EP0072893B1 - Metallic glasses having a combination of high permeability, low coercivity, low ac core loss, low exciting power and high thermal stability - Google Patents
Metallic glasses having a combination of high permeability, low coercivity, low ac core loss, low exciting power and high thermal stability Download PDFInfo
- Publication number
- EP0072893B1 EP0072893B1 EP82104504A EP82104504A EP0072893B1 EP 0072893 B1 EP0072893 B1 EP 0072893B1 EP 82104504 A EP82104504 A EP 82104504A EP 82104504 A EP82104504 A EP 82104504A EP 0072893 B1 EP0072893 B1 EP 0072893B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- atom percent
- low
- boron
- particles
- iron
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
- 239000005300 metallic glass Substances 0.000 title claims description 60
- 230000035699 permeability Effects 0.000 title claims description 22
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 77
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 44
- 239000000203 mixture Substances 0.000 claims description 34
- 229910045601 alloy Inorganic materials 0.000 claims description 30
- 239000000956 alloy Substances 0.000 claims description 30
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 26
- 229910052796 boron Inorganic materials 0.000 claims description 26
- 239000002245 particle Substances 0.000 claims description 25
- 229910052750 molybdenum Inorganic materials 0.000 claims description 24
- 229910052742 iron Inorganic materials 0.000 claims description 23
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 21
- 239000011733 molybdenum Substances 0.000 claims description 21
- 239000011651 chromium Substances 0.000 claims description 20
- 229910052804 chromium Inorganic materials 0.000 claims description 19
- 229910052759 nickel Inorganic materials 0.000 claims description 17
- 229910052758 niobium Inorganic materials 0.000 claims description 17
- 239000010955 niobium Substances 0.000 claims description 17
- 229910052721 tungsten Inorganic materials 0.000 claims description 17
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical group [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 16
- 239000010941 cobalt Substances 0.000 claims description 16
- 229910017052 cobalt Inorganic materials 0.000 claims description 16
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 16
- 229910052710 silicon Inorganic materials 0.000 claims description 16
- 239000010703 silicon Substances 0.000 claims description 16
- 229910052715 tantalum Inorganic materials 0.000 claims description 16
- 229910052720 vanadium Inorganic materials 0.000 claims description 16
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical group [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 15
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 15
- 229910052799 carbon Inorganic materials 0.000 claims description 15
- 229910052719 titanium Inorganic materials 0.000 claims description 15
- 239000010936 titanium Substances 0.000 claims description 15
- 229910052726 zirconium Inorganic materials 0.000 claims description 14
- 229910052735 hafnium Inorganic materials 0.000 claims description 13
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 13
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 13
- 239000010937 tungsten Substances 0.000 claims description 13
- 238000000137 annealing Methods 0.000 claims description 12
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 12
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 12
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 11
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 11
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 claims description 11
- 238000000034 method Methods 0.000 claims description 7
- 229910052752 metalloid Inorganic materials 0.000 claims description 4
- 239000000470 constituent Substances 0.000 claims description 2
- 239000011521 glass Substances 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 239000011159 matrix material Substances 0.000 claims description 2
- 238000001556 precipitation Methods 0.000 claims description 2
- 230000002708 enhancing effect Effects 0.000 claims 1
- 125000004429 atom Chemical group 0.000 description 49
- 238000002425 crystallisation Methods 0.000 description 18
- 230000008025 crystallization Effects 0.000 description 18
- 230000006698 induction Effects 0.000 description 13
- 239000000463 material Substances 0.000 description 8
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000002184 metal Substances 0.000 description 6
- 230000010363 phase shift Effects 0.000 description 4
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 239000000696 magnetic material Substances 0.000 description 3
- 230000005415 magnetization Effects 0.000 description 3
- 239000000155 melt Substances 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 239000011574 phosphorus Substances 0.000 description 3
- 229910000815 supermalloy Inorganic materials 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910018540 Si C Inorganic materials 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910000808 amorphous metal alloy Inorganic materials 0.000 description 2
- 229910052787 antimony Inorganic materials 0.000 description 2
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 description 2
- 229910052790 beryllium Inorganic materials 0.000 description 2
- ATBAMAFKBVZNFJ-UHFFFAOYSA-N beryllium atom Chemical compound [Be] ATBAMAFKBVZNFJ-UHFFFAOYSA-N 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000000113 differential scanning calorimetry Methods 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 229910052732 germanium Inorganic materials 0.000 description 2
- GNPVGFCGXDBREM-UHFFFAOYSA-N germanium atom Chemical compound [Ge] GNPVGFCGXDBREM-UHFFFAOYSA-N 0.000 description 2
- 229910052738 indium Inorganic materials 0.000 description 2
- APFVFJFRJDLVQX-UHFFFAOYSA-N indium atom Chemical compound [In] APFVFJFRJDLVQX-UHFFFAOYSA-N 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 229910010271 silicon carbide Inorganic materials 0.000 description 2
- 229910052718 tin Inorganic materials 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- PMVSDNDAUGGCCE-TYYBGVCCSA-L Ferrous fumarate Chemical group [Fe+2].[O-]C(=O)\C=C\C([O-])=O PMVSDNDAUGGCCE-TYYBGVCCSA-L 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 125000005843 halogen group Chemical group 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052809 inorganic oxide Inorganic materials 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 150000002738 metalloids Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000000075 oxide glass Substances 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 229910000889 permalloy Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 238000009738 saturating Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000007669 thermal treatment Methods 0.000 description 1
- 229910052723 transition metal Inorganic materials 0.000 description 1
- 150000003624 transition metals Chemical class 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/02—Amorphous alloys with iron as the major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
- C22C27/02—Alloys based on vanadium, niobium, or tantalum
Definitions
- the invention relates to metallic glasses having high permeability, low magnetostriction, low coercivity, low ac core loss, low exciting power and high thermal stability.
- metallic glasses are metastable materials lacking any long range order.
- X-ray diffraction scans of glassy metal alloys show only a diffuse halo similar to that observed for inorganic oxide glasses.
- Metallic glasses have been disclosed in US-A-3 856 513. These alloys include compositions having the formula M a Y b Z e , where 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 an element selected from the group consisting of aluminum, silicon, tin, germanium, indium, antimony and beryllium, "a” ranges from about 60 to 90 atom percent, "b” ranges from about 10 to 30 atom percent and "c” ranges from about 0.1 to 15 atom percent.
- 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
- Z is an element selected from the group consisting of aluminum, silicon, tin, germanium, indium, antimony and beryllium
- metallic glassy wires having the formula T i X j , where T is at least one transition metal and X is an element selected from the group consisting of phosphorus, boron, carbon, aluminum, silicon, tin, germanium, indium, beryllium and antimony, "i” ranges from about 70 to 87 atom percent and "j” ranges from about 13 to 30 atom percent.
- T is at least one transition metal
- X is an element selected from the group consisting of phosphorus, boron, carbon, aluminum, silicon, tin, germanium, indium, beryllium and antimony
- i ranges from about 70 to 87 atom percent
- j ranges from about 13 to 30 atom percent.
- Metallic glasses are also disclosed in US-A-4 067 732 issued January 10, 1978. These glassy alloys include compositions having the formula M a M' t ,Cr, : M" d B e , where M is one iron group element (iron, cobalt and nickel), M' is at least one of the two remaining iron group elements, M" is at least one element of vanadium, manganese, molybdenum, tungsten, niobium and tantalum, Bis boron, "a” ranges from about 40 to 85 atom percent, "b” ranges from 0 to about 45 atom percent, "c” and “d” both range from 0 to about 20 atom percent and “e” ranges from about 15 to 25 atom percent, with the provision that "b", "c” and “d” cannot be zero simultaneously.
- Such glassy alloys are disclosed as having an unexpected combination of improved ultimate tensile strength, improved hardness and improved thermal stability.
- FR-A-2 376 218 glassy alloys comprising about 63 to 83 atom percent iron and/or cobalt, 0 to about 60 atom percent of which may be replaced by nickel, about 2 to 12 atom percent at least one element selected from the group consisting of molybdenum, tungsten, niobium and titanium and about 15 to 25 atom percent at least one element selected from the group consisting of boron, phosphorus and carbon, but containing no silicon are known.
- the US ⁇ A ⁇ 4 140 525 discloses glassy alloys consisting of 56 to 68 atom percent iron, 4 to 9 atom percent chromium, 1 to 6 atom percent molybdenum and 27 to 29 atom percent boron.
- the EP-A-20 937 discloses. at least 90% amorphous metal alloys consisting essentially 80 to 82 atom percent iron, 12.5 to 14.5 atom percent boron, 2.5 to 5.0 atom percent silicon and 1.5 to 2.5 atom percent carbon.
- the EP-A-49 770 discloses special amorphous alloys having the formulae Fe 81 B 13.5 Si 3.5 C 2 , Fe s ,B '4 Si s and Fe 79 B 16 Si 5 .
- metallic glasses possessing a combination of higher permeability, lower magnetostriction, lower coercivity, lower core loss, lower exciting power and higher thermal stability than prior art metallic glasses are required for specific applications such as tape recorder head, relay cores, transformers and the like.
- metallic glasses having a combination of high permeability, low saturation magnetostriction, low coercivity, low ac core loss, low exciting power and high thermal stability.
- the metallic glasses consist of 62 to 79 atom percent of iron, 2 to 8 atom percent of at least one element selected from the group consisting of nickel, cobalt, and mixtures thereof, 2 to 4 atom percent of at least one element selected from the group consisting of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, zirconium and hafnium, 17 to 28 atom percent of boron, from 0.5 to 6 atom percent of said boron being replaced with silicon and up to 2 atom percent of boron being, optionally, replaced with carbon, plus incidental impurities.
- the metallic glasses of the invention are suitable for use in tape recorder heads, relay cores, transformers and the like.
- a concentration of less than about 1 atom percent of Cr, Mo, W, V, Nb, Ta, Ti, Zr and/or Hf does not result in sufficient improvement of the properties of permeability, saturation magnetostriction, coercivity, ac core loss and thermal stability.
- a concentration greater than about 6 atom percent of at least one of these elements results in an unacceptably low Curie temperature.
- the metal content is preferably substantially iron, with up to about 8 atom percent nickel and/or cobalt in order to compensate the reduction of the room temperature saturation magnetization due to the presence of chromium, molybdenum, tungsten, niobium, tantalum, titanium, zirconium and/or hafnium.
- nickel increases permeability.
- the replacement of boron with silicon and carbon provides said glass with a metalloid element selected from the group consisting of substantially boron and from 0.5 to 4 atom percent silicon, and boron plus silicon together with from 0 to 2 atom percent carbon.
- the metallic glasses according to the invention consist of 70 to 79 atom percent iron, 2 to 4 atom percent of at least one element selected from the group consisting of nickel, cobalt and mixtures thereof, 2 to 4 atom percent of an element selected from the group consisting of molybdenum and chromium and 17 to 22 percent of an element selected from the group consisting of boron, silicon and mixtures thereof.
- the alloys according to the invention are at least 85 percent amorphous and comprise discrete particles of its constituents, said particles having an average size ranging from 0.1 ⁇ m to 0.3 ⁇ m and an average said discrete particles occupy an average volume fraction of 0.005 to 0.01.
- Examples of metallic glasses of the invention include (the subscripts are in atom percent). The purity of all alloys is that found in normal commercial practice.
- chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or hafnium raises the crystallization temperature while simultaneously lowering the Curie temperature of the glassy alloy.
- the increased separation of these temperatures provided ease of magnetic annealing, that is, thermal annealing at a temperature near the Curie temperature.
- thermal annealing at a temperature near the Curie temperature.
- annealing a magnetic material close to its Curie temperature generally results in improved properties.
- annealing can be easily accomplished at elevated temperatures near the Curie temperature and below the crystallization temperature. Such annealing cannot be carried out for many alloys similar to those of the invention but lacking these elements.
- too high a concentration of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or hafnium reduces the Curie temperature to a level that may be undesirable in certain applications.
- the metalloid content ranges from 17 to 26 atom percent for maximum thermal stability.
- Preferred metallic glass systems are as follows:
- Magnetic permeability is the ratio of induction to applied magnetic field. A higher permeability renders a material more useful in certain applications such as tape recorder heads, due to the increased response.
- the frequency dependence of permeability of the glassy alloys of the invention is similar to that of the 4-79 Permalloys in the medium-to-high frequency range (1-50 kHz), and at higher frequencies (about 50 kHz to 1 MHz), the permeability is comparable to that of the supermalloys.
- Saturation magnetostriction is the change in length under the influence of a saturating magnetic field.
- a lower saturation magnetostriction renders a material more useful in certain application such as tape recorder heads.
- Magnetostriction is usually discussed in terms of the ratio of the change in length to the original length, and is given in ppm.
- Prior art iron rich metallic glasses evidence saturation magnetostrictions of about 30 ppm as do metallic glasses without the presence of the any of the elements belonging to the IVB, VB and VIB columns of the periodic table such as molybdenum.
- a prior art iron rich metallic glass designated for use in high frequency applications and having the composition Fe 79 B 16 Si 5 has a saturation magnetostriction of about 30 ppm.
- a metallic glass of the invention having the composition Fe 75 Ni 4 Mo 3 B 16 Si 2 has a saturation magnetostriction of about 20 ppm.
- a lower saturation magnetostriction leads to a lower phase angle between the exciting field and the resulting induction. This results in lower exciting power as discussed below.
- Ac core loss is that energy loss dissipated as heat. It is the hysteresis in an ac field and is measured by the area of a B-H loop for low frequencies (less than about 1 kHz) and from the complex input power in the exciting coil for high frequencies (about 1 kHz to 1 MHz). The major portion of the ac core loss at high frequencies arises from the eddy current generated during flux change. However, a smaller hysteresis loss and hence a smaller coercivity is desirable. A lower core loss renders a material more useful in certain applications such as tape recorder heads and transformers. Core loss is discussed in units of watts/kg.
- Prior art heat-treated metallic glasses typically evidence ac core losses of about 0.05 to 0.1 watts/kg at an induction of 0.1 Tesla and at the frequency range of 1 kHz.
- a prior art heat-treated metallic glass having the composition Fe 4o Ni 36 Mo 4 B 2o has an ac core loss of 0.07 watts/kg at an induction of 0.1 Tesla and at the frequency of 1 kHz
- a metallic glass having the composition Fe, 6 Mo 4 B 2o has an ac core loss of 0.08 watts/kg at an induction of 0.1 Tesla and at the same frequency.
- a metallic glass alloy of the invention having the composition Fe 75 Ni 4 Mo 3 B 16 Si 2 has an ac core loss of 0.02 watts/kg at an induction of 0.1 Tesla and at the same frequency.
- Exciting power is a measure of power required to maintain a certain flux density in a magnetic material. It is therefore desirable that a magnetic material to be used in magnetic devices has an exciting power as low as possible.
- the phase shift is also related to the magnetostriction in such a way that a lower magnetostriction value leads to lower phase shift. It is than advantageous to have the magnetostriction value as low as possible.
- prior art iron-rich metallic glasses such as Fe 79 B 16 Si 5 have the magnetostriction value near 30 ppm, in contrast to the magnetostriction value of about 20 ppm of the metallic glasses of the present invention.
- This difference results in a considerable phase shift difference.
- optimally annealed prior art metallic glass Fe 79 B 16 Si 5 has 6 near 70° while the metallic glasses of the present invention have 5 near 50°. This results, for a given core loss, in a higher exciting power by a factor of two for the prior art metallic glass than the metallic glass of the present invention.
- Crystallization temperature is the temperature at which a metallic glass begins to crystallize.
- a higher crystallization temperature renders 'a material more useful in high temperature applications and, in conjunction with a Curie temperature that is substantially lower than the cyrstallization temperature, permits magnetic annealing just above the Curie temperature.
- Some metallic glasses crystallize in multiple steps.
- the first crystallization temperature (the lowest value of the crystallization temperatures) is the meaningful one as far as the materials' thermal stability is concerned.
- the crystallization temperature as discussed herein is measured by differential scanning calorimetry. Prior art glassy alloys evidence crystallization temperatures of about 660 K to 750 K.
- a metallic glass having the composition Fe 78 MO 2 B 20 has a crystallization temperature of 680 K
- a metallic glass having the composition Fe 74 MO 6 B 20 has a crystallization temperature of 750 K
- metallic glasses of the invention evidence increases in crystallization temperatures to a level above 750 K.
- the magnetic properties of the metallic glasses of the present invention are improved by thermal treatment, characterized by choice of annealing temperatures (T a ), holding time (t a ), applied magnetic field (either parallel or perpendicular to the ribbon direction and in the ribbon plane), and post-treatment cooling rate.
- T a annealing temperatures
- t a holding time
- applied magnetic field applied magnetic field
- post-treatment cooling rate post-treatment cooling rate.
- the optimal properties are obtained after an anneal which causes the controlled precipitation of a certain number of crystalline particles from the glassy matrix. Under these conditions, for compositions having boron content ranging from about 17 to 20 atom percent, the discrete particles have a body-centered cubic structure.
- the particles are composed essentially of iron, up to 22 atom percent of the iron being adapted to be replaced by at least one of nickel, cobalt, chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium, hafnium, silicon and carbon.
- the discrete particles consist essentially of a mixture of particles, a major portion of which mixture contains particles having a crystalline Fe 3 B structure.
- the particles of such portion are composed of iron and boron, up to 14 atom percent of the iron being adapted to be replaced by at least one of nickel, cobalt, chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and hafnium and up to 2 atom percent of the boron being adapted to be replaced by carbon.
- a small number of such particles introduces a certain decrease in the average domain wall spacing with concomitant decrease in core loss. Too large a number of particles increases the coercivity and thus the hysteresis loss.
- a metallic glass of the present invention with composition Fe 75 Ni 4 MO 3 B 16 Si 2 has a combination of low loss and high permeability with a coercivity of only 2 A/m when optimally annealed.
- an optimally annealed prior art metallic glass Fe 79 B 16 Si 5 has a coercivity of about 8 A/m.
- the crystalline particle size in the optimally heat-treated materials of the present invention ranges between 100 and 300 nm, and their volume fraction is less than 1%.
- the interparticle spacing is of the order of 1-10 pm.
- the metallic glasses of the invention have a combination of high permeability, low saturation magnetostriction, low coercivity, low ac core loss, low exciting power and high crystallization temperature and are useful as tape heads, relay cores, transformers and the like.
- the metallic glasses of the invention are prepared by cooling a melt of the desired composition at a rate of at least about 10 5 °C/sec, employing quenching techniques well known to the metallic glass art; see e.g., US-A-3,856,513.
- the metallic glasses are substantially completely glassy, that is, at least 90% glassy, and consequently possess lower coercivities and are more ductile than less glassy alloys.
- a variety of techniques are available for fabricating continuous ribbon, wire, sheet, etc. Typically, a particular composition is selected, powders or granules of the requisite elements in the desired portions are melted and homogenized and the molten alloy is rapidly quenched on a chill surface such as a rapidly rotating cylinder.
- Ribbons having compositions given by Fe, oo -a- b - e - d Ni a Mo b B e Si d and having dimensions about 1 to 2.5 cm wide and about 25 to 50 ⁇ m thick were formed by squirting a melt of the particular composition by overpressure of argon onto a rapidly rotating copper chill wheel (surface speed about 1500 to 3000 cm/sec).
- Molybdenum content was varied from 1 to 6 atom percent, for which substantially glassy ribbons were obtained. Molybdenum content higher than 6 atom percent reduced the Curie temperature to an unacceptable low value.
- Permability, magnetostriction, core loss, magnetization and coercive force were measured by conventional techniques employing B-H toops, metallic strain gauges and a vibrating sample magnetometer. Curie temperature and crystallization temperature were measured respectively by an induction method and differential scanning calorimetry. The measured values of room temperature saturation induction, Curie temperature, room temperature saturation magnetostriction and the first crystallization temperature are summarized in Table I below. The magnetic properties of these glassy alloys are annealing are presented in Table II. Optimum annealing conditions for the metallic glass Fe 75 Ni 4 MO 3 B 16 Si 2 and the obtained results are summarized in Table III. Frequency dependence of permeability and ac core loss of this optimally annealed alloy are listed in Table IV.
- the optimally heat-treated metallic glass Fe 75 Ni 4 MO 3 B 16 Si 2 of the present invention has a coercivity reaching as low as 2.5 A/m and yet has a low core loss of 6.5 W/kg and permeability of 12500 at 50 kHz and at the induction level of 0.1 Tesla.
- the combination of these properties make these compositions suitable for high frequency transformer and tape-head applications.
- Ribbons having compositions given by Fe 100-a-b-c-d M a -M' b -B c -Si d when M is nickel and/or cobalt, M' is one of the elements chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and hafnium, and having dimensions about 1 cm wide and about 25 to 50 ⁇ m thick were formed as in Example 1.
- Metal "M”' content was varied from 1 to 6 atom percent, for which substantially glassy ribbons were obtained. Higher metal “M”' content reduced the Curie temperature to an unacceptably low value.
- a combination of low ac core loss and high permeability at high frequency is achieved in the metallic glasses of the present invention.
- the thermal stability is also shown to be excellent as evidenced by high crystallization temperature.
- the metal "M”' content was varied from 1 to 6 atom percent, and the carbon content “e” was up to 2 atom percent for which substantially glassy ribbons were obtained.
- the metal "M"' content greater than about 6 atom percent reduced the Curie temperature to an unacceptably low value.
- the magnetic and thermal data are summarized in Table VII below.
- the magnetic properties of these metallic glasses after annealing are presented in Table VIII.
- a combination of low ac core loss, high permeability, and high thermal stability of the metallic glasses of the present invention renders these compositions suitable in the magnetic cores of transformers, recording heads and the like.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Soft Magnetic Materials (AREA)
- Adornments (AREA)
- Powder Metallurgy (AREA)
Description
- The invention relates to metallic glasses having high permeability, low magnetostriction, low coercivity, low ac core loss, low exciting power and high thermal stability.
- As is known, metallic glasses are metastable materials lacking any long range order. X-ray diffraction scans of glassy metal alloys show only a diffuse halo similar to that observed for inorganic oxide glasses.
- Metallic glasses (amorphous metal alloys) have been disclosed in US-A-3 856 513. These alloys include compositions having the formula MaYbZe, where 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 an element selected from the group consisting of aluminum, silicon, tin, germanium, indium, antimony and beryllium, "a" ranges from about 60 to 90 atom percent, "b" ranges from about 10 to 30 atom percent and "c" ranges from about 0.1 to 15 atom percent. Also disclosed are metallic glassy wires having the formula TiXj, where T is at least one transition metal and X is an element selected from the group consisting of phosphorus, boron, carbon, aluminum, silicon, tin, germanium, indium, beryllium and antimony, "i" ranges from about 70 to 87 atom percent and "j" ranges from about 13 to 30 atom percent. Such materials are conveniently prepared by rapid quenching from the melt using processing techniques that are now well-known in the art.
- Metallic glasses are also disclosed in US-A-4 067 732 issued January 10, 1978. These glassy alloys include compositions having the formula MaM't,Cr,:M"dBe, where M is one iron group element (iron, cobalt and nickel), M' is at least one of the two remaining iron group elements, M" is at least one element of vanadium, manganese, molybdenum, tungsten, niobium and tantalum, Bis boron, "a" ranges from about 40 to 85 atom percent, "b" ranges from 0 to about 45 atom percent, "c" and "d" both range from 0 to about 20 atom percent and "e" ranges from about 15 to 25 atom percent, with the provision that "b", "c" and "d" cannot be zero simultaneously. Such glassy alloys are disclosed as having an unexpected combination of improved ultimate tensile strength, improved hardness and improved thermal stability.
- By the FR-A-2 376 218 glassy alloys comprising about 63 to 83 atom percent iron and/or cobalt, 0 to about 60 atom percent of which may be replaced by nickel, about 2 to 12 atom percent at least one element selected from the group consisting of molybdenum, tungsten, niobium and titanium and about 15 to 25 atom percent at least one element selected from the group consisting of boron, phosphorus and carbon, but containing no silicon are known. The US―A―4 140 525 discloses glassy alloys consisting of 56 to 68 atom percent iron, 4 to 9 atom percent chromium, 1 to 6 atom percent molybdenum and 27 to 29 atom percent boron.
- The EP-A-20 937 discloses. at least 90% amorphous metal alloys consisting essentially 80 to 82 atom percent iron, 12.5 to 14.5 atom percent boron, 2.5 to 5.0 atom percent silicon and 1.5 to 2.5 atom percent carbon. Finally the EP-A-49 770 discloses special amorphous alloys having the formulae Fe81 B13.5Si3.5C2, Fes,B'4Sis and Fe79B16Si5.
- These disclosures also mention unusual or unique magnetic properties for many metallic glasses which fall within the scope of the broad claims. However, metallic glasses possessing a combination of higher permeability, lower magnetostriction, lower coercivity, lower core loss, lower exciting power and higher thermal stability than prior art metallic glasses are required for specific applications such as tape recorder head, relay cores, transformers and the like.
- In accordance with the invention, metallic glasses having a combination of high permeability, low saturation magnetostriction, low coercivity, low ac core loss, low exciting power and high thermal stability are provided. The metallic glasses consist of 62 to 79 atom percent of iron, 2 to 8 atom percent of at least one element selected from the group consisting of nickel, cobalt, and mixtures thereof, 2 to 4 atom percent of at least one element selected from the group consisting of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, zirconium and hafnium, 17 to 28 atom percent of boron, from 0.5 to 6 atom percent of said boron being replaced with silicon and up to 2 atom percent of boron being, optionally, replaced with carbon, plus incidental impurities. The metallic glasses of the invention are suitable for use in tape recorder heads, relay cores, transformers and the like.
- A concentration of less than about 1 atom percent of Cr, Mo, W, V, Nb, Ta, Ti, Zr and/or Hf does not result in sufficient improvement of the properties of permeability, saturation magnetostriction, coercivity, ac core loss and thermal stability. A concentration greater than about 6 atom percent of at least one of these elements results in an unacceptably low Curie temperature.
- Iron provides high saturation magnetization at room temperature. Accordingly the metal content is preferably substantially iron, with up to about 8 atom percent nickel and/or cobalt in order to compensate the reduction of the room temperature saturation magnetization due to the presence of chromium, molybdenum, tungsten, niobium, tantalum, titanium, zirconium and/or hafnium. The addition of nickel increases permeability.
- Preferably the replacement of boron with silicon and carbon provides said glass with a metalloid element selected from the group consisting of substantially boron and from 0.5 to 4 atom percent silicon, and boron plus silicon together with from 0 to 2 atom percent carbon.
- Suitably the metallic glasses according to the invention consist of 70 to 79 atom percent iron, 2 to 4 atom percent of at least one element selected from the group consisting of nickel, cobalt and mixtures thereof, 2 to 4 atom percent of an element selected from the group consisting of molybdenum and chromium and 17 to 22 percent of an element selected from the group consisting of boron, silicon and mixtures thereof.
- Preferably the alloys according to the invention are at least 85 percent amorphous and comprise discrete particles of its constituents, said particles having an average size ranging from 0.1 µm to 0.3 µm and an average said discrete particles occupy an average volume fraction of 0.005 to 0.01.
-
- The presence of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or hafnium raises the crystallization temperature while simultaneously lowering the Curie temperature of the glassy alloy. The increased separation of these temperatures provided ease of magnetic annealing, that is, thermal annealing at a temperature near the Curie temperature. As is well-known, annealing a magnetic material close to its Curie temperature generally results in improved properties. As a consequence of the increase in crystallization temperature with increase in the concentration of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium, and/or hafnium, annealing can be easily accomplished at elevated temperatures near the Curie temperature and below the crystallization temperature. Such annealing cannot be carried out for many alloys similar to those of the invention but lacking these elements. On the other hand, too high a concentration of chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and/or hafnium reduces the Curie temperature to a level that may be undesirable in certain applications.
- Preferably, the metalloid content ranges from 17 to 26 atom percent for maximum thermal stability.
- Preferred metallic glass systems are as follows:
- 1. Fe-M-Mo-B-Si: Fe100-a-b-c-dMaMobBcSid, where M is at least one of nickel and cobalt. When (c+d) is about 18, the preferred ranges of a, b, c and d are from about 2 to 8, from about 2 to 4, from about 14 to 17.5 and from about 0.5 to 4, respectively. When (c+d) is about 22, the preferred ranges for a, b, c and d are from about 2 to 8, from about 2 to 6, from about 15 to 20.5 and from about 0.5 to 6, respectively. When (c+d) is close to 25, the preferred ranges of a, b, c and d are from about 2 to 8, from about 2 to 6, from about 21 to 25 and from about 1 to 6 respectively. These metallic glasses have a combination of saturation induction (Ba) of 1.0-1.4 Tesla, saturation magnetostriction (λs) between 12 and 24 ppm, Curie temperature (8f) between about 475 and 705 K and first crystallization temperature of 750-880 K. When optimally heat-treated, these alloys have excellent ac magnetic properties especially at high frequencies (f>103 Hz). The ac core loss (L) and exciting power (Pe) taken at f=50 kHz' and the induction level of Bm=0.1 Tesla of, for example, a heat-treated Fe75Ni4Mo3B16Si2 metallic glass are 6.5 W/kg and 13.4 VA/kg,. respectively. These values are to be compared with L=7 W/kg and Pe=20 VA/kg for a heat treated prior art metallic glass of the same thickness having the composition Fe79B16Si5. The permeability p at Bm=0.1 Tesla is 10500 and 8000 for the heat-treated Fe75Ni3Mo4B16Si2 and Fe79B16Si5, respectively. The smaller saturation magnetostriction (λs) of about 20 ppm) of the present alloy as compared to λs = 30 ppm for the aforesaid prior art alloy makes the alloys of the present invention especially suited for magnetic device applications such as cores for high frequency transformers. Beyond f=50 kHz; the alloys of the present invention have permeabilities comparable or higher than those for crystalline supermalloys which have Bs near 0.8 Tesla. The higher values of Bs for the present alloys make these alloys better suited than supermalloy for magnetic applications of f>50 kHz.
- 2. Fe-M-M'-B-Si: Fe100-a-b-c-dMaM'bBcSid where M is nickel and/or cobalt and M' is selected from Cr, W, V, Nb, Ta, Ti, Zr or Hf. When (c+d) is about 18, the preferred ranges of a, b, c and d are about 2 to 8, from about 2 to 4, from about 14 to 17.5 and from about 0.5 to 4, respectively. When (c+d) is about 22, the preferred ranges for a, b, c and d are from about 2 to 8, from about 2 to 6, from about 16 to 21.5 and from about 0.5 to 6, respectively. When (c+d) is close to 25, the preferred ranges for a, b, c and d are from about 2 to 8, from about 2 to 6, from about 21 to 25 and from about 1 to 6, respectively.
- 3. Fe-M-M'-B-Si-C: Fe100-a-b-c-d-eMaM'bBcSidCe wherein 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. When (c+d) is about 18, the preferred ranges for a, b, c, d and e are from about 2 to 8, from about 2 to 4, from about 12 to 17.5, from about 0.5 to 4 and from 0 to 2, respectively. When (c+d) is about 22, the preferred ranges for a, b, c, d and e are from about 2 to 8, from about 2 to 6, from about 14 to 21.5, from about 0.5 to 6 and from about 0 to 2, respectively. When (c+d) is close to 25, the preferred ranges for a, b, c, d and e are from about 2 to 8, from about 2 to 6, from about 20 to 27, from about 1 to 6 and from about 0 to 2, respectively.
- Magnetic permeability is the ratio of induction to applied magnetic field. A higher permeability renders a material more useful in certain applications such as tape recorder heads, due to the increased response. The frequency dependence of permeability of the glassy alloys of the invention is similar to that of the 4-79 Permalloys in the medium-to-high frequency range (1-50 kHz), and at higher frequencies (about 50 kHz to 1 MHz), the permeability is comparable to that of the supermalloys. Especially noted is the fact that a heat-treated Fe75Ni4Mo3B16Si2 metallic glass has permeability of 24,000 while the best-heat-treated prior art Fe4oNi3gMo4B2o metallic glass has a permeability of 14,000 at 1 kHz and the induction level of 0.01 Tesla.
- Saturation magnetostriction is the change in length under the influence of a saturating magnetic field. A lower saturation magnetostriction renders a material more useful in certain application such as tape recorder heads. Magnetostriction is usually discussed in terms of the ratio of the change in length to the original length, and is given in ppm. Prior art iron rich metallic glasses evidence saturation magnetostrictions of about 30 ppm as do metallic glasses without the presence of the any of the elements belonging to the IVB, VB and VIB columns of the periodic table such as molybdenum. For example, a prior art iron rich metallic glass designated for use in high frequency applications and having the composition Fe79B16Si5 has a saturation magnetostriction of about 30 ppm. In contrast, a metallic glass of the invention having the composition Fe75Ni4Mo3B16Si2 has a saturation magnetostriction of about 20 ppm. A lower saturation magnetostriction leads to a lower phase angle between the exciting field and the resulting induction. This results in lower exciting power as discussed below.
- Ac core loss is that energy loss dissipated as heat. It is the hysteresis in an ac field and is measured by the area of a B-H loop for low frequencies (less than about 1 kHz) and from the complex input power in the exciting coil for high frequencies (about 1 kHz to 1 MHz). The major portion of the ac core loss at high frequencies arises from the eddy current generated during flux change. However, a smaller hysteresis loss and hence a smaller coercivity is desirable. A lower core loss renders a material more useful in certain applications such as tape recorder heads and transformers. Core loss is discussed in units of watts/kg. Prior art heat-treated metallic glasses typically evidence ac core losses of about 0.05 to 0.1 watts/kg at an induction of 0.1 Tesla and at the frequency range of 1 kHz. For example, a prior art heat-treated metallic glass having the composition Fe4oNi36Mo4B2o, has an ac core loss of 0.07 watts/kg at an induction of 0.1 Tesla and at the frequency of 1 kHz, while a metallic glass having the composition Fe,6Mo4B2o has an ac core loss of 0.08 watts/kg at an induction of 0.1 Tesla and at the same frequency. In contrast, a metallic glass alloy of the invention having the composition Fe75Ni4Mo3B16Si2 has an ac core loss of 0.02 watts/kg at an induction of 0.1 Tesla and at the same frequency.
- Exciting power is a measure of power required to maintain a certain flux density in a magnetic material. It is therefore desirable that a magnetic material to be used in magnetic devices has an exciting power as low as possible. Exciting power (Pe) is related to the above-mentioned core loss (L) through the relationship L=Pe cos 6 where 6 is the phase shift between the exciting field and the resultant induction. The phase shift is also related to the magnetostriction in such a way that a lower magnetostriction value leads to lower phase shift. It is than advantageous to have the magnetostriction value as low as possible. As mentioned earlier, prior art iron-rich metallic glasses such as Fe79B16Si5 have the magnetostriction value near 30 ppm, in contrast to the magnetostriction value of about 20 ppm of the metallic glasses of the present invention. This difference results in a considerable phase shift difference. For example, optimally annealed prior art metallic glass Fe79B16Si5 has 6 near 70° while the metallic glasses of the present invention have 5 near 50°. This results, for a given core loss, in a higher exciting power by a factor of two for the prior art metallic glass than the metallic glass of the present invention.
- Crystallization temperature is the temperature at which a metallic glass begins to crystallize. A higher crystallization temperature renders 'a material more useful in high temperature applications and, in conjunction with a Curie temperature that is substantially lower than the cyrstallization temperature, permits magnetic annealing just above the Curie temperature. Some metallic glasses crystallize in multiple steps. In such cases, the first crystallization temperature (the lowest value of the crystallization temperatures) is the meaningful one as far as the materials' thermal stability is concerned. The crystallization temperature as discussed herein is measured by differential scanning calorimetry. Prior art glassy alloys evidence crystallization temperatures of about 660 K to 750 K. For example, a metallic glass having the composition Fe78MO2B20 has a crystallization temperature of 680 K, while a metallic glass having the composition Fe74MO6B20 has a crystallization temperature of 750 K. In contrast, metallic glasses of the invention evidence increases in crystallization temperatures to a level above 750 K.
- The magnetic properties of the metallic glasses of the present invention are improved by thermal treatment, characterized by choice of annealing temperatures (Ta), holding time (ta), applied magnetic field (either parallel or perpendicular to the ribbon direction and in the ribbon plane), and post-treatment cooling rate. For the present alloys, the optimal properties are obtained after an anneal which causes the controlled precipitation of a certain number of crystalline particles from the glassy matrix. Under these conditions, for compositions having boron content ranging from about 17 to 20 atom percent, the discrete particles have a body-centered cubic structure. The particles are composed essentially of iron, up to 22 atom percent of the iron being adapted to be replaced by at least one of nickel, cobalt, chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium, hafnium, silicon and carbon. For compositions having boron content ranging from about 21 to 25 atom percent and iron content ranging from about 69 to 78 atom percent, the discrete particles consist essentially of a mixture of particles, a major portion of which mixture contains particles having a crystalline Fe3B structure. The particles of such portion are composed of iron and boron, up to 14 atom percent of the iron being adapted to be replaced by at least one of nickel, cobalt, chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and hafnium and up to 2 atom percent of the boron being adapted to be replaced by carbon. A small number of such particles introduces a certain decrease in the average domain wall spacing with concomitant decrease in core loss. Too large a number of particles increases the coercivity and thus the hysteresis loss. A metallic glass of the present invention with composition Fe75Ni4MO3B16Si2 has a combination of low loss and high permeability with a coercivity of only 2 A/m when optimally annealed. In contrast to this, an optimally annealed prior art metallic glass Fe79B16Si5 has a coercivity of about 8 A/m. The crystalline particle size in the optimally heat-treated materials of the present invention ranges between 100 and 300 nm, and their volume fraction is less than 1%. The interparticle spacing is of the order of 1-10 pm.
- In summary, the metallic glasses of the invention have a combination of high permeability, low saturation magnetostriction, low coercivity, low ac core loss, low exciting power and high crystallization temperature and are useful as tape heads, relay cores, transformers and the like.
- The metallic glasses of the invention are prepared by cooling a melt of the desired composition at a rate of at least about 105°C/sec, employing quenching techniques well known to the metallic glass art; see e.g., US-A-3,856,513. The metallic glasses are substantially completely glassy, that is, at least 90% glassy, and consequently possess lower coercivities and are more ductile than less glassy alloys.
- A variety of techniques are available for fabricating continuous ribbon, wire, sheet, etc. Typically, a particular composition is selected, powders or granules of the requisite elements in the desired portions are melted and homogenized and the molten alloy is rapidly quenched on a chill surface such as a rapidly rotating cylinder.
- Ribbons having compositions given by Fe,oo-a-b-e-dNiaMobBeSid and having dimensions about 1 to 2.5 cm wide and about 25 to 50 µm thick were formed by squirting a melt of the particular composition by overpressure of argon onto a rapidly rotating copper chill wheel (surface speed about 1500 to 3000 cm/sec).
- Molybdenum content was varied from 1 to 6 atom percent, for which substantially glassy ribbons were obtained. Molybdenum content higher than 6 atom percent reduced the Curie temperature to an unacceptable low value.
- Permability, magnetostriction, core loss, magnetization and coercive force were measured by conventional techniques employing B-H toops, metallic strain gauges and a vibrating sample magnetometer. Curie temperature and crystallization temperature were measured respectively by an induction method and differential scanning calorimetry. The measured values of room temperature saturation induction, Curie temperature, room temperature saturation magnetostriction and the first crystallization temperature are summarized in Table I below. The magnetic properties of these glassy alloys are annealing are presented in Table II. Optimum annealing conditions for the metallic glass Fe75Ni4MO3B16Si2 and the obtained results are summarized in Table III. Frequency dependence of permeability and ac core loss of this optimally annealed alloy are listed in Table IV.
- The presence of molybdenum is seen to increase the permeability and the crystallization temperature and to lower the ac core loss, exciting power and magnetostriction. Especially noted is the fact that the optimally heat-treated metallic glass Fe75Ni4MO3B16Si2 of the present invention has a coercivity reaching as low as 2.5 A/m and yet has a low core loss of 6.5 W/kg and permeability of 12500 at 50 kHz and at the induction level of 0.1 Tesla. The combination of these properties make these compositions suitable for high frequency transformer and tape-head applications.
- Ribbons having compositions given by Fe100-a-b-c-dMa-M'b-Bc-Sid when M is nickel and/or cobalt, M' is one of the elements chromium, molybdenum, tungsten, vanadium, niobium, tantalum, titanium, zirconium and hafnium, and having dimensions about 1 cm wide and about 25 to 50 µm thick were formed as in Example 1.
- Metal "M"' content was varied from 1 to 6 atom percent, for which substantially glassy ribbons were obtained. Higher metal "M"' content reduced the Curie temperature to an unacceptably low value.
- The magnetic and thermal data are summarized in Table V below. The magnetic properties of these glassy alloys after annealing are presented in Table VI.
- Low field magnetic properties of these metallic glasses were comparable to those for the metallic glasses containing molybdenum (Example 1).
- A combination of low ac core loss and high permeability at high frequency is achieved in the metallic glasses of the present invention. The thermal stability is also shown to be excellent as evidenced by high crystallization temperature. These improved combination of properties of the metallic glasses of the present invention renders these compositions suitable in the magnetic cores of transformers, tape- recording heads and the like.
- Ribbons having compositions given by Fe100-a-b-c-d-eNiaM'bBcSidCe where M'=Cr, Mo, W, V, Nb, Ta, Ti, or Zr and having dimensions about 1 cm wide and about 25 to 50 µm thick were formed as in Example 1. The metal "M"' content was varied from 1 to 6 atom percent, and the carbon content "e" was up to 2 atom percent for which substantially glassy ribbons were obtained. The metal "M"' content greater than about 6 atom percent reduced the Curie temperature to an unacceptably low value.
- The magnetic and thermal data are summarized in Table VII below. The magnetic properties of these metallic glasses after annealing are presented in Table VIII. A combination of low ac core loss, high permeability, and high thermal stability of the metallic glasses of the present invention renders these compositions suitable in the magnetic cores of transformers, recording heads and the like.
- Having thus described the invention in rather full detail, it will be understood that this detail need not be strictly adhered to but that various changes and modifications may suggest themselves to one skilled in the art, all falling within the scope of the present invention as defined by the subjoined claims.
Claims (9)
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US29516581A | 1981-08-21 | 1981-08-21 | |
US295165 | 1981-08-21 | ||
US31951481A | 1981-11-09 | 1981-11-09 | |
US319514 | 1981-11-09 |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0072893A1 EP0072893A1 (en) | 1983-03-02 |
EP0072893B1 true EP0072893B1 (en) | 1986-12-03 |
Family
ID=26968961
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP82104504A Expired EP0072893B1 (en) | 1981-08-21 | 1982-05-24 | Metallic glasses having a combination of high permeability, low coercivity, low ac core loss, low exciting power and high thermal stability |
Country Status (6)
Country | Link |
---|---|
EP (1) | EP0072893B1 (en) |
JP (1) | JPH0639663B2 (en) |
KR (1) | KR870001283B1 (en) |
AU (1) | AU557318B2 (en) |
CA (1) | CA1222646A (en) |
DE (1) | DE3274562D1 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US11198927B1 (en) * | 2019-09-26 | 2021-12-14 | United States Of America As Represented By The Secretary Of The Air Force | Niobium alloys for high temperature, structural applications |
Families Citing this family (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4588452A (en) * | 1983-03-16 | 1986-05-13 | Allied Corporation | Amorphous alloys for electromagnetic devices |
AU573895B2 (en) * | 1984-09-17 | 1988-06-23 | Ovonic Synthetic Materials Company, Inc. | Hard magnetic material |
US4881989A (en) * | 1986-12-15 | 1989-11-21 | Hitachi Metals, Ltd. | Fe-base soft magnetic alloy and method of producing same |
JP3279399B2 (en) * | 1992-09-14 | 2002-04-30 | アルプス電気株式会社 | Method for producing Fe-based soft magnetic alloy |
JP3231149B2 (en) * | 1993-07-30 | 2001-11-19 | アルプス電気株式会社 | Noise filter |
US6187112B1 (en) | 1995-04-13 | 2001-02-13 | Ryusuke Hasegawa | Metallic glass alloys for mechanically resonant marker surveillance systems |
US5628840A (en) * | 1995-04-13 | 1997-05-13 | Alliedsignal Inc. | Metallic glass alloys for mechanically resonant marker surveillance systems |
US6093261A (en) * | 1995-04-13 | 2000-07-25 | Alliedsignals Inc. | Metallic glass alloys for mechanically resonant marker surveillance systems |
JP4636365B2 (en) * | 2004-07-05 | 2011-02-23 | 日立金属株式会社 | Fe-based amorphous alloy ribbon and magnetic core |
US8704134B2 (en) | 2005-02-11 | 2014-04-22 | The Nanosteel Company, Inc. | High hardness/high wear resistant iron based weld overlay materials |
US7935198B2 (en) | 2005-02-11 | 2011-05-03 | The Nanosteel Company, Inc. | Glass stability, glass forming ability, and microstructural refinement |
US7553382B2 (en) * | 2005-02-11 | 2009-06-30 | The Nanosteel Company, Inc. | Glass stability, glass forming ability, and microstructural refinement |
KR100904664B1 (en) * | 2008-06-03 | 2009-06-25 | 주식회사 에이엠오 | Magnetic core for electric current sensors |
US8317949B2 (en) * | 2008-06-16 | 2012-11-27 | The Nanosteel Company, Inc. | Ductile metallic glasses |
EP2596140B1 (en) | 2010-07-21 | 2018-05-16 | Rolex S.A. | Watch-making or clock-making component comprising an amorphous metal alloy |
WO2012010940A2 (en) | 2010-07-21 | 2012-01-26 | Institut Polytechnique De Grenoble | Amorphous metal alloy |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0020937A1 (en) * | 1979-05-25 | 1981-01-07 | Allied Corporation | Method of enhancing the magnetic properties of amorphous metal alloys |
EP0049770A2 (en) * | 1980-09-26 | 1982-04-21 | Allied Corporation | Amorphous alloys for electromagnetic devices |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4052201A (en) * | 1975-06-26 | 1977-10-04 | Allied Chemical Corporation | Amorphous alloys with improved resistance to embrittlement upon heat treatment |
US4152146A (en) * | 1976-12-29 | 1979-05-01 | Allied Chemical Corporation | Glass-forming alloys with improved filament strength |
US4152144A (en) * | 1976-12-29 | 1979-05-01 | Allied Chemical Corporation | Metallic glasses having a combination of high permeability, low magnetostriction, low ac core loss and high thermal stability |
US4188211A (en) * | 1977-02-18 | 1980-02-12 | Tdk Electronics Company, Limited | Thermally stable amorphous magnetic alloy |
US4225339A (en) * | 1977-12-28 | 1980-09-30 | Tokyo Shibaura Denki Kabushiki Kaisha | Amorphous alloy of high magnetic permeability |
US4140525A (en) * | 1978-01-03 | 1979-02-20 | Allied Chemical Corporation | Ultra-high strength glassy alloys |
-
1982
- 1982-05-24 EP EP82104504A patent/EP0072893B1/en not_active Expired
- 1982-05-24 DE DE8282104504T patent/DE3274562D1/en not_active Expired
- 1982-05-31 AU AU84338/82A patent/AU557318B2/en not_active Ceased
- 1982-07-12 CA CA000407099A patent/CA1222646A/en not_active Expired
- 1982-08-19 KR KR8203736A patent/KR870001283B1/en active
-
1991
- 1991-03-11 JP JP3072435A patent/JPH0639663B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0020937A1 (en) * | 1979-05-25 | 1981-01-07 | Allied Corporation | Method of enhancing the magnetic properties of amorphous metal alloys |
EP0049770A2 (en) * | 1980-09-26 | 1982-04-21 | Allied Corporation | Amorphous alloys for electromagnetic devices |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US11198927B1 (en) * | 2019-09-26 | 2021-12-14 | United States Of America As Represented By The Secretary Of The Air Force | Niobium alloys for high temperature, structural applications |
Also Published As
Publication number | Publication date |
---|---|
JPH0639663B2 (en) | 1994-05-25 |
AU8433882A (en) | 1983-02-24 |
EP0072893A1 (en) | 1983-03-02 |
AU557318B2 (en) | 1986-12-18 |
JPH04314846A (en) | 1992-11-06 |
DE3274562D1 (en) | 1987-01-15 |
CA1222646A (en) | 1987-06-09 |
KR870001283B1 (en) | 1987-06-30 |
KR840001228A (en) | 1984-03-28 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US4152144A (en) | Metallic glasses having a combination of high permeability, low magnetostriction, low ac core loss and high thermal stability | |
EP0072893B1 (en) | Metallic glasses having a combination of high permeability, low coercivity, low ac core loss, low exciting power and high thermal stability | |
EP0574513B1 (en) | PROCESS FOR THE PRODUCTION OF SOFT MAGNETIC ALLOYS ON THE BASIS OF Fe-Ni HAVING NANOCRYSTALLINE STRUCTURE | |
US5200002A (en) | Amorphous low-retentivity alloy | |
EP0430085B1 (en) | Magnetic alloy with ultrafine crystal grains and method of producing same | |
EP0049770B1 (en) | Amorphous alloys for electromagnetic devices | |
JP2008231533A (en) | Soft magnetic thin band, magnetic core, magnetic component, and method for producing soft magnetic thin band | |
EP0240600B1 (en) | Glassy metal alloys with perminvar characteristics | |
EP0119432B1 (en) | Amorphous alloys for electromagnetic devices | |
EP0088244B1 (en) | Cobalt rich manganese containing near-zero magnetostrictive metallic glasses having high saturation induction | |
EP0575190B1 (en) | Fe-base soft magnetic alloy and process for making same | |
EP0513385B1 (en) | Iron-base soft magnetic alloy | |
EP0084138B1 (en) | Near-zero magnetostrictive glassy metal alloys with high magnetic and thermal stability | |
US4834814A (en) | Metallic glasses having a combination of high permeability, low coercivity, low AC core loss, low exciting power and high thermal stability | |
JP3434844B2 (en) | Low iron loss, high magnetic flux density amorphous alloy | |
US4473400A (en) | Magnetic metallic glass alloy | |
EP0351051B1 (en) | Fe-based soft magnetic alloy | |
JPH0351785B2 (en) | ||
US4938267A (en) | Glassy metal alloys with perminvar characteristics | |
EP0329704B1 (en) | Near-zero magnetostrictive glassy metal alloys for high frequency applications | |
US4588452A (en) | Amorphous alloys for electromagnetic devices | |
JPH0641698A (en) | Fe-base soft-magnetic alloy | |
JPH0463253A (en) | Fe-base soft-magnetic alloy and its production and magnetic core using same |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
AK | Designated contracting states |
Designated state(s): DE FR GB IT NL SE |
|
17P | Request for examination filed |
Effective date: 19830414 |
|
ITF | It: translation for a ep patent filed | ||
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): DE FR GB IT NL SE |
|
REF | Corresponds to: |
Ref document number: 3274562 Country of ref document: DE Date of ref document: 19870115 |
|
ET | Fr: translation filed | ||
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed | ||
ITTA | It: last paid annual fee | ||
EAL | Se: european patent in force in sweden |
Ref document number: 82104504.4 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 19990322 Year of fee payment: 18 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 19990406 Year of fee payment: 18 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 19990504 Year of fee payment: 18 Ref country code: FR Payment date: 19990504 Year of fee payment: 18 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 19990531 Year of fee payment: 18 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20000524 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20000525 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20001201 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20000524 |
|
EUG | Se: european patent has lapsed |
Ref document number: 82104504.4 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20010131 |
|
NLV4 | Nl: lapsed or anulled due to non-payment of the annual fee |
Effective date: 20001201 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20010301 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST |