Patent Grant
10490347
This application in the U.S. National Phase of International Application No. PCT/EP2014/067852, filed Aug. 21, 2014, designating the U.S. and claiming priority to French Application No. 13 58177, filed Aug. 26, 2013. Any and all applications for which a foreign or domestic priority claim is identified here or in the Application Data Sheet as filed with the present application are hereby incorporated by reference under 37 CFR 1.57.
The present invention relates to a method for producing monolithic electromagnetic components.
More specifically, the invention relates to a method for producing a monolithic electromagnetic component comprising several elements including a magnetic core of spinel ferrite and at least one planar coil comprising several turns.
Recent research in power electronics has focused on the miniaturization of converters and electronic components that they comprise, in particular decreasing the size of the active and passive components.
In this context, there is a need for monolithic components able to be integrated as closely as possible with semiconductors and to transfer increasingly significant power densities, i.e., to work at a higher frequency and discharge heat more effectively.
In a known manner, some spinel ferrites are used to manufacture this type of component by conventional sintering at temperatures of approximately 950° C. The ferrites obtained then have good performance levels up to several hundred megahertz, owing to a high resistivity.
However, producing monolithic electronic components from these ferrites using the known methods is only possible with coils made up of noble metals such as silver or palladium, which makes it expensive to produce large quantities of these power components. Furthermore, the known manufacturing methods involve many separate steps carried out on separate premises, and sometimes cause delamination, cracks in the materials or diffusions of material at the interfaces between the metal and the oxides.
One aim of the present invention is to propose a method for producing a monolithic electromagnetic component that does not have these drawbacks.
To that end, the invention relates to a method of the aforementioned type, characterized in that it comprises the following series of steps:
According to other embodiments, the method according to the invention comprises one or more of the features below, considered alone or according to any technically possible combination(s):
The invention further relates to a monolithic electromagnetic component, characterized in that it can be produced using a production method as defined above.
According to other embodiments, the component according to the invention comprises one or more of the features below, considered alone or according to any technically possible combinations(s):
The invention will be better understood upon reading the following detailed description, done solely for information and non-limitingly, and in reference to the appended drawings, in which:
In reference to
In the example of
“Can be produced” means that the production method according to the invention and as described below makes it possible to obtain a component according to the invention, but it is not ruled out that another production method may exist or be discovered in the future that could also make it possible to obtain such a component.
The base 12 constitutes the most voluminous structure of the component 10 and gives it its general appearance.
The base 12 has a general cylindrical shape with longitudinal axis X-X′, height h and diameter d.
In the example of
Alternatively, the diameter d is comprised between 5 and 50 mm, and the height h is comprised between 1 and 20 mm.
The base 12 has a high resistivity.
The base 12 is made from a spinel ferrite. Spinels are ferrites with the following general formula (G): AB2−δO4, where A has mean valence 2 and is an element or a combination of elements from the group of cations preferably formed by Mg2+, Ni2+, Co2+, Zn2+, V2+, Ti2+, Sc2+, Mn2+ and optionally Fe2+, where B has mean valence 3 and is an element or combination of elements from the group of cations preferably formed by Fe3+ and Al3+, and where δ represents a potential material flaw. The material flaw δ can be introduced deliberately and is for example comprised between 0 and 0.05. Furthermore, spinel ferrites have the crystallographic structure of the reference compound MgAl2O4.
Preferably, the spinel ferrite of the component 10 has a composition with the following formula (1):
NixZn1−x−y−ϵ+δCuyCoϵFe2−δO)4, with 0.15≤x≤0.6; 0<y≤0.2; 0≤ϵ≤0.1 and 0≤δ≤0.05.
It has thus been observed that the components 10 whereof the ferrite of the base 12 had formula (1) had good results in terms of magnetic performance (low losses) in the frequency band between 300 kHz and 3 MHz in particular and densification during sintering at a low temperature (below 1000° C.).
As will be seen below, the ferrite 12 is obtained by densification of the mixture of nanometric oxides or by successive grinding and calcination of the mixture of nanometric oxides, the calcination being done at a temperature comprised between 600° C. and 1100° C.
For the components whereof the ferrite obeys formula (1), the nanometric oxides are zinc oxide ZnO, copper oxide CuO, nickel oxide NiO, cobalt oxide Co3O4 and iron oxide Fe2O3, the mixture also having a composition obeying formula (1).
Nanometric means that the particle size of the oxides can vary from several nanometers to several micrometers (approximately 5 μm at most). The particle size is then determined as a function of the frequency at which the component 10 is designed to operate.
In the example of
The coil 14 is able to allow the proper circulation of the electrical currents through it and to be secured to the ferrite of the base 12 by co-sintering.
Preferably, the coil 14 is made from copper.
Alternatively, it is made from a noble metal such as silver Ag or palladium Pd, or an alloy of palladium Pd, or an alloy of Palladium Pd and silver Ag.
The coil 14 is at least partially embedded in the ferrite of the base 12.
Still in reference to
In the example of
Alternatively (not shown), the turns have a general square spiral shape.
The coil 14 also comprises an inner tab 18 and an outer tab 19, which make up bent ends of the inner turn 161 and outer turn 162, respectively.
The coil also has a non-zero thickness e, is substantially planar and is orthogonal to the axis X-X′, such that the coil 14 is substantially comprised in a discoid edge T of the base 12, orthogonal to the axis X-X′ and with thickness e.
The inner 161 and outer 162 turns respectively define an inner discoid portion 20 and an outer discoid portion 22 with thickness e of the edge T and the component 10.
Furthermore, two successive turns 16 of the coil 14 define a radial interstice 24.
In reference to
Only the upper and lower parts of the turns 16 of the coil 14 are in contact with the ferrite.
This embodiment advantageously makes it possible to limit the stray capacitances that may appear between the turns 16 during the operation of the component 10 via the electrical insulation resulting from the presence of the dielectric material 15.
In reference to
This embodiment is advantageously used in order to limit the stray capacitances that may appear between the turns 16 during the operation of the component 10, while minimizing the quantity of dielectric material 15 used.
In reference to
This alternative is advantageously used when the frequency at which the component 10 is designed to operate is less than 10 MHz. Past this value, it is preferable to add dielectric material 15.
In reference to
The inner 18 and outer 19 tabs are able to allow the connection of the component 10 to other elements, for example to an electronic device in which it is integrated.
To that end, the inner 18 and outer 19 tabs are bent relative to the inner turn 161 and the outer turn 162, respectively.
The inner tab 18 is oriented along the axis X-X′ and has a length such that it is flush with the upper surface of the component 10.
The outer tab 19 is oriented radially and has a length such that it is flush with the lateral surface of the component 10.
Alternatively, both tabs 18, 19 are oriented along the axis X-X′ and are flush with the upper and/or lower surface of the component 10.
The tabs 18, 19 are designed to be placed in contact with an electrically conductive cable (not shown), for example directly or via a metal lacquer attached to the component 10 that makes it possible to facilitate the placement of the cable in contact with the tabs 18, 19.
The second coil 14B is at least partially embedded in the ferrite of the base 12.
The second coil 14B is substantially comprised in a discoid edge TB of the component 10 parallel to the edge T and spaced away therefrom, such that the two sections T and TB define a layer C between them with thickness c of the component 10.
In the example of
Alternatively, the second coil 14B has a number of turns different from the number of turns of the coil 14. This alternative is advantageously implemented to modify the behavior of the coils 14, 14B with similar operating conditions.
In the example of
In this alternative, during the operation of the component 10, the current entering one of the coils 14, 14B results in a current leaving through the other coil and magnetically induced therein.
The value of c is then predetermined based on criteria known by those skilled in the art, such as the desired value of the inductance of the coils, the mutual inductance and the coupling coefficient between the coils.
Thus, the value of c is comprised between 100μm and 1 mm.
When the component 10 is a transformer, a value of c close to 100μm is preferable. Conversely, when the component 10 is a magnetic coupler, a value of c close to 1 mm is preferable.
In the example of
In the example of
This embodiment is advantageously implemented in order to limit the stray capacitances that may appear between the respective turns 16 of the two coils 14, 14B during the operation of the component 10, or when it is desirable to modify the topology of the magnetic field of each of the turns 161.
In the embodiment of
This embodiment is advantageously implemented so as to optimize the coupling between the coils, for example when the component 10 is a magnetic coupler, and to limit the leakage fields that may appear during the operation of the component 10.
In the embodiment of
This embodiment is advantageously used when it is desirable not to alter the magnetic field resulting from the circulation of the current in each of the turns 161.
Alternatively (not shown), in addition to the elements already described in the embodiments of
Two successive metal layers are then separated by a layer at least partially filled with dielectric material 15.
The manufacturing method 30 according to the invention for producing the component 10 made from a ferrite with general composition (G), and preferably with composition (1), will now be described in reference to
First, during an initial step 110, a precursor 32 of the ferrite is obtained that will make up the base 12 of the component 10.
The precursor 32 is a ferrite powder obtained by alternating successive grinding and calcination operations of a mixture of nanometric oxides, said calcination being done at a temperature substantially comprised between 600° C. and 1100° C., preferably substantially equal to 760° C.
For a ferrite with composition (1), the precursor 32 is a ferrite powder obtained by alternating successive grinding and calcination operations of a mixture of nanometric oxides of zinc ZnO, copper CuO, nickel NiO, cobalt Co3O4 and iron Fe2O3, said calcination being done at a temperature substantially comprised between 600° C. and 1100° C., and preferably substantially equal to 760°.
The grinding operations are intended to decrease the diameter of the oxides, and thus to decrease the sintering temperature of the obtained ferrite powder.
The calcination operations are intended to form the spinel phase of the ferrite, i.e., to transform the basic oxide mixture into a single phase with a spinel structure.
A phase refers to a crystallographic structure.
During the grinding operations, undesirable iron additions may occur or be done through the tools used, such as steel beads.
The initial step 110 then comprises compensating these unwanted additions in the obtained mixture, for example by forming an excess of iron oxide of approximately 5%, for instance.
In some embodiments where the iron flaw δ is not zero, the initial step 110 also comprises suppressing the corresponding quantity of iron of the precursor 32. This makes it possible to ensure the absence of Fe2 + that could appear following a slight reduction during sintering (related to the presence of carbon) or an addition of iron during grinding. It should be noted that the presence of Fe2 + must be avoided because it greatly increases the conductivity of the ferrite, which would produce additional losses by Foucault currents during the operation of the component. Consequently, preferably, the element A of the general formula of the ferrite is not iron or does not contain iron.
At the end of this initial step 110, the obtained precursor 32 is a ferrite powder whose composition obeys general formula (G), preferably formula (1), and the spinel phase of which is formed.
During a following preparation step 120, the elements of the component, including the coil(s) 14 and other than the ferrite, are embedded in the precursor 32 of the ferrite in a mold 34.
The progression therefore varies slightly depending on the structure of the component 10 one wishes to obtain.
More specifically, in reference to
For a component with a single coil 14 comprising dielectric material 15, after having deposited the coil 14 on the first layer 36 of precursor 32, the dielectric material 15 is deposited on the coil 14 and the first layer 36, with the exception of at least the locations of the turns 16 of the coil 14, so as to form the desired structure of the edge T (
For a component 10 comprising two coils 14, 14B and dielectric material 15, after the first layer 36, a layer of dielectric material 15 is deposited so as to form the desired structure of the edge T and the layer C, then the second coil 14B is deposited. A second layer of dielectric material is next deposited with a thickness substantially equal to e with the exception of at least the locations of the turns 16 of the second coil 14B, so as to form the desired structure of the edge TB. The second layer 38 of precursor 32 is deposited last.
For a component 10 with two coils 14, 14B not comprising dielectric material, during step 120, the deposition of the layers of dielectric material 15 described above is then replaced by the deposition of precursor layers 32.
This preparation step 120 is preferably done in a controlled environment, for example a sealed hood, which result in limiting the presence of stray particles that may become deposited in the mold and thus decrease the quality of the obtained component 10.
This step 120 is for example done manually, or automatically using any appropriate device.
The mold 34 is preferably made from graphite. Alternatively, it is made from metal or a refractory metal alloy, or electrically conductive ceramic.
Following this preparation step 120, during a co-sintering step 130, the precursor 32 is secured to the ferrite with the other elements of the component 10 by co-sintering under a load by a pulsed electric current. “Under a load” means that the elements of the component are subjected to a force, in particular an axial force tending to compress the components 10.
During a compression step 131 of this co-sintering step 130, the mold 34 obtained by the preparation step 120 is placed under a neutral gas, and it is subjected to a uniaxial pressure comprised between 50 and 100 MPa. This pressure is shown by arrows in
Alternatively, the mold 34 is placed under vacuum or under oxygen.
Next, during a discharge step 132 of this step 130 and which corresponds to co-sintering by pulsed electric current strictly speaking, an electric current is discharged through the mold 34 with a controlled intensity i comprised between 1 A and 20,000 A, and preferably between 1 A and 1,000 A or between 1 and 10 A per square millimeter of component surface. This makes it possible to raise the temperature in the mold 34 and to secure the elements of the component 10 to one another. The temperature inside the mold 34 is controlled by checking the intensity of the current.
The discharge step 132 comprises a co-sintering plateau, during which the temperature inside the mold 34 is kept between 650° C. and 850° C., and preferably between 700° C. and 800° C. The co-sintering plateau has a length comprised between 1 min. and 30 min.
The progression of the discharge step 132 is as follows. The temperature is initially brought to a speed of approximately 100° K per minute, from the ambient temperature, to a value comprised between the above values. The co-sintering plateau is then done. Next, the temperature inside the mold 34 is quickly decreased by interrupting the current. As previously indicated, the uniaxial pressure resulting from the compression step is maintained during the discharge step 132.
The average duration of the discharge step 132 is comprised between 10 min. and 60 min., and advantageously is substantially equal to 20 minutes.
This discharge step 132 is preferably done automatically, via a programmable device suitable for checking the temperature in the mold 34, such that the temperature in the mold 34 is quickly brought to a setpoint temperature and kept at that temperature during the sintering plateaus.
Alternatively, the precursor 32 obtained at the end of the initial step 110 is a mixture of nanometric oxides corresponding to general formula (G), preferably to formula (1), and the spinel phase of which is not formed.
In order to obtain this precursor 32, during the initial step 110, the different oxides are weighed, then mixed, then the obtained mixture is ground order to mix these oxides and decrease their diameter. As before, the iron contribution due to the grinding tools must then be compensated. No calcination occurs during this step, unlike the previously described embodiments.
The following steps of the method 30 remain the same, with the exception of the discharge phase 132 during which a first reaction plateau is observed. The function of the first reaction plateau is to carry out the formation of the spinel phase of the precursor 32. This first reaction plateau is done at a temperature comprised between 400° C. and 600° C. The first reaction plateau is prior to the co-sintering plateau.
The method 30 according to this alternative is called reactive sintering, during which the mixture of ground oxides transforms into a spinel phase during the discharge phase 130, unlike the method 30 described above, which is called direct sintering and in which the precursor 32 is a ground and calcinated ferrite powder and the spinel phase of which is already formed at the end of the initial step 110.
This alternative of the method 30 has several advantages:
Alternatively (not shown), during the initial step 110, the precursor 32 with general formula (G), preferably formula (1), is obtained chemically, the initial steps 110 of the direct and reactive sintering methods described above corresponding to so-called solid methods. This alternative makes it possible to obtain a ferrite with a more homogenous composition and having a closer particle size distribution than by using the solid method.
The precursor 32 obtained through the chemical method is then a ferrite powder with general composition (G) whereof the grains are mixed spinel particles. For a ferrite powder with formula (1), the simple spinel particles are for example Fe3O4, NiFe2O4, CoFe2O4 or particles with a more complex composition, for example with composition (1).
The initial step 110 according to the chemical method is then done using one of the three following protocols:
Based on the reaction conditions and the selected synthesis protocol, the precursor of the precursor 32 obtained at the end of the protocol may not have a formed spinel phase, or have a partially formed spinel phase.
In this case, the initial step 110 comprises an additional calcination phase seeking to form the spinel phase of the precursor 32, such that the precursor 32 obtained at the end of step 110 has a formed spinel phase.
Also alternatively, during the initial step 110, the precursor 32 is obtained by the so-called “polyol” route, during which simple acetate, nitrate and chloride compounds are dissolved in liquid polyols, such as 1,2-propane diol, 1,2-ethane diol and bis(2-hydroxy ethyl) ether. Due to their relatively high dielectric constant, which allows them to dissolve inorganic solids, these polyols constitute mediums favorable to obtaining various inorganic materials: metals, hydroxides and oxides. Complexes comprising alkoxy groups then form, from which oxides and hydroxides are obtained by hydrolysis and polymerization.
The competition between these reactions can be checked by regulating the hydrolysis rate and the reaction temperature. Checking the germination and growth steps makes it possible to obtain nanometric, sub-micronic and micronic particles having optimized properties from which the precursor 32 is obtained.
As before, based on the conditions for carrying out the initial step 110 by the polyol method, the precursor of the obtained precursor 32 may not have a formed spinel phase, or may have a partially formed spinel phase.
In this case, the initial step 110 comprises an additional calcination phase seeking to form the spinel phase of the precursor 32, such that the precursor 32 obtained at the end of step 110 has a formed spinel phase.
In summary, the precursor 32 with general formula (G), preferably formula (1), obtained at the end of the initial step 110 is:
The Applicant has implemented the method 30 described above successfully and obtained, inter alia, an example component 10 whereof the ferrite with composition Ni0.195Cu0.2Zn0.5999Co0.006Fe2O4 was co-sintered with a copper coil 14 by direct sintering under a uniaxial pressure of 50 MPa, under argon, and at a temperature between 650° C. and 800° C.
The component 10 that was obtained has a magnetic moment at saturation equal to 54 A·m2/kg and a relative density greater than 90%.
The method 30 according to the invention makes it possible to perform the co-sintering of ferrites with metals other than noble metals, such as silver Ag or Palladium Pd. In particular, it makes it possible to produce monolithic components having one or more coils made from copper, which the known methods do not allow.
Indeed, the conventional sintering methods require the prolonged exposure, for durations sometimes up to several days, of the elements of the component to temperatures relatively close to the melting temperature of copper.
This results in causing diffusions of the copper in the ferrite, which damages the obtained compositions or even makes them unusable.
The components obtained using the method according to the invention are therefore less expensive.
Furthermore, because it has only a small number of steps, the method 30 decreases the risks of occurrence of a manipulation error of the elements of the material, or damage to them during transportation between the premises where they respectively take place, such that the method according to the invention is globally safer and less expensive than the known methods for producing this type of electronic components.
Furthermore, the method according to the invention does not have any particular susceptibility to the dimensions of the desired components, unlike the methods such as the so-called LTCC (Low Temperature Cofired Ceramic) method, which can only produce small components (maximum 10 mm in diameter and 2 mm thick, with larger dimensions resulting in delamination and cracks), such that the only limitations of the method 30 are due to the limitations intrinsic to the materials used.
The components 10 obtained using such a method 30 are not subject to any oversizing required by any limitations related to their production method, and have a compactness of 100%.
Furthermore, the obtained electromagnetic components have a closed magnetic structure that completely confines the magnetic flow and prevents these components from radiating and interfering with the adjacent components, such that the integration of the components 10 obtained using the method 30 is made easier.
Conversely, a method like LTCC, which only makes it possible to produce small components, makes it very difficult to manufacture components with a confined magnetic flow, the obtained components proving complex to integrate.
In reference to
In reference to
In reference to
One can see good mechanical strength of the co-sintered part and a regular interface between the different materials. The copper remains well confined between the dielectric and ferrite layers. Furthermore, there are none of the elements of the dielectric in the layer of copper and conversely, there is no copper in the dielectric. This indicates that there has not been any diffusion between the various elements of each layer on the micron scale.
In reference to
A component 10 according to the invention comprising a single coil 14 is for example an inductance intended to be used in a filtering device.
A component 10 according to the invention comprising two coils 14, 14B is for example a transformer or magnetic coupler.
| Number | Date | Country | Kind |
|---|---|---|---|
| 13 58177 | Aug 2013 | FR | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2014/067852 | 8/21/2014 | WO | 00 |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2015/028389 | 3/5/2015 | WO | A |
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| 2010-177319 | Aug 2010 | JP |
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| Number | Date | Country | |
|---|---|---|---|
| 20160203908 A1 | Jul 2016 | US |
