chemical formula of the amorphous alloy strip is Fe aPbCrcBdSieCuhNifMog, wherein a, b, c, d, e, f, g, h is atomic percent, a is 68-88,10-b is 13, c is 5-10, d is 3-6, e is 0-2, f+g is 4.5-8, h is 0-2, f/g is 1-2, and a+b+c+d+e+f+g+h=100. The amorphous alloy strip obtained in the range has better resistivity and further improves the strength and hardness of the amorphous alloy strip.
As a further solution, the Fe is derived from industrial pure iron, the P is derived from ferrophosphorus, the Cr is derived from chromium, the B is derived from ferroboron, the Si is derived from polysilicon, the Ni is derived from nickel, the Mo is derived from molybdenum, and the Cu is derived from copper.
As a further aspect, the amorphous alloy ribbon has a glass transition temperature of 440 ℃ to 500 ℃.
The invention also provides a preparation method of the amorphous alloy strip, which comprises the following steps:
S1, weighing raw materials according to the atomic percentage of an amorphous alloy strip, wherein the raw materials comprise one or more of industrial pure iron, ferrophosphorus, chromium, ferroboron, polysilicon, nickel, molybdenum and copper;
s2, cleaning the raw materials obtained in the step S1;
S3, smelting the raw material cleaned in the step S2 for a plurality of times in a vacuum environment to obtain a mother alloy ingot;
And S4, melting the master alloy ingot, and then rapidly cooling to obtain the non-alloy strip.
The optimal mode of cleaning in the step S2 is that pure iron, molybdenum and nickel are treated by adopting 5% dilute hydrochloric acid until the surface is bright, then are soaked by absolute ethyl alcohol, are cleaned in an ultrasonic cleaner, copper is cleaned by adopting 2% sulfuric acid and then are put into absolute ethyl alcohol for ultrasonic cleaning, and ferrophosphorus, chromium, ferroboron and polysilicon are cleaned by adopting absolute ethyl alcohol in ultrasonic cleaning. And acid washing to remove the oxide layer on the metal surface.
As a further scheme, argon with the pressure of 0.04Mpa-0.06Mpa is added into the vacuum environment in the step S3.
As a further scheme, the smelting in the step S3 is specifically that the raw materials with low melting points are added in sequence from high melting points to low melting points in the first smelting, so that the upper layer of the raw materials with low melting points is ensured.
As a further scheme, the optimal smelting times of the S3 are 4-5 times. Ensure the uniform distribution of each component in the non-alloy strip.
The invention also provides the application of the amorphous alloy strip, and the amorphous alloy strip can be used in the field of low-temperature heating below 300 ℃.
As a further option, the amorphous alloy ribbon can be used in the low temperature heating field below 300 ℃ and above 200 ℃.
As a still further aspect, the amorphous alloy ribbon can be used in the low temperature heating field below 300 ℃ and above 250 ℃.
The invention has the characteristics and beneficial effects that:
(1) The amorphous alloy strip provided by the invention has higher glass transition temperature, ensures the application of the amorphous alloy strip in the field of low-temperature heating, has high resistivity, high strength and high hardness, can meet the use requirements in different environments, and has good application prospects in the fields of low-temperature electric heating such as indoor and outdoor heating, pipeline heat tracing and the like.
(2) The amorphous alloy strip has the capabilities of low cost and high corrosion resistance.
(3) The amorphous alloy strip provided by the invention has good processing flexibility, can be suitable for the field of low-temperature heating at 200-300 ℃, has high resistivity, and improves the electrothermal conversion rate.
(4) The glass transition temperature of the amorphous alloy strip is 440-500 ℃, the resistivity is 160 mu omega cm-175 mu omega cm, the Vickers microhardness HV0.3 of the amorphous alloy is 650-750, and the tensile strength is 1600-2400 MPa.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are needed in the embodiments or the description of the prior art will be briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and other drawings can be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is a DSC of comparative example 9 of the present invention.
FIG. 2 is a DSC of example 1 of the present invention.
FIG. 3 shows the corrosion resistance of the present invention in example 4 and comparative example 2, wherein a in FIG. 3 is example 4 and b is comparative example 2.
Detailed Description
In order to facilitate an understanding of the present invention, a more complete description of a high resistivity amorphous alloy strip is provided below, but the scope of the present invention is not limited thereby.
