US20190256944A1 - Iron-based amorphous alloy having low stress sensitivity, and preparation method therefor - Google Patents
Iron-based amorphous alloy having low stress sensitivity, and preparation method therefor Download PDFInfo
- Publication number
- US20190256944A1 US20190256944A1 US16/335,257 US201716335257A US2019256944A1 US 20190256944 A1 US20190256944 A1 US 20190256944A1 US 201716335257 A US201716335257 A US 201716335257A US 2019256944 A1 US2019256944 A1 US 2019256944A1
- Authority
- US
- United States
- Prior art keywords
- iron
- amorphous alloy
- based amorphous
- strip
- stress
- 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.)
- Abandoned
Links
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims abstract description 207
- 229910000808 amorphous metal alloy Inorganic materials 0.000 title claims abstract description 101
- 229910052742 iron Inorganic materials 0.000 title claims abstract description 88
- 230000035945 sensitivity Effects 0.000 title abstract description 4
- 238000002360 preparation method Methods 0.000 title description 7
- 238000000034 method Methods 0.000 claims abstract description 35
- 230000006698 induction Effects 0.000 claims abstract description 20
- 238000010791 quenching Methods 0.000 claims abstract description 11
- 230000000171 quenching effect Effects 0.000 claims abstract description 11
- 238000010438 heat treatment Methods 0.000 claims description 30
- 230000005284 excitation Effects 0.000 claims description 27
- 238000003723 Smelting Methods 0.000 claims description 11
- 238000004804 winding Methods 0.000 claims description 10
- 239000002994 raw material Substances 0.000 claims description 7
- 239000007788 liquid Substances 0.000 claims description 6
- 239000011162 core material Substances 0.000 abstract description 16
- 230000015572 biosynthetic process Effects 0.000 abstract description 4
- 229920006395 saturated elastomer Polymers 0.000 abstract description 3
- 230000035882 stress Effects 0.000 description 65
- 230000000052 comparative effect Effects 0.000 description 45
- 239000000463 material Substances 0.000 description 28
- 238000000137 annealing Methods 0.000 description 26
- 230000006866 deterioration Effects 0.000 description 25
- 239000000203 mixture Substances 0.000 description 21
- 230000008569 process Effects 0.000 description 18
- 229910045601 alloy Inorganic materials 0.000 description 16
- 239000000956 alloy Substances 0.000 description 16
- 238000012360 testing method Methods 0.000 description 10
- 238000013461 design Methods 0.000 description 8
- 230000006355 external stress Effects 0.000 description 7
- 238000010008 shearing Methods 0.000 description 6
- 229910052710 silicon Inorganic materials 0.000 description 6
- 238000004088 simulation Methods 0.000 description 6
- 229910052796 boron Inorganic materials 0.000 description 5
- 238000001816 cooling Methods 0.000 description 5
- 230000004907 flux Effects 0.000 description 5
- 230000003647 oxidation Effects 0.000 description 5
- 238000007254 oxidation reaction Methods 0.000 description 5
- 238000002425 crystallisation Methods 0.000 description 4
- 230000008025 crystallization Effects 0.000 description 4
- 230000003247 decreasing effect Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000002474 experimental method Methods 0.000 description 4
- 238000007496 glass forming Methods 0.000 description 4
- 229910000976 Electrical steel Inorganic materials 0.000 description 3
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 3
- 230000002180 anti-stress Effects 0.000 description 3
- 238000009413 insulation Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 239000011574 phosphorus Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 239000012768 molten material Substances 0.000 description 2
- 238000005457 optimization Methods 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- 229910008423 Si—B Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- ZDVYABSQRRRIOJ-UHFFFAOYSA-N boron;iron Chemical compound [Fe]#B ZDVYABSQRRRIOJ-UHFFFAOYSA-N 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 239000011810 insulating material Substances 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
-
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/03—Amorphous or microcrystalline structure
-
- 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
Definitions
- the present disclosure relates to the field of iron-based amorphous alloy technology, especially to an iron-based amorphous alloy having low stress sensibility, and a method for preparing the same.
- Fe-based amorphous alloy strips such as Fe-Si-B amorphous alloys are widely used as iron cores for power transformers and high-frequency transformers. Based on the above characteristics, iron-based amorphous materials have taken the lead in the transformer field for a long period of time ever since they were invented.
- amorphous materials have significantly low saturated magnetic density, low magnetic induction, poor anti-stress sensibility and so on.
- a lot of works have been done to improve the saturation magnetic induction and reduce the loss of amorphous materials, but there is no noticeable result for the study of the anti-stress sensibility of amorphous materials.
- the stress removal is the fundamental guarantee of the low loss characteristics of amorphous materials.
- the thickness of the amorphous alloy strip is 20-30 ⁇ m.
- the cross section of iron core of amorphous alloy transformer is rectangular, so that the corresponding high and low voltage windings are rectangular. Rectangular windings have relatively poor ability to withstand short circuits with respect to the circular windings, so it is necessary to improve the ability of the amorphous alloy transformers to withstand short-circuits.
- the stress of the amorphous transformer core is mainly composed of two parts of stress, one is the internal stress generated during the preparation process of amorphous material, i.e., the internal stress generated during quenching of the amorphous material, the other is an unavoidable assembly external stress due to the characteristics of the iron core during the manufacturing process of the iron core.
- a large number of researches for reduce the stress mainly focus on the annealing process and optimizing the transformer core structure.
- the internal stress generated during quenching of amorphous materials is mainly related to the formation of amorphous materials. Rapid cooling is a necessary condition for the formation of amorphous materials.
- Rapid cooling is a necessary condition for the formation of amorphous materials.
- a high-temperature molten material is poured onto a cooling substrate and cooled at a speed of 10 6 ° C./s, an amorphous strip with a short-range order and long-range disorder structure is formed.
- This short-range disorder liquid is “frozen,” and internal stresses are generated in these “frozen” structures.
- the internal stress of the amorphous material can be effectively removed through the annealing process, and the amorphous industry has done a lot of works to remove the internal stress through the annealing process.
- thermal stress is induced by the large difference of the temperature in core at the same time, i.e., the internal stress cannot be completely removed.
- the assembly external stress is mainly caused by the process of producing the iron core from the amorphous strip during core assembly and the external stress caused by the structural characteristics of the core itself.
- This kind of stress is unavoidable and there is little study on the removal of it, which is mainly through the optimization of the iron core structure of the transformer and the specification of the operation.
- Amorphous alloy transformer windings have a rectangular structure, and the electric power received by them is far less uniform than that of a circular winding of ordinary transformers. It is easier to be deformed when subjected to sudden short circuit electric power. Since the iron core material of amorphous alloy transformer is very sensitive to mechanical stress, both tensile and bending stress will affect its performance, which should be fully considered in the structure design to reduce the force on the iron core.
- the amorphous alloy transformer body is an axial bearing structure.
- the stresses on the amorphous alloy core and the rectangular windings do not interfere with each other.
- the rectangular windings are pressed by the upper and lower clamps and the pressure plate to form a compression structure by itself. Therefore, it suffers more from the short-circuit electric power in the axial and radial directions of the rectangular winding than the circular winding.
- Japanese Patent No. JPS63-45318 discloses a method for improving the annealing process, mainly by reducing the temperature difference in the iron core.
- a heat insulating material is installed on the inner and outer circumferential surfaces of the iron core to minimize the temperature difference in the iron core during cooling, so as to improve the properties of thin strip itself and improve the weight and bulk of the iron core.
- Iron core is put into a heat treatment furnace and heated, and temperature variation occurs in various parts of the iron core.
- Annealing and removing stress in this method does not cause crystallization due to excessive core temperature in the furnace or does not cause the phenomenon of incomplete stress removal due to low temperature.
- the specific procedures of this method are not described in the disclosure, and the process of annealing the iron core and the annealing cost are increased, so that it is not practical in actual annealing process.
- the Chinese Patent No. CN1281777 C discloses that by adding a specific range of P in the restricted ranges of Fe, Si, B, and C, it is found that under the situation of uneven temperature in various parts of the iron core during annealing, iron core annealing at lower temperatures can also exhibit excellent soft magnetic properties.
- the inventors only considered the effect of P on reducing the temperature unevenness of the amorphous iron core, and not the problems of oxidation and surface crystallization of the phosphorus-containing amorphous strip.
- the element P has extremely poor oxidation resistance. When annealing in an aerobic environment, the performance and the apparent quality of iron core will easily become worse due to oxidation.
- the above method avoids the defects of large temperature difference inside the iron core, but introduces problems such as oxidation during annealing and of the amorphous strip and crystallization on the strip surface.
- the technical problem solved by the present disclosure is to provide an iron-based amorphous alloy strip, and the iron-based amorphous alloy strip of the present disclosure has relatively low stress sensibility.
- the saturation magnetic induction of the iron-based amorphous alloy is ⁇ 1.60 T.
- the atomic percentage of Fe is 80.0 ⁇ a ⁇ 81.5.
- the atomic percentage of B is 11.0 ⁇ b ⁇ 12.5.
- the atomic percentage of Si is 7.0 ⁇ c ⁇ 8.0.
- a 80.0, 12.0 ⁇ b ⁇ 13.0, 7.0 ⁇ c ⁇ 8.0.
- a 80.5, 11.5 ⁇ b ⁇ 12.5, 7.0 ⁇ c ⁇ 8.0.
- the iron-based amorphous alloy 81.0 ⁇ a ⁇ 81.5, 11.0 ⁇ b ⁇ 13.0, 7.0 ⁇ c ⁇ 8.0.
- the present disclosure further provides a method for preparing the iron-based amorphous alloy strip represented by formula (I), comprising:
- the iron-based amorphous alloy is subjected to heat treatment.
- the iron-based amorphous alloy is winded into a sample ring with an inside diameter of 50.5 mm and an outside diameter from 53.5 to 54 mm.
- the allowable gauge factor of the sample ring loss is 10.0%, and allowable gauge factor of the excitation power is 6%.
- coercive force of the heat treated iron-based amorphous alloy strip is ⁇ 3.5 A/m; under a condition of 50 Hz and 1.35 T, excitation power of the heat treated iron-based amorphous alloy strip is ⁇ 0.1450 VA/kg, and core loss is ⁇ 0.1100 W/kg; and under a condition of 50 Hz and 1.40 T, excitation power of the heat treated iron-based amorphous alloy strip is ⁇ 0.1700 VA/kg, and core loss is ⁇ 0.1500 W/kg.
- the iron-based amorphous alloy strip is in completely amorphous phase with a limit thickness of at least 75 nm and a shearing limit strip thickness of at least 29 nm.
- the present disclosure prepares an iron-based amorphous alloy having high saturation magnetic induction strength, high ductility and low stress sensibility, which makes the transformer assembled by the iron core made from the alloy having strong sudden short circuit resistance.
- FIG. 1 is a schematic diagram of the simulation experiment equipment for the iron-based amorphous alloy sample ring prepared in the present disclosure under condition of no stress.
- FIG. 2 is a schematic diagram of the simulation experiment equipment for the iron-based amorphous alloy sample ring prepared in the present disclosure under condition of stress.
- a main object of the present disclosure is to establish a range of amorphous composition having low stress sensibility through adjusting components and evaluating the stress (internal stress and external stress) of strip with different components, so as to effectively show excellent soft magnetic properties of amorphous products, and produce an amorphous transformer that has a relatively good ability of withstanding sudden short-circuit.
- the present disclosure discloses an iron-based amorphous alloy represented by formula (I):
- the iron-based amorphous alloy provided by the present disclosure comprises Fe, Si and B, and through adjusting the content of the above elements to give alloy a relatively good glass forming ability, saturation magnetic induction and soft magnetic property. Furthermore, after heat treatment, the strip made of the iron-based amorphous alloy provided by the present disclosure has relatively low anti-stress sensibility.
- Fe is the base element, and the content of it is 79.5 ⁇ a ⁇ 82.5 by atomic percentage. If the atomic percentage of Fe is unduly low, the saturation magnetic induction of the iron-based amorphous alloy will be unduly low, so that it cannot improve the defect of low magnetic flux density of the amorphous and cannot obtain enough magnetic flux density and an iron core with compact structure. When the content is unduly high, the thermal stability of iron-based amorphous alloy and the formability of strip are decreased, making it hard to smooth operation of the strip and obtain a good magnetic product. In the embodiments, the atomic percentage of Fe is 79.5 ⁇ a ⁇ 81.5, more specifically, the atomic percentage of Fe is 80.0 ⁇ a ⁇ 81.5.
- the atomic percentage of Si is 6.5 ⁇ c ⁇ 8.5.
- the content of Si is 7.0 ⁇ c ⁇ 8.0.
- the atomic percentage of B is 11.0 ⁇ b ⁇ 13.5.
- the content of B is unduly low, it is hard to form a stable amorphous material.
- the content of B in the above range gives the iron.-based amorphous alloy of the present disclosure excellent soft magnetic property.
- the content of B is 11.0 ⁇ b ⁇ 13.0, more specifically, the content of B is 11.0 ⁇ b ⁇ 12.5.
- the iron-based amorphous alloy composition and contents provided by the present disclosure is a reasonable combination of improving magnetic induction and improving glass forming ability, forming an iron-based amorphous alloy with high saturation magnetic induction. Further, on the base of high saturation magnetic induction, the iron-based amorphous alloy of the present disclosure also has low stress sensibility. The reason why the iron-based amorphous alloy provided by the present disclosure has high saturation magnetic induction and low stress sensibility is due to the adjustment of the composition and content of the iron-based amorphous alloy.
- the present disclosure further provides a method for preparing the iron-based amorphous alloy strip represented by formula (I), comprising:
- the process of preparing the iron-based amorphous alloy strip conventional methods in the art are used to prepare the iron-based amorphous alloy strip with the specific composition of the present disclosure.
- the preparing and smelting processes above are well known to one of ordinary skill in the art, which would not be descripted in details in the present disclosure.
- the metal raw materials are smelted in a medium frequency furnace, and the smelting temperature is from 1300 to 1500° C., and the duration is from 80 to 120 minutes.
- the molten material is heated and insulated, and subjected to single roller rapid quenching, so as to obtain the iron-based amorphous alloy strip.
- the heating temperature is preferably from 1350 to 1470° C., and the insulating duration is preferably from 20 to 50 minutes.
- an iron-based amorphous alloy strip is obtained in completely amorphous state, and limit thickness of the formed amorphous is at least 75 ⁇ m, and toughness of the strip is relatively good, which will not crack after 180 degree folding.
- the shearable limit thickness of the strip is at least 29 ⁇ m, so that the present product has pretty large production margin in industrial production and requirement of the cooling equipment in the industrial process is decreased.
- the raw iron-based amorphous alloy strip is prepared, it is subjected to heat treatment for ease of application.
- the iron-based amorphous alloy provided by the present disclosure is capable to be treated in a relatively wide annealing range, and the iron-based amorphous alloy strip obtained has relatively low excitation power and loss.
- the heat treatment temperature is from 325 to 395° C.; and in embodiments, the heat treatment temperature is from 335 to 385° C.
- the obtained iron-based amorphous alloy is preferably winded into a sample ring with an inside diameter of 50.5 mm and an outside diameter of from 53.5 to 54 mm, and then the above sample ring is subjected to heat treatment.
- Loss and deterioration of excitation power of the heat treated sample ring under conditions of stress are detected through simulation experiments, so as to illustrate transition of the properties of iron-based amorphous alloy strip under condition of stress. If the loss and the deterioration coefficient of excitation power of the iron-based amorphous alloy strip still lay in an acceptable range under conditions with a relatively large gauge factor, the iron-based amorphous alloy strip has relatively low stress sensibility. If the loss and the deterioration coefficient of excitation power of the iron-based amorphous alloy strip are unacceptable when the gauge factor is relatively small, the stress sensibility of the iron-based amorphous alloy strip is relatively bad. Through the simulation experiment of the present disclosure, the experiment results show that the iron-based amorphous alloy strip has relatively low stress sensibility.
- the magnetic property of the iron-based amorphous alloy is improved and the stress sensibility of the iron-based amorphous alloy strip is decreased at the same time.
- alloy components represented by formula Fe a B b Si c industrial pure iron, silicon and boron were used to prepare the alloys shown in Table 1. Except for the main elements, there are unavoidable impurity elements in the alloys, such as C, Mn, S, and so on.
- the materials with different components were successively added to a medium frequency furnace of a furnace volume of 100 kg in the order of boron iron, silicon and pure iron for remelting (the smelting temperature was from 1300 to 1500° C., and the duration was from 80 to 120 minutes). After holding, the molten steel was casted to the spraying ladle for producing an amorphous strip with a width of 20 mm by single roller planar flow casting.
