WO2021060366A1 - SiC半導体装置の製造方法及びSiC半導体装置 - Google Patents
SiC半導体装置の製造方法及びSiC半導体装置 Download PDFInfo
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- H—ELECTRICITY
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- H01L21/00—Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
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- H01L21/02367—Substrates
- H01L21/0237—Materials
- H01L21/02373—Group 14 semiconducting materials
- H01L21/02378—Silicon carbide
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- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B23/00—Single-crystal growth by condensing evaporated or sublimed materials
- C30B23/02—Epitaxial-layer growth
- C30B23/06—Heating of the deposition chamber, the substrate or the materials to be evaporated
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- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
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- H01L21/02005—Preparing bulk and homogeneous wafers
- H01L21/02032—Preparing bulk and homogeneous wafers by reclaiming or re-processing
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- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
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- H01L21/02365—Forming inorganic semiconducting materials on a substrate
- H01L21/02518—Deposited layers
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- H01L21/02524—Group 14 semiconducting materials
- H01L21/02529—Silicon carbide
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- H—ELECTRICITY
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- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
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- H01L21/02612—Formation types
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- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
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- H01L21/02365—Forming inorganic semiconducting materials on a substrate
- H01L21/02612—Formation types
- H01L21/02617—Deposition types
- H01L21/02631—Physical deposition at reduced pressure, e.g. MBE, sputtering, evaporation
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L21/00—Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/04—Manufacture or treatment of semiconductor devices or of parts thereof the devices having potential barriers, e.g. a PN junction, depletion layer or carrier concentration layer
- H01L21/18—Manufacture or treatment of semiconductor devices or of parts thereof the devices having potential barriers, e.g. a PN junction, depletion layer or carrier concentration layer the devices having semiconductor bodies comprising elements of Group IV of the Periodic Table or AIIIBV compounds with or without impurities, e.g. doping materials
- H01L21/20—Deposition of semiconductor materials on a substrate, e.g. epitaxial growth solid phase epitaxy
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- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/04—Manufacture or treatment of semiconductor devices or of parts thereof the devices having potential barriers, e.g. a PN junction, depletion layer or carrier concentration layer
- H01L21/18—Manufacture or treatment of semiconductor devices or of parts thereof the devices having potential barriers, e.g. a PN junction, depletion layer or carrier concentration layer the devices having semiconductor bodies comprising elements of Group IV of the Periodic Table or AIIIBV compounds with or without impurities, e.g. doping materials
- H01L21/26—Bombardment with radiation
- H01L21/263—Bombardment with radiation with high-energy radiation
- H01L21/268—Bombardment with radiation with high-energy radiation using electromagnetic radiation, e.g. laser radiation
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- H01L21/00—Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
- H01L21/70—Manufacture or treatment of devices consisting of a plurality of solid state components formed in or on a common substrate or of parts thereof; Manufacture of integrated circuit devices or of parts thereof
- H01L21/77—Manufacture or treatment of devices consisting of a plurality of solid state components or integrated circuits formed in, or on, a common substrate
- H01L21/78—Manufacture or treatment of devices consisting of a plurality of solid state components or integrated circuits formed in, or on, a common substrate with subsequent division of the substrate into plural individual devices
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- H01L21/77—Manufacture or treatment of devices consisting of a plurality of solid state components or integrated circuits formed in, or on, a common substrate
- H01L21/78—Manufacture or treatment of devices consisting of a plurality of solid state components or integrated circuits formed in, or on, a common substrate with subsequent division of the substrate into plural individual devices
- H01L21/7806—Manufacture or treatment of devices consisting of a plurality of solid state components or integrated circuits formed in, or on, a common substrate with subsequent division of the substrate into plural individual devices involving the separation of the active layers from a substrate
- H01L21/7813—Manufacture or treatment of devices consisting of a plurality of solid state components or integrated circuits formed in, or on, a common substrate with subsequent division of the substrate into plural individual devices involving the separation of the active layers from a substrate leaving a reusable substrate, e.g. epitaxial lift off
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L29/00—Semiconductor devices specially adapted for rectifying, amplifying, oscillating or switching and having potential barriers; Capacitors or resistors having potential barriers, e.g. a PN-junction depletion layer or carrier concentration layer; Details of semiconductor bodies or of electrodes thereof ; Multistep manufacturing processes therefor
- H01L29/02—Semiconductor bodies ; Multistep manufacturing processes therefor
- H01L29/12—Semiconductor bodies ; Multistep manufacturing processes therefor characterised by the materials of which they are formed
- H01L29/16—Semiconductor bodies ; Multistep manufacturing processes therefor characterised by the materials of which they are formed including, apart from doping materials or other impurities, only elements of Group IV of the Periodic Table
- H01L29/1608—Silicon carbide
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- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/36—Carbides
Definitions
- the present invention relates to a method for manufacturing a SiC semiconductor device and a SiC semiconductor device.
- Silicon carbide (SiC: silicon carbide) has superior material properties such as dielectric breakdown strength, thermal conductivity, and radiation resistance compared to silicon (Si: silicon), so research and development has been promoted as a material that constitutes electronic devices. ing.
- the quality of SiC semiconductor devices is affected by the warpage caused by the internal stress of the SiC single crystal wafer.
- the warp may make patterning on a SiC single crystal wafer difficult. Further, the warp causes an adsorption error of the SiC single crystal wafer, a machine stop, cracking of the SiC single crystal wafer, and the like, which is a major factor that hinders device manufacturing.
- SiC wafers having a substrate thickness larger than necessary may be used, and there is room for improvement in economic efficiency.
- Patent Document 1 is a method of manufacturing SiC substrates having an epitaxial layer one by one, which includes growing an epitaxial layer on a seed crystal substrate and growing a SiC substrate, and the obtained epitaxial layer is used.
- An invention relating to a manufacturing method further comprising a step of removing the SiC substrate having the carbide from the seed crystal substrate is disclosed.
- Patent Document 1 since the SiC substrate having the obtained epitaxial layer is sent to the subsequent device manufacturing process, it cannot be said that the influence of the warp on the manufacturing process of the SiC semiconductor device can be eliminated. ..
- the present invention is a problem to be solved to provide a high quality SiC semiconductor device.
- the present invention comprises a growth step of forming a growth layer on an object to be treated containing a SiC single crystal, a device formation step of forming at least a part of a SiC semiconductor device in the growth layer, and the above-mentioned A separation step of separating at least a part of the SiC semiconductor device from the object to be processed is included.
- the SiC wafer including the part can be separated. Therefore, SiC. It is possible to realize the manufacture of a highly economical SiC semiconductor device while suppressing the influence of wafer warpage on the process.
- the growth step heat-treats the object to be treated in an atmosphere containing Si element and C element.
- Si element and C element With such a configuration, high-quality SiC wafers can be manufactured while eliminating or suppressing the occurrence of strain, crystal defects, basal dislocations (BPD: Basic Plane Dislocation) and macrostep bunching (MSB), and SiC semiconductors.
- BPD Basic Plane Dislocation
- MSB macrostep bunching
- the growth step heat-treats the object to be treated in a semi-closed space where the SiC material is exposed.
- the present invention can manufacture a high-quality SiC wafer while eliminating or suppressing the occurrence of distortion, crystal defects, BPD and MSB, and then manufacture a SiC semiconductor device.
- the device forming step is a patterning step of forming a circuit pattern on the object to be processed.
- the present invention can suitably perform patterning on a SiC wafer in which the wafer warp is suppressed, and can manufacture a high-quality SiC semiconductor device.
- the device forming step is a doping step of introducing a dopant atom into the object to be treated.
- the present invention can suitably perform doping on a SiC wafer in which the wafer warp is suppressed, and can manufacture a high-quality SiC semiconductor device.
- the device forming step is an insulating film forming step of introducing an insulating film into the object to be processed.
- the present invention can suitably form an insulating film on a SiC wafer in which the wafer warp is suppressed, and can manufacture a high-quality SiC semiconductor device.
- the device forming step is an electrode forming step of forming an electrode on the object to be processed.
- the present invention can suitably form electrodes on a SiC wafer in which the wafer warp is suppressed, and can manufacture a high-quality SiC semiconductor device.
- the separation step includes a separation layer forming step of forming a separation layer inside the object to be processed and a peeling step of peeling a part of the object to be processed starting from the separation layer. Including.
- the present invention can realize the separation of the SiC wafer including at least a part of the SiC semiconductor device while suppressing the material loss.
- the separation layer in the separation layer forming step, is formed by irradiating the object to be treated with a laser so that the inside is the focal point.
- the separation layer in the SiC single crystal which is the starting point of peeling, can be formed flat.
- an etching step