WO2005031762A2 - 高周波用磁性薄膜およびその作製方法ならびに磁気素子 - Google Patents
高周波用磁性薄膜およびその作製方法ならびに磁気素子 Download PDFInfo
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- WO2005031762A2 WO2005031762A2 PCT/JP2004/014405 JP2004014405W WO2005031762A2 WO 2005031762 A2 WO2005031762 A2 WO 2005031762A2 JP 2004014405 W JP2004014405 W JP 2004014405W WO 2005031762 A2 WO2005031762 A2 WO 2005031762A2
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Classifications
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/14—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for applying magnetic films to substrates
- H01F41/30—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for applying magnetic films to substrates for applying nanostructures, e.g. by molecular beam epitaxy [MBE]
- H01F41/302—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for applying magnetic films to substrates for applying nanostructures, e.g. by molecular beam epitaxy [MBE] for applying spin-exchange-coupled multilayers, e.g. nanostructured superlattices
- H01F41/303—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for applying magnetic films to substrates for applying nanostructures, e.g. by molecular beam epitaxy [MBE] for applying spin-exchange-coupled multilayers, e.g. nanostructured superlattices with exchange coupling adjustment of magnetic film pairs, e.g. interface modifications by reduction, oxidation
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- H01F10/08—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers
- H01F10/10—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers characterised by the composition
- H01F10/12—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers characterised by the composition being metals or alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y25/00—Nanomagnetism, e.g. magnetoimpedance, anisotropic magnetoresistance, giant magnetoresistance or tunneling magnetoresistance
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y40/00—Manufacture or treatment of nanostructures
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- H01—ELECTRIC ELEMENTS
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- H01F10/08—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers
- H01F10/10—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers characterised by the composition
- H01F10/12—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers characterised by the composition being metals or alloys
- H01F10/13—Amorphous metallic alloys, e.g. glassy metals
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- H01F10/08—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers
- H01F10/10—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers characterised by the composition
- H01F10/12—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers characterised by the composition being metals or alloys
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- H01F10/132—Amorphous metallic alloys, e.g. glassy metals containing cobalt
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- H01F10/32—Spin-exchange-coupled multilayers, e.g. nanostructured superlattices
- H01F10/324—Exchange coupling of magnetic film pairs via a very thin non-magnetic spacer, e.g. by exchange with conduction electrons of the spacer
- H01F10/3286—Spin-exchange coupled multilayers having at least one layer with perpendicular magnetic anisotropy
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- H01F17/00—Fixed inductances of the signal type
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
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- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/14—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for applying magnetic films to substrates
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- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
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- H01F17/0006—Printed inductances
- H01F2017/0066—Printed inductances with a magnetic layer
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- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/04—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing coils
- H01F41/041—Printed circuit coils
- H01F41/046—Printed circuit coils structurally combined with ferromagnetic material
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/32—Composite [nonstructural laminate] of inorganic material having metal-compound-containing layer and having defined magnetic layer
- Y10T428/325—Magnetic layer next to second metal compound-containing layer
Definitions
- Magnetic thin film for high frequency method for producing the same, and magnetic element
- the present invention relates to a high-frequency magnetic thin film used in a high-frequency region of the GHz band, a method for manufacturing the same, and a magnetic element having the high-frequency magnetic thin film. More specifically, the present invention relates to a high-frequency magnetic film such as a thin film inductor or a thin film transformer. The present invention relates to a high-frequency magnetic thin film preferably used for a planar magnetic element for use in a semiconductor device, a monolithic microwave integrated circuit (hereinafter abbreviated as MMIC), a method for manufacturing the same, and a magnetic element.
- MMIC monolithic microwave integrated circuit
- the demand for MMIC which is increasing mainly in wireless transmission / reception devices and portable information terminals, is based on a semiconductor substrate such as Si, GaAs or InP, on which active elements such as transistors, lines, resistors, capacitors, and inductors are mounted.
- active elements such as transistors, lines, resistors, capacitors, and inductors are mounted.
- passive elements such as inductors and capacitors, occupy a larger area than active elements, especially in this MMIC. ing.
- the occupation of a large area of passive devices in an MMIC results in a large consumption of expensive semiconductor substrates, which leads to an increase in the cost of the MMIC.
- To reduce the manufacturing cost of MMICs it is necessary to reduce the chip area. For that purpose, reducing the area occupied by passive elements is an issue.
- a planar spiral coil is often used as an inductor.
- the inductance is increased by providing a soft magnetic thin film on the upper and lower surfaces or on one surface in order to obtain the same inductance even in a small occupied area (for example, J. Appl. .Phys., 85, 7919 (1999)).
- it is first necessary to develop soft magnetic thin film materials that have high permeability in the GHz band and low high-frequency loss.
- high specific resistance is required to reduce eddy current loss at high frequencies. Is also required.
- a Co-based amorphous alloy As a material having excellent soft magnetic properties, a Co-based amorphous alloy is known.
- This Co-based non-crystalline alloy is mainly composed of Co and mainly non-crystalline containing one or more elements selected from Y, Ti, Zr, Hf, Nb, Ta, etc. It is.
- the force loss component imaging part of magnetic permeability; z 2
- a magnetic thin film is formed into a strip having a longitudinal direction parallel to the axis of easy magnetization. Attempts have been made to shift the resonance frequency to a higher frequency side by increasing the shape magnetic anisotropy energy (see, for example, Journal of the Japan Society of Applied Magnetics, 24,879 (2000)).
- the resonance frequency could be raised to the GHz band, but the drawback is that it is necessary to fabricate strip-shaped micropatterns as complex as photolithography.
- the present invention has been made to solve the above problems, and a first object of the present invention is to provide a high-frequency magnetic thin film that can be used in a high-frequency region in a GHz band.
- a second object of the present invention is to provide a method for producing a high-frequency magnetic thin film having such characteristics.
- a third object of the present invention is to provide a magnetic element using a high-frequency magnetic thin film having good high-frequency characteristics in the GHz band.
- the inventor of the present invention has been conducting research on a high-frequency magnetic thin film using a Co-based amorphous alloy having soft magnetic properties. It was found that an anisotropic magnetic field appeared when multilayered with the oxidizing layer of the alloy, and as a result of further research on high-frequency magnetic thin films using the large anisotropic magnetic field, it was found that It was found that when the volume of the oxide layer is within a predetermined range, a large anisotropic magnetic field appears, and a magnetic thin film having excellent high-frequency characteristics in the GHz band can be obtained.
- the high-frequency magnetic thin film of the present invention that achieves the first object is based on the above findings, and includes a Co-based amorphous alloy layer and an acid of the Co-based amorphous alloy.
- a multilayer film comprising an iridani layer, wherein the ratio of the iridani layer to the entire volume of the multilayer film is 5 to 50%.
- the multilayer film having the above-mentioned constitution has a high specific resistance and high! (4) Since an anisotropic magnetic field appears, a magnetic thin film having excellent high-frequency characteristics in the GHz band is obtained.
- another magnetic thin film for high frequency wave includes a Co-based amorphous alloy layer having such a property that a magnetic field application direction during film formation is an easy axis of magnetization, and an acid of the Co-based amorphous alloy.
- a multilayer film composed of a multilayer film and a magnetic layer which is formed so that the axis of easy magnetization of the manufactured multilayer film is orthogonal to the magnetic field application direction when the multilayer film is formed.
- the Co-based amorphous alloy layer usually has a property that the direction of application of a magnetic field during film formation is an axis of easy magnetization.
- the Co-based amorphous alloy layer is When a multilayer film is formed with the oxidation film and the multilayer film is formed in an applied magnetic field such that the ratio of the oxidation film to the entire volume of the multilayer film is in the range of 5 to 50%.
- an inversion phenomenon of the magnetization easy axis Z hard axis in which the magnetization easy axis of the manufactured multilayer film is orthogonal to the magnetic field application direction at the time of forming the multilayer film, appears.
- Such a phenomenon is considered to be the opposite effect of magnetostriction.
- the high-frequency magnetic thin film of the present invention exhibits a large anisotropic magnetic field developed based on the phenomenon and also has a high specific resistance. It becomes an excellent magnetic thin film.
- the Co-based amorphous alloy layer is formed of a CoZrNb alloy
- the GO specific resistance is 150 ⁇ cm or more
- the ferromagnetic resonance frequency is 2 GHz or more.
- the method for producing a high-frequency magnetic thin film of the present invention that achieves the second object is characterized in that a multilayer film composed of a Co-based amorphous alloy layer and an oxide layer of the Co-based amorphous alloy is formed by applying a multilayer film in an applied magnetic field.
- the method for producing a high-frequency magnetic thin film according to (1) characterized in that the oxide layer is formed so that the ratio of the oxide layer to the entire volume of the multilayer film falls within the range of 5 to 50%.
- Another method for producing a high-frequency magnetic thin film according to the present invention is a method for forming a Co-based amorphous alloy layer having a property that the direction of application of an external magnetic field during film formation is an axis of easy magnetization under an external magnetic field.
- a multilayer film composed of a layer and an oxide layer thereof is formed, and the axis of easy magnetization of the manufactured multilayer film as a whole is orthogonal to the direction in which an external magnetic field is applied.
- the Co-based amorphous alloy layer is formed of a CoZrNb alloy.
- a CoZrNb alloy is used, a composition such that the magnetostriction becomes zero can be easily realized, and as a result, the force is excellent in soft magnetic properties and high magnetic permeability can be obtained.
- the magnetic element of the present invention that achieves the third object includes, in part, the high-frequency magnetic thin film of the present invention described above or the high-frequency magnetic thin film manufactured by the above-described method of the present invention. It is characterized by having.
- the high-frequency magnetic thin film is disposed to face the coil, (b) the magnetic thin film is used for an inductor or a transformer, or (c) a monolithic magnetic thin film is used. It is preferably used for a microwave integrated circuit.
- the high-frequency magnetic thin film of the present invention has a high anisotropic magnetic field and a high specific resistance. Can be offered.
- the magnetic thin film for high frequency of the present invention can be preferably used as a magnetic thin film for the GHz band applied to, for example, an inductor having a planar spiral coil mounted on an MMIC.
- the high-frequency magnetic thin film of the present invention can obtain good performance even in a state of being formed at room temperature (as-deposit), so that it can be used in a semiconductor process that dislikes a heating step, such as an MMIC. Ideal for manufactured high-frequency integrated circuits.
- a high-frequency magnetic thin film exhibiting a large anisotropic magnetic field and a high specific resistance due to a phenomenon considered to be an adverse effect of magnetostriction can be produced.
- Magnetic thin films with excellent high-frequency characteristics in the band can be produced by an extremely easy method.
- the magnetic element of the present invention includes a high-frequency magnetic thin film having a high anisotropic magnetic field and a high specific resistance in a part thereof, so that a magnetic element having excellent high-frequency characteristics can be obtained. It can.
- the high-frequency magnetic thin film is applied to a spiral coil in a planar inductor mounted on an MMIC, the inductor is connected to the resonance frequency in the GHz band. It can function well as a magnetic element having a number.
- FIG. 1 is a schematic view showing an example of a cross-sectional structure of a high-frequency magnetic thin film according to an embodiment of the present invention.
- FIG. 2 is a graph showing a magnetic hysteresis curve of a CoZrNb thin film (comparative example) obtained by forming a film on a substrate while applying a magnetic field from a certain direction during film formation.
- FIG. 3 is a graph showing resonance frequency characteristics of the CoZrNb thin film in FIG.
- FIG. 4 Magnetic hysteresis of a multilayer film (embodiment) composed of a CoZrNb thin film and a natural oxide layer obtained by forming a film on a substrate while applying a magnetic field from a certain direction during film formation. This is a graph showing a curve.
- FIG. 5 is a graph showing resonance frequency characteristics of the multilayer film in FIG.
- FIG. 6A is a plan view showing a configuration of an inductor when a planar magnetic element is applied to the inductor.
- FIG. 6B is a sectional view showing the configuration of the inductor shown in FIG. 6A. This is an example.
- FIG. 7 is a schematic cross-sectional view showing another example in which the planar magnetic element according to the embodiment of the present invention is applied to an inductor.
- FIG. 8 is a schematic plan view showing a conductor layer portion of the inductor.
- FIG. 9 is a schematic view of a cross section taken along the line AA of FIG. 8.
- FIG. 10 shows the results of an experiment for confirming the magnetization reversal phenomenon.
- FIG. 1 is a schematic sectional view showing an example of a sectional form of the magnetic thin film for high frequency wave of the present invention.
- the high-frequency magnetic thin film 1 of the present invention comprises, on a substrate 4, a Co-based amorphous alloy layer 2 and a natural oxide layer of the Co-based amorphous alloy.
- 3 is a multilayer film formed by alternately laminating 3 and 3. The characteristic is that the ratio of the natural oxide layer 3 to the volume of the entire multilayer film is 5—
- the Co-based amorphous alloy layer 2 is a non-crystalline alloy containing Co, and has such a property that the direction of applying a magnetic field during film formation is the axis of easy magnetization. Since the Co-based amorphous alloy has a high magnetic permeability and a high resistance (specific resistance of 100-120 ⁇ « ⁇ ), it is effective in suppressing eddy current loss in a high frequency range, and is preferably applied in the present invention. You.
- the Co-based amorphous alloy contains Co as a main component and includes B, C, Si, Ti, V, Cr, Mn, Fe, Ni, Y, Zr, Nb, Mo, Hf, Ta and W. It contains one or more added caro elements selected from the group, and is mainly composed of an amorphous phase.
- an amorphous alloy or an amorphous phase generally refers to an aspect in which a diffraction pattern obtained by X-ray diffraction measurement does not have a remarkable crystalline peak, and a so-called broad diffraction peak appears.
- the ratio (total amount in the case of two or more) of the elements added to the Co-based amorphous alloy is usually 5 to 50 at% (atomic%), preferably 10 to 30 at%. If the ratio of the added element exceeds 50 at%, there is a disadvantage that the saturation magnetization is reduced. On the other hand, if the ratio of the added element is less than 5 at%, it becomes difficult to control the magnetostriction, and there is a disadvantage that effective soft magnetic characteristics cannot be obtained.
- Co-based amorphous alloy examples include CoZr, CoHf, CoNb, CoMo, CoZrNb, CoZrTa, CoFeZr, CoFeNb, CoTiNb, CoZrMo, CoFeB, CoZrNbMo, CoZr MoNi, CoFeZrB, CoFeSiB, CoZrCrMo and the like.
- Particularly preferred is CoZrNb.
- CoZrNb is suitable is that it is easy to realize a composition with zero magnetostriction (for example, Co87Zr5Nb8), and as a result, a high-frequency magnetic thin film with excellent soft magnetic properties and high magnetic permeability can be obtained. This is because there is an advantage.
- the natural oxide layer 3 is an oxidation layer that is naturally generated when the surface of the Co-based amorphous alloy layer 2 comes into contact with oxygen, for example, in the air, in pure water, or in a chemical solution.
- oxygen for example, in the air, in pure water, or in a chemical solution.
- the oxide layer formed by the residual oxygen and residual moisture in the film forming apparatus Layers are also included.
- the formed native oxide layer 3 is usually about 0.1-2. Onm thick, and is not formed so thick because it is a native oxide layer.
- the specific resistance is about 10 3 to 10 6 ⁇ cm.
- the multilayer film 1 according to the present invention is formed by alternately laminating Co-based amorphous alloy layers 2 and natural oxide layers 3. Specifically, a step of forming a Co-based amorphous alloy layer 2 on a substrate while applying a magnetic field from a certain direction during film formation, and a step of forming a natural oxide layer on the surface of the Co-based amorphous alloy layer. It is formed by performing the step of forming 3 alternately.
- the multilayer film 1 is preferably formed by a vacuum thin film forming method, in particular, a sputtering method.
- RF sputtering DC sputtering, magnetron sputtering, ion beam sputtering, inductively coupled RF plasma assisted sputtering, ECR ⁇ sputtering, facing target type sputtering, etc. are used. It is needless to say that sputtering is just one mode of the present embodiment, and other thin film formation processes can be applied.
- a target for depositing a Co-based amorphous alloy layer As a target for depositing a Co-based amorphous alloy layer, a composite target in which pellets of a desired additive element are arranged on a Co target, or a Co alloy containing a desired additive component can be used. Use the target.
- a glass substrate, a ceramic material substrate, a semiconductor substrate, a resin substrate and the like can be exemplified.
- the ceramic material include alumina, zirconia, silicon carbide, silicon nitride, aluminum nitride, steatite, mullite, cordierite, forsterite, spinel, and ferrite.
- aluminum nitride is preferable because of its high thermal conductivity and high bending strength.
- the multilayer film of the present embodiment can exhibit its performance as it is formed at room temperature (about 15 to 35 ° C.). It is the best material for integrated circuits. Therefore, as the substrate 4, a semiconductor substrate such as Si, GaAs, InP, or SiGe can be exemplified.
- the multilayer film 1 has a force formed by repeating such a process.
- the number of layers is not particularly limited, and the thickness of the entire multilayer film is not particularly limited.
- the specific resistance is equal to or greater than 0.99 Omega cm
- the specific resistance of the Co-based amorphous alloy layer 2 itself is at 10 0 ⁇ ⁇ cm or higher
- more natural resistivity of the oxide layer 3 is 10 3 mu Omega cm or more Because there is.
- the reason why the anisotropic magnetic field is 10 5 ⁇ 4 ⁇ [AZm] or more is considered to be based on the following magnetization reversal phenomenon.
- the produced multilayer film 1 is easy to make.
- Axial force A magnetization reversal phenomenon that is perpendicular to the direction in which the magnetic field was applied during the formation of the multilayer film (meaning a 90 ° shift) appears. Such a phenomenon is considered to be a so-called reverse effect phenomenon of magnetostriction.
- the natural oxide layer 3 is preferably at least 10% and at most 45% of the volume of the entire multilayer film.
- FIG. 2 is a graph showing a magnetization hysteresis curve of a 500-nm-thick CoZrNb thin film (comparative example) obtained by forming a film on a substrate while applying a magnetic field from a certain direction during film formation.
- FIG. 3 is a graph showing the resonance frequency characteristics of the obtained CoZrNb thin film.
- Fig. 4 shows that an 8nm-thick CoZrNb thin film obtained by forming a film on a substrate while applying a constant directional magnetic field during film formation and a lnm-thick natural oxide layer are alternately laminated.
- FIG. 1 is a graph showing a magnetization hysteresis curve of a 500-nm-thick CoZrNb thin film (comparative example) obtained by forming a film on a substrate while applying a magnetic field from a certain direction during film formation.
- FIG. 3 is a graph showing the resonance frequency characteristics of the obtained CoZrNb thin film.
- FIG. 5 is a graph showing a magnetic hysteresis curve of a multilayer film having a thickness of 450 nm (Example), and FIG. 5 is a graph showing resonance frequency characteristics of the obtained multilayer film.
- the volume of the natural oxide layer is 11% of the total volume of the multilayer film.
- the horizontal axis represents the externally applied magnetic field H (unit: Oe), and the vertical axis represents the magnetization (unit: G).
- Symbol E indicates a magnetization curve in the direction of easy magnetization
- symbol D indicates a magnetization curve in the direction of hard axis.
- the horizontal axis represents the frequency (unit: MHz)
- the vertical axis represents the real part 1 and the imaginary part 2 of the magnetic permeability.
- the direction of the magnetic field Happl applied at the time of film formation generally coincides with the direction of the easy axis E, and therefore, the magnetization is difficult.
- the direction of the axis H is orthogonal to the direction of the applied magnetic field Happl.
- the direction of the magnetic field Happl applied at the time of film formation coincides with the direction of the magnetic easy axis E.
- the two are orthogonal.
- the direction of the magnetic field Happl applied at the time of film formation matches the direction of the hard axis H.
- the anisotropic magnetic field Hk is larger, a multilayer film having higher high-frequency characteristics can be obtained, so that the resonance frequency characteristics do not actually drop even if fr exceeds 2 GHz, as shown in FIG. This has the effect.
- the ratio of the natural oxide layer 3 is less than 5% of the whole, such a magnetization reversal phenomenon may not appear.
- the ratio of the natural oxide layer 3 exceeds 50% of the whole, the ratio of the non-magnetic component becomes larger than the ratio of the magnetic component, so that it is difficult to use the soft magnetic material.
- the magnetic element of the present invention is characterized in that a part of the above-described magnetic thin film for high frequency is provided.
- FIG. 6A schematically illustrates a planar structure of an inductor to which a planar magnetic element is applied
- FIG. 6B schematically illustrates a cross-sectional structure taken along line AA of FIG. 6A. is there.
- the inductor 10 is formed so as to cover a substrate 11, planar coils 12 and 12 formed in a spiral shape on both surfaces of the substrate 11, and covering these planar coils 12 and 12 and the surface of the substrate 11. It comprises insulating films 13 and 13 and a pair of high-frequency magnetic thin films 1 formed so as to cover the insulating films 13 and 13 respectively.
- the magnetic thin film for high frequency 1 is similar to that shown in FIG. Having a structure.
- the two planar coils 12 and 12 are electrically connected to each other through a through hole 15 formed in a substantially central portion of the substrate 11. Furthermore, terminals 16 for connection are respectively drawn out of the substrate 11 from the planar coils 12 and 12 on both surfaces of the substrate 11.
- Such an inductor 10 is configured such that the planar coils 12, 12 are sandwiched by a pair of high-frequency magnetic thin films 1 via insulating films 13, 13, and an inductor is formed between the connection terminals 16, 16. You.
- the inductor thus formed is small, thin and lightweight, and exhibits excellent inductance particularly in a high frequency band of 1 GHz or more.
- a transformer can be formed by providing a plurality of the planar coils 12 and 12 in parallel.
- FIG. 7 is a schematic cross-sectional view showing another example in which the planar magnetic element of the present embodiment is applied to an inductor.
- the inductor 20 shown in this figure includes a substrate 21, an oxide film 22 formed on the substrate 21 as necessary, and a high-frequency magnetic thin film formed on the oxide film 22. la, and an insulating film 23 formed on the high-frequency magnetic thin film la, and a planar coil 24 formed on the insulating film 23, and covering the planar coil 24 and the insulating film 23. And a high-frequency magnetic thin film lb formed on the insulating film 25.
- the high-frequency magnetic thin films la and lb have the same structure as the above-described high-frequency magnetic thin film 1 (FIG. 1).
- the inductor 20 thus formed is also small, thin and light, and exhibits excellent inductance particularly in a high frequency band of 1 GHz or more.
- a transformer can be formed by providing a plurality of planar coils 24 in parallel.
- FIGS. 8 and 9 show an embodiment in which the high-frequency magnetic thin film 1 is applied as an MMIC inductor.
- FIG. 8 schematically shows a plan view of a conductor layer portion of the inductor.
- FIG. 9 is a drawing schematically showing a cross section taken along line AA of FIG.
- the inductor 30 shown in these drawings includes a substrate 31, an insulating oxide film 32 formed on the substrate 31 as necessary, and a high-frequency wave formed on the insulating oxide film 32.
- the high-frequency magnetic thin films la and lb have the same structure as the above-described high-frequency magnetic thin film 1 (FIG. 1).
- the spiral coil 34 is connected to a pair of electrodes 37 via a wiring 36.
- a pair of ground patterns 39 provided so as to surround the spiral coil 34 are connected to a pair of ground electrodes 38, respectively, and a ground-signal ground (G—S—G) type probe is used. It has a shape to evaluate the frequency characteristics on the wafer!
- the MMIC inductor that works in the shape of the present embodiment employs a cored structure in which the sinusoidal coil 34 is sandwiched between high-frequency magnetic thin films la and lb that are magnetic cores. Therefore, the inductance value is improved by about 50% as compared with an air-core inductor having no high-frequency magnetic thin films la and lb, although the spiral coil 34 has the same shape. Therefore, the area occupied by the spiral coil 34 required to obtain the same inductance value may be small, and as a result, the size of the spiral coil 34 can be reduced.
- a material of the magnetic thin film applied to the inductor for the MMIC a material having a high magnetic permeability at a high frequency in a GHz band, a high performance index Q (low loss) characteristic, an integration by a semiconductor manufacturing process, etc. Is required.
- a material having a high resonance frequency and a large saturation magnetization is advantageous, and it is necessary to control the uniaxial magnetic anisotropy. Also, in order to obtain a high figure of merit Q, it is important to suppress eddy current loss due to high resistance. Further, in order to apply to the integration process, it is desirable that the film can be formed at room temperature and can be used as it is. This is to ensure that the performance and fabrication process of other on-chip components that are already set are not adversely affected by heating.
- the high-frequency magnetic thin film of Example 1 was produced according to the following film forming method.
- a 500 nm thick SiO 2 film formed on a Si wafer was used as a substrate.
- a high-frequency magnetic thin film was deposited on the substrate in the following manner using a facing target type sputtering apparatus. That is, the facing target in a sputtering apparatus 8 X 10 - were preliminarily evacuated to 5 Pa, the pressure introducing Ar gas until LOPA, RF Pawa one 10 minute 100W, the substrate surface was sputter etched. Next, adjust the flow rate of Ar gas so that the pressure becomes 0.4 Pa, and sputter the Co Zr Nb target with a power of 300 W.
- the natural oxide layer is formed by forming each metal layer and then introducing 2 sccm O gas into the sputtering device for 30 seconds to oxidize the surface of the metal layer.
- a DC bias of 0.8 V was applied to the substrate. Presputtering was performed for 10 minutes or more with the shutter closed to prevent the influence of impurities on the target surface. Thereafter, a film was formed on the substrate by opening the shutter. The film formation rate was 0.33 nmZ seconds when forming the CoZrNb layer. The thickness of the Co-based amorphous alloy layer was adjusted by controlling the opening and closing time of the shutter.
- FIG. 4 described above is a hysteresis curve of the magnetic thin film obtained in Example 1, and FIG. 5 is a high-frequency characteristic of the magnetic thin film.
- FIG. 5 is a high-frequency characteristic of the magnetic thin film.
- the resonance frequency exceeded the measurement limit of 3 GHz, and the value of the real part (1) of the permeability was 1.
- a value of 80 was obtained at OGHz. .
- the specific resistance was 180 ⁇ cm.
- the high-frequency magnetic permeability was measured using an ultrahigh-frequency band magnetic permeability measurement device (Ryowa Electronics, PMF-3000), and the magnetic properties were measured using a vibrating sample magnetometer (RIKEN ELECTRONICS, BHV-35).
- Example 2 Based on the film forming method of Example 1 described above, 2.3 nm thick CoZrNb and 1. Onm natural oxidized layer were alternately formed 121 times in order to obtain a total film thickness of 400 nm (corresponding to a total of 242 layers). A magnetic thin film (Example 2) was formed. At this time, the ratio of the natural oxide layer to the total volume of the multilayer film was 30%.
- Table 1 shows the magnetic properties of the obtained magnetic thin film.
- a value of 40 was obtained at 1. OGHz as the value of the real part 1) of the magnetic permeability, and the specific resistance was 860 ⁇ cm.
- m native oxide layer was formed.
- a 1.6 nm thick CoZrNb layer and a 1.3 nm natural oxide layer were alternately formed 138 times alternately to form a magnetic thin film having a total film thickness of 400 nm (corresponding to a total of 276 layers) (Example 3).
- the ratio of the natural oxide layer to the total volume of the multilayer film was 45%.
- Table 1 shows the magnetic properties of the obtained magnetic thin film.
- the value of the real part ( ⁇ 1) of the magnetic permeability is: 1.
- a value of 25 is obtained at OGHz, and the specific resistance is 1416 Qcm.
- Example 1 Based on the film forming method of Example 1 described above, a single layer of a CoZrNb film having a thickness of 500 / zm was formed, and a magnetic thin film of Comparative Example 1 was formed.
- Example 1-3-1 is smaller than 1 of Comparative Example.
- the example seems to have worse characteristics.
- the imaginary part 2 represents the loss, and the smaller the imaginary part, the larger the Q value.
- a large Q value means a small loss. That is, in the example, the loss at 1 GHz is reduced as compared with the comparative example, and it can be seen that the characteristics are remarkably improved.
- FIG. 10 shows the results of an experiment for confirming the magnetization reversal phenomenon.
- the sample was rotated in the in-plane direction using a vibrating sample magnetometer (RIKEN ELECTRONICS, BHV-35) (angle deviation with respect to the direction of the applied magnetic field during film formation is shown on the horizontal axis as ⁇ ).
- the residual magnetism Mr
- the value was standardized with the saturation magnetization (Ms) and the value was plotted on the vertical axis.
- Ms saturation magnetization
- the direction of application of the magnetic field during film formation is orthogonal to the direction of the easy axis of the obtained magnetic thin film (see FIG. 4). What is the direction of the applied magnetic field during film formation and the easy axis of the magnetic thin film obtained?
- the present invention has been described with reference to some embodiments and examples.
- the present invention is not limited to these embodiments and examples, and various modifications are possible.
- the Co-based amorphous alloy is not limited to the materials and compositions described in the above embodiments and examples.
- the oxidized layer of the Co-based amorphous alloy in the present invention is not limited to the natural oxide layer 3, and may be an oxide film generated by a forced oxidation treatment such as thermal oxidation.
- the application of the high-frequency magnetic thin film is not limited to a high-frequency planar magnetic element such as a thin-film inductor or a thin-film transformer, or a device such as an MMIC, but can be applied to other devices.
Abstract
Description
Claims
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US10/573,801 US20070202359A1 (en) | 2003-09-30 | 2004-09-30 | Magnetic Thin Film For High Frequency, and Method of Manufacturing Same, and Magnetic Device |
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JP2003342470A JP2005109246A (ja) | 2003-09-30 | 2003-09-30 | 高周波用磁性薄膜、その作製方法及び磁気素子 |
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JP (1) | JP2005109246A (ja) |
KR (1) | KR100742555B1 (ja) |
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US9812448B2 (en) | 2014-12-17 | 2017-11-07 | Samsung Electronics Co., Ltd. | Semiconductor devices and methods for fabricating the same |
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JP5156939B2 (ja) * | 2006-02-06 | 2013-03-06 | 国立大学法人 名古屋工業大学 | 高周波軟磁性体膜の製造方法 |
EP2915212A4 (en) * | 2012-11-01 | 2016-07-20 | Indian Inst Scient | INTEGRATED HIGH FREQUENCY FACILITY WITH IMPROVED INDUCTIVITY AND METHOD THEREFOR |
KR102479826B1 (ko) * | 2016-07-07 | 2022-12-21 | 주식회사 위츠 | 자성체 시트 및 전자기기 |
CN107907145A (zh) * | 2017-11-06 | 2018-04-13 | 上海交通大学 | 低噪声平面磁传感器 |
EP3886126A4 (en) * | 2018-12-17 | 2021-12-22 | Huawei Technologies Co., Ltd. | THIN FILM COIL AND MANUFACTURING PROCESS FOR IT, INTEGRATED CIRCUIT AND TERMINAL DEVICE |
CN113996793B (zh) * | 2021-10-15 | 2023-08-04 | 中国航发北京航空材料研究院 | 一种高熵非晶微叠层复合材料及其制备方法 |
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JPH0547555A (ja) * | 1991-08-19 | 1993-02-26 | Amorphous Denshi Device Kenkyusho:Kk | 非晶質軟磁性多層薄膜及びその製造方法 |
JP2000054083A (ja) * | 1998-08-07 | 2000-02-22 | Alps Electric Co Ltd | 軟磁性多層膜とこの軟磁性多層膜を用いた平面型磁気素子、フィルタ、及び薄膜磁気ヘッド、ならびに前記軟磁性多層膜の製造方法 |
JP2000252121A (ja) * | 1999-02-26 | 2000-09-14 | Alps Electric Co Ltd | 高周波用Co基金属アモルファス磁性膜とそれを用いた磁気素子、インダクタ、トランス |
WO2003060933A1 (fr) * | 2002-01-16 | 2003-07-24 | Tdk Corporation | Film mince magnetique haute frequence, film mince magnetique composite et dispositif magnetique l'utilisant |
-
2003
- 2003-09-30 JP JP2003342470A patent/JP2005109246A/ja not_active Withdrawn
-
2004
- 2004-09-30 US US10/573,801 patent/US20070202359A1/en not_active Abandoned
- 2004-09-30 WO PCT/JP2004/014405 patent/WO2005031762A2/ja active Application Filing
- 2004-09-30 KR KR1020067005910A patent/KR100742555B1/ko not_active IP Right Cessation
- 2004-09-30 CN CNA2004800283931A patent/CN1860561A/zh active Pending
Patent Citations (4)
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JPH0547555A (ja) * | 1991-08-19 | 1993-02-26 | Amorphous Denshi Device Kenkyusho:Kk | 非晶質軟磁性多層薄膜及びその製造方法 |
JP2000054083A (ja) * | 1998-08-07 | 2000-02-22 | Alps Electric Co Ltd | 軟磁性多層膜とこの軟磁性多層膜を用いた平面型磁気素子、フィルタ、及び薄膜磁気ヘッド、ならびに前記軟磁性多層膜の製造方法 |
JP2000252121A (ja) * | 1999-02-26 | 2000-09-14 | Alps Electric Co Ltd | 高周波用Co基金属アモルファス磁性膜とそれを用いた磁気素子、インダクタ、トランス |
WO2003060933A1 (fr) * | 2002-01-16 | 2003-07-24 | Tdk Corporation | Film mince magnetique haute frequence, film mince magnetique composite et dispositif magnetique l'utilisant |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US9812448B2 (en) | 2014-12-17 | 2017-11-07 | Samsung Electronics Co., Ltd. | Semiconductor devices and methods for fabricating the same |
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CN1860561A (zh) | 2006-11-08 |
JP2005109246A (ja) | 2005-04-21 |
KR20060054471A (ko) | 2006-05-22 |
US20070202359A1 (en) | 2007-08-30 |
WO2005031762A3 (ja) | 2005-06-30 |
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