- alloy strips with different thicknesses were produced by adjusting parameters such as roller speed, liquid level and so on (in the strip producing process, the roller speed was from 1000 to 1400 r/min, and the linear speed of the strip producing is from 20 to 30 m/s, and the liquid level was from 200 mm to 300 mm).
- XRD XRD was used to test the free face of strips with different components until the strip thickness was in the amorphous state.
- Table 1 showed the limit thicknesses of each strip with different amorphous alloy compositions.
- the saturation magnetization induction of the amorphous alloy strips were measured with VSM.
- the alloy compositions were comprehensively evaluated by the glass forming ability and saturation magnetic induction of the strips. According to the number of brittle points, maximum shearing thickness of the strip was evaluated.
- the method for evaluating brittle point is: taking the strip which has a length equal to the perimeter of the crystallizer and shearing the strip along the longitudinal direction. When the number of the brittle point was not more than 2, the strip was considered to be shearable, and when the number of the brittle point was 2, the length was regarded as the shearable limit thickness of the alloy strip.
- Example 1 80.0 8.0 12.0 80 30 1.60
- Example 2 80.0 7.5 12.5 82 29 1.60
- Example 3 80.0 7.0 13.0 80 30 1.61
- Example 4 80.5 8.0 11.5 80 30 1.61
- Example 5 80.5 7.5 12.0 80 33 1.62
- Example 6 80.5 7.0 12.5 80 33 1.62
- Example 7 81.0 8.0 11.0 75 32 1.62
- Example 8 81.0 7.5 11.5 75
- Example 9 81.0 7.0 12.0 75 33 1.62
- Example 10 81 6.5 12.5 75 33 1.63
- Example 11 81.5 7.0 11.5 65 38 1.62 Comparative 78.0 9.0 13.0 85 26 1.55
- Example 2 Comparative 79.0 9.0 12.0 80 27 1.56
- Example 3 Comparative 80.0 9.0 11.0 75 26 1.57
- Example 4 Comparative 80.0 6.0 14.0 78
- Table 1 showed the limit thickness of the amorphous strips, toughness limit thickness of strip producing and saturation magnetic induction of alloys with different compositions.
- the amorphous strip limit thickness and the toughness limit thickness of strip producing are the tests for strip producing technology. The thicker the strip thickness was, the more relax the requirement for the strip producing equipment was.
- the relatively high saturation magnetic induction of the amorphous alloy was expected for the design of transformer.
- the maximum shearing thickness was between 36 and 38 ⁇ m, which was absolutely superior in terms of efficiency in core molding.
- its amorphous forming ability was obviously insufficient based on the limit thickness of the amorphous strip, so it did not meet the requirements for smooth operation of producing strip and it also affected its excitation power and loss.
- Strips with a thickness of 26 to 28 ⁇ m and a width of 30 mm in Table 1 were wound into sample rings with an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm.
- the sample rings were subjected to stress relief annealing using a box type annealing furnace.
- Annealing was carried out under the protection of argon-with a temperature from 325 to 395° C. at an interval of 10° C. and 1 hour insulation.
- a magnetic field along the direction of strip preparing was added during the heat treatment process with a magnetic field strength of 1200 A/m.
- the silicon steel tester was used to test the excitation magnetic and loss of the strip after heat treatment.
- the test conditions were 1.35 T/50 Hz and 1.40 T/50 Hz respectively.
- the test results of the characteristic tests were shown in Table 2.
- amorphous materials with high saturation magnetic induction allow a greater working magnetic density, i.e., showing relatively low excitation power and losses at magnetic density of 1.4 T.
- the comparative examples 8 to 9 show a better performance at 1.4 T test.
- the loss and excitation magnetic at 1.4 T increased, resulting in a relatively large value at 1.4 T.
- Examples 1 to 11 exhibited excellent soft magnetic properties at 1.35 T/50 Hz and 1.40 T/50 Hz; loss at 1.35 T/50 Hz was below 0.11 W/kg, and loss at 1.40 T/50 Hz was below 0.15 W/kg.
- amorphous materials have relatively low unavoidable loss values, and the performances of amorphous materials were deteriorated by external stress after they were assembled into an iron core.
- a stress model of amorphous sample ring was established to characterize the performance deterioration of amorphous alloys with different compositions after stress deformation, and simulated the performance changes caused by stress when amorphous strip assembled into transformer cores.
- Sample processing the amorphous strips listed in Table 3 were selected, wound into a sample ring with an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm, and subjected to stress removing and annealing with a box annealing furnace under the protection of argon.
- Sample rings prepared with different compositions were chosen, and subjected to heat treatment according to the above requirements.
- the thermal insulation temperature of the heat treatment was from 325 to 395° C. with 5° C. as a gradient for the heat treatment, the insulation duration was from 60 to 120 min, and the magnetic field strength was from 800 to 1400 A/m.
- the optimal heat treatment performances of each component in the above heat treatment process were chosen to test the performance deterioration of the strip after stress.
- FIG. 1 was a schematic diagram of the simulation experiment equipment of the sample ring under condition of no stress
- FIG. 2 was a schematic diagram of the simulation experiment equipment of the sample ring under condition of stress.
- the A plate was fixed, and the feeding amount of the sample ring was given with the action of pushing plate B.
- the sample ring was deformed by the stress, and the pushing plate B was fixed.
- the loss P 1 and excitation power Pe 1 of the material under deformation conditions were measured, and the performance of the sample at 1.35 T/50 Hz was tested with a silicon steel tester.
- the initial sample ring (without deformation) has an inner diameter of D 0 and performance values of P 0 and Pe 0 respectively. After deformation, the inner diameter was D 1 , and the performance values were P 1 and Pe 1 respectively.
- the gauge factor (D 1 ⁇ D 0 )*100%/D 0 .
- the loss deterioration coefficient (P 1 ⁇ P 0 )*100%/P 0 .
- the excitation power deterioration coefficient (Pe 1 ⁇ Pe 0 )/Pe 0 .
- Tables 4 and 5 clearly showed that iron-based amorphous alloys undergone a certain degree of performance deterioration due to the influence of stress, and the performance deterioration coefficient increased as the deformation coefficient increased. Comparing the loss and the excitation power of each component, it could be found that the deterioration of the excitation power significantly exceeded its loss.
- the allowable deterioration coefficient of excitation power was 6%, while the allowable deterioration coefficient of loss was 10%. That is, the application of external stress to the amorphous strip has a greater effect on the excitation power.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Soft Magnetic Materials (AREA)
Abstract
Description
- This application claims the priority of Chinese Patent Application No. 201710447487.1, filed on Jun. 14, 2017, and titled with “IRON-BASED AMORPHOUS ALLOY HAVING LOW STRESS SENSITIVITY, AND PREPARATION METHOD THEREFOR”, and the disclosures of which are hereby incorporated by reference.
- The present disclosure relates to the field of iron-based amorphous alloy technology, especially to an iron-based amorphous alloy having low stress sensibility, and a method for preparing the same.
- Due to its low iron loss, high saturation magnetic flux density, high permeability, and other advantages, Fe-based amorphous alloy strips such as Fe-Si-B amorphous alloys are widely used as iron cores for power transformers and high-frequency transformers. Based on the above characteristics, iron-based amorphous materials have taken the lead in the transformer field for a long period of time ever since they were invented.
- With the continuous renewal of silicon steel materials, the advantages of amorphous materials are relatively weakened. For example, amorphous materials have significantly low saturated magnetic density, low magnetic induction, poor anti-stress sensibility and so on. In recent years, a lot of works have been done to improve the saturation magnetic induction and reduce the loss of amorphous materials, but there is no noticeable result for the study of the anti-stress sensibility of amorphous materials. The stress removal is the fundamental guarantee of the low loss characteristics of amorphous materials. In addition, as a main material of the transformer magnetic circuit, the thickness of the amorphous alloy strip is 20-30 μm. Because it is hard and brittle and difficult to be cut, the cross section of iron core of amorphous alloy transformer is rectangular, so that the corresponding high and low voltage windings are rectangular. Rectangular windings have relatively poor ability to withstand short circuits with respect to the circular windings, so it is necessary to improve the ability of the amorphous alloy transformers to withstand short-circuits.
- The stress of the amorphous transformer core is mainly composed of two parts of stress, one is the internal stress generated during the preparation process of amorphous material, i.e., the internal stress generated during quenching of the amorphous material, the other is an unavoidable assembly external stress due to the characteristics of the iron core during the manufacturing process of the iron core. A large number of researches for reduce the stress mainly focus on the annealing process and optimizing the transformer core structure.
- The internal stress generated during quenching of amorphous materials is mainly related to the formation of amorphous materials. Rapid cooling is a necessary condition for the formation of amorphous materials. When a high-temperature molten material is poured onto a cooling substrate and cooled at a speed of 106° C./s, an amorphous strip with a short-range order and long-range disorder structure is formed. This short-range disorder liquid is “frozen,” and internal stresses are generated in these “frozen” structures. The internal stress of the amorphous material can be effectively removed through the annealing process, and the amorphous industry has done a lot of works to remove the internal stress through the annealing process. When the internal stress generated during quenching is removed by annealing, thermal stress is induced by the large difference of the temperature in core at the same time, i.e., the internal stress cannot be completely removed.
- The assembly external stress is mainly caused by the process of producing the iron core from the amorphous strip during core assembly and the external stress caused by the structural characteristics of the core itself. This kind of stress is unavoidable and there is little study on the removal of it, which is mainly through the optimization of the iron core structure of the transformer and the specification of the operation. Amorphous alloy transformer windings have a rectangular structure, and the electric power received by them is far less uniform than that of a circular winding of ordinary transformers. It is easier to be deformed when subjected to sudden short circuit electric power. Since the iron core material of amorphous alloy transformer is very sensitive to mechanical stress, both tensile and bending stress will affect its performance, which should be fully considered in the structure design to reduce the force on the iron core. Generally, special fastening designs are used, and the amorphous alloy transformer body is an axial bearing structure. The stresses on the amorphous alloy core and the rectangular windings do not interfere with each other. The rectangular windings are pressed by the upper and lower clamps and the pressure plate to form a compression structure by itself. Therefore, it suffers more from the short-circuit electric power in the axial and radial directions of the rectangular winding than the circular winding. In order to reduce the difficulty in the assembly and design of the transformer, it is important to reduce the stress sensibility of the amorphous alloy.
- For example, Japanese Patent No. JPS63-45318 discloses a method for improving the annealing process, mainly by reducing the temperature difference in the iron core. In this method, a heat insulating material is installed on the inner and outer circumferential surfaces of the iron core to minimize the temperature difference in the iron core during cooling, so as to improve the properties of thin strip itself and improve the weight and bulk of the iron core. Iron core is put into a heat treatment furnace and heated, and temperature variation occurs in various parts of the iron core. Annealing and removing stress in this method does not cause crystallization due to excessive core temperature in the furnace or does not cause the phenomenon of incomplete stress removal due to low temperature. However, the specific procedures of this method are not described in the disclosure, and the process of annealing the iron core and the annealing cost are increased, so that it is not practical in actual annealing process.
- The Chinese Patent No. CN1281777 C discloses that by adding a specific range of P in the restricted ranges of Fe, Si, B, and C, it is found that under the situation of uneven temperature in various parts of the iron core during annealing, iron core annealing at lower temperatures can also exhibit excellent soft magnetic properties. The inventors only considered the effect of P on reducing the temperature unevenness of the amorphous iron core, and not the problems of oxidation and surface crystallization of the phosphorus-containing amorphous strip. The element P has extremely poor oxidation resistance. When annealing in an aerobic environment, the performance and the apparent quality of iron core will easily become worse due to oxidation. For example, when phosphorus-containing amorphous materials are annealed under the conditions for Fe, Si, B, and C annealing, the surfaces of the strip become blue due to oxidation, and the performance deteriorates. This has very strict requirements for the oxygen content of the annealing atmosphere. At present, there is no preparation of ferrophosphorus of the amorphous strip, and the introduction of phosphorus and iron will generate unavoidable impurities, and the crystallization on the strip surface will easily occur. In summary, the above method avoids the defects of large temperature difference inside the iron core, but introduces problems such as oxidation during annealing and of the amorphous strip and crystallization on the strip surface.
- The U.S. Patent Publication No. US20160172087 discloses the study of the stress release based on different components, pointing out the effect of B and C on the stress release, and illustrating the amount of stress released after the strip annealing through an experimental model. However, the inventor only explained the degree of stress release from the point of internal stress removing and stress release after annealing from a single strip, without considering the final soft magnetic properties of the material and the performance deterioration of the transformer core due to the assembly stress.
- In view of the above, although the embodiments of the above disclosures have optimized the annealing process or the assembly process of the amorphous transformer iron core and the stress of the amorphous strip can be removed to a great extent. However, the feasibility of strip preparation and implementation of these optimizations are not specifically considered, and a more comprehensive understanding of the stress relieving (stress avoidance) of amorphous strips is missing. The results are relatively one-sided.
- The technical problem solved by the present disclosure is to provide an iron-based amorphous alloy strip, and the iron-based amorphous alloy strip of the present disclosure has relatively low stress sensibility.
- In view of this, the present disclosure provides an iron-based amorphous alloy represented by formula (I):
-
FeaBbSic (I); - wherein a, b and c are each independently atomic percentages of corresponding components; 79.5≤a≤82.5, 11.0≤b≤13.5, 6.5≤c≤8.5, and a+b+c=100.
- Preferably, the saturation magnetic induction of the iron-based amorphous alloy is ≥1.60 T.
- Preferably, the atomic percentage of Fe is 80.0≤a≤81.5.
- Preferably, the atomic percentage of B is 11.0≤b≤12.5.
- Preferably, the atomic percentage of Si is 7.0≤c≤8.0.
- Preferably, in the iron-based amorphous alloy, a=80.0, 12.0≤b≤13.0, 7.0≤c≤8.0.
- Preferably, in the iron-based amorphous alloy, a=80.5, 11.5≤b≤12.5, 7.0≤c≤8.0.
- Preferably, in the iron-based amorphous alloy, 81.0≤a≤81.5, 11.0≤b≤13.0, 7.0≤c≤8.0.
- The present disclosure further provides a method for preparing the iron-based amorphous alloy strip represented by formula (I), comprising:
- preparing raw materials according to the atomic percentages indicated in formula (I); smelting the raw materials; heating and insulating the molten liquid after smelting; performing single roller rapid quenching to obtain an iron-based amorphous alloy strip;
-
FeaBbSic (I); - wherein a, b and c are each independently atomic percentages of corresponding components; 79.5≤a≤82.5, 11.0≤b≤13.5, 6.5≤c≤8.5, and a+b+c=100.
- Preferably, after the single roller rapid quenching, the iron-based amorphous alloy is subjected to heat treatment.
- Preferably, prior to the heat treatment, the iron-based amorphous alloy is winded into a sample ring with an inside diameter of 50.5 mm and an outside diameter from 53.5 to 54 mm.
- After heat treatment, the allowable gauge factor of the sample ring loss is 10.0%, and allowable gauge factor of the excitation power is 6%.
- Preferably, coercive force of the heat treated iron-based amorphous alloy strip is ≤3.5 A/m; under a condition of 50 Hz and 1.35 T, excitation power of the heat treated iron-based amorphous alloy strip is ≤0.1450 VA/kg, and core loss is ≤0.1100 W/kg; and under a condition of 50 Hz and 1.40 T, excitation power of the heat treated iron-based amorphous alloy strip is ≤0.1700 VA/kg, and core loss is ≤0.1500 W/kg.
- Preferably, the iron-based amorphous alloy strip is in completely amorphous phase with a limit thickness of at least 75 nm and a shearing limit strip thickness of at least 29 nm.
- The present disclosure provides an iron-based amorphous alloy strip, which has an atomic composition represented by formula FeaBbSic, wherein a, b and c are each independently atomic percentages of corresponding components; 79.5≤a≤82.5, 11.0≤b≤13.5, 6.5≤c≤8.5, and a+b+c=100; Fe in the iron-based amorphous alloy provided by the present disclosure ensures obtaining stable amorphous iron-based alloys having lower preparation requirements and higher yield; Si element is conducive to the stable formation of amorphous materials; and B is the element that contributes most to the amorphousness of the alloy. Thus, by adjusting the contents of Fe, Si, and B, the present disclosure prepares an iron-based amorphous alloy having high saturation magnetic induction strength, high ductility and low stress sensibility, which makes the transformer assembled by the iron core made from the alloy having strong sudden short circuit resistance.
-
FIG. 1 is a schematic diagram of the simulation experiment equipment for the iron-based amorphous alloy sample ring prepared in the present disclosure under condition of no stress. -
FIG. 2 is a schematic diagram of the simulation experiment equipment for the iron-based amorphous alloy sample ring prepared in the present disclosure under condition of stress. - In order to further understand the present disclosure, the preferred embodiment of the present disclosure is described hereinafter in conjunction with the examples of the present disclosure. It is to be understood that the description is merely illustrating the characters and advantages of the present disclosure, and is not intended to limit the claims of the present disclosure.
- Either internal stress or external stress is inevitable. Stress still exists after optimizing the annealing process, optimizing the iron-core structure of transformer and standardizing the operation. A main object of the present disclosure is to establish a range of amorphous composition having low stress sensibility through adjusting components and evaluating the stress (internal stress and external stress) of strip with different components, so as to effectively show excellent soft magnetic properties of amorphous products, and produce an amorphous transformer that has a relatively good ability of withstanding sudden short-circuit. Thus, the present disclosure discloses an iron-based amorphous alloy represented by formula (I):
-
FeaBbSic (I); - wherein a, b and c are each independently atomic percentages of corresponding components; 79.5≤a≤82.5, 11.0≤b≤13.5, 6.5≤c≤8.5, and a+b+c=100.
- The iron-based amorphous alloy provided by the present disclosure comprises Fe, Si and B, and through adjusting the content of the above elements to give alloy a relatively good glass forming ability, saturation magnetic induction and soft magnetic property. Furthermore, after heat treatment, the strip made of the iron-based amorphous alloy provided by the present disclosure has relatively low anti-stress sensibility.
- In the iron-based amorphous alloy, Fe is the base element, and the content of it is 79.5≤a≤82.5 by atomic percentage. If the atomic percentage of Fe is unduly low, the saturation magnetic induction of the iron-based amorphous alloy will be unduly low, so that it cannot improve the defect of low magnetic flux density of the amorphous and cannot obtain enough magnetic flux density and an iron core with compact structure. When the content is unduly high, the thermal stability of iron-based amorphous alloy and the formability of strip are decreased, making it hard to smooth operation of the strip and obtain a good magnetic product. In the embodiments, the atomic percentage of Fe is 79.5≤a≤81.5, more specifically, the atomic percentage of Fe is 80.0≤a≤81.5.
- The atomic percentage of Si is 6.5≤c≤8.5. When the content is unduly low, the formability of iron-based amorphous alloy strip and the thermal stability of amorphous alloy strip are decreased, making it hard to form a stable amorphous material. When the content is unduly high, the brittleness of the iron-based amorphous alloy becomes high, and the ductility of the annealed strip becomes worse. In the embodiments, the content of Si is 7.0≤c≤8.0.
- The atomic percentage of B is 11.0≤b≤13.5. When the content of B is unduly low, it is hard to form a stable amorphous material. When the content is unduly high, the ability of forming amorphous state does not further improve, i.e., the content of B in the above range gives the iron.-based amorphous alloy of the present disclosure excellent soft magnetic property. In embodiments, the content of B is 11.0≤b≤13.0, more specifically, the content of B is 11.0≤b≤12.5.
- In the present disclosure, a preferably composition of the iron-based amorphous alloy is: a=80.0, 12.0≤b≤13.0, and 7.0≤c≤8.0; or a=80.5, 11.5≤b≤12.5, and 7.0≤c≤8.0; or 81.0≤a≤81.5, 11.0≤b≤13.0, and 7.0≤c≤8.0.
- The iron-based amorphous alloy composition and contents provided by the present disclosure is a reasonable combination of improving magnetic induction and improving glass forming ability, forming an iron-based amorphous alloy with high saturation magnetic induction. Further, on the base of high saturation magnetic induction, the iron-based amorphous alloy of the present disclosure also has low stress sensibility. The reason why the iron-based amorphous alloy provided by the present disclosure has high saturation magnetic induction and low stress sensibility is due to the adjustment of the composition and content of the iron-based amorphous alloy.
- The present disclosure further provides a method for preparing the iron-based amorphous alloy strip represented by formula (I), comprising:
- preparing raw materials according to the atomic percentage of formula (I); smelting the raw materials; heating and insulating the molten liquid after smelting; performing single roller rapid quenching to obtain an iron-based amorphous alloy strip;
-
FeaBbSic (I); - wherein a, b and c are each independently atomic percentages of corresponding components; 79.5≤a≤82.5, 11.0≤b≤13.5, 6.5≤c≤8.5, and a+b+c=100.
- In the process of preparing the iron-based amorphous alloy strip, conventional methods in the art are used to prepare the iron-based amorphous alloy strip with the specific composition of the present disclosure. The preparing and smelting processes above are well known to one of ordinary skill in the art, which would not be descripted in details in the present disclosure. In the smelting process, the metal raw materials are smelted in a medium frequency furnace, and the smelting temperature is from 1300 to 1500° C., and the duration is from 80 to 120 minutes. After smelting, in the present disclosure, the molten material is heated and insulated, and subjected to single roller rapid quenching, so as to obtain the iron-based amorphous alloy strip. The heating temperature is preferably from 1350 to 1470° C., and the insulating duration is preferably from 20 to 50 minutes. After single roller rapid quenching, an iron-based amorphous alloy strip is obtained in completely amorphous state, and limit thickness of the formed amorphous is at least 75 μm, and toughness of the strip is relatively good, which will not crack after 180 degree folding.
- For the present disclosure, the shearable limit thickness of the strip is at least 29 μm, so that the present product has pretty large production margin in industrial production and requirement of the cooling equipment in the industrial process is decreased.
- In the present disclosure, after the raw iron-based amorphous alloy strip is prepared, it is subjected to heat treatment for ease of application. The iron-based amorphous alloy provided by the present disclosure is capable to be treated in a relatively wide annealing range, and the iron-based amorphous alloy strip obtained has relatively low excitation power and loss. In the present disclosure, the heat treatment temperature is from 325 to 395° C.; and in embodiments, the heat treatment temperature is from 335 to 385° C.
- According to the present disclosure, prior to the heat treatment, the obtained iron-based amorphous alloy is preferably winded into a sample ring with an inside diameter of 50.5 mm and an outside diameter of from 53.5 to 54 mm, and then the above sample ring is subjected to heat treatment.
- Loss and deterioration of excitation power of the heat treated sample ring under conditions of stress are detected through simulation experiments, so as to illustrate transition of the properties of iron-based amorphous alloy strip under condition of stress. If the loss and the deterioration coefficient of excitation power of the iron-based amorphous alloy strip still lay in an acceptable range under conditions with a relatively large gauge factor, the iron-based amorphous alloy strip has relatively low stress sensibility. If the loss and the deterioration coefficient of excitation power of the iron-based amorphous alloy strip are unacceptable when the gauge factor is relatively small, the stress sensibility of the iron-based amorphous alloy strip is relatively bad. Through the simulation experiment of the present disclosure, the experiment results show that the iron-based amorphous alloy strip has relatively low stress sensibility.
- In the present disclosure, by adjusting the components and content of the components, i.e., components and content of the components cooperate with each other, the magnetic property of the iron-based amorphous alloy is improved and the stress sensibility of the iron-based amorphous alloy strip is decreased at the same time.
- In order to understand the present disclosure better, the iron-based amorphous alloy will be illustrated in details in conjunction with embodiments hereinafter, and the protection scope of the present disclosure is not limited by the following embodiments.
- According to the alloy components represented by formula FeaBbSic, industrial pure iron, silicon and boron were used to prepare the alloys shown in Table 1. Except for the main elements, there are unavoidable impurity elements in the alloys, such as C, Mn, S, and so on. The materials with different components were successively added to a medium frequency furnace of a furnace volume of 100 kg in the order of boron iron, silicon and pure iron for remelting (the smelting temperature was from 1300 to 1500° C., and the duration was from 80 to 120 minutes). After holding, the molten steel was casted to the spraying ladle for producing an amorphous strip with a width of 20 mm by single roller planar flow casting. In the strip producing process, alloy strips with different thicknesses were produced by adjusting parameters such as roller speed, liquid level and so on (in the strip producing process, the roller speed was from 1000 to 1400 r/min, and the linear speed of the strip producing is from 20 to 30 m/s, and the liquid level was from 200 mm to 300 mm).
- XRD was used to test the free face of strips with different components until the strip thickness was in the amorphous state. Table 1 showed the limit thicknesses of each strip with different amorphous alloy compositions. The saturation magnetization induction of the amorphous alloy strips were measured with VSM. The alloy compositions were comprehensively evaluated by the glass forming ability and saturation magnetic induction of the strips. According to the number of brittle points, maximum shearing thickness of the strip was evaluated. The method for evaluating brittle point is: taking the strip which has a length equal to the perimeter of the crystallizer and shearing the strip along the longitudinal direction. When the number of the brittle point was not more than 2, the strip was considered to be shearable, and when the number of the brittle point was 2, the length was regarded as the shearable limit thickness of the alloy strip.
-
TABLE 1 iron-based amorphous alloy with different compositions and their properties Limit Thickness Shearable of the Obtained limit Composition Amorphous Strip thickness Bs Group Fe Si B (μm) (μm) (T) Example 1 80.0 8.0 12.0 80 30 1.60 Example 2 80.0 7.5 12.5 82 29 1.60 Example 3 80.0 7.0 13.0 80 30 1.61 Example 4 80.5 8.0 11.5 80 30 1.61 Example 5 80.5 7.5 12.0 80 33 1.62 Example 6 80.5 7.0 12.5 80 33 1.62 Example 7 81.0 8.0 11.0 75 32 1.62 Example 8 81.0 7.5 11.5 75 32 1.62 Example 9 81.0 7.0 12.0 75 33 1.62 Example 10 81 6.5 12.5 75 33 1.63 Example 11 81.5 7.0 11.5 65 38 1.62 Comparative 78.0 9.0 13.0 85 26 1.55 Example 1 Comparative 79.5 9.5 11.0 80 27 1.56 Example 2 Comparative 79.0 9.0 12.0 80 27 1.56 Example 3 Comparative 80.0 9.0 11.0 75 26 1.57 Example 4 Comparative 80.0 6.0 14.0 78 30 1.61 Example 5 Comparative 80.5 9.0 10.5 75 25 1.58 Example 6 Comparative 80.5 6.0 13.5 80 32 1.63 Example 7 Comparative 82.0 6.0 12.0 50 36 1.63 Example 8 Comparative 83.0 6.5 10.5 45 37 1.64 Example 9 - Table 1 showed the limit thickness of the amorphous strips, toughness limit thickness of strip producing and saturation magnetic induction of alloys with different compositions. The amorphous strip limit thickness and the toughness limit thickness of strip producing are the tests for strip producing technology. The thicker the strip thickness was, the more relax the requirement for the strip producing equipment was.
- Under the same strip producing condition, the thicker the amorphous strip limit thickness of the alloy, the higher the degree of non-crystallinity of strip was. Although comparative examples 1 to 4 have a relatively high amorphous strip limit thickness, the maximum shearing thickness was below 27 μm. This not only puts more stringent requirements on the cooling intention of the strip producing equipment, but also influences the assembly efficiency of iron core. At the same time, it also carried foreshadows of breaking in assembly and operation process of transformer, leading to an increasing of potential safety hazard in operation of transformer. In addition, the saturation magnetic induction was less than 1.57 T, giving less flexibility to the design of amorphous transformers, and could not meet the design trend of high flux density of transformers. Comparing the comparative example 6 with the examples 4 to 6, it could be concluded that when the content of Fe was the same, the higher the content of Si was, the thinner the shearing thickness was.
- In the comparative examples 8 to 9, the relatively high saturation magnetic induction of the amorphous alloy was expected for the design of transformer. The maximum shearing thickness was between 36 and 38 μm, which was absolutely superior in terms of efficiency in core molding. However, its amorphous forming ability was obviously insufficient based on the limit thickness of the amorphous strip, so it did not meet the requirements for smooth operation of producing strip and it also affected its excitation power and loss.
- It could be concluded from Table 1 that from the comprehensive consideration of smooth operation of strip producing and transformer design, the alloy compositions of examples 1 to 11 have a smooth operation performance and a wide range of transformer design.
- Strips with a thickness of 26 to 28 μm and a width of 30 mm in Table 1 were wound into sample rings with an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm. The sample rings were subjected to stress relief annealing using a box type annealing furnace.
- Annealing was carried out under the protection of argon-with a temperature from 325 to 395° C. at an interval of 10° C. and 1 hour insulation. A magnetic field along the direction of strip preparing was added during the heat treatment process with a magnetic field strength of 1200 A/m. The silicon steel tester was used to test the excitation magnetic and loss of the strip after heat treatment. The test conditions were 1.35 T/50 Hz and 1.40 T/50 Hz respectively. The test results of the characteristic tests were shown in Table 2.
-
TABLE 2 Property data of the samples and the comparative samples after the heat treatment 1.35 T/50 Hz 1.4 T/50 Hz Composition Pe P Pe P Group Fe Si B (VA/kg) (W/kg) (VA/kg) (W/kg) Example 1 80.0 8.0 12.0 0.130 0.099 0.170 0.130 Example 2 80.0 7.5 12.5 0.135 0.098 0.165 0.133 Example 3 80.0 7.0 13.0 0.128 0.103 0.168 0.140 Example 4 80.5 8.0 11.5 0.132 0.102 0.165 0.138 Example 5 80.5 7.5 12.0 0.125 0.085 0.145 0.115 Example 6 80.5 7.0 12.5 0.120 0.090 0.150 0.118 Example 7 81.0 8.0 11.0 0.140 0.108 0.158 0.135 Example 8 81.0 7.5 11.5 0.138 0.100 0.162 0.130 Example 9 81.0 7.0 12.0 0.133 0.105 0.165 0.139 Example 10 81 6.5 12.5 0.135 0.102 0.160 0.138 Example 11 81.5 7.0 11.5 0.140 0.106 0.165 0.145 Comparative 78.0 9.0 13.0 0.156 0.138 0.230 0.165 Example 1 Comparative 79.5 9.5 11.0 0.141 0.123 0.223 0.167 Example 2 Comparative 79.0 9.0 12.0 0.145 0.121 0.215 0.154 Example 3 Comparative 80.0 9.0 11.0 0.136 0.104 0.187 0.150 Example 4 Comparative 80.0 6.0 14.0 0.146 0.110 0.170 0.150 Example 5 Comparative 80.5 9.0 10.5 0.142 0.125 0.225 0.155 Example 6 Comparative 80.5 6.0 13.5 0.130 0.093 0.154 0.120 Example 7 Comparative 82.0 6.0 12.0 0.169 0.148 0.189 0.165 Example 8 Comparative 83.0 6.5 10.5 0.167 0.145 0.187 0.170 Example 9 - It could be concluded form the Table 2 that under the condition of 1.35 T/50 Hz, the loss values of comparative examples 1 to 3 and comparative examples 8 to 9 were relatively high, and the performance was above 0.12 W/kg; and under the condition of 1.4 T/50 Hz, the excitation and loss of comparative examples 1 to 4 and 6 were significantly higher than that of 1.35 T/50 Hz, and were significantly higher than other samples at 1.4 T/50 Hz, and this was mainly related to the low saturated magnetic flux density of the above samples. The excitation magnetic and loss of the amorphous material increase with the increase of the magnetic density. Especially, the performance of excitation power was particularly prominent. Comparing with materials with low saturation magnetic induction, amorphous materials with high saturation magnetic induction allow a greater working magnetic density, i.e., showing relatively low excitation power and losses at magnetic density of 1.4 T. Normally speaking, the comparative examples 8 to 9 show a better performance at 1.4 T test. However, due to the relative large values of them at 1.35 T, the loss and excitation magnetic at 1.4 T increased, resulting in a relatively large value at 1.4 T.
- Examples 1 to 11 exhibited excellent soft magnetic properties at 1.35 T/50 Hz and 1.40 T/50 Hz; loss at 1.35 T/50 Hz was below 0.11 W/kg, and loss at 1.40 T/50 Hz was below 0.15 W/kg.
- The study above mentioned that amorphous materials have relatively low unavoidable loss values, and the performances of amorphous materials were deteriorated by external stress after they were assembled into an iron core. In the present study, a stress model of amorphous sample ring was established to characterize the performance deterioration of amorphous alloys with different compositions after stress deformation, and simulated the performance changes caused by stress when amorphous strip assembled into transformer cores.
- Sample processing: the amorphous strips listed in Table 3 were selected, wound into a sample ring with an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm, and subjected to stress removing and annealing with a box annealing furnace under the protection of argon. Sample rings prepared with different compositions were chosen, and subjected to heat treatment according to the above requirements. The thermal insulation temperature of the heat treatment was from 325 to 395° C. with 5° C. as a gradient for the heat treatment, the insulation duration was from 60 to 120 min, and the magnetic field strength was from 800 to 1400 A/m. The optimal heat treatment performances of each component in the above heat treatment process were chosen to test the performance deterioration of the strip after stress.
- The application of stress was considered by calculating the retraction distance of the circular strip. The feed amount of the sample ring was calculated according to the deformation coefficient formula. As shown in
FIG. 1 ,FIG. 1 was a schematic diagram of the simulation experiment equipment of the sample ring under condition of no stress, andFIG. 2 was a schematic diagram of the simulation experiment equipment of the sample ring under condition of stress. When the sample ring was under stress, the A plate was fixed, and the feeding amount of the sample ring was given with the action of pushing plate B. The sample ring was deformed by the stress, and the pushing plate B was fixed. The loss P1 and excitation power Pe1 of the material under deformation conditions were measured, and the performance of the sample at 1.35 T/50 Hz was tested with a silicon steel tester. - The initial sample ring (without deformation) has an inner diameter of D0 and performance values of P0 and Pe0 respectively. After deformation, the inner diameter was D1, and the performance values were P1 and Pe1 respectively. The gauge factor=(D1−D0)*100%/D0. The loss deterioration coefficient=(P1−P0)*100%/P0. The excitation power deterioration coefficient=(Pe1−Pe0)/Pe0.
- Comprehensively considering the difference of the selected performances and the permissible degree of deterioration of the performance after deformation, this experiment stipulated that the performance deterioration within 50% was an acceptable range, and the sample ring deformation corresponding to the performance value was the maximum allowable deformation coefficient value of the corresponding component material.
- It could be concluded from Table 3 that due to the difference in the composition itself, the best performances were slightly different. The performance value of the Comparative Example 9 was relatively large, and other performance values were basically at the same level. The heat treatment temperature ranged from 345 to 385° C. due to the difference in composition. In the stress experiment, the samples with different compositions having best performance after annealing were selected for stress sensibility experiments.
-
TABLE 3 Performance data of samples with different compositions after optimum heat treatment 1.35 T/50 Hz Best Thermal Composition Treatment P Pe Group Fe Si B Temperature (W/kg) (VA/kg) Comparative 79 9 12 385 0.121 0.145 Example 3 Example 4 80.5 8 11.5 355 0.106 0.131 Example 5 80.5 7.5 12 365 0.085 0.125 Example 6 80.5 7 12.5 365 0.09 0.12 Example 12 79.5 8.5 12 385 0.103 0.137 Example 13 82.5 6.5 11 345 0.110 0.145 Comparative 80.5 6 13.5 355 0.093 0.13 Example 7 Comparative 83 6.5 10.5 345 0.145 0.167 Example 9 -
TABLE 4 Loss values and deterioration coefficient under different gauge factors P(W/kg) Gauge Factor Category 0% 2.0% 4.0% 6.0% 8.0% 10.0% Comparative 0.121 0.134 0.144 0.15 0.178 0.235 Example 3 Example 4 0.106 0.109 0.114 0.118 0.125 0.156 Example 5 0.085 0.089 0.093 0.098 0.103 0.121 Example 6 0.09 0.093 0.098 0.102 0.107 0.123 Example 12 0.103 0.109 0.113 0.121 0.137 0.151 Example 13 0.110 0.116 0.125 0.138 0.148 0.16 Comparative 0.093 0.105 0.109 0.115 0.128 0.165 Example 7 Comparative 0.145 0.165 0.173 0.186 0.198 0.258 Example 9 -
TABLE 4 Loss values and deterioration coefficient under different gauge factors (Continued Table) Deterioration Coefficient of P Maximum Gauge Factor Gauge Category 2.0% 4.0% 6.0% 8.0% 10.0% Factor Comparative 10.7% 19.0% 24.0% 47.1% 94.2% 8.0% Example 3 Example 4 2.8% 7.5% 11.3% 17.9% 47.2% 10.0% Example 5 4.7% 9.4% 15.3% 21.2% 42.4% 10.0% Example 6 3.3% 8.9% 13.3% 18.9% 36.7% 10.0% Example 12 5.8% 9.7% 17.5% 33.0% 46.6% 10.0% Example 13 5.5% 13.6% 25.5% 34.5% 45.5% 10.0% Comparative 12.9% 17.2% 23.7% 37.6% 77.4% 8.0% Example 7 Comparative 13.8% 19.3% 28.3% 36.6% 77.9% 8.0% Example 9 -
TABLE 5 Excitation power and deterioration coefficient under different gauge factors Pe(VA/kg) Gauge Factor Category 0% 2.0% 4.0% 6.0% 8.0% 10.0% Comparative 0.145 0.18 0.351 0.507 1.022 1.441 Example 3 Example 4 0.131 0.144 0.165 0.176 0.24 0.302 Example 5 0.125 0.138 0.16 0.185 0.205 0.401 Example 6 0.12 0.132 0.154 0.176 0.207 0.354 Example 12 0.137 0.148 0.164 0.185 0.215 0.367 Example 13 0.145 0.158 0.179 0.192 0.208 0.42 Comparative 0.13 0.178 0.33 0.428 0.854 1.025 Example 7 Comparative 0.167 0.195 0.225 0.403 0.784 0.998 Example 9 -
TABLE 5 Excitation power and deterioration coefficient under different gauge factors (Continued table) Deterioration Coefficient of Pe Maximum Gauge Factor Gauge Category 2.0% 4.0% 6.0% 8.0% 10.0% Factor Comparative 24.1% 142.1% 249.7% 604.8% 893.8% 2.0% Example 3 Example 4 9.9% 26.0% 34.4% 83.2% 130.5% 6.0% Example 5 10.4% 28.0% 48.0% 64.0% 220.8% 6.0% Example 6 10.0% 28.3% 46.7% 72.5% 195.0% 6.0% Example 12 8.0% 19.7% 35.0% 56.9% 167.9% 6.0% Example 13 9.0% 23.4% 32.4% 43.4% 189.7% 8.0% Comparative 36.9% 153.8% 229.2% 556.9% 688.5% 2.0% Example 7 Comparative 16.8% 34.7% 141.3% 369.5% 497.6% 4.0% Example 9 - Tables 4 and 5 clearly showed that iron-based amorphous alloys undergone a certain degree of performance deterioration due to the influence of stress, and the performance deterioration coefficient increased as the deformation coefficient increased. Comparing the loss and the excitation power of each component, it could be found that the deterioration of the excitation power significantly exceeded its loss. The allowable deterioration coefficient of excitation power was 6%, while the allowable deterioration coefficient of loss was 10%. That is, the application of external stress to the amorphous strip has a greater effect on the excitation power.
- Comparing the examples with comparative examples, it could be found that there was a big difference in the performance deterioration coefficient of strips with different compositions when subjected to stress. The loss of the amorphous alloy strips in examples 4 to 6 and 12 to 13 allowed a gauge factor of 10%, and excitation power of examples 4 to 6 and 12 to 13 allowed a deterioration coefficient of 6%. Considering the bucket effect of the performance comprehensively, the allowable deterioration coefficient of the embodiments was 6%. The allowable gauge factors for the losses and excitation power of the comparative example were 8% and 2%, respectively, and the allowable deterioration factor for the comparative example was 2%. In view of above, the annealed post-amorphous tape embodiment had significant advantages in the resistance to stress sensibility, allowing greater deformation and ensuring that the material properties were within an acceptable range.
- The above description of the embodiments is merely for helping to understand the method of the present disclosure and its core idea. It should be pointed out that one of ordinary skill in the art can also make several improvements and modifications to the present disclosure without departing from the principles of the present invention, and these improvements and modifications also fall into the protection scope of the claims of the present invention.
- The above description of the disclosed embodiments enables one of ordinary skill in the art to implement or use the present invention. Various modifications to these embodiments will be readily apparent to one of ordinary skill in the art, and the general principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present disclosure will not be limited to the embodiments shown herein but will be consistent with the widest scope consistent with the principles and novel features disclosed herein.
Claims (13)
FeaBbSic (I);
FeaBbSic (I);
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201710447487.1A CN107267889B (en) | 2017-06-14 | 2017-06-14 | A kind of Fe-based amorphous alloy and preparation method thereof with low stress sensibility |
CN201710447487.1 | 2017-06-14 | ||
PCT/CN2017/100862 WO2018227792A1 (en) | 2017-06-14 | 2017-09-07 | Iron-based amorphous alloy having low stress sensitivity, and preparation method therefor |
Publications (1)
Publication Number | Publication Date |
---|---|
US20190256944A1 true US20190256944A1 (en) | 2019-08-22 |
Family
ID=60066147
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US16/335,257 Abandoned US20190256944A1 (en) | 2017-06-14 | 2017-09-07 | Iron-based amorphous alloy having low stress sensitivity, and preparation method therefor |
Country Status (4)
Country | Link |
---|---|
US (1) | US20190256944A1 (en) |
JP (1) | JP2020524222A (en) |
CN (1) | CN107267889B (en) |
WO (1) | WO2018227792A1 (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN112593052A (en) * | 2020-12-10 | 2021-04-02 | 青岛云路先进材料技术股份有限公司 | Iron-based amorphous alloy and annealing method of iron-based amorphous alloy |
CN113073178A (en) * | 2021-03-23 | 2021-07-06 | 电子科技大学 | Preparation method of GHz-frequency-band high-wave-absorption-performance iron-based nanocrystalline alloy |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN108018504B (en) | 2017-12-21 | 2020-05-08 | 青岛云路先进材料技术股份有限公司 | Iron-based amorphous alloy and preparation method thereof |
CN109594006A (en) * | 2018-12-10 | 2019-04-09 | 国网上海市电力公司 | The method for recycling the smelting iron-based amorphous master alloy of amorphous transformer core |
CN109504924B (en) * | 2018-12-17 | 2021-02-09 | 青岛云路先进材料技术股份有限公司 | Iron-based amorphous alloy strip and preparation method thereof |
CN115896648B (en) * | 2022-12-19 | 2024-05-14 | 青岛云路先进材料技术股份有限公司 | Iron-based amorphous alloy strip and preparation method thereof |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB2038358B (en) * | 1978-11-29 | 1982-12-08 | Gen Electric | Amorphous fe-b-si alloys |
JPS6436726A (en) * | 1987-07-31 | 1989-02-07 | Kawasaki Steel Co | Annealing method for iron based amorphous alloy thin strip |
JP2718948B2 (en) * | 1987-07-31 | 1998-02-25 | 川崎製鉄株式会社 | Manufacturing method of iron-based amorphous alloy ribbon |
JPH02175813A (en) * | 1988-12-27 | 1990-07-09 | Tokin Corp | Manufacture of amorphous magnetic alloy foil |
JP4288687B2 (en) * | 2006-12-04 | 2009-07-01 | 株式会社 東北テクノアーチ | Amorphous alloy composition |
JP5361149B2 (en) * | 2007-06-28 | 2013-12-04 | 新日鐵住金株式会社 | Fe-based amorphous alloy ribbon |
US9290831B2 (en) * | 2009-09-14 | 2016-03-22 | Hitachi Metals, Ltd. | Soft-magnetic, amorphous alloy ribbon and its production method, and magnetic core constituted thereby |
IN2014DN08435A (en) * | 2012-03-15 | 2015-05-08 | Hitachi Metalsltd | |
CN105358727A (en) * | 2013-07-30 | 2016-02-24 | 杰富意钢铁株式会社 | Thin amorphous iron alloy strip |
WO2015022904A1 (en) * | 2013-08-13 | 2015-02-19 | 日立金属株式会社 | Iron-based amorphous transformer core, production method therefor, and transformer |
CN103628003B (en) * | 2013-12-13 | 2015-10-07 | 青岛云路新能源科技有限公司 | Magnetic core preparation method |
WO2017090402A1 (en) * | 2015-11-26 | 2017-06-01 | 日立金属株式会社 | Iron-based amorphous alloy ribbon |
CN105970119B (en) * | 2016-07-13 | 2019-09-20 | 江苏非晶电气有限公司 | A kind of process improving alloy melt amorphous formation ability |
CN106906431A (en) * | 2017-04-06 | 2017-06-30 | 青岛云路先进材料技术有限公司 | A kind of Fe-based amorphous alloy and preparation method thereof |
-
2017
- 2017-06-14 CN CN201710447487.1A patent/CN107267889B/en active Active
- 2017-09-07 JP JP2020519164A patent/JP2020524222A/en active Pending
- 2017-09-07 WO PCT/CN2017/100862 patent/WO2018227792A1/en active Application Filing
- 2017-09-07 US US16/335,257 patent/US20190256944A1/en not_active Abandoned
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN112593052A (en) * | 2020-12-10 | 2021-04-02 | 青岛云路先进材料技术股份有限公司 | Iron-based amorphous alloy and annealing method of iron-based amorphous alloy |
CN113073178A (en) * | 2021-03-23 | 2021-07-06 | 电子科技大学 | Preparation method of GHz-frequency-band high-wave-absorption-performance iron-based nanocrystalline alloy |
Also Published As
Publication number | Publication date |
---|---|
WO2018227792A1 (en) | 2018-12-20 |
CN107267889A (en) | 2017-10-20 |
CN107267889B (en) | 2019-11-01 |
JP2020524222A (en) | 2020-08-13 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US20190256944A1 (en) | Iron-based amorphous alloy having low stress sensitivity, and preparation method therefor | |
JP5668460B2 (en) | Method for producing non-oriented electrical steel sheet | |
US10526673B2 (en) | Non-oriented electrical steel sheet and method for producing the same, and motor core and method of producing the same | |
US10597759B2 (en) | Non-oriented electrical steel sheet having high magnetic flux density and motor | |
US11767583B2 (en) | FeCo alloy, FeSi alloy or Fe sheet or strip and production method thereof, magnetic transformer core produced from said sheet or strip, and transformer comprising same | |
JP6020863B2 (en) | Non-oriented electrical steel sheet and manufacturing method thereof | |
JP5927754B2 (en) | Oriented electrical steel sheet and manufacturing method thereof | |
JP6025864B2 (en) | High silicon steel plate excellent in productivity and magnetic properties and method for producing the same | |
US11505845B2 (en) | Soft high-silicon steel sheet and manufacturing method thereof | |
JP2013189693A (en) | Method for producing non-oriented magnetic steel sheet | |
US20150243419A1 (en) | Method for producing grain-oriented electrical steel sheet | |
EP4254440A2 (en) | Method of production of tin containing non grain-oriented silicon steel sheet | |
WO2011115120A1 (en) | Method for producing directional electromagnetic steel sheet | |
JP2011246810A (en) | Nonoriented magnetic steel sheet and motor core using the same | |
JP2019505664A (en) | Annealing separator for grain-oriented electrical steel sheet, grain-oriented electrical steel sheet, and method for producing grain-oriented electrical steel sheet | |
JP5206017B2 (en) | Method for producing high silicon steel sheet | |
JP6623795B2 (en) | Electrical steel sheet and method for manufacturing electrical steel sheet | |
KR101633611B1 (en) | High silicon electrical steel sheet with superior magnetic properties, and method for fabricating the high silicon electrical steel | |
JP6294028B2 (en) | Method for producing Fe-Ni permalloy alloy | |
JP2015224349A (en) | Nonoriented electromagnetic steel sheet and manufacturing method therefor, hot rolled sheet for nonoriented electromagnetic steel sheet and manufacturing method therefor | |
JP5826284B2 (en) | Wire rods, steel wires having excellent magnetic properties, and methods for producing them | |
JP5967357B2 (en) | Iron-based amorphous alloy ribbon | |
JP2017128759A (en) | Non-oriented magnetic steel sheet and production method therefor | |
US20230036214A1 (en) | Non-oriented electrical steel sheet and manufacturing method therefor | |
CN104302801A (en) | Non-oriented magnetic steel sheet that exhibits minimal degradation in iron-loss characteristics from punching process |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AS | Assignment |
Owner name: QINGDAO YUNLU ADVANCED MATERIALS TECHNOLOGY CO., L Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:LI, XIAOYU;PANG, JING;LI, QINGHUA;AND OTHERS;REEL/FRAME:048655/0878 Effective date: 20190216 |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: APPLICATION DISPATCHED FROM PREEXAM, NOT YET DOCKETED |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: NON FINAL ACTION MAILED |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: FINAL REJECTION MAILED |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: RESPONSE AFTER FINAL ACTION FORWARDED TO EXAMINER |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: ADVISORY ACTION MAILED |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: NON FINAL ACTION MAILED |
|
STCB | Information on status: application discontinuation |
Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION |