JPH0351785B2 - - Google Patents

Description

[Detailed description of the invention]

The present invention relates to at least 90% vitreous metallic glasses with high magnetic permeability, low magnetostriction, low coercivity, low ac core loss, low excitation power and high thermal stability. As is well known, metallic glasses are metastable materials without extensive order. X-ray diffraction scans of glass-like alloys only show scattering halos similar to those observed for inorganic oxide glasses. Metallic glass (amorphous alloy) is covered by U.S. Patent No.
No. 3856513 (issued to HS Chien et al. on December 24, 1974). These alloys include
Included are compositions with the formula MaYbZc. In the formula, M is a metal selected from the group consisting of iron, nickel, cobalt, vanadium and chromium, Y is an element selected from the group consisting of phosphorus, boron and carbon, and Z is aluminum, silicon, tin, germanium, An element selected from the group consisting of indium, antimony, and beryllium, and “a”
is in the range of approximately 60 to 90 atomic percent, and “b” is approximately 10 to 90 atomic percent.
In the range of 30 at%, “c” is about 0.1 to 15 at%
within the range of Also shown is a metallic glass wire with the formula TiXj. where T is at least one transition metal; in the range of %,
"j" ranges from about 13 to 30 atomic percent. These materials are now conveniently produced by quenching from a melt using processing techniques well known in the art. Metallic glass is disclosed in U.S. Patent No. 4067732 (1978).
(granted on the 10th of the month) is also shown on the statement. These glass-like alloys include compositions with the formula M _a M′ _b Cr _c M″ _d B _e , where M is one of the iron group elements (iron, cobalt, and nickel); M′ is at least one of the remaining two iron group elements,
M″ is at least one element among vanadium, manganese, molybdenum, tungsten, niobium, and tantalum, B is boron, and “a”
is about 40 to 85 atom%, "b" is 0 to about 45 atom%,
“c” and “d” are both 0 to about 20 atomic percent;
"e" is in the range of about 15 to 25 atomic percent, with the proviso that "b", "c" and "d" are not simultaneously zero.
Such glass-like alloys are described as having an unexpected combination of improved ultimate tensile strength, improved hardness, and improved thermal stability. These descriptions also mention special or unique magnetic properties for a number of metallic glasses that fall within the scope of the broader claims. However, for special applications such as tape recorder heads, relay cores, and transformers, it has higher magnetic permeability, lower magnetostriction, lower coercivity, lower core loss, lower excitation power, and higher thermal stability than prior art metallic glasses. A metallic glass with both of these properties is required. The present invention provides at least 90% vitreous metallic glasses that combine high magnetic permeability, low magnetostriction, low coercivity, low AC core loss, low excitation power, and high thermal stability. These metallic glasses essentially contain 66 to 82 atomic percent iron (1 to 8 atoms of this metal are replaced by at least one of nickel and cobalt), chromium, molybdenum, tungsten, vanadium, niobium, 1 to 6 atom% of at least one element selected from the group consisting of tantalum, titanium, zirconium, and hafnium, 17 to 28 atom% of boron (0.5 to 6 atom% of boron)
Atomic % is substituted by silicon or
0.5 to 6 at% by silicon and an additional 2 at%
up to the point where it is replaced by carbon. ) and accompanying impurities. The metallic glass of the present invention is suitable for use in tape recorder heads, relay cores, transformers, etc. The metallic glasses of the present invention are characterized by a combination of high magnetic permeability, low saturation magnetostriction, low coercivity, low AC core loss, low excitation power, and high thermal stability. The glassy alloy of the present invention comprises at least
90% glassy, consisting essentially of 66-82 at.% iron (with 1-8 at.% of this metal replaced by at least one of nickel and cobalt), chromium, molybdenum, tungsten, vanadium , 1 to 6 at% of at least one element selected from the group consisting of niobium, tantalum, titanium, zirconium, and hafnium, and boron 17 to 28
atomic % (0.5 to 6 atomic % of this boron may be substituted by silicon, and 2 atomic % of this metalloid
up to atomic % by carbon) and accompanying impurities. Cr, Mo, W, V,
The concentration of Nb, Ta, Ti, Zr and/or Hf is 1
If it is lower than atomic %, magnetic permeability, saturation magnetostriction, coercive force, AC core loss, and thermal stability will not be sufficiently improved. Furthermore, if the concentration of at least one of these elements is greater than 6 atomic percent, the Curie temperature will become unacceptably low. Iron provides high saturation magnetization at room temperature. The metal content is therefore preferably substantial iron, chromium,
Up to 8 atom % of nickel and/or cobalt to compensate for the reduction in room temperature saturation magnetization due to the presence of molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or hafnium. Adding nickel increases magnetic permeability. Examples of metallic glasses of the present invention include the following. Fe ₈₀ Ni ₁ Mo ₁ B ₁₆ Si ₂ , Fe ₇₆ Ni ₄ Mo ₂ B _17.5 Si _0.5 ,
Fe ₇₅ Ni ₂ Co ₂ Mo ₃ B ₁₆ Si ₂ , Fe ₇₅ Co ₄ Mo ₃ B ₁₆ Si ₂ ,
Fe ₇₅ Ni ₄ Mo ₃ B ₁₆ Si ₂ , Fe ₇₇ Ni ₂ Mo ₃ B ₁₆ Si ₂ ,
Fe ₇₅ Ni ₄ Mo ₃ B ₁₄ Si ₄ , Fe ₇₁ Ni ₄ Mo ₃ B ₁₇ Si ₅ ,
Fe ₇₄ Ni ₄ Mo ₄ B ₁₆ Si ₂ , Fe ₇₀ Ni ₆ Mo ₆ B ₁₅ Si ₃ ,
Fe ₇₅ Ni ₄ V ₃ B ₁₄ Si ₂ C ₂ , Fe ₇₁ Ni ₄ Mo ₃ B ₁₆ Si ₄ C ₂ ,
Fe ₇₈ Ni ₂ Mo ₂ B ₁₂ Si ₄ C ₂ , Fe ₇₈ Ni ₂ Cr ₂ B ₁₆ Si ₂ ,
Fe ₇₅ Ni ₄ Nb ₃ B ₁₆ Si ₂ , Fe ₇₅ Ni ₄ W ₃ B ₁₆ Si ₂ ,
Fe ₇₅ Ni ₄ V ₃ B ₁₆ Si ₂ , Fe ₇₉ Ni ₄ Ta ₁ B ₁₆ Si ₂ ,
Fe ₇₅ Ni ₄ Ti ₃ B ₁₆ Si ₂ , Fe ₇₅ Ni ₄ Zr ₃ B ₁₆ Si ₂ ,
Fe ₇₉ Ni ₄ Hf ₁ B ₁₆ Si ₂ , Fe ₇₂ Ni ₂ Mo ₂ B ₂₂ Si ₂ ,
Fe ₇₀ Ni ₂ Mo ₂ B ₂₂ Si ₂ , and Fe ₇₀ Ni ₂ Mo ₂ B ₂₄ Si ₂
(The numbers written below are atomic percent). The purity of all alloys is of commercially acceptable purity. The presence of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or hafnium increases the crystallization temperature, while at the same time lowering the Curie temperature of the glass-like alloy. The large spacing between these temperatures facilitates magnetic annealing, that is, thermal annealing near the Curie temperature.
It is well known that annealing magnetic materials near their Curie temperature generally provides improved properties. With increasing concentrations of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or hafnium, the crystallization temperature increases, resulting in an elevated temperature near the Curie temperature but below the crystallization temperature. Annealing can be easily performed at temperatures as low as 0. Such annealing cannot be performed for many alloys similar to the alloy of the present invention but not containing these elements. On the other hand, chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or
Alternatively, if the concentration of hafnium is too high, the Curie temperature decreases to a level that may be undesirable for some applications. Preferred concentrations of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or hafnium for metallic glasses in which boron and silicon are the major and minor metalloid components, respectively, are 2 to 4 atom %. Preferably, the metalloid content consists essentially of (1) a substantial amount of boron with a small amount of silicon, (2) boron plus silicon, and (3) boron and silicon plus a small amount of carbon. Metalloy content is 17-28 at%
is preferred for maximum thermal stability. Preferred metallic glass systems are as follows. 1 Fe-M-Mo-B-Si: Fe _100-abcd M
_a Mo _b B _c Si _d . In the formula, MH is at least one of nickel and cobalt, when (c + d) is 18,
The preferred ranges of a, b, c and d are each 2
-8, 1-4, 14-17.5 and 0.5-4.
If (c+d) is 22, then a, b, c and d
The preferred ranges are 2 to 8, 1 to 6, and 15 to 1, respectively.
20.5 and 0.5-6. When (c+d) is 25, the preferred ranges of a, b, c and d are 2-8, 1-6, 21-25 and 1-6, respectively.
These metallic glasses have saturation induction (B _S ) 1.0-1.4 Tesla (Tesla), saturation magnetostriction (λ _S ) 12-24 ppm,
They have a combined Curie temperature (θ _f of approximately 475-705 K and a first crystallization temperature of 750-880 K. When properly heat-treated, these alloys have a particularly high frequency (f > 10 ³ Hz)
It has excellent alternating magnetism. For example, f = 50kHz for heat-treated Fe ₇₅ Ni ₄ Mo ₃ B ₁₆ Si ₂ alloy glass.
The AC core loss (L) and excitation power (P _e ) determined at the induction level B _n =0.1 terrace are respectively
6.5W/Kg and 13.4VA/Kg. These numbers can be converted into L= for a prior art heat-treated metallic glass of the same thickness with a composition of Fe ₇₉ B ₁₆ Si ₅
It should be compared with 7W/Kg and Pe=20VA/Kg. The magnetic permeabilities at B _n =0.01 Tesla are 10500 and 8000 for heat-treated Fe ₇₅ Ni ₃ Mo ₄ B ₁₆ Si ₂ and Fe ₇₉ B ₁₆ Si ₅ , respectively. Saturation magnetostriction (λ _S ) for the prior art alloys mentioned above =
The saturation magnetostriction of the present alloy is 20ppm compared to 30ppm.
and smaller, making the alloys of the invention particularly suitable for use in magnetic devices such as high frequency transformer cores. Above f=50kHz, the alloy of the present invention has approximately
It has a magnetic permeability comparable to or higher than that for crystalline supermalloy with a B _S of 0.8 Tesla. The higher values of B _S for the alloys of the invention make these alloys more suitable than supermalloy for applying a magnetic field of f=50 kHz. Fe-M-M'-B-Si: Fe _100-abcd M _a M
′ _b B _c Si _d . In the formula, M is nickel and/or cobalt, and M′ is Cr, W, V, Nb, Ta, Ti, Zr or
Selected from Hf. If (c+d) is 18,
The preferred ranges of a, b, c and d are each 2
-8, 1-4, 14-17.5 and 0.5-4.
If (c+d) is 22, then a, b, c and d
The preferred ranges are 2 to 8, 1 to 6, and 16 to
21.5 and 0.5-6. When (c+d) is close to 25, the preferred ranges of a, b, c and d are 2-8, 1-6, 21-25 and 1-6, respectively. Fe-M-M'-B-Si-C: Fe _100-abcd
M _a M′ _b B _c Si _d C _e . where M is nickel and/or cobalt and M' is selected from the group consisting of Cr, Mo, W, V, Nb, Ta, Ti, Zr or Hf. (c+d) is 18
, the preferred ranges of a, b, c, d and e are 2 to 8, 1 to 4, 12 to 17.5, and 0.5, respectively.
-4 and 0-2. When (c+d) is 22, the preferred ranges of a, b, c, d and e are 2-8, 1-6, 14-21.5, 0.5-6 and 0-2, respectively. If (c+d) is close to 25,
The preferred ranges of a, b, c, d and e are 2-8, 1-6, 20-27, 1-6 and 0-2, respectively.
It is. Magnetic permeability is the ratio of magnetic induction to applied magnetic field. Higher magnetic permeability increases the response of some materials, making them useful in certain applications such as tape recorder heads. The frequency dependence of the magnetic permeability of the glass-like alloy of the present invention is found in the medium to high frequency region (1
~50kHz), its permeability is similar to that of 4-79 permalloy, and in the higher frequency range (approximately 50kHz to 1MHz) its permeability is comparable to that of ultrapermalloy. Of particular note is that at 1 kHz and an induction level of 0.01 Tesla, the heat-treated Fe ₇₅ Ni ₄ Mo ₃ B ₁₆ Si ₂ metallic glass has a permeability of 24000, whereas that of the prior art heat-treated under the best conditions Fe ₄₀ Ni ₃₆ Mo ₄ B ₂₀
Metallic glass has a magnetic permeability of 14,000. Saturation magnetostriction is the change in length under the action of a saturation magnetic field. The lower the saturation magnetostriction, the more advantageous the material is for certain applications such as tape recorder heads. Magnetostriction is usually discussed in terms of the ratio of change in length to the original length, and is expressed as ppm
It is indicated by. Iron-containing metallic glasses according to the prior art exhibit a saturation magnetostriction of approximately 30 ppm, similar to metallic glasses in the absence of B, B, and any element belonging to group B of the periodic table (eg, molybdenum). For example, it was devised for high frequencies, and Fe ₄₇ B ₁₆ Si ₅
Prior art iron-rich metallic glasses with the composition of
It has a saturation magnetostriction of approximately 30ppm. In contrast,
The metallic glass of the present invention with the composition Fe ₇₅ Ni ₄ Mo ₃ B ₁₆ Si ₂ has a magnetostriction of approximately 20 ppm. The lower the saturation magnetostriction, the smaller the phase angle between the excitation field and the resulting induction. As a result, the excitation power becomes smaller, as will be discussed later. AC core loss is energy loss that is dissipated as heat. This is hysteresis in an alternating magnetic field, and for low frequencies (below about 1 kHz), B-
It is measured by the area of the H-loop, and is measured at high frequencies (approximately
1kHz-1MHz) is measured from the complex input at the excitation coil. The main part of AC core loss in the high frequency region is caused by eddy currents generated when magnetic flux changes. However, lower hysteresis losses and therefore lower coercivity are desirable. The lower the core loss, the more useful a material becomes in certain applications such as tape recorder heads and transformers. Core losses are discussed in units of W/Kg. Heat-treated metallic glass according to the prior art
It typically exhibits AC core losses of about 0.05 to 0.1 Watts/Kg in the 0.1 Tesla induction and 1 kHz frequency range. For example, a heat-treated metallic glass according to the prior art with the composition Fe ₄₀ Ni ₃₆ Mo ₄ B ₂₀ has a power consumption of 0.07 W/at an induction of 0.1 Tesla and a frequency of 1 kHz.
Kg, while a metallic glass with the composition Fe ₇₆ Mo ₄ B ₂₀ exhibits an AC core loss of 0.08 W/Kg at a dielectric of 0.1 Tesla and the same frequency. In contrast, the metal-glass alloy of the present invention with the composition Fe ₇₅ Ni ₄ Mo ₃ B ₁₆ Si ₂ exhibits an AC core loss of 0.02 W/Kg at a dielectric of 0.1 Tesla and at the same frequency. Excitation power is a measure of the power required to maintain a characteristic magnetic flux density in a magnetic material. Therefore, it is desirable that the excitation power of the magnetic material used in the magnetic device be as low as possible. Excitation power (P _e )
is related to the core loss (L) mentioned above by the relationship L=P _e cos δ, where δ is the phase difference between the excitation field and the resulting induction. This phase difference is also related to magnetostriction in that the smaller the value of magnetostriction, the smaller the phase difference. Therefore, it is advantageous for the magnetostriction value to be as small as possible. As mentioned earlier, iron-rich prior art metallic glasses such as Fe ₇₉ B ₁₆ Si ₅ have magnetostriction values of approximately 30 ppm, compared to magnetostriction values of approximately 20 ppm for the metallic glasses of the present invention. have. Due to this difference, the phase difference is quite different. For example, the prior art metallic glass Fe ₇₉ B ₁₆ Si ₅ annealed under optimal conditions has a δ of approximately 70°, whereas the metallic glass of the present invention has a δ of approximately 50°. As a result, for a given core loss, the prior art metallic glass exhibits a factor 2 higher excitation power than the inventive metallic glass. Crystallization temperature is the temperature at which metallic glass begins to crystallize. The higher the crystallization temperature, the more useful a material is for high-temperature applications, and in conjunction with the Curie temperature, which is substantially lower than the crystallization temperature, magnetic annealing can be carried out at a temperature slightly above the Curie temperature. can. Some metallic glasses crystallize in multiple stages. In such cases, the first crystallization temperature (lowest crystallization temperature) is important as far as the thermal stability of the material is concerned. The crystallization temperatures discussed herein are measured by differential scanning calorimetry. Glass-like alloys according to the prior art exhibit crystallization temperatures of about 660-750K. For example, a metallic glass with the composition Fe ₇₈ Mo ₂ B ₂₀ has a crystallization temperature of 680 K, while
A metallic glass with the composition Fe ₇₄ Mo ₆ B ₂₀ has a crystallization temperature of 750K. In contrast, the metallic glass of the present invention exhibits an increase in crystallization temperature to a level exceeding 750K. The magnetic properties of the metallic glasses of the present invention are determined by the choice of annealing temperature (T _a ), holding time (t _a ), applied magnetic field (in the direction of the ribbon and parallel or perpendicular to the plane of the ribbon) and the cooling rate after processing. Improved by featured heat treatment. For the alloys of the present invention, optimum properties are obtained after annealing, which results in controlled precipitation of a certain number of crystal grains from the glass-like matrix. Under these conditions, the individual particles have a body-centered cubic structure for compositions with boron contents in the range of 17 to 20 atom %. These particles consist essentially of iron, with up to 22 atomic percent of iron being nickel, cobalt, chromium,
At least one of molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium, hafnium, silicon, and carbon is substituted. For compositions with a boron content in the range 21-25 atom % and an iron content in the range 69-78 atom %, each individual particle consists essentially of a mixture of particles, the major part of which is Contains particles with crystals of Fe ₃ B structure. The particles of such part consist of iron and boron, up to 14 atomic percent of the iron being replaced by at least one of nickel, cobalt, chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and hafnium. It is adjusted such that up to 2 atom % of the boron is replaced by carbon. When the number of particles of this type is small, the average domain wall spacing is reduced to a certain extent, and at the same time the core loss is reduced. Too many particles will increase the coercivity and therefore the hysteresis losses. When the metallic glass of the present invention with the composition Fe ₇₅ Ni ₄ Mo ₃ B ₁₆ Si ₂ is annealed under optimal conditions,
It has a coercive force of only 2 A/m, combined with low loss and high magnetic permeability. In contrast, prior art metallic glasses annealed under optimal conditions
Fe ₇₉ B ₁₆ Si ₅ has a coercive force of about 8 A/m. The grain size of the inventive material heat-treated under optimal conditions is
They range from 100 to 300 nm, and their volume fraction is less than 1%. The interparticle spacing is approximately 1-10 μm. In summary, the metallic glass of the present invention has high magnetic permeability, low saturation magnetostriction, low coercive force, low AC core loss, low excitation power, and high crystallization temperature, and can be used as tape heads, relay cores, transformers, etc. . The metallic glasses of the present invention are prepared by cooling the initial composition of the melt at a rate of at least about 10 ⁵ C/sec by quenching techniques well known in the metallic glass art (see, e.g., U.S. Pat. No. 3,856,513). Manufactured. These metallic glasses are substantially completely glassy (i.e., at least 90% glassy), resulting in lower coercivity and greater ductility than less glassy alloys. . There are various methods for processing into continuous ribbons, wires, sheets, etc. Generally, a specific composition is chosen, powders or granules of the essential elements in desired proportions are melted, homogenized, and the molten alloy is quenched on a cooling surface such as a rapidly rotating cylinder. Example 1 Fe-Ni-Mo-B-Si system By ejecting a melt of a specific composition onto a rapidly rotating copper chill wheel (surface velocity 3000-6000 ft/min) with argon overpressure. ,
_Ribbons were produced having a composition represented by Fe _100-abcd Nia _{Mob Bc} Si _d and having dimensions of 1-2.5 cm wide and 25-50 μm thick. The molybdenum content was varied from 1 atomic % to 6 atomic %, resulting in a substantially glassy ribbon. For molybdenum contents higher than 6 atom %, the Curie temperature decreased to unacceptably low values. Magnetic permeability, magnetostriction, core loss, magnetizing force and coercive force were measured in conventional manner using B-H loops, metal strain gauges and vibrating sample magnetometers.
The Curie temperature and crystallization temperature were measured by induction method and differential scanning calorimetry, respectively. Measured values of room temperature saturation induction, Curie temperature, room temperature saturation magnetostriction, and first crystallization temperature are summarized in the table below.
The magnetic properties of these glass-like alloys after annealing are shown in the table. The optimal annealing conditions for the metallic glass Fe ₇₅ Ni ₄ Mo ₃ B ₁₆ Si ₂ and the results obtained are summarized in the table. The frequency dependence of magnetic permeability and core loss for alloys annealed under these optimum conditions is listed in the table. The presence of molybdenum appears to increase the magnetic permeability and crystallization temperature, while decreasing the AC core loss, excitation power, and magnetostriction. Of particular note is that the metallic glass Fe ₇₅ Ni ₄ Mo ₃ B ₁₆ Si ₂ of the present invention heat-treated under optimal conditions has a coercive force as low as 2.5 A/m, and even at 50 kHz and an induction level of 0.1 Tesla. Low core loss of 6.5W/Kg and 12500
It has a magnetic permeability of . These properties together make these compositions suitable for use in high frequency transformers and tape heads.

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[Table] Example 2 Fe-Ni-M-B-Si system Fe _100-abcd M-M'-
A composition represented by B-Si (where M is nickel and/or cobalt, M' is one element among chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and hafnium) Ribbons with dimensions of 1 cm width and 25-50 μm thickness were produced. The content of metal "M'" was varied from 1 atomic % to 6 atomic %, resulting in substantially glassy ribbons.
Higher "M'" contents lowered the Curie temperature to unacceptably low values. The magnetic and thermal data are summarized in the table below. The magnetic properties of these alloys after annealing are shown in the table. The magnetism of these metallic glasses in a low magnetic field is
This corresponded to the magnetism associated with metallic glass containing molybdenum (Example 1). In the metallic glasses of the present invention, a combination of low AC core loss and high magnetic permeability at high frequencies is achieved. Excellent thermal stability is also shown, as expressed by high crystallization temperatures. The combination of these improved properties of the metallic glasses of the present invention makes these compositions suitable for magnetic cores in transformers, tape recording heads, and the like.

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[Table] Example 3 Fe-Ni-M-B-Si-C system Fe _100-abcde Ni _a M' _b B _c in the same manner as in Example 1
Si _d C _e (where M′ is Cr, Mo, W, V, Nb, Ta, Ti
Ribbons were produced having the composition represented by Zr or Zr) and having dimensions of 1 cm width and 25-50 μm thickness. The metal "M'" content was varied from 1 at.% to 6 at.%. Carbon contents of up to 2 atom % resulted in substantially glassy ribbons. When the content of metal "M'" was greater than 6 atom %, the Curie temperature decreased to unacceptably low values. The magnetic and thermal data are summarized in the table below. The magnetism of these metals after annealing is shown in the table. The combination of low AC core loss, high magnetic permeability, and high thermal stability of the metallic glasses of the present invention makes the compositions suitable for transformer magnetic cores, recording heads, and the like.

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[Table] Although the present invention has been described in great detail above, it is not necessary to adhere strictly to this detailed discussion, and it is obvious that various changes and modifications can be made to those skilled in the art, all of which are within the scope of the patent claims. within the scope of the invention.

Claims (1)

[Scope of Claims] 1 Essentially 66 to 82 atomic percent of iron (1 to 8 atomic percent of this iron is replaced by at least one element selected from the group consisting of nickel, cobalt, and mixtures thereof) , chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium, and hafnium.
at least 1 atomic % is substituted by silicon) and accompanying impurities, which has a combination of high magnetic permeability, low magnetostriction, low coercive force, low AC core loss, low excitation power and high thermal stability.
90% vitreous metal glass. 2 essentially 66 to 79 atom% of iron, 2 to 8 atom% of at least one element selected from the group consisting of nickel, cobalt and mixtures thereof, and chromium, molybdenum, tungsten, vanadium,
At least one selected from the group consisting of niobium, tantalum, titanium, zirconium and hafnium
Claim 1 containing 2 to 4 at% of the species element
Metallic glass as described in section. 3. The metallic glass according to claim 1 or 2, wherein the metallic glass contains a metalloid element which is essentially a combination of boron and 0.5 to 4 at % silicon. 4. The metallic glass according to any one of claims 1 to 3, wherein the metalloid element is in the range of 17 to 26 at %. 5. At least one element selected from the group consisting essentially of 70 to 79 atomic percent iron, 2 to 4 atomic percent of at least one element selected from the group consisting of nickel, cobalt, and mixtures thereof, and at least one element selected from the group consisting of molybdenum and chromium. 5. A metallic glass according to any one of claims 1, 3 and 4, comprising metalloids in the range of ~4 at.% and 17-22 at.%. 6 Essentially 66 to 82 atom % of iron (1 to 8 atom % of this iron is replaced by at least one element selected from the group consisting of nickel, cobalt and mixtures thereof), chromium, molybdenum, tungsten , vanadium, niobium, tantalum, titanium, zirconium, and hafnium.
% by silicon and up to 2 atomic % further substituted by carbon) and incidental impurities, resulting in high magnetic permeability, low magnetostriction, low coercive force, low AC core loss, low excitation power and high A metallic glass that is at least 90% vitreous and has thermal stability. 7 Essentially 66 to 79 atom% of iron, 2 to 8 atom% of at least one element selected from the group consisting of nickel, cobalt and mixtures thereof, and chromium, molybdenum, tungsten, vanadium,
At least one selected from the group consisting of niobium, tantalum, titanium, zirconium and hafnium
7. The metallic glass according to claim 6, comprising 2 to 4 at.% of the seed element. 8. According to either claim 6 or 7, the metallic glass has a metalloid element consisting essentially of a combination of boron, 0.5 to 4 atomic % silicon, and 2 atomic % or less carbon. metal glass. 9. The metallic glass according to any one of claims 6 to 8, wherein the metalloid element is in the range of 17 to 26 at %.