JP5645108B2 - Amorphous alloy ribbon and magnetic component having amorphous alloy ribbon - Google Patents

Description

The present invention includes various transformers, reactors, choke coils, noise countermeasure parts, laser power supplies and accelerators, communication pulse transformers, motor cores,
The present invention relates to an amorphous alloy ribbon and an amorphous alloy ribbon that are excellent in workability and soft magnetic properties used for generators, magnetic sensors, antenna cores, current sensors, magnetic shields, and the like.

Soft magnetic materials used in various transformers, reactors / choke coils, noise countermeasure components, laser power supplies and accelerators, pulse transformers for communication, motors, generators, magnetic sensors, antennas, current sensors, etc. Examples of such materials include silicon steel sheets, ferrite, Fe-based, and Co-based amorphous alloys.
Ferrite materials have low saturation magnetic flux density and poor temperature characteristics, and are easily magnetically saturated for applications that use high energy density, such as large-capacity inverters, power supply coil parts, and distribution transformers. It is unsuitable because the size increases.
A silicon steel sheet is inexpensive and has a high magnetic flux density, but has a problem that the magnetic core loss is larger than that of an amorphous alloy.

  Amorphous alloys are usually manufactured by quenching from the liquid phase or gas phase, and Fe-Co-Ni amorphous alloys do not have crystals, so there is no magnetocrystalline anisotropy, and there are also grain boundaries. Therefore, it is known to exhibit excellent soft magnetic properties. Among amorphous alloys, Fe-based amorphous alloys having a high saturation magnetic flux density Bs have excellent soft magnetism and low loss, and are therefore used as magnetic core materials for power distribution transformers, reactors, choke coils, and the like. On the other hand, a Co-based amorphous alloy having a small magnetostriction and particularly excellent in soft magnetism is used as a magnetic core material for magnetic heads, saturable cores, current sensors and the like.

  Amorphous alloy ribbon is usually produced by a rapid quenching method such as a single roll method. The single roll method is a method for producing an alloy ribbon by ejecting molten alloy from a nozzle onto a cooling roll made of alloy rotating at high speed. Because of its excellent mass productivity, it is generally used for the production of amorphous alloy ribbons. When mass-producing amorphous alloy ribbons, continuous amorphous alloy ribbons can be produced by producing wide amorphous alloy ribbons for a long time in order to improve productivity and reduce material costs. After the production, the continuous alloy ribbon is subjected to processing such as slitting and cutting as necessary, and the processed amorphous alloy ribbon is formed into a magnetic part / member. Is a heat treated product. For this reason, it is important that the amorphous alloy ribbon as produced before heat treatment is excellent in workability and exhibits excellent soft magnetic properties after heat treatment.

Patent Document 1 discloses an amorphous alloy ribbon for _{Fe 100-a-bcd M a} Si b B c Cu d Fe group nanocrystalline soft magnetic alloy having a composition containing Cu as a main component . In this document 1, it is reported that the workability is remarkably deteriorated unless the surface segregation of Cu is controlled. That is, a Cu segregation portion having a concentration higher than that of the outermost surface portion exists in the depth direction from the surface (free surface and roll surface) of the amorphous alloy ribbon, and the maximum value of the Cu concentration of this Cu segregation portion is 4 It is controlled to atomic% or less.

Patent Document 2 discloses a Fe-based amorphous alloy ribbon having _a Fe _a Si _b B _c C _d composition that does not contain Cu as a main component. This document 2 reports that the squareness can be improved by controlling the surface segregation of C. That is, the control is performed so that the peak value of the C concentration exists in the range of 2 to 20 nm in depth from the surface (free surface and roll surface) of the amorphous alloy ribbon.

JP 2009-263775 A JP 2006-045662 A

  However, there is a problem that thermal stability is lowered by adding C even in an Fe-based amorphous alloy ribbon that does not contain Cu as a main component as in Patent Document 2. In both Patent Document 1 and Patent Document 2, the workability and soft magnetic properties of a wide amorphous alloy ribbon are easily affected by manufacturing conditions. Since the properties are affected, it is strongly desired to develop amorphous alloy ribbons that are excellent in workability, particularly in cutting properties, and have good soft magnetic properties at the mass production level.

  Therefore, the present invention is an amorphous amorphous Fe-Si-B-based amorphous alloy ribbon that does not contain Cu as a main component, is less prone to cracking at the time of cutting or slitting, and has both excellent workability and soft magnetic properties. An object is to provide a quality alloy ribbon.

  Although the present invention has an alloy composition that does not contain Cu as a main component, Cu is segregated on the surface of the ribbon immediately after ultra-quenching, and the fact that this Cu segregation has an effect on workability and soft magnetic properties. I found out. The Cu concentration differs between the free surface and the roll contact surface, and in particular, it is important to control the Cu concentration appearing on the roll contact surface side to a predetermined amount, which makes it possible to manufacture with excellent workability and soft magnetic properties. As a result, the inventors have come up with the following invention.

That is, the amorphous alloy ribbon of the present invention is Fe _100-ab Si _a B _b (where a and b are atomic%, respectively 1 ≦ a ≦ 20, 4 ≦ b ≦ 20, 14 ≦ a + b ≦). And an unheat-treated amorphous alloy having an alloy composition that does not contain Cu as a main component other than inevitable impurities and is manufactured by a single roll method using a copper alloy roll. A thin ribbon, on the roll contact surface side of the ribbon, a Cu concentration peak in a range of 2 to 50 nm in depth excluding the outermost surface is 0.1 atomic% or more and 4 atomic% or less.

  In the vicinity of the ribbon surface on the roll contact surface side, if there is a region where the Cu concentration exceeds 4 atomic%, the amorphous alloy tends to become brittle after the ribbon production, and cracks occur during cutting and slitting. Processing becomes difficult. Furthermore, since the vicinity of the roll contact surface is easily crystallized after the heat treatment, the appropriate heat treatment temperature cannot be increased, and the iron loss is greatly affected by the heat treatment conditions. As a result, a large magnetic core is not preferable because heat treatment becomes difficult and characteristics tend to vary. On the other hand, when the Cu concentration in the vicinity of the roll contact surface side is less than 0.1 atomic%, the apparent power is increased and the squareness is deteriorated, and the soft magnetic characteristics tend to be inferior.

  In the single roll apparatus according to the present invention, a Cu alloy roll having good thermal conductivity is generally used as the cooling roll used for cooling the molten metal. An alloy melt is ejected onto the Cu alloy roll and is rapidly quenched and solidified to produce an amorphous alloy ribbon. As a result of various studies, we have found that an appropriate reaction between the roll made of Cu alloy and the molten metal is effective in improving the workability and soft magnetic properties of these amorphous alloy ribbons. That is, an amorphous alloy ribbon having a low Cu concentration in the vicinity of the ribbon surface on the roll contact surface side and having a small or low Cu concentration peak is not preferable because of poor soft magnetic properties, particularly iron loss. On the other hand, an alloy ribbon in which the molten metal reacts moderately with the roll and a Cu concentration peak exists in the vicinity of the ribbon surface on the roll contact surface side of the amorphous alloy ribbon is excellent in workability and iron loss. Became clear. Specifically, if there is a region where the peak value of Cu concentration in the vicinity of the roll contact surface exceeds 4 atomic%, the amorphous alloy is likely to become brittle after the production of the ribbon, and the vicinity of the roll contact surface is crystallized after the heat treatment. This is not preferable because the iron loss tends to deteriorate. Preferably, when the peak value of the Cu concentration in the high Cu concentration region is 0.2 atomic% or more and 4 atomic% or less, an amorphous alloy ribbon having excellent workability can be obtained and heat treatment is performed. Later, crystallization is suppressed and excellent soft magnetic properties are exhibited. More preferably, when the Cu concentration peak value is approximately 0.2 atomic% or more and 0.5 atomic% or less, the workability is particularly excellent and the effect of low iron loss can be stably obtained. Further, when the Cu concentration in the vicinity of the roll contact surface side is less than 0.1 atomic%, soft magnetic characteristics such as an increase in apparent power and a deterioration in squareness occur, which is not preferable.

Even in the case of an alloy ribbon that does not contain Cu as a main component, Cu may be mixed as an inevitable impurity from the iron source material, etc., but the content is still less than about 0.01 atomic%. In the present invention, the Cu concentration peak is considered to be formed mainly by the diffusion of Cu from the surface of the roll contact surface of the alloy ribbon in combination with an appropriate reaction during casting. The high Cu concentration region including the Cu concentration peak is in the vicinity of the ribbon surface on the roll contact surface side. Although the segregation of Cu tends to appear on the surface, the oxide layer formed on the surface is obstructed, and due to this, it exists at a position deeper than 2 nm and up to 50 nm from the surface in contact with the roll. The outermost surface tends to increase the Cu concentration because the molten metal comes into contact with the Cu alloy roll and solidifies. In the present invention, the Cu concentration peak means not in the outermost surface but in the inside.
On the other hand, the Cu concentration on the free surface side is almost uniformly less than 0.1 atomic% in the depth direction and is considered to continue up to the parent phase, but at least at a position up to a depth of 50 nm. A high region and a peak of Cu concentration do not appear. We believe that the Cu concentration on the free surface side has no effect on the workability and iron loss described above. Rather, it is necessary to prevent a region with a high Cu concentration or a peak of Cu concentration from appearing on the free surface side. is there. On the contrary, when these appear, it cannot be said that it is an alloy composition which does not contain Cu as a main component any longer.

  In order to control the high Cu concentration region and the peak of the Cu concentration, in addition to controlling the cooling of the amorphous alloy ribbon and controlling the surface temperature of the alloy ribbon, When producing an amorphous alloy ribbon, it is necessary to polish the roll surface being produced by an appropriate method and maintain the smoothness of the roll surface during production. When the roll surface becomes rough, the concave portion reflected on the surface of the ribbon becomes an elongated air pocket shape, and the efficiency of heat diffusion is lowered and the cooling performance is deteriorated. At this time, the ribbon is locally damaged and the surface temperature is increased. As a result, it is considered that reactivity increases and Cu segregation is likely to occur, and a region having a high Cu concentration and a peak of Cu concentration appear. Although the substance of the moderate reaction during casting is unknown, it is thought that it is necessary to maintain good wettability with the roll so as to avoid the manufacturing situation as described above. For this purpose, the surface temperature of the ribbon is set to 300 ° C. or higher and lower than 400 ° C., preferably 320 ° C. or higher and lower than 390 ° C., more preferably around 340 ° C. Further, Ra on the roll side is preferably about 0.1 μm to 0.6 μm so that the surface roughness Ra of the ribbon is 0.6 μm or less.

Hereinafter, the reasons for limiting the composition will be described.
In the alloy composition of the present invention described above, an alloy in which the Si amount a is 2 ≦ a ≦ 8 and the B amount b is 13 ≦ b ≦ 18 has a relatively high saturation magnetic flux density and soft magnetic characteristics even when the plate thickness is large. Therefore, an amorphous alloy ribbon suitable for a transformer having good resistance can be obtained, and a more preferable result can be obtained. A particularly preferable range of the Si amount a is 2 ≦ a ≦ 5, and a range of the B amount b is 13 ≦ b ≦ 16.

  10% or less of the total amount of Si and B can be replaced with at least one element selected from C, P, Ga, and Ge. When these elements are substituted, magnetostriction and Curie temperature can be adjusted. On the other hand, if these elements are substituted in an amount exceeding 10% of the total amount of Si and B, the alloy becomes extremely brittle and the workability is greatly deteriorated.

2% or less of the amount of Fe can be replaced with at least one element selected from Cr, Mn, V, Nb, Mo, Ta, W, Sn, and a platinum group element. By substituting these elements, it is possible to improve soft magnetic properties and corrosion resistance. Substituting these elements with an amount exceeding 2% of the amount of Fe is not preferable because a significant decrease in saturation magnetic flux density and deterioration of workability occur.
Moreover, 10 atomic% or less of the amount of Fe can be substituted with at least one element selected from Co and Ni.

  Inevitable impurities may include S, Al, O, Ti, N, etc. Among these elements, Al and Ti are elements that promote surface crystallization, and deteriorate soft magnetic properties. Therefore, as few as possible is desirable.

When producing the amorphous alloy ribbon of the present invention by the single roll method, the thickness of the alloy ribbon to be produced is about 5 μm to 100 μm, but the plate thickness with good workability is 50 μm or less, particularly workability. However, the preferable thickness is 30 μm or less.
The width of the alloy ribbon immediately after being produced by a single roll apparatus is usually 100 mm or more, and the effect of the present invention is remarkably exhibited when a large amount of a wide alloy ribbon is produced.

  The amorphous alloy ribbon of the present invention is easy to process before the heat treatment and can be processed such as cutting, slitting and punching. The effect is great in that a high performance amorphous alloy ribbon magnetic core can be produced. In general, when an amorphous alloy ribbon is used for a transformer, the amorphous alloy ribbon is cut to produce a magnetic core having a structure such as an overlap or a step wrap. For this reason, the amorphous alloy ribbon of the present invention having good workability is particularly suitable for applications such as transformers. If the amorphous alloy ribbon becomes brittle before the heat treatment, the ribbon will be broken at the time of cutting, or the cut surface cannot be cleaned.

The amorphous alloy ribbon of the present invention is prepared by applying a powder of SiO ₂ , MgO, Al ₂ O ₃ or the like to the alloy surface as necessary after the preparation of the amorphous alloy ribbon, or SiO ₂ , MgO, Al ₂ Oxide such as O ₃ or a film mainly composed of nitride is formed to cover the alloy surface, surface treatment is performed by chemical conversion treatment such as phosphate treatment, and an insulating layer is formed. Processing such as formation of an insulating layer can be performed. By such treatment, the insulation between layers is further improved when a magnetic core is produced, and a more preferable result is obtained. This is because, in particular, the effect of eddy currents at high frequencies across the layers is reduced, and the magnetic core loss at high frequencies is improved. This effect is particularly remarkable when used in a magnetic core having a good surface state and a wide alloy ribbon.

Furthermore, impregnation and coating can be performed as necessary when producing a magnetic core from the alloy of the present invention.
The amorphous alloy ribbon of the present invention can be a laminated magnetic core, or can be used as a laminated magnetic core by applying a resin or the like to the alloy surface and bonding it.
The amorphous alloy ribbon of the present invention can be used for high frequency applications, sensors and low frequency magnetic parts. In particular, Fe-based amorphous alloy ribbons can exhibit excellent characteristics in applications where magnetic saturation is a problem, and are suitable for power transformers, generators, reactors, and magnetic cores for high energy density power electronics. Co-based alloys have low magnetostriction, high permeability, and excellent high-frequency magnetic properties, and are therefore suitable for magnetic cores such as current sensors, saturable cores for switching power supplies, and pulse power applications. Ni-based alloys are suitable for sensor materials.

  When the amorphous alloy ribbon of the present invention is heat-treated while applying a magnetic field in the same direction as the direction of magnetization during use, it has a high squareness ratio and low apparent power, and is suitable for a distribution transformer and a saturable reactor. Further, when heat treatment is performed while applying a magnetic field in a direction substantially perpendicular to the direction of magnetization during use, a low core loss can be obtained at high frequencies.

  Since the amorphous alloy ribbon of the present invention is easily processed in the amorphous alloy ribbon state before heat treatment, it can be efficiently processed such as slitting, cutting, punching, etc. Can be produced. This magnetic core exhibits a particularly low core loss after heat treatment, and can realize a high-performance magnetic core. Further, the obtained alloy ribbon can be pulverized and used as a powder material used for a dust core and the like, and excellent characteristics can be obtained as well.

Results of measurement of Cu concentration distribution measured by GD-OES from the surface of the roll contact surface (surface solidified by contact with the roll) of the amorphous alloy ribbon produced by the single roll method according to the present invention. It is the figure which showed an example. The figure which showed an example of the measurement result of Cu concentration distribution measured by GD-OES toward the inside from the surface of the free surface (free solidified surface) of the amorphous alloy ribbon manufactured by the single roll method concerning the present invention It is. A comparative example prepared without performing roll polishing when producing by a single roll method is shown, and the measurement result of Cu concentration distribution measured by GD-OES from the surface of the roll contact surface of the amorphous alloy ribbon toward the inside It is the figure which showed an example.

  EXAMPLES Next, although an Example demonstrates this invention concretely, this invention is not limited by these Examples.

Example 1
A molten alloy of Fe ₈₁ Si ₄ B ₁₅ (atomic%) composed of 4 atomic% Si, 15 atomic% B, the balance Fe and inevitable impurities is jetted into a single roll device rotating at 25 m / s in the air and quenched. Thus, an amorphous alloy ribbon having a width of 170 mm and a thickness of about 25 μm was produced. The roll of the single roll apparatus was a water-cooled roll made of Cu—Be alloy, and an amorphous alloy ribbon was produced while polishing the roll with a brush made of stainless wire. The polishing powder generated by roll polishing was sucked with a suction device. The temperature of the alloy ribbon in the steady state was 340 ° C. at a position 45 mm above the roll from the nozzle tip. As a result of X-ray diffraction on the roll contact surface and free surface side of the produced amorphous alloy ribbon, it showed a halo pattern unique to the amorphous alloy ribbon and was confirmed to be an amorphous single phase. .

Next, the roll contact surface side (the surface solidified in contact with the roll) and free of the alloy ribbon by glow discharge optical emission spectroscopy (GD-OES, JY-5000RF manufactured by HORIBA, Ltd.) The Cu concentration distribution on the surface side (free solidified surface) was measured from the surface toward the inside. The measurement area is a range having a diameter of 2 mm, and the measurement value indicates an average value in this range.
FIG. 1 shows the concentration distribution of Cu element on the roll contact surface side measured by GD-OES. FIG. 2 shows the concentration distribution of the Cu element on the free surface side. From FIG. 1, on the roll contact surface side, the Cu concentration in the vicinity of the ribbon surface is higher than the internal Cu concentration, and there is a peak of Cu concentration exceeding 0.3 atomic% at a depth of about 10 nm from the surface. I understand. On the other hand, as shown in FIG. 2, the Cu concentration on the free surface side did not change between the inside and the surface and was uniformly less than 0.1 atomic%, and there was no clear peak of Cu concentration. Although the Cu concentration on the outermost surface on the roll contact surface side shows the maximum value, it is excluded from the Cu concentration peak as described above.

  Next, this alloy ribbon was cut and examined for cracks. The amorphous alloy ribbon of the present invention was confirmed to be excellent in workability without cracking even when cut. Further, the surface roughness Ra of the alloy ribbon was 0.3 to 0.6 μm, and the surface roughness on the roll side was 0.6 μm or less.

Next, an overlap structure magnetic core was produced using the cut amorphous alloy ribbon. First, heat treatment in a magnetic field was performed while applying a magnetic field of 1600 A / m in the magnetic path direction of the magnetic core. The holding heat treatment temperature was 340 ° C., the holding time was 1 h, the heating rate was about 5 ° C./min, and the cooling rate was about 3.5 ° C./min.
Then, when the following magnetic properties were measured, the magnetic flux density B ₈₀₀ = 1.63T at ₈₀₀ A / m, the coercive force Hc = 2.0 A / m, and the iron loss P _14/50 = 0.50 at 50 Hz, 1.4 T. 18 W / kg was obtained, and it was confirmed that it had characteristics suitable as a magnetic core for a transformer.

(Comparative Example 1)
Although the same manufacturing apparatus as the same alloy as the above Example was used, for comparison, an amorphous alloy ribbon was prepared without roll polishing. The temperature of the alloy ribbon in the steady state was 390 ° C. at a position 45 mm above the roll from the nozzle tip. As a result of X-ray diffraction on the roll contact surface side and the free surface side of the prepared amorphous alloy ribbon, a halo pattern peculiar to the amorphous alloy ribbon was shown, and it was confirmed that it was an amorphous single phase. It was.

  Next, the Cu concentration distribution on the roll contact surface side of this alloy ribbon was measured toward the inside by GD-OES as in Example 1 above. FIG. 3 shows the measurement results of the concentration distribution of the Cu element. In this example, the vicinity of the surface is a region having a high Cu concentration, and although there is a Cu concentration peak near a depth of 10 nm other than the outermost surface, a high Cu concentration exceeding 4 atomic% exists and the reaction with the roll proceeds. It was confirmed that Note that the Cu element concentration distribution was also measured on the free surface side by GD-OES. The result was the same as in FIG. 2, and the Cu concentration was uniformly less than 0.1 atomic%, and there was no clear peak of Cu concentration.

  Next, this alloy ribbon was cut and examined for cracks in the same manner as in Example 1. As a result, the alloy ribbon after cutting was partially cracked and could not have a clean cut surface. Further, the surface roughness Ra of the alloy ribbon was 1.0 μm or more, and the surface roughness on the roll side was 1.0 μm or more.

Next, a magnetic core having an overlap structure was manufactured using an amorphous alloy ribbon cut in the same manner as in Example 1. Heat treatment in a magnetic field was performed while applying a magnetic field of 1600 A / m in the magnetic path direction of the magnetic core. The holding heat treatment temperature was 340 ° C., the holding time was 1 h, the heating rate was about 5 ° C./min, and the cooling rate was about 3.5 ° C./min.
In this example, the iron loss P _14/50 = 0.28 W / kg at 50 Hz and 1.4 T, and the iron loss increased compared to the above example.

  The results are shown in Table 1. As described above, it was confirmed that the amorphous alloy ribbon of the present invention is excellent in workability, and a magnetic core produced using this can realize a lower loss magnetic core.

(Example 2)
The molten alloy having the composition shown in Table 2 was jetted and rapidly cooled to a single roll apparatus rotating at 25 m / s to produce an amorphous alloy ribbon having a width of 100 to 170 mm and a thickness of about 25 to 30 μm. The roll of the single roll apparatus used here was a water-cooled roll made of Cu—Cr—Zr alloy, and an amorphous alloy ribbon was produced while polishing the roll with a brush made of stainless wire. The polishing powder generated by roll polishing was sucked with a suction device. The temperature of the alloy ribbon in a steady state was 320 ° C. at a position 45 mm above the roll from the nozzle tip. As a result of X-ray diffraction of the roll contact surface and free surface side of the produced amorphous alloy ribbon, a halo pattern peculiar to the amorphous alloy was shown, and it was confirmed that the amorphous alloy was an amorphous single phase.

  Next, the Cu concentration distribution on the roll contact surface side and the free surface side of the alloy ribbon was measured toward the inside by glow discharge optical emission spectrometry (GD-OES). As a result of measuring the Cu concentration peak value on the roll contact surface side, it was confirmed that the Cu concentration peak was present at a depth of 5 to 50 nm from the surface. Table 2 shows the Cu concentration peak values at this time. Moreover, about the free surface side, presence or absence of the peak of Cu concentration exceeding 0.1 atomic% was confirmed. Further, the produced amorphous alloy ribbon was cut in the same manner as in Example 1 above, and the presence or absence of cracks was confirmed. The results are shown in Table 2. The surface roughness Ra of the alloy ribbon was between 0.3 and 0.6 μm, and many were between 0.3 and 0.45 μm. Moreover, the surface roughness of the roll side at this time was 0.6 micrometer or less.

Furthermore, a magnetic core having an overlap structure was produced using the cut amorphous alloy ribbon. Heat treatment in a magnetic field was performed while applying a magnetic field of 1600 A / m in the magnetic path direction of the magnetic core. The holding heat treatment temperature was 320 ° C. to 370 ° C., the holding time was 1 h, the heating rate was about 5 ° C./min, and the cooling rate was about 3.5 ° C./min.
And about this magnetic core, the iron loss P14 / 50 in 50 Hz and _1.4T was measured. The results are shown in Table 2.

(Comparative Example 2)
For comparison, an amorphous alloy ribbon was prepared while roll polishing of a molten alloy having a composition shown in Table 2 with a brush made of stainless steel using a roll made of Cu-Be alloy (without water cooling). The polishing powder generated by roll polishing was sucked with a suction device. The temperature of the steady state alloy ribbon was 420 ° C. at a position 45 mm above the roll from the nozzle tip. As a result of X-ray diffraction of the roll contact surface and free surface side of the produced amorphous alloy ribbon, a halo pattern peculiar to the amorphous alloy was shown, and it was confirmed that the amorphous alloy was an amorphous single phase.
In the same manner as in Example 2, the Cu concentration distribution and the presence or absence of cracks were confirmed, an overlap structure magnetic core was prepared, and heat treatment was performed under the same conditions to measure the iron loss. The results obtained as described above are shown in Table 2.

From Table 2, the amorphous alloy ribbon of the present invention has a peak with a Cu concentration of more than 0.1 atomic% and less than 3.5 atomic% in a depth range of 5 to 50 nm from the surface on the roll contact surface side. Was. On the other hand, no peak of Cu concentration exceeding 0.1 atomic% was present on the free surface side. In addition, the workability was found to be slightly cracked in some cases, but there was no practical problem, and the others were extremely good with no cracks. And the magnetic core of the overlap structure could be manufactured cleanly and efficiently. Further, 50 Hz of the magnetic core, iron loss _{P 14/50} good results in the following low iron loss either 0.20 W / Kg at 1.4T was obtained.

On the other hand, in the amorphous alloy ribbon of the comparative example, the Cu concentration on the roll contact surface side has a peak exceeding 4 atomic%. The reason for this is considered to be that the cooling ability of the roll being manufactured is poor, the surface of the roll becomes rough, the reaction with the roll proceeds, the heat transfer of the alloy ribbon becomes poor, and the segregation of Cu increases. In addition, the surface roughness Ra of the alloy ribbon was about 1.3 to 1.6 μm, and the surface roughness on the roll side was also about the same. In the comparative example, cracks occurred, the workability was extremely poor, and the iron loss was relatively large.
From the above results, it was confirmed that the amorphous alloy ribbon of the present invention was excellent in workability, and when a magnetic core was produced using this amorphous alloy ribbon, a lower loss magnetic core could be realized.

  The present invention is used for magnetic parts such as various transformers, reactors, choke coils, noise countermeasure parts, laser power supplies and accelerators, pulse transformers for communication, motor cores, generators, magnetic sensors, antenna cores, current sensors, and magnetic shields. It can be used as an amorphous alloy ribbon with excellent workability. Moreover, the alloy of the present invention exhibits excellent soft magnetic properties particularly after heat treatment, and when used as a magnetic core material, a product exhibiting excellent properties can be realized.

Claims (7)

Fe _100-a-b Si _a B _b (where a and b are numbers in atomic percent satisfying the conditions of 1 ≦ a ≦ 20, 4 ≦ b ≦ 20, and 14 ≦ a + b ≦ 30) and inevitable impurities A non-heat-treated amorphous alloy ribbon manufactured by a single roll method using a copper alloy roll, having an alloy composition that does not contain Cu as a main component other than the roll contact surface of the ribbon An amorphous alloy ribbon characterized in that the Cu concentration on the side is such that the Cu concentration peak in the range of 5 to 50 nm in depth excluding the outermost surface is 0.1 atomic% to 4 atomic%. 2. The amorphous alloy ribbon according to claim 1, wherein a Cu concentration between the surface on the free surface side of the ribbon and a depth of at least 50 nm is less than 0.1 atomic%. 3. The amorphous alloy ribbon according to claim 1, wherein the Si amount a is 2 ≦ a ≦ 5 and the B amount b is 13 ≦ b ≦ 16. The amorphous material according to any one of claims 1 to 3, wherein 10 atomic% or less of the total amount of Si and B is substituted with at least one element selected from C, P, Ga, and Ge. Quality alloy ribbon. 5% or less of the amount of Fe is substituted with at least one element selected from Cr, Mn, V, Nb, Mo, Ta, W, Sn, and a platinum group element. The amorphous alloy ribbon according to any one of the above. The amorphous alloy ribbon according to any one of claims 1 to 5, wherein 10 atomic% or less of the amount of Fe is substituted with at least one element selected from Co and Ni. A magnetic component comprising the amorphous alloy ribbon according to any one of claims 1 to 6.

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