The amorphous strip of the invention is prepared by the following steps:
An amorphous alloy strip of the formula Fe aPbCrcBdSieCuhNifMog is prepared, wherein a, b, c, d, e, f, g, h is atomic percent, a is more than or equal to 65 and less than or equal to 77,8, b is more than or equal to 13, c is more than or equal to 5 and less than or equal to 10, d is more than or equal to 3 and less than or equal to 6, e is more than or equal to 0 and less than or equal to 2, f is more than or equal to 0 and less than or equal to 0 not less than 5,1 not less than g not more than 5,0< h not more than 2 and a+b+c+d+e+f+g+h=100, the method comprises the following specific steps:
S1, proportioning 99.9wt% of iron, 99.99wt% of silicon, 99.95wt% of copper, 99.95wt% of nickel, 99.99wt% of chromium, 99.95wt% of molybdenum, 17.58wt% of ferroboron and 25.10wt% of ferrophosphorus according to the percentage content of atoms in the alloy expression, and polishing, pickling and cleaning raw materials.
S2, placing the cleaned raw materials into a crucible of a vacuum arc melting furnace, vacuumizing to less than 5X 10 -4 Pa, then charging 0.05Mpa argon, and melting in a high-purity argon atmosphere to prepare a master alloy ingot.
And S3, grinding the master alloy ingot obtained in the step to remove oxide scales, placing the master alloy ingot in a quartz tube, melting the master alloy ingot into metal melt by utilizing induction melting, spraying the alloy melt onto a copper roller rotating at a high speed, wherein the rotating speed of the copper roller is 35m/S, and rapidly cooling the molten alloy by utilizing heat conduction of the copper roller to obtain the amorphous alloy strip.
Comparative examples 1-4, 6 the crystalline phase structure of amorphous alloy strips was tested at 180 deg.c.
Comparative example 5 the crystalline phase structure of amorphous alloy ribbon was tested at 250C.
We will also obtain amorphous ribbons for performing various performance tests:
and (3) resistivity testing, namely measuring the resistivity of the amorphous alloy strip at room temperature by adopting a four-probe resistivity tester.
Hardness testing the hardness of the strip was tested using a vickers hardness tester.
Strength testing, namely testing the strength of the strip by adopting a universal tester.
Structure testing the crystalline phase structure of amorphous alloy strips was tested at 250 ℃.
Testing amorphous ability the structure of the strip was characterized using an X-ray diffractometer.
And (5) testing corrosion resistance through a 48-hour salt spray test.
And (3) verification result analysis:
table 1 results of testing amorphous alloy strips of examples and comparative examples of the present invention
Table 2 test results of inventive examples and comparative examples
| Sequence number | Composition of the components | ΔTx | Trg | γ |
| Comparative example 7 | Fe74.8P13Cr5B2Si1Cu0.2Ni4Mo2 | 18 | 0.6028 | 0.3864 |
| Comparative example 8 | Fe72.8P13Cr5B5Si0Cu0.2Ni4Mo2 | 42 | 0.6438 | 0.4214 |
| Comparative example 9 | Fe82.8P2Cr5B5Si1Cu0.2Ni4Mo2 | 15 | 0.5896 | 0.3822 |
| Example 8 | Fe69.8P13Cr5B5Si1Cu0.2Ni4Mo2 | 55 | 0.6547 | 0.4514 |
The amorphous alloy strip of the invention is successfully obtained by the preparation method of the invention, and the amorphous alloy strip obtained by the invention and the amorphous alloy strip in the prior art are tested, and the test results are shown in tables 1-2. As can be seen from Table 1, by comparing examples 1-15 with comparative examples 1-3, the amorphous alloy strips obtained by the invention have better resistivity and amorphous capability, and can balance processing flexibility, hardness and strength. The amorphous alloy strip is mainly designed to be used as an electric heating material, so that on one hand, the resistivity of the amorphous alloy strip needs to be improved, and on the other hand, the production cost of the material can be reduced. Therefore, we need to design a higher atomic percent of Fe in the amorphous alloy strip, we designed the atomic percent in the amorphous alloy material to be between 65% -77%, while promoting an increase in the electrical resistance of the amorphous alloy material, but the increase in Fe will decrease the amorphous forming ability of the electrical amorphous alloy material on the one hand, and will also result in a decrease in the toughness of the amorphous alloy strip on the other hand, as we can verify by comparative example 1. It can be found that in comparative example 1, the amorphous forming ability is reduced due to the higher atomic percentage of Fe, and partial crystalline phase is precipitated even though the content of the metalloid element is 23 (at%), so that the resistivity is reduced, the electrothermal conversion rate is reduced, rapid heating cannot be performed, and the waste of energy resources is caused. In order to further improve the amorphous capability of the amorphous alloy strip of the present invention, we have further matched a P-B-Si-Cu doping system in the amorphous alloy material system to further enhance the capability and flexibility of the amorphous alloy, and we can verify from comparison of comparative example 1 with comparative example 2-comparative example 3 that P-B-Si-Cu doping systems are matched in both comparative example 2 and comparative example 3, so that the amorphous capability of the amorphous alloy strips prepared in comparative example 2 and comparative example 3 is increased. We have found that for high iron-based material compositions above 65%, to accommodate heating use requirements above 200 ℃, the heat stability and amorphous ability of the amorphous alloy strip can only be improved when the atomic percent ratio of P is above 8% and/or the atomic percent ratio of B is above 6%, and that as the Fe content increases, the addition amounts of P and B often need to increase, but when the atomic percent ratio of P in the amorphous alloy strip is above 8% or the atomic percent ratio of B is below 6%, on the one hand, the amorphous ability of the amorphous alloy strip may be impaired, and on the other hand, the atomic percent ratio of P is above 8% easily results in segregation of the amorphous alloy elements, resulting in a decrease in the processing flexibility of the amorphous alloy strip, as we can verify by comparing example 4 with table 2. In the present invention, we designed that the atomic percentage of P in the doping system P-B-Cu-Si is 8% -13% and the atomic percentage of B is 3% -6% in the amorphous alloy strip, the amorphous alloy strip still has good amorphous ability, we believe that, firstly, the amorphous alloy strip of the present invention has higher atomic percentage of Fe and lower atomic percentage of B, then the higher atomic percentage of P or lower atomic percentage of B is needed to match the decrease of amorphous ability caused by the high atomic percentage of Fe, we can verify by comparing the example 1-example 17 with the comparative example 5, secondly, we doped with Mo-Ni system in the present invention, we can further improve amorphous ability and balance flexibility and strength of amorphous alloy strip, The hardness can be verified by comparing example 1-example 17 with comparative example 6. In addition, the increase of the Fe content can lead to the decrease of the glass transition temperature, thereby influencing the use temperature width, and we can verify through fig. 1 and fig. 2 that fig. 1 is a DSC curve of comparative example 9, and the glass transition temperature is about 350 ℃ and the Tg is lower, thus influencing the use temperature width. The DSC curve of example 1 is shown in fig. 2, and the glass transition temperature is about 470 ℃, so that the amorphous alloy strip with good resistivity is obtained by the design of the invention, the processing flexibility, the hardness and the strength of the amorphous alloy strip are balanced, and the amorphous alloy strip of the invention can be suitable for the low-temperature heating field with the temperature not higher than 300 ℃.
On this basis, we also conducted corrosion resistance tests for example 4 and comparative example 2 of the present invention, and the test results are shown in fig. 3. It was found that corrosion occurred on the surface of the non-alloy strip of comparative example 2, and it was found that Cr in the non-alloy strip improved the corrosion resistance of the amorphous alloy strip.
We have further studied the interplay of the atomic percent of Fe and the Mo-Ni doped system in the amorphous alloy strip of the present invention. From comparison of examples 1-17 in table 1, we found that the strength improvement for amorphous alloy strips was more pronounced as the sum of the atomic percentages of Mo and Ni in the amorphous alloy strips was varied. Since the amorphous alloy ribbon of the present invention needs to be applied in many environments, even in more specific fields (e.g., aqueous solutions having fluidity), sufficient strength is required. Therefore, the strength of the amorphous alloy strip of the invention is required to be higher than 1800Mp, the sum of the atomic percentages of Mo and Ni in the amorphous alloy strip is required to be higher than 4.5%, and the addition of more Mo and Ni in the amorphous alloy strip tends to affect the atomic percentages of Fe in the amorphous alloy strip, so that the resistivity of the amorphous alloy strip is reduced, and for balancing the strength and the resistivity of the amorphous alloy strip, the sum of the atomic percentages of Mo and Ni is further selected to be lower than 8%, and the atomic percentage of Fe in the amorphous alloy strip is higher than 68%. On this basis, we further compare example 7 with example 10, and found that example 10 has better strength and hardness, and we believe that when the sum of the atomic percentages of Ni and Mo in the amorphous alloy strip is equal, the difference between the atomic ratios of Ni and Mo also improves the strength and hardness of the amorphous alloy strip to a different extent. It was found that when the atomic percentage of Ni and Mo in the amorphous alloy strip was 1-2, the amorphous alloy in this range had better strength and hardness while obtaining better resistivity, and the atomic ratio of Ni and Mo was 2.5 in example 7 and 1.3 in example 10, as well as comparative verification by example 6 and example 9. It is further preferred that the amorphous alloy strip has an atomic ratio of Ni to Mo of 1≤f/g≤2.
In conclusion, the amorphous alloy strip which can be applied to the field of low-temperature electric heating at 200-300 ℃ is obtained through the design of the invention, and the amorphous alloy strip has higher resistivity, electrothermal conversion rate, corrosion resistance and amorphous capability on the basis of good processing flexibility.
It should be noted that the above-mentioned embodiments are only preferred embodiments of the present invention, and are not intended to limit the present invention, and any modifications, equivalent substitutions, improvements, etc. within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (9)
1. An amorphous alloy strip with high resistivity, which is characterized in that the chemical formula of the amorphous alloy strip is Fe aPbCrcBdSieCuhNifMog, wherein a, B, c, d, e, f, g, h is atomic percent, a is 68-88,10-13, c is 5-10, d is 3-6, e is 0-2, f is 0-5, g is 1-5, 4.5 f+g is 8, h is 0-2, and a+b+c+d+e+f+g+h=100, wherein Fe represents iron element, P represents phosphorus element, cr represents chromium element, B represents boron element, si represents silicon element, ni represents nickel element, mo represents molybdenum element and Cu represents copper element;
The resistivity of the amorphous alloy strip is 160 mu omega cm-175 mu omega cm, the Vickers microhardness HV0.3 of the amorphous alloy is 650-750, and the tensile strength is 1600-2400 MPa.
2. The high resistivity amorphous alloy strip of claim 1, wherein the amorphous alloy strip has a chemical formula of Fe aPbCrcBdSieCuhNifMog, wherein a, b, c, d, e, f, g, h is atomic percent, 68-a-88,10-b-13, 5-c-10, 3-d-6, 0-e-2, 4.5-f+g-8, 0-h-2, 1-f/g-2, and a+b+c+d+e+f+g+h=100.
3. The high resistivity amorphous alloy strip of claim 1, wherein said Fe is derived from commercially pure iron, said P is derived from ferrophosphorus, said Cr is derived from chromium, said B is derived from ferroboron, said Si is derived from polysilicon, said Ni is derived from nickel, said Mo is derived from molybdenum, and said Cu is derived from copper.
4. The high resistivity amorphous alloy ribbon of claim 1, wherein the amorphous alloy ribbon has a glass transition temperature of 440 ℃ to 500 ℃.
5. The method of producing an amorphous alloy strip according to any one of claims 1 to 4, comprising:
S1, weighing raw materials according to the atomic percentage of an amorphous alloy strip, wherein the raw materials are iron, ferrophosphorus, chromium, ferroboron, silicon, nickel, molybdenum and copper;
s2, cleaning the raw materials obtained in the step S1;
S3, smelting the raw material cleaned in the step S2 for a plurality of times in a vacuum environment to obtain a mother alloy ingot;
And S4, melting the master alloy ingot, and then rapidly cooling to obtain the amorphous alloy strip.
6. The preparation method according to claim 5, wherein 0.04-0.06 Mpa argon is added into the vacuum environment in S3;
The smelting in the step S3 is specifically that the raw materials with high melting points are added in sequence from low melting points to high melting points in the first smelting, so that the upper layer of the raw materials with high melting points is ensured.
7. Use of an amorphous alloy strip according to any one of claims 1-4, characterized in that the amorphous alloy strip can be used in the field of low temperature heating below 300 ℃.
8. The use according to claim 7, characterized in that the amorphous alloy ribbon can be used in the field of low-temperature heating below 300 ℃ and above 200 ℃.
9. The use according to claim 7, characterized in that the amorphous alloy ribbon can be used in the field of low-temperature heating below 300 ℃ and above 250 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310590815.9A CN116607085B (en) | 2023-05-24 | 2023-05-24 | Amorphous alloy strip with high resistivity and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202310590815.9A CN116607085B (en) | 2023-05-24 | 2023-05-24 | Amorphous alloy strip with high resistivity and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN116607085A CN116607085A (en) | 2023-08-18 |
| CN116607085B true CN116607085B (en) | 2025-06-13 |
Family
ID=87683232
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202310590815.9A Active CN116607085B (en) | 2023-05-24 | 2023-05-24 | Amorphous alloy strip with high resistivity and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN116607085B (en) |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104073749A (en) * | 2014-06-18 | 2014-10-01 | 安泰科技股份有限公司 | Iron-based amorphous magnetically soft alloy with uniform element distribution and preparation method thereof |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102007028275A1 (en) * | 2007-06-15 | 2008-12-18 | Vacuumschmelze Gmbh & Co. Kg | Brazing foil on an iron basis as well as methods for brazing |
| CN102314985B (en) * | 2011-09-29 | 2013-01-09 | 安泰科技股份有限公司 | Iron-based amorphous-alloy broadband and manufacturing method thereof |
| JP6347606B2 (en) * | 2013-12-27 | 2018-06-27 | 井上 明久 | High magnetic flux density soft magnetic iron-based amorphous alloy with high ductility and high workability |
| US10316396B2 (en) * | 2015-04-30 | 2019-06-11 | Metglas, Inc. | Wide iron-based amorphous alloy, precursor to nanocrystalline alloy |
| CN106119739B (en) * | 2016-06-24 | 2018-06-05 | 郑州大学 | Iron-based amorphous and nanocrystalline soft magnetic alloy and preparation method thereof |
| JP6472939B2 (en) * | 2017-01-27 | 2019-02-20 | 株式会社トーキン | Soft magnetic powder, Fe-based nanocrystalline alloy powder, magnetic parts and dust core |
-
2023
- 2023-05-24 CN CN202310590815.9A patent/CN116607085B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104073749A (en) * | 2014-06-18 | 2014-10-01 | 安泰科技股份有限公司 | Iron-based amorphous magnetically soft alloy with uniform element distribution and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN116607085A (en) | 2023-08-18 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102703754B (en) | Cu-Ni-Si-based alloy and preparation method thereof | |
| CN113174509B (en) | High-strength beryllium copper alloy bar and preparation process thereof | |
| CN106636734B (en) | High-intensitive, highly conductive, high resistance to stress relaxation copper alloy elastic material and preparation method thereof | |
| CN102527724B (en) | A method of manufacturing an alloy pipe | |
| CN101033530A (en) | Ferrum-base block non-crystalline alloy material | |
| CN108411225B (en) | A kind of zirconium-based amorphous alloy and preparation method thereof | |
| CN105861935B (en) | Excellent Fe 36Ni invar alloy materials of a kind of thermoplasticity and preparation method thereof | |
| CN101358324A (en) | A rare earth-based amorphous alloy and its preparation method | |
| CN110157945A (en) | A kind of anti-softening copper alloy and its preparation method and application | |
| JPS63103041A (en) | Alloy of copper, chromium, titanium and silicon, and its production and use | |
| CN116607085B (en) | Amorphous alloy strip with high resistivity and preparation method thereof | |
| WO2003025239A1 (en) | Invar alloy wire excellent in strength and turning characteristics and method for production thereof | |
| CN102936701B (en) | Iron-based shape memory alloy with outstanding memory recovery characteristic and preparation method thereof | |
| CN115094266A (en) | A kind of high-strength conductive elastic copper alloy and preparation method thereof | |
| CN103084753B (en) | A kind of ferronickel Precise Alloy welding wire | |
| CN113106286A (en) | High-conductivity beryllium copper alloy bar for 5G communication and preparation process thereof | |
| CN107557621A (en) | It is a kind of suitable for aluminium alloy conductor of overhead transmission line and preparation method thereof | |
| CN118581387A (en) | A corrosion-resistant cable clamp and a preparation method thereof | |
| SE431660B (en) | FORMABLE AUSTENITIC Nickel Alloy | |
| CN108588368B (en) | The method that prediction ferrimanganic silicon-base alloy austenite increases temperature ferrite dual phase area warm area | |
| CN105256203A (en) | Preparation method of aluminum alloy conductors | |
| CN110257734A (en) | Corrosion resistant iron-base amorphous alloy material and its preparation method and application | |
| CN116815010A (en) | Micro-nano particle hybrid reinforced high-strength high-conductivity Cu-Ni-Si-X alloy and preparation method thereof | |
| CN116694978A (en) | Low-cost heat-resistant stainless medium-entropy alloy and its preparation method | |
| CN115011856A (en) | Low-expansion high-temperature alloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |