JPS60234949A - High silicon steel strip and its manufacture - Google Patents

Abstract

PURPOSE:To obtain a high silicon steel strip having good bendability, workability and superior in magnetic characteristic by contg. high silicon content, Co or/ and Ni comprising columnar crystal having a prescribed particle diameter and growing vertically to the strip surface and contg. no super lattice of Fe3Si. CONSTITUTION:Said high silicon steel strip contains basically 4-10% Si, <=10% Co, <=3% Ni and the balance Fe with inevitable impurities, further, <=2% Al and Mn can be added respectively. In said strip, 1-100mum crystal grains and substantially no super lattice Fe3Si exist, and the columnar crystals grow vertically to the strip surface. For manufacturing said strip, a molten silicon steel having said compsn. is cooled directly and ultrarapidly at 10<3>-10<6> deg.C/sec cooling rate, then immediately finished to the strip having prescribed thickness. Namely, usually indispensable hot and cold rolling processes are eliminated thoroughly. As the result, the high silicon steel strip having aforementioned characteristics is obtained.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention comprises 4 to 10% silicon, 10% or less cobalt,
The present invention relates to a high-silicon steel ribbon containing 3% or less of nickel and a method for producing the same.

Silicon steel ribbon, which is made by adding about 3% silicon to iron, is widely used as a core material for electrical equipment such as transformers.

These silicon steel sheets are usually divided into non-oriented silicon steel sheets in which the crystal axis orientations of the crystal grains vary in various directions, and grain-oriented silicon steel sheets in which the [100] axes of the crystal grains are aligned in the rolling direction. The former is mainly used for core materials of rotating machines and generators where magnetic flux is applied in various directions, while the latter is used for iron core materials such as transformers where magnetic flux is applied only in one direction. In such applications, the most strongly required points are:
The first is to minimize the core loss of the material. This is expected to become more and more strongly demanded due to the soaring energy prices. The second goal is to keep equipment noise caused by magnetostrictive vibration of the material as low as possible. This demand is also expected to become even stronger. In order to meet these demands, technology has been developed to minimize the amount of impurities such as carbon, nitrogen, oxygen, and sulfur that degrade iron loss in non-oriented silicon steel, and to align the [100] axis with the plate surface. , is becoming more effective. On the other hand, for grain-oriented silicon steel, techniques have been developed to further increase the degree of integration in the rolling direction of the [100] axis, and techniques to apply tension to the steel plate through coating treatment to reduce iron loss and apparent magnetostriction.

However, the conventional silicon steel sheet technology has almost reached the stage of completion, and improvements in magnetic properties and magnetostrictive properties are on the verge of saturation. Improvements are expected to be modest.

On the other hand, high-silicon steel, which is made by adding about 6.5% silicon to iron, has a low saturation magnetic flux density of about 1.80 T (Tesla), but magnetostriction virtually disappears, and magnetic anomaly Since the orientation is also halved, it has a soft magnetic property (approximately 3% silicon steel) that is superior to that of silicon steel.
High magnetic permeability μ and low coercive force Hc)
Known since the 50's. When this material is assembled into a transformer or the like, it has extremely low iron loss at a suitable excitation magnetic flux density and virtually eliminates noise, making it an extremely attractive material for applications. However, when the amount of silicon exceeds about 4%, the material matrix hardens and, in addition, a regular lattice (Fe3Si) appears and rapidly becomes brittle. This makes rolling extremely difficult, making not only production practically impossible but also processing such as shearing and punching impossible. Under these circumstances, high-silicon steels with a silicon content of 4% or more, especially high-silicon steels with a silicon content of about 6.5%, are not put into practical use despite their excellent magnetic properties.

On the other hand, the present inventors found that a ribbon obtained by ultra-quenching a melt of silicon steel containing 4 to 10% silicon, 10% or less cobalt, and 3% or less nickel has extremely large crystal grains. minute,
It has virtually no regular grid and is extremely flexible and workable.
They discovered that a high-silicon steel ribbon with excellent magnetic properties could be obtained, and conducted extensive research to complete the present invention.

Figures 1 (A) and (B) show an example of microstructure photographs of a silicon steel ribbon of the present invention consisting of 6.5% silicon and the remainder substantially iron; The surface structure of the thin strip obtained by
B) is its cross-sectional structure, which is about 5 to 10 μm from this photo.
It can be seen that crystal grains with a diameter of m are arranged and grown in a direction perpendicular to the surface of the thin plate. FIG. 2 shows the bending workability of a similar thin strip, and FIG. 2(A) shows the thin strip of the present invention wound around a rod-shaped body of 4 mmφ, and FIG. 2(B) shows the bending workability of a similar thin strip. This shows the state of bending. Figure 2 (A
) and (B), it will be understood that it can be bent to a degree that was previously thought to be impossible.

On the other hand, cylinder 3 contains a molten body containing various proportions of 3 to 11% silicon, with the remainder essentially consisting of iron at 103 to 104 °C/sec.
The coercive force Hc (curve A) when a ribbon obtained by ultra-quenching at c is magnetized to a maximum of 10 KG is shown in comparison with that of high-silicon steel made by a conventional method (curve B). As is clear from FIG. 3, the ribbon of the present invention, like the conventional high-silicon steel, exhibits a phenomenon in which Hc gradually decreases in the high-silicon region, and in the vicinity of 6.5% silicon, it is lower than the conventional 3% silicon steel. Shows similar Hc.

The ribbon of the present invention has a higher Hc than conventional products when it is rapidly cooled from the molten state, but it can be improved by annealing as described below, and it can be brought to the level of conventional high-silicon iron materials. be able to.

The characteristics related to the workability of the present invention are that the crystal grains are the
This is because, as shown in Figures (A) and (B), it is fine and no regular lattice is substantially observed. However, if the crystal grains exceed 100 μm in the ultra-quenched state, the workability will be reduced, which is undesirable.On the other hand, even if the crystal grains are made finer than 1 μm, there will be no substantial improvement in the workability, and too high-speed cooling will be required. This will hurt economic efficiency.

When the silicon and steel ribbon obtained by the method of the present invention is heat-treated, the crystals become coarser and the magnetic properties (Hc) are significantly improved. This can be explained using microscopic photographs as follows.

Figure 1 (C) and (D) are 6.4%Si-93.6%
The results of heat treatment of a silicon steel ribbon having a composition of Fe at 1200° C. in an argon gas atmosphere for 40 minutes are shown, (C) is a photograph of the surface structure, and (D) is a photograph of the cross-sectional structure. The size of the crystal grains shown in the photograph indicates that grain growth has progressed due to heat treatment and the crystal grain size has become significantly coarser. The crystal grain size is about 150 μm or more, as seen from the photo.

The grain size of the crystal grains in this ribbon is a function of heat treatment time and heat treatment temperature. Magnetic properties (Hc) increase as the ribbon crystals become coarser.
was significantly improved.

Even after the heat treatment described above, the ribbon has sufficient workability, but this is because the crystal grains develop in a direction perpendicular to the sheet surface, as shown in the micrograph in Figure 1 (D). It is presumed that this is due to the fact that there is no regular lattice, and the fact that there is no regular grid.

Next, the component composition will be explained.

The silicon steel ribbon of the present invention basically contains 4 to 10% silicon.
It contains 10% or less of cobalt, 3% or less of nickel, and the remainder consists essentially of iron and unavoidable impurities.

If the silicon content is less than 4%, the magnetic properties will be comparable to those of conventional products, and if the silicon content exceeds 10%, it will become brittle and the magnetic properties will deteriorate.

Note that since silicon exhibits the best magnetic properties when the content is 5 to 7%, this range is suitable. Silicon steel contains oxygen, sulfur, carbon, and nitrogen as unavoidable impurities.
If any of these are present in the product, they will deteriorate the iron loss characteristics, make the ribbon brittle, and deteriorate the workability, so it is desirable to keep them as low as possible. If the total amount of these impurities exceeds 0.1%, the iron loss increases and is inferior to conventional silicon steel, so the upper limit is set at 0.1%. In addition, in the current steelmaking technology, O < 50 ppm, S 80 ppm, G 100 ppm.
, N<50 ppm, so it is particularly preferable to keep it within this range.

The composition of the present invention further includes 2% or less aluminum and 2% aluminum.
% or less of manganese can be added.

Aluminum is a stronger deoxidizing element than silicon, so by adding aluminum, a material with lower oxygen content can be obtained. Further, since it increases electrical resistance, it is preferable in terms of lowering eddy current loss. However, since aluminum increases magnetostriction, it is not preferable to add more than 2%, and the upper limit is set at 2%.

Manganese is contained as an unavoidable mixed element in an amount of about 0.05% in ordinary steel manufacturing. Unlike oxygen and sulfur, this element is known to be preferable for silicon steel for its rollability and magnetic properties.

Also in the present invention, the addition amount is 2% or less, preferably 0.2 to
It has been found that addition of 1.3% not only improves the magnetic properties but also provides an ultra-quenched ribbon with good shape (no holes or cracks at the edges in the width direction of the ribbon). The cause of these phenomena is not clear, but by adding manganese, the impurity sulfur changes from a solid solution state or a fine precipitate state to a large MnS precipitate, which improves rolling properties and magnetic properties. It is thought that However, if manganese exceeds 2%, the magnetic properties will deteriorate and the product will be difficult to process due to further hardening, so the maximum content was limited to 2%.

Since the ribbon of the present invention has a high silicon content, it has the disadvantage of inevitably having a low saturation magnetic flux density. Adding cobalt to the Fe-Si alloy increases the saturation magnetic flux density, so in the present invention as well, cobalt can be added as needed to compensate for the above disadvantages. However, since cobalt is an extremely expensive element, the upper limit of cobalt is limited to 10% in the present invention. Nickel is an element that has the effect of increasing toughness in Fe-Si alloys, and in the present invention, nickel is added to 3%.
It has been suggested below that adding preferably 0.2 to 1.5% makes it possible to produce a high-quality ultra-quenched ribbon.

In addition to the above-mentioned impurities, there may be trace amounts of 0.1% or less of elements such as chromium, molybdenum, tungsten, vanadium, titanium, and tin.
This does not in any way impede the effects of the present invention.

Now, in the conventional production of silicon steel sheets, a steel ingot or continuous cast slab is hot rolled into a hot strip with a thickness of 1.5 to 4 mm, and then a suitable cold rolling and heat treatment are combined to give a thickness of 0.2 mm. A product with a thickness of ~0.50 mm is produced, but in the present invention, a silicon steel melt having the above-mentioned composition is directly ultra-quenched at a cooling rate of 103 to 106 °C/sec to immediately form a thin product with a predetermined thickness. It is finished into an obi. In other words, a silicon steel melt is directly made into a finished product or a semi-finished product, completely eliminating the hot rolling and cold rolling steps that are essential to conventional processes. Any method can be used to ultra-quench a molten material to form a thin ribbon, as long as it is wide enough, has a specified thickness, has a uniform thickness, and can be drawn out continuously into a coil. However, typically, as shown in Figures 4 and 5, the molten material is jetted out continuously from holes of an appropriate shape on a continuously moving moving surface, rapidly solidified, and formed into a predetermined shape. It is preferable to obtain a thick strip in the form of a coil.

FIG. 4(a) is a schematic diagram of an apparatus that uses a bowl-shaped rotating body 2 as a moving surface and ejects a melt 4 from a jet nozzle 1 onto the inner rotating surface to obtain a rapidly solidified continuous ribbon 3. It is shown. In addition, in Figures (b) and (c), molten silicon steel is poured from the spout holes onto one rotating roll 5 or between two adjacent rotating rolls 5' and 5'', which are not necessarily of the same size. A schematic diagram of an apparatus for obtaining a continuous ribbon by continuous jetting and ultra-quenching between two rolls is shown.
d) shows a schematic diagram of an apparatus in which molten silicon steel 4 is supplied between an endless metal belt conveyor 7 and a rotating roll 5, and is rapidly cooled to continuously obtain a thin ribbon.

When manufacturing a silicon steel ribbon according to the present invention using the above-described apparatus, it is important that the melt solidify and cool at a sufficiently fast rate. First of all, if it takes a long time for the ejected molten material to solidify when it hits the moving cooling body, the flow of the ejected molten material will no longer be integrated, which may result in holes or voids, or the formation of thin strips with uneven thickness. In addition, when manufactured in the atmosphere, the ribbon is oxidized and nitrided, making it impossible to produce a ribbon with a good shape, or even if it is possible, the magnetic properties deteriorate due to the inclusion of oxygen and nitrogen in the finished product. on the other hand,
If it takes a long time from solidification to reach a temperature of approximately 400°C, at which no grain growth or regular lattice formation occurs, the resulting ribbon will partially have an ordered lattice, and the crystal grains will become coarse and later. Subsequent shearing, punching, or optional rolling becomes difficult. The inventors conducted experiments by varying the rotation speed of the cooling rotor and the injection pressure of the molten material, and found that after the molten material is ejected from the nozzle, it is solidified and cooled, and the temperature of the ribbon reaches 400°C. It has been found that a desired ribbon cannot be obtained if the average cooling rate during the process is less than 103° C./sec. In other words, if it is produced in an atmosphere that cools slower than this critical cooling rate, it may not be possible to obtain a continuous ribbon with a good shape due to oxidation, or even if it is obtained, it may be extremely brittle due to grain growth, etc. or In order to economically and reliably obtain a ribbon with sufficiently fine grains and substantially no ordered lattice,
It is preferable to cool down to 0°C at a cooling rate of 103 to 106°C/sec.

Incidentally, the high-silicon steel ribbon according to the present invention must also be manufactured industrially with a sufficiently wide width. in general,
A nozzle with a slit-shaped ejection hole over the required width is used for this purpose, but in order to obtain a thin strip with a uniform thickness across the width, two steps are required as shown in Figures 5 and 6. It is preferable to use a nozzle 1 in which two or more ejection holes 10 are placed close to each other and arranged in a line over a necessary width. At this time, if an auxiliary jet hole 10' is provided at the end of the nozzle, a more uniform melt jet 9 can be obtained over the entire width.

Therefore, by doing so, a ribbon having a uniform thickness can be obtained.

Note that in order to continuously produce high-silicon steel ribbons industrially, it is necessary to eject the melt continuously from the nozzle over a long period of time, resulting in significant damage to the nozzle. The nozzle is typically made of a refractory material with a high melting point, such as boron nitride ceramics, or in this case, continuous cooling of the area around the nozzle with water, liquid metal or gas to prevent damage may cause the nozzle to evaporate. This is advantageous because the life of the product is significantly extended.

Furthermore, in order to reliably prevent oxidation and nitridation and obtain a ribbon with few impurities, the entire ribbon manufacturing apparatus is placed in one tank under a protective gas atmosphere or under vacuum, as shown in Figure 7. It's also good. In addition, argon, helium, or CO2 gas may be sprayed as a protective gas near the nozzle.

FIG. 7 shows a manufacturing apparatus for obtaining a silicon steel ribbon according to the present invention under vacuum. 11 is a vacuum chamber, and a rotating roll 5 is installed in this vacuum chamber 11. The rotating roll 5 is made of a material with good thermal conductivity, such as copper, and is connected to a motor that drives it. Directly above the rotating roll 5, a nozzle 1 for storing a high-silicon auxiliary material is installed so as to be movable up and down.

Reference numeral 12 denotes a pipe for introducing the high-silicon iron material into the nozzle 1. Further, 13 is a pipe for injecting gas to jet the molten high-silicon steel material from the nozzle 1. 14 is a cylinder that moves the nozzle 1 up and down, and adjusts the distance between the nozzle 1 and the rotating roll 5. 15 is a vacuum bellows which expands and contracts in accordance with the vertical movement of the nozzle 1 and seals the space between the vacuum chamber 11 and the nozzle 1. 16
A heater is arranged around the tip of the nozzle 1 and heats the nozzle 1 at a temperature of, for example, 1400 to 1600°C to melt the high silicon iron material housed within the nozzle 1.

17 is an exhaust port of the vacuum chamber 11 and is connected to an exhaust system.

18 is a collection port for the silicon-iron ribbon produced by this apparatus.

Spouting the molten crystalline high silicon steel material from the nozzle 1,
When a silicon steel ribbon is obtained by ultra-quenching on the rotating surface of the rotating roll 5, the inside of the vacuum chamber 11 may be a natural atmosphere under atmospheric pressure, or may be a protective atmosphere such as Ar or N2.

In the silicon steel ribbon manufacturing apparatus shown in FIGS. 4 to 7 described above, it is important to select the material of the rotary cooling body in consideration of the wettability between the cooling body and silicon iron. Also, if the melting temperature of silicon or steel melts is 300°C or more higher than the melting point,
The viscosity of the molten material decreases, and the molten material oozes out from the nozzle during heating of the molten material, or the jet stream becomes mist-like when it is ejected from the nozzle, or it spreads widely on the surface of the rotary table or cooling body.
Because the thin strip may not have a constant width, the thin strip may become too thin or become slant-like. On the other hand, if the melting temperature of the molten material is too low, the viscosity of the molten material increases, and the jet flow of the molten material will not be able to sufficiently cling to the surface of the rotating cooling body and move, resulting in super rapid cooling of the molten material. The initial effect cannot be obtained.

Furthermore, if the jet pressure of the bath melt from the nozzle is too high, the jet stream of the melt becomes irregularly shaped fine particles and scatters.

Therefore, when carrying out the invention, the melt is placed on the cooling body with a contact angle of between 10° and 170°, preferably approximately 90°.
It is necessary to select the viscosity so that it will rise. For this purpose, the temperature of the melt must be 100°C to 130°C below the melting point.
It is preferable to use a temperature higher than 0.degree.

According to the present invention, the pressure at which the melt is ejected from the nozzle is 0.
．． 01-1.5 atm. It is recommended that the range be within the range of . This is because if the ejection pressure of the molten material is too high, the molten material may become mist, become scattered in the form of fine particles, or the resulting thin ribbon may become slant-like, depending on the viscosity of the molten material.

Note that if the melt is ejected in a vacuum, the disadvantages of the thin ribbon to be obtained colliding with air and forming a slit, a hangnail at the periphery, or a porous state as described above can be eliminated.

By the method described above, a high-silicon steel ribbon is produced immediately from the melt into a coil. The crystal grains of the ribbon thus obtained are extremely fine and usually have a size of 1 to 100 μm.

Such a thin ribbon has a good shape and magnetic properties to the extent that it can be made into a finished product in this state, but in order to develop even higher magnetic properties, it must be heated to 400 to 1300
℃, preferably 800 to 1250℃ for a short time to remove internal strain and at the same time reduce the grain size to 0.05 to 10
It is best to grow it up to mm. When this process is performed, for example, the coercive force Hc is significantly reduced. If the heat treatment temperature exceeds 1300° C., the ribbon becomes brittle and cannot be put to practical use. Furthermore, it is impossible to eliminate internal strain at temperatures below 400°C. This heat treatment may be carried out by any method, but from an industrial perspective it is preferable to anneal the material in a continuous annealing furnace for about 60 seconds and cool it as quickly as possible.

Figure 8 shows a ribbon A having an average grain size of 5 μm and a thickness of 80 μm, consisting of 6.5% silicon and essentially iron, and a ribbon B having the same composition and an average grain size of 15 μm and a thickness of 80 μm. 2 at temperature
This is the result of annealing for min. It will be understood that as a result of annealing, a decrease in Hc is observed at a temperature of 400°C or higher, and it becomes saturated at about 1300°C.

On the other hand, from a practical point of view, it is desirable that the space factor of the core be as high as possible when incorporating it into the core. For this purpose, the surface of the ribbon needs to be smooth. In the present invention, the thin ribbon in the ultra-rapidly solidified state exhibits a sufficiently smooth surface condition under appropriate manufacturing conditions, but when an even higher level of smoothness is required, It is desirable that the rapidly cooled and solidified ribbon is subjected to heat treatment if necessary, then rolled at a rolling reduction of 5% or more and annealed at the above temperature. Rolling can be carried out satisfactorily in an energized cold rolling mill, but if the silicon content is particularly high (7 to 10%) and cracking during rolling is a concern, it is recommended to perform warm rolling at 100°C to 500°C. Ru. Appropriate rolling heat treatment makes the surface of the ribbon smooth, and at the same time, the rolling heat treatment improves the magnetic properties. The cause of this is not clear at present, but it is presumed that the texture changes due to the geothermal treatment after cold rolling.

The ribbons produced as described above are laminated and used as cores for electrical equipment such as transformers and cores for rotating machines. At that time, if the laminated core is annealed in that state to generate a regular lattice in the ribbon, Hc can be significantly reduced. In this case, even if a regular lattice occurs, since it has already been formed into an iron core, it does not pose any problem and can be said to be a logical method of use.

Figure 9 shows a ribbon consisting of 6.5% silicon, 0.2% manganese, and the remainder substantially iron, which was annealed for 3 minutes at 1200°C and then further heated for 35 minutes.
This figure shows changes in magnetic properties (Hc) obtained by annealing at temperatures ranging from 0 to 700°C for various periods of time.

Clearly, good results are obtained when the temperature is maintained at 400-650°C for 30 minutes or more. Therefore, the above-mentioned annealing in the core state is preferably performed within this temperature range.

Next, the present invention will be specifically explained with reference to Examples.

Example 1 Silicon 6.5%, manganese 0.6%, aluminum 0.3
%, and the unavoidable impurities are 0.007% carbon, 0.004% nitrogen, 0.003% oxygen, and 0.005% sulfur.
A copper (300 rpm) rotating molten iron containing
A thin ribbon with a thickness of 80 μm was made by ejecting it onto a rotary cooling body of mmφ). Table 1 shows the magnetic properties (Hc) and workability of this ribbon.

The ribbon was annealed at 1200°C for 3 minutes, rolled to 65 μm, and further annealed at 1000°C for 3 minutes. Finally, this was wound into a coil and annealed at 500° C. for 3 hours.

In Table 1, the magnetic properties (Hc) show the values when magnetized to 1.5 (Tesla). In addition, the minimum radius of curvature indicates the minimum radius that will not cause damage when wrapped around glass rods of various radii.
As for the shearability, ○ means that there is no shear burr and good shearability; △ means that there is some shear burr, but shearing is sufficient; and × means that shearing is difficult.

Example 2 Contains 9.5% silicon, 1.5% manganese, 2% cobalt, 0.1% aluminum, 0.7% nickel, and 0.004% carbon, 0.0025% nitrogen as unavoidable impurities.
Molten silicon iron containing 0.0023% oxygen and 0.003% sulfur is heated in a stainless steel (100
A thin ribbon with a thickness of 100 μm was produced by ejecting it onto a twin rotating body of mmφ). This was immediately rolled to 50 μm and annealed at 950° C. for 2 minutes.

Further, this was annealed at 420°C for 70 hours. The magnetic properties and workability after each of these treatments are shown in Table 2.

Table 2 Note that the measurement conditions for each item are the same as in Example 1.

According to the method of the present invention, an extremely flexible high-silicon iron ribbon can be produced continuously at high speed, and the high-silicon iron ribbon can be easily processed, and rolling and heat treatment are also possible.

According to the present invention, a high-silicon iron ribbon without an ordered lattice, which has excellent bendability and shearability, is produced, and after being formed into a transformer core or the like, heat treatment is performed to generate an ordered lattice, and magnetic properties (Hc ), which is extremely useful industrially.

[Brief explanation of the drawing]

Figure 1 (A) and (B) show 6.4%S in the ultra-quenched state.
Micrographs of the surface and cross section of i-Fe silicon-iron ribbon,
(C) and (D) are 6.4% Si-F in a heat-treated state.
e Micrograph of the surface and cross section of the silicon-iron ribbon, Fig. 2 (
A) and (B) are drawings showing the silicon-iron ribbon of the present invention wound around a rod-shaped body having a diameter of 4 mm and a bent state, respectively. Fig. 3 is a magnetic characteristic diagram showing the relationship between silicon content and coercive force (Hc) of the silicon-iron ribbon of the present invention in comparison with that of the conventional one, and Fig. 4 (a), (b), (c ) and (d) are schematic diagrams showing an example of the apparatus for producing the silicon-iron ribbon of the present invention, and FIGS. FIG. 1 is a cross-sectional view of a nozzle and a vertical cross-sectional view of the nozzle, showing an example of a multi-hole nozzle for manufacturing an iron ribbon. FIG. 7 is an explanatory diagram showing an example of an apparatus for manufacturing a silicon-iron ribbon according to the present invention. Fig. 2 is a heat treatment characteristic diagram comparing the magnetic properties (Hc) (A curve) before annealing and the magnetic properties after annealing of the silicon-iron ribbon of the present invention, and Fig. 9 is a heat treatment characteristic diagram of the silicon-iron ribbon of the present invention. It is a magnetic characteristic diagram showing the relationship between temperature, heat treatment time, and coercive force (Hc). DESCRIPTION OF SYMBOLS 1... Ejection nozzle, 2... Bowl-shaped rotating body, 3... Continuous ribbon, 4... Melt, 5, 5', 5''... Rotating roll, 6... Backup roll, 7... Conveyor, 9... Melt jet, 12... Pipe, 13...
...Gas injection pipe, 14...Cylinder, 15...
Vacuum bellows, 16... Heater, 17... Exhaust port, 18... Thin strip collection port. 100th A; Teto'. Q"-・-・(th LBx-< 8-1/θri μm. 1st (';i4 do-!θθμ'-1 11th) Figure μ, -da μ'--1 21st si 4 1 ＼t、L＼ ゝ≧51ζ 碕 ・Figure 3 S-11 (%n Figure 4 (a) (b) (c) (d) Figure 5 Figure 7 - "Continued amendment book 1985 5 Manabu Shiga, Commissioner of the Japan Patent Office, dated 13th January 1985 Characteristics Application No. 73841 2, Name of the invention High silicon steel ribbon and its manufacturing method 3, Relationship with the amended person case Patent applicant Miyagi Noboru Tsuya 4 Agent, 2-1iff 38, Aiki 2-chome, Sendai City, Prefecture

Claims (14)

[Claims] 1. The mold breakage percentage consists of 4 to 10% silicon, the remainder substantially iron and unavoidable impurities, and contains one or more of cobalt 10% or less and nickel 3% or less as subcomponents, and has a crystal grain size of 1. ~100 μm and regular lattice Fe3Si
A high-silicon steel ribbon with virtually no grains, consisting of columnar crystals grown perpendicular to the ribbon surface, and with good workability and magnetic properties. 2. The high silicon steel ribbon according to claim 1, wherein the unavoidable impurity elements include carbon, nitrogen, oxygen, and sulfur in a total amount of 0.1% or less. 3. Aluminum 2% or less, manganese 2% as subcomponents
A high silicon steel ribbon according to claim 1, which contains: 4. 0.1 of one or two of chromium, molybdenum, tungsten, vanadium, and titanium as impurity elements
% or less of high silicon steel ribbon according to claim 1. 5. A molten body containing 4 to 10% silicon, the balance consisting of iron and unavoidable impurities, and containing one or both of 10% or less cobalt and 3% or less nickel as subcomponents.
A thin film made of columnar crystals that are ultra-quenched at a cooling rate of 03 to 106°C/sec, have crystal grains of 1 to 100 μm, are substantially free of regular lattices, and have crystal grains grown perpendicular to the surface of the ribbon. A method for producing a high-silicon steel ribbon with excellent workability and magnetic properties. 6. 6. A method for producing a high silicon steel ribbon according to claim 5, which comprises rapidly cooling the melt on an ultra-quenched body at a rate of 103 to 106°C/sec until it reaches 400°C. 7. 6. The method for producing a high-silicon steel ribbon according to claim 5, wherein the melting temperature of the melt is not higher than the melting point by 300° C. or more. 8. A method for producing a high-silicon steel ribbon according to claim 5, which comprises jetting the molten material from a multi-hole nozzle having two or more jet holes arranged in close proximity over a required width of the ribbon. 9. Contains 4 to 10% silicon, the remainder essentially consists of iron and unavoidable impurities, and contains less than 10% cobalt and less than 3% nickel as subcomponents, and has crystal grains of 7 to 100 μm.
A method for producing a high-silicon steel ribbon with excellent workability and magnetic properties by annealing a high-silicon steel ribbon with substantially no regular lattice to grow crystal grains. 10. The silicon steel ribbon obtained by the method described in claim 5 is annealed at 400 to 1300°C to eliminate crystal grains.
．． 10. The method for producing a high silicon steel ribbon according to claim 9, wherein the high silicon steel ribbon is grown to a thickness of 0.05 to 10 mm. 11. A high-silicon steel thin film containing 4 to 10% silicon, 10% or less cobalt, and 3% or less nickel, with the remainder consisting essentially of iron and unavoidable impurities, with fine crystal grains and substantially no ordered lattice Fe3Si. Roll the strip and further roll 400
A method for producing a high-silicon steel ribbon having excellent workability and magnetic properties by annealing at ~1300°C to grow crystal grains to a size of 0.05 to 10 mm. 12. 12. The method for producing a high silicon steel ribbon according to claim 11, wherein the rolling is performed at a reduction rate of 5% or more. 13. High-silicon steel containing 4 to 10% silicon, 10% or less cobalt, and 3% or less nickel, with the remainder consisting essentially of iron and unavoidable impurities, with crystal grains of 1 to 100 μm and substantially no ordered lattice. An iron core for electrical equipment made of laminated thin ribbons. 14. The iron core according to claim 13 is heated to 400°C or more.
Regular lattice Fe3 annealed at a temperature of 650℃ for 10 minutes to 5 hours
An iron core for electrical equipment made by generating Si.