WO2021124955A1 - 振動板接合体 - Google Patents
振動板接合体 Download PDFInfo
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- WO2021124955A1 WO2021124955A1 PCT/JP2020/045500 JP2020045500W WO2021124955A1 WO 2021124955 A1 WO2021124955 A1 WO 2021124955A1 JP 2020045500 W JP2020045500 W JP 2020045500W WO 2021124955 A1 WO2021124955 A1 WO 2021124955A1
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- diaphragm
- joint
- ceramic plate
- rigidity
- rigidity ceramic
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- KZHJGOXRZJKJNY-UHFFFAOYSA-N dioxosilane;oxo(oxoalumanyloxy)alumane Chemical compound O=[Si]=O.O=[Si]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O KZHJGOXRZJKJNY-UHFFFAOYSA-N 0.000 claims description 3
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- JSKIRARMQDRGJZ-UHFFFAOYSA-N dimagnesium dioxido-bis[(1-oxido-3-oxo-2,4,6,8,9-pentaoxa-1,3-disila-5,7-dialuminabicyclo[3.3.1]nonan-7-yl)oxy]silane Chemical compound [Mg++].[Mg++].[O-][Si]([O-])(O[Al]1O[Al]2O[Si](=O)O[Si]([O-])(O1)O2)O[Al]1O[Al]2O[Si](=O)O[Si]([O-])(O1)O2 JSKIRARMQDRGJZ-UHFFFAOYSA-N 0.000 claims 2
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- G02B27/00—Optical systems or apparatus not provided for by any of the groups G02B1/00 - G02B26/00, G02B30/00
- G02B27/01—Head-up displays
- G02B27/0101—Head-up displays characterised by optical features
-
- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N30/00—Piezoelectric or electrostrictive devices
- H10N30/20—Piezoelectric or electrostrictive devices with electrical input and mechanical output, e.g. functioning as actuators or vibrators
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B37/00—Joining burned ceramic articles with other burned ceramic articles or other articles by heating
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- G—PHYSICS
- G02—OPTICS
- G02B—OPTICAL ELEMENTS, SYSTEMS OR APPARATUS
- G02B26/00—Optical devices or arrangements for the control of light using movable or deformable optical elements
- G02B26/08—Optical devices or arrangements for the control of light using movable or deformable optical elements for controlling the direction of light
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- G—PHYSICS
- G02—OPTICS
- G02B—OPTICAL ELEMENTS, SYSTEMS OR APPARATUS
- G02B26/00—Optical devices or arrangements for the control of light using movable or deformable optical elements
- G02B26/08—Optical devices or arrangements for the control of light using movable or deformable optical elements for controlling the direction of light
- G02B26/10—Scanning systems
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- G—PHYSICS
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-
- H—ELECTRICITY
- H03—ELECTRONIC CIRCUITRY
- H03H—IMPEDANCE NETWORKS, e.g. RESONANT CIRCUITS; RESONATORS
- H03H9/00—Networks comprising electromechanical or electro-acoustic devices; Electromechanical resonators
- H03H9/25—Constructional features of resonators using surface acoustic waves
-
- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N30/00—Piezoelectric or electrostrictive devices
- H10N30/01—Manufacture or treatment
- H10N30/07—Forming of piezoelectric or electrostrictive parts or bodies on an electrical element or another base
- H10N30/072—Forming of piezoelectric or electrostrictive parts or bodies on an electrical element or another base by laminating or bonding of piezoelectric or electrostrictive bodies
-
- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N30/00—Piezoelectric or electrostrictive devices
- H10N30/80—Constructional details
- H10N30/85—Piezoelectric or electrostrictive active materials
- H10N30/853—Ceramic compositions
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- C—CHEMISTRY; METALLURGY
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- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/02—Aspects relating to interlayers, e.g. used to join ceramic articles with other articles by heating
- C04B2237/16—Silicon interlayers
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/30—Composition of layers of ceramic laminates or of ceramic or metallic articles to be joined by heating, e.g. Si substrates
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/30—Composition of layers of ceramic laminates or of ceramic or metallic articles to be joined by heating, e.g. Si substrates
- C04B2237/32—Ceramic
- C04B2237/36—Non-oxidic
- C04B2237/366—Aluminium nitride
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/50—Processing aspects relating to ceramic laminates or to the joining of ceramic articles with other articles by heating
- C04B2237/52—Pre-treatment of the joining surfaces, e.g. cleaning, machining
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- G—PHYSICS
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- G02B27/01—Head-up displays
- G02B27/0101—Head-up displays characterised by optical features
- G02B2027/0123—Head-up displays characterised by optical features comprising devices increasing the field of view
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- G—PHYSICS
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- G02B—OPTICAL ELEMENTS, SYSTEMS OR APPARATUS
- G02B26/00—Optical devices or arrangements for the control of light using movable or deformable optical elements
- G02B26/08—Optical devices or arrangements for the control of light using movable or deformable optical elements for controlling the direction of light
- G02B26/0816—Optical devices or arrangements for the control of light using movable or deformable optical elements for controlling the direction of light by means of one or more reflecting elements
- G02B26/0833—Optical devices or arrangements for the control of light using movable or deformable optical elements for controlling the direction of light by means of one or more reflecting elements the reflecting element being a micromechanical device, e.g. a MEMS mirror, DMD
- G02B26/0858—Optical devices or arrangements for the control of light using movable or deformable optical elements for controlling the direction of light by means of one or more reflecting elements the reflecting element being a micromechanical device, e.g. a MEMS mirror, DMD the reflecting means being moved or deformed by piezoelectric means
Definitions
- the present invention relates to a bonded body formed by bonding a high-rigidity ceramic diaphragm that can be used for a MEMS (Micro Electro Mechanical System) mirror or the like to a support substrate.
- MEMS Micro Electro Mechanical System
- a head-up display is a "device that displays necessary information overlapping the field of view while keeping the line of sight forward.”
- the information can be visually recognized while keeping the line of sight forward, which is effective in preventing sideways driving and also reduces the focus movement of the eyes. This can reduce driver fatigue and improve safety.
- HUD The principle of HUD will be described. Images from fluorescent tubes, CRTs and LCDs are projected on the windshield of a car or a transparent screen (combiner).
- the HUD has the following two methods depending on the difference in optical structure. (1) Direct Projection method that directly projects an image using the windshield as a screen (2) Virtual Imaging method that acts as a reflection mirror on the windshield and forms an image on the driver's retina.
- the big difference between these methods is the sense of distance when the driver sees the image.
- the Direct Projection method recognizes the image on the screen (combiner) like a normal projector, but the Virtual Imaging method recognizes the image in the space several meters away from the driver's line of sight.
- the driver's front view and the line-of-sight movement between the instrument panel and console panel are significantly reduced.
- the focus shift from the field of view during normal driving is small, so that the driver can concentrate more attention on driving and less fatigue.
- the Virtual Imaging method the development of a new method for scanning and drawing a laser beam has been progressing in recent years.
- a laser beam of three RGB colors is combined by an optical element called a combiner, and this one beam is reflected by a minute mirror and scanned in two dimensions to perform drawing. Similar to CRT electron beam scanning, but instead of exciting the phosphor, it controls the pulse width and output of each laser at the position corresponding to the pixel on its horizontal scanning line to change the color and brightness, and points the pixel at high speed. draw.
- the achievable resolution depends on the vibration frequency of the mirror and the modulation frequency of the laser.
- the main advantages of this method are as follows. (1) Since the number of parts is small, miniaturization, cost reduction, and reliability improvement can be realized. (2) Since the laser is turned on with the brightness required for each pixel, low power consumption can be realized. (3) Since the collimated (parallel light) laser light is used, focus adjustment becomes unnecessary.
- the micro mirror which is the core component of the laser scanning display, processes Si with MEMS (Micro Electro Mechanical System) technology and deposits metal.
- Mirror driving methods include an electrostatic method driven by an electrostatic attraction, an electromagnetic method driven by an electromagnetic force, and a piezoelectric method driven by a piezoelectric element.
- the advantages of the piezoelectric method include high-speed driving, low power consumption, and large driving force, and the disadvantages are that it is difficult to form a piezoelectric element.
- Patent Document 1 a MEMS mirror using an SOI substrate has been proposed.
- JP 2012-037578 Japanese Patent Application Laid-Open No. 2014-086400
- the HUD will be required to have a larger screen and a wider angle of view, and there is also a request to increase the angle of view up to 20 degrees from the current angle of view of 7 to 8 degrees.
- it is necessary to improve the frequency, amplitude and reliability of the piezoelectric element of the MEMS mirror. In particular, improvements in scan width and speed are required. However, this cannot be realized by the piezoelectric element formed by film formation on the conventional Si substrate.
- a high-rigidity ceramic plate as the diaphragm used under the piezoelectric layer.
- the thickness of the high-rigidity ceramic plate is 100 ⁇ m or less, the mechanical strength is insufficient. Therefore, after joining the high-rigidity ceramic plate to the support substrate to obtain a bonded body, it was examined to polish the high-rigidity ceramic plate to a thickness of 100 ⁇ m or less.
- An object of the present invention is a joint body of a diaphragm made of high-rigidity ceramics having a thickness of 100 ⁇ m or less and a support substrate, which has a structure capable of preventing the diaphragm from peeling or cracking while maintaining the strength of the diaphragm. Is to provide.
- the diaphragm joint according to the present invention is Support substrate made of silicon, It is provided with a diaphragm made of high-rigidity ceramics having a thickness of 100 ⁇ m or less, and a joint layer made of ⁇ -Si, which is located between the support substrate and the diaphragm and is in contact with the joint surface of the diaphragm.
- the arithmetic average roughness Ra of the joint surface of the diaphragm is 0.01 nm or more and 10.0 nm or less, and the pit density of the joint surface of the diaphragm is 10 or more per 100 ⁇ m 2. ..
- the present invention is a step of providing a bonding layer made of ⁇ -Si on the surface of a high-rigidity ceramic plate made of high-rigidity ceramics.
- the diaphragm comprises a step of joining the joining surface of the joining layer and the joining surface of the support substrate made of silicon, and then a step of obtaining a diaphragm having a thickness of 100 ⁇ m or less by processing the high-rigidity ceramic plate.
- the surface of the high-rigidity ceramic plate has an arithmetic mean roughness Ra of 0.01 nm or more and 10.0 nm or less, and the surface of the high-rigidity ceramic plate has a pit density of 10 or more per 100 ⁇ m 2. And.
- a bulk-shaped high-rigidity ceramic plate is directly bonded to a support substrate made of silicon, it cannot withstand the polishing process when polishing the high-rigidity ceramic plate to a thickness of 100 ⁇ m or less, and the high-rigidity ceramic plate is peeled or cracked. Occurs. Therefore, the present inventor has attempted to provide an ⁇ -Si bonding layer on a bulk-shaped high-rigidity ceramic plate and bond the bonding layer to a support substrate made of silicon.
- the reason why the ⁇ -Si bonding layer is provided is that, for example, the cost can be suppressed in the etching process for making the diaphragm a hollow structure.
- the bonding strength between the bonding layer made of ⁇ -Si and the supporting substrate made of silicon is high, and it should be able to withstand the process of polishing the thickness of the high-rigidity ceramic plate to 100 ⁇ m or less.
- the present inventor has attempted to increase the smoothness of the surface of the high-rigidity ceramic plate (the joint surface to which the joint layer should be provided). In some cases, even if the joint surface is smooth. It was found that peeling and cracking are less likely to occur at the interface with the bonding layer during polishing.
- the present inventor further examined a diaphragm joint that exhibited characteristics exceeding such expectations.
- the joint surface of the high-rigidity ceramic plate is a smooth surface with an extremely small arithmetic mean roughness (Ra)
- Ra arithmetic mean roughness
- the arithmetic mean roughness Ra of the joint surface of the diaphragm exceeds 10.0 nm, the bending strength when vibrated as the diaphragm is weak and it cannot withstand high-amplitude, high-frequency vibration. Is an ultra-smooth surface of 10.0 nm or less. Even in this case, it was found that cracking or peeling of the diaphragm during polishing can be prevented by setting the pit density of the joint surface of the diaphragm to 10 or more per 100 ⁇ m 2.
- (A) shows a state in which the bonding layer 2 is provided on the bonding surface 1a of the high-rigidity ceramic plate 1, and (b) shows a state in which the surface 2b of the bonding layer 2 is activated by a neutralized atomic beam.
- (C) shows a state in which the joint surface 3a of the support substrate 3 is activated by the neutralized atomic beam.
- (A) shows the joint body 4 of the high-rigidity ceramic plate 1 and the support substrate 3, and (b) shows the joint body 5 of the diaphragm 1A and the support substrate 3. It is an AFM measurement image which shows the state of the surface pit of the joint surface of a high-rigidity ceramic plate.
- the high-rigidity ceramic plate 1 is prepared.
- the arithmetic average roughness Ra of the surface 1a of the high-rigidity ceramic plate is 0.01 nm or more and 10.0 nm or less, and the pit density on the surface of the high-rigidity ceramic plate is 10 or more per 100 ⁇ m 2.
- Reference numeral 1b is the back surface of the high-rigidity ceramic plate 1.
- a bonding layer 2 made of ⁇ -Si is formed on the surface 1a of the high-rigidity ceramic plate 1.
- the bonding surface 2a of the bonding layer 2 is irradiated with a neutralized atomic beam as shown by arrow A to activate it.
- the joint surface 3a of the support substrate 3 is activated by irradiating the neutralized atomic beam as shown by the arrow B.
- the activated joint surface 2b of the joint layer 2 and the activated joint surface 3a of the support substrate 3 are brought into contact with each other and directly bonded to form the bonded body 4. obtain.
- the thickness of the high-rigidity ceramic plate is reduced by processing the back surface 1b of the high-rigidity ceramic plate 1 of the joint body 4, and the diaphragm 1A having a thickness of 100 ⁇ m or less is formed. By forming, a diaphragm joint 5 is obtained.
- 1c is a machined surface.
- the thickness of the support substrate made of silicon is not particularly limited, but from the viewpoint of maintaining strength during processing, 200 ⁇ m or more is preferable, and 400 ⁇ m or more is more preferable. Further, the arithmetic mean thickness Ra of the joint surface of the support substrate is preferably 1 nm or less, more preferably 0.3 nm or less, from the viewpoint of promoting direct bonding.
- High-rigidity ceramics are defined as ceramic materials with Young's modulus ⁇ 200 GPa and 3-point bending strength ⁇ 300 GPa.
- Sialon, Cordellite, Mullite, translucent alumina, aluminum nitride, silicon nitride or silicon carbide are preferable.
- the thickness of the high-rigidity ceramic plate is preferably 100 ⁇ m or more, and more preferably 200 ⁇ m or more, from the viewpoint of handleability of processes such as substrate cleaning and joining.
- the upper limit of the high-rigidity ceramic plate is not particularly limited, but 300 ⁇ m or less is preferable from the viewpoint of shortening the processing time.
- the arithmetic mean roughness Ra of the surface of the diaphragm (the surface on which the bonding layer is provided) is 0.01 nm or more and 10.0 nm or less, and the pit density of the surface of the diaphragm is 10 per 100 ⁇ m 2. That is all.
- the Ra and pit density on the surface of the diaphragm are the same as the Ra and pit density on the surface of the high-rigidity ceramic plate before processing. To do.
- the surface is measured with an atomic force microscope (AFM) in a field of view of 10 ⁇ m ⁇ 10 ⁇ m, and Ra is calculated according to JIS B 0601.
- the number of pits is counted in the same measurement field of view (area 100 ⁇ m 2).
- the criteria for determining the pit are as follows. That is, among the recesses observed on the surface, the following are defined as pits. (1) The recess is ⁇ 50 nm or more and ⁇ 2000 nm or less. (2) The depth of the recess is 1 nm or more.
- the arithmetic mean roughness Ra of the surfaces of the diaphragm and the high-rigidity ceramic plate is 0.01 nm or more and 10.0 nm or less, but from the viewpoint of bending strength, 7.0 nm or less is more preferable, and 5.0 nm or less is particularly preferable. Further, from the viewpoint of adhesion to the bonding layer, Ra is set to 0.01 nm or more, but more preferably 0.02 nm or more. Further, the pit density of the surface of the diaphragm is 10 or more per 100 ⁇ m 2, but more preferably 20 or more. Further, the pit density of the surface of the diaphragm can be usually 200 or less per 100 ⁇ m 2 , more preferably 96 or less, and particularly preferably 70 or less.
- the pits existing on the surface facing the joint layer of the diaphragm and the high-rigidity ceramic plate are generated by the sintering aid added to precisely sinter the high-rigidity ceramic plate.
- Most of the sintering aid that is left over during firing is agglomerated at the grain boundaries of the ceramic particles.
- the part where the sintering aid is agglomerated has a faster polishing rate than the high-rigidity ceramic itself, so the sintering aid agglomerates.
- the part that has been fired becomes a pit. From this, there is a correlation between the amount of the sintering aid added and the number of pits, and the number of pits can be adjusted by the amount of the sintering aid added.
- the relative density of the high-rigidity ceramic plate is preferably 95% or more, more preferably 99% or more.
- the type and amount of the sintering aid suitable for obtaining Ra and the pit density as described above are appropriately selected depending on the type of the high-rigidity ceramics to be sintered.
- examples of the sintering aid include Y 2 O 3 , CaO, MgO, and ZrO 2 .
- the arithmetic mean roughness Ra of the back surface of the diaphragm and the high-rigidity ceramic plate is 0.01 nm or more and 10.0 nm or less from the viewpoint of bending strength. Is preferable.
- a method of polishing the surface of a high-rigidity ceramic plate for example, after grinding to a desired thickness with a # 3000 grindstone, lap polishing is performed with a diamond slurry having a particle size of 3 ⁇ m, and finishing is performed by chemical mechanical polishing (CMP). Mirrored.
- CMP chemical mechanical polishing
- the thickness of the bonding layer 2 formed on the high-rigidity ceramic plate is not particularly limited, but is preferably 0.01 to 10 ⁇ m, more preferably 0.05 to 0.5 ⁇ m from the viewpoint of manufacturing cost.
- the method for forming the bonding layer 2 is not limited, and examples thereof include a sputtering method, a chemical vapor deposition method (CVD), and thin film deposition.
- Methods for flattening the joint surface of the joint layer 2 and the joint surface of the support substrate include lap polishing and chemical mechanical polishing (CMP).
- the neutralized atomic beam can activate the surface 2b of the bonding layer 2 and the surface 3a of the supporting substrate 3.
- the surface 2b of the bonding layer 2 and the surface 3a of the support substrate 3 are flat surfaces, direct bonding is easy.
- the surface When the surface is activated by the neutralized atomic beam, it is preferable to generate and irradiate the neutralized beam by using an apparatus as described in Patent Document 2. That is, a saddle field type high-speed atomic beam source is used as the beam source. Then, an inert gas is introduced into the chamber, and a high voltage is applied to the electrodes from a DC power source. As a result, the saddle field type electric field generated between the electrode (positive electrode) and the housing (negative electrode) causes the electrons e to move, and a beam of atoms and ions due to the inert gas is generated.
- a saddle field type high-speed atomic beam source is used as the beam source.
- an inert gas is introduced into the chamber, and a high voltage is applied to the electrodes from a DC power source.
- the saddle field type electric field generated between the electrode (positive electrode) and the housing (negative electrode) causes the electrons e to move, and a beam of atoms and ions due to the inert gas
- the ion beam is neutralized by the grid, so that the beam of neutral atoms is emitted from the high-speed atomic beam source.
- the atomic species constituting the beam is preferably an inert gas (argon, nitrogen, etc.).
- the voltage at the time of activation by beam irradiation is preferably 0.5 to 2.0 kV, and the current is preferably 50 to 200 mA.
- the temperature at this time is room temperature, but specifically, it is preferably 40 ° C. or lower, and more preferably 30 ° C. or lower. Further, the temperature at the time of joining is particularly preferably 20 ° C. or higher and 25 ° C. or lower.
- the pressure at the time of joining is preferably 100 to 20000 N.
- a diaphragm having a thickness of 100 ⁇ m or less is obtained. Since the thickness of the diaphragm is selected according to the target frequency, there is no particular lower limit to the thickness, but 1 ⁇ m or more is preferable from the viewpoint of ease of processing.
- this processing method for example, after grinding to a desired thickness with a # 3000 grindstone, lap polishing is performed with a diamond slurry having a particle size of 3 ⁇ m, and the finish is mirrored by chemical mechanical polishing (CMP).
- CMP chemical mechanical polishing
- Examples 1 to 8 A diaphragm joint was prototyped as described with reference to FIGS. 1 and 2. Specifically, a wafer-shaped Sialon substrate having a diameter of 4 inches and a thickness of 250 ⁇ m was used as the high-rigidity ceramic plate 1. The surface 1a of the high-rigidity ceramic plate 1 is ground to a desired thickness with a # 3000 grindstone so that the arithmetic mean roughness Ra becomes the respective values shown in Tables 1, 2 and 3, respectively, and then the table is shown.
- the Ra on the surface 1a of the high-rigidity ceramic diaphragm 1 was measured with an atomic force microscope (AFM) in a field of view of 10 ⁇ m ⁇ 10 ⁇ m. At this time, the number of pits having a diameter of 50 nm or more was counted in a field of view of 10 ⁇ m ⁇ 10 ⁇ m by an atomic force microscope (AFM). However, when measuring the number of pits on the surface 1a of the high-rigidity ceramic plate 1, the center point of the wafer-shaped plate 1, the point 10 mm inside the orientation flat of the plate 1, and the opposite of the orientation flat of the plate 1.
- AFM atomic force microscope
- each high-rigidity ceramic plate having the same material, thickness, Ra, and pit density as the high-rigidity ceramic substrate 1 of each example is prepared in advance, and each test piece is cut out from each high-rigidity ceramic plate.
- the bending strength at three points was measured.
- the bending strength was measured according to the 3-point bending strength test standard in JIS R 1601 (room temperature bending strength test method for fine ceramics).
- the size of the test piece is a sample length of 40.0 mm, a width of 4.0 mm, and a thickness of 3.0 mm.
- a bonding layer 2 was formed on the surface 1a of the high-rigidity ceramic plate 1 by a DC sputtering method. Boron-doped Si was used as the target. The thickness of the bonding layer 2 was 30 to 200 nm. The arithmetic mean roughness Ra of the surface 2a of the bonding layer 2 was 0.2 to 0.6 nm. Next, the bonding layer 2 was subjected to chemical mechanical polishing (CMP) to adjust the film thickness to 20 to 150 nm and Ra to 0.08 to 0.4 nm.
- CMP chemical mechanical polishing
- a support substrate 3 having an orientation flat (OF) portion and made of silicon having a diameter of 4 inches and a thickness of 500 ⁇ m was prepared.
- the surface of the support substrate 3 is finished by chemical mechanical polishing (CMP), and the arithmetic average roughness Ra is 0.2 nm.
- the surface 2b of the bonding layer 2 and the surface 3a of the support substrate 3 were washed to remove stains, and then introduced into a vacuum chamber. After vacuuming to 10-6 Pa, each surface was irradiated with a high-speed atomic beam (acceleration voltage 1 kV, Ar flow rate 27 sccm) for 120 seconds. Then, the activated surface 2b of the bonding layer 2 and the activated surface 3a of the support substrate 3 were brought into contact with each other, and then pressed at 10000 N for 2 minutes for bonding (FIG. 2A). Then, the obtained conjugate 4 of each example was heated at 100 ° C. for 20 hours. Next, the back surface 1b of the high-rigidity ceramic plate 1 was ground and polished so that the thickness was changed from the initial 250 ⁇ m to 40 ⁇ m (see FIG. 2B).
- a high-speed atomic beam acceleration voltage 1 kV, Ar flow rate 27 sccm
- the pit density is 10 to 96, and the Ra is 0.02 to 9.97 nm, but even if the diaphragm 1A is polished to a thickness of 40 ⁇ m, no peeling occurs. It was.
- the larger the Ra, the lower the bending strength of the ceramic tends to be, but even when Ra 9.97 nm, the result of the bending strength was as high as 500 MPa.
- Comparative example 1 In Comparative Example 1, the bonding layer 2 made of ⁇ -Si was not formed on the high-rigidity ceramic plate 1. Instead, a high-speed atomic beam is applied to the surface 1a of the high-rigidity ceramic plate 1 to bring the activated surface 1a of the high-rigidity ceramic plate 1 into contact with the activated surface 3a of the support substrate 3. They were joined to obtain a joined body. However, the number of pits on the surface 1a of the high-rigidity ceramic plate 1 of Comparative Example 1 was 51, and Ra was 0.03 nm. Further, it was produced under the same conditions as in Example 1 except that the ⁇ -Si bonding layer was not formed.
- the back surface 1b of the high-rigidity ceramic plate 1 of the obtained joint was ground and polished, and an attempt was made to grind and polish the thickness from the initial 250 ⁇ m.
- the thickness of the high-rigidity ceramic plate 1 became 110 ⁇ m, peeling occurred at the bonding interface between the high-rigidity ceramic plate and the support substrate. The peeling occurred because the bonding strength between the high-rigidity ceramic plate 1 and the support substrate 3 in the bonded body was lower than the bonding strength in Examples 1 to 8, and the processing stress when polishing the high-rigidity ceramic plate 1 caused the peeling. It is probable that it was unbearable.
- Comparative Examples 2 and 3 Each of the joints of Comparative Examples 2 and 3 is prepared under the same conditions as in Examples 1 to 8. However, in Comparative Example 2, the number of pits on the surface 1a of the high-rigidity ceramic plate 1 was as small as 4, and the Ra on the surface 1a was 0.01 nm. In this case, when the back surface of the high-rigidity ceramic plate 1 was thinned by grinding and polishing until the thickness became 100 ⁇ m, peeling occurred at the interface between the surface of the high-rigidity ceramic plate 1 and the joint layer 2. It is considered that this is because the adhesion strength between the high-rigidity ceramic plate 1 and the joint layer 2 could not withstand the processing stress when polishing the high-rigidity ceramic plate 1.
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Abstract
Description
(1) フロントガラスなどをスクリーンとして直接画像を投影するDirect Projection方式
(2) フロントガラスなどを反射ミラーとして作用させドライバーの網膜上に結像させるVirtual Imaging方式
(1) 部品点数が少ないため小型化、低コスト化、信頼性向上を実現できる。
(2) 各画素に必要な明るさでレーザーを点灯するため、低消費電力を実現できる。
(3) コリメート(平行光)されたレーザー光を用いるため、フォーカス調整が不要になる。
シリコンからなる支持基板、
高剛性セラミックスからなる厚さ100μm以下の振動板、および
前記支持基板と前記振動板との間にあり、前記振動板の接合面に接し、α-Siからなる接合層を備えており、
前記振動板の前記接合面の算術平均粗さRaが0.01nm以上、10.0nm以下であり、前記振動板の前記接合面のピット密度が100μm2あたり10個以上であることを特徴とする。
次いで前記接合層の接合面とシリコンからなる支持基板の接合面とを接合する工程、および
次いで前記高剛性セラミック板を加工することによって、厚さ100μm以下の振動板を得る工程を備える、振動板接合体の製法であって、
前記高剛性セラミック板の前記表面の算術平均粗さRaが0.01nm以上、10.0nm以下であり、前記高剛性セラミック板の前記表面のピット密度が100μm2あたり10個以上であることを特徴とする。
図1(a)に示すように、高剛性セラミック板1を準備する。高剛性セラミック板の表面1aの算術平均粗さRaを0.01nm以上、10.0nm以下とし、高剛性セラミック板の表面のピット密度を100μm2あたり10個以上とする。1bは高剛性セラミック板1の背面である。
高剛性セラミックスとしては、サイアロン、コージェライト、ムライト、透光性アルミナ、窒化アルミニウム、窒化珪素または炭化珪素が好ましい。
(1) 凹部のΦ50nm以上、Φ2000nm以下である。
(2) 凹部の深さが1nm以上である。
また、振動板の前記表面のピット密度は100μm2あたり10個以上とするが、20個以上とすることが更に好ましい。また、振動板の前記表面のピット密度は通常は100μm2あたり200個以下とすることができ、更には96個以下とすることが好ましく、70個以下であることが特に好ましい。
接合層2の成膜方法は限定されないが、スパッタリング(sputtering)法、化学的気相成長法(CVD)、蒸着を例示できる。
ビーム照射による活性化時の電圧は0.5~2.0kVとすることが好ましく、電流は50~200mAとすることが好ましい。
図1~図2を参照しつつ説明したようにして、振動板接合体を試作した。
具体的には、直径が4インチ、厚さが250μmのウエハー形状のサイアロン基板を、高剛性セラミック板1として使用した。高剛性セラミック板1の表面1aは、算術平均粗さRaが、表1、表2、表3に示す各数値となるように、それぞれ、#3000の砥石で所望の厚みまで研削した後、表1に示す振動板表面(Ra≦1nm)の場合、粒度3μmのダイヤスラリーにてラップ(lap)研磨し、仕上げに化学機械研磨加工(CMP)により鏡面化した。Raの数値を調整するために、CMP研磨時の加工圧力、加工時間を調整した。表2に示す振動板表面(Ra>1nm)の場合、ダイヤスラリーにてラップ(lap)研磨し、鏡面化した。Raの数値を調整するために、仕上げに使用するダイヤスラリーは粒度0.5μmから6μmの中から選択して使用した。
なお、図3には、実施例4で用いた高剛性セラミック板の表面状態を示す(Ra=0.07nm、10μm×10μmの視野におけるピット密度=58個)
次いで、高剛性セラミックス板1の背面1bを厚みが当初の250μmから40μmになるように研削及び研磨した(図2(b)参照)。
比較例1では、α-Siからなる接合層2を高剛性セラミックス板1に成膜しなかった。その代わりに、高剛性セラミック板1の表面1aに対して高速原子ビームを当てて、高剛性セラミックス板1の活性化された表面1aと支持基板3の活性化された表面3aとを接触させて接合し、接合体を得た。ただし、比較例1の高剛性セラミックス板1の表面1aのピット数は51個であり、Raは0.03nmであった。また、α-Siの接合層を成膜しなかったこと以外は、実施例1と同条件にて作製している。
比較例2、3の各接合体は、実施例1~8と同じ条件にて作成している。
ただし、比較例2では、高剛性セラミックス板1の表面1aのピット数は4個と少なく、表面1aのRaは0.01nmであった。この場合、高剛性セラミックス板1の背面を厚みが100μmとなるまで研削及び研磨にて薄くした際に、高剛性セラミックス板1の表面と接合層2の界面にて剥がれが生じた。これは、高剛性セラミックス板1と接合層2の密着強度が、高剛性セラミックス板1を研磨する際の加工応力に耐えられなかったためと考えられる。
Claims (7)
- シリコンからなる支持基板、
高剛性セラミックスからなる厚さ100μm以下の振動板、および
前記支持基板と前記振動板との間にあり、前記振動板の表面に接し、α-Siからなる接合層を備えており、
前記振動板の前記表面の算術平均粗さRaが0.01nm以上、10.0nm以下であり、前記振動板の前記表面のピット密度が100μm2あたり10個以上であることを特徴とする、振動板接合体。 - 前記接合層と前記支持基板とが直接接合されていることを特徴とする、請求項1記載の振動板接合体。
- 前記高剛性セラミックスが、サイアロン、コージェライト、ムライト、透光性アルミナ、窒化アルミニウム、窒化珪素および炭化珪素からなる群より選ばれることを特徴とする、請求項1または2記載の振動板接合体。
- 高剛性セラミックスからなる高剛性セラミック板の表面に、α-Siからなる接合層を設ける工程、
次いで前記接合層の接合面とシリコンからなる支持基板の接合面とを接合する工程、および
次いで前記高剛性セラミック板を加工することによって、厚さ100μm以下の振動板を得る工程を備える、振動板接合体の製法であって、
前記高剛性セラミック板の前記表面の算術平均粗さRaが0.01nm以上、10.0nm以下であり、前記高剛性セラミック板の前記表面のピット密度が100μm2あたり10個以上であることを特徴とする、振動板接合体の製造方法。 - 前記接合層の前記接合面と前記支持基板の前記接合面を直接接合することを特徴とする、請求項4記載の振動板接合体の製造方法。
- 前記接合層の前記接合面と前記支持基板の前記接合面とをそれぞれ中性化原子ビームによって活性化し、次いで直接接合することを特徴とする、請求項5記載の振動板接合体の製造方法。
- 前記高剛性セラミックスが、サイアロン、コージェライト、ムライト、透光性アルミナ、窒化アルミニウム、窒化珪素および炭化珪素からなる群より選ばれることを特徴とする、請求項4~6のいずれか一つの請求項に記載の振動板接合体の製造方法。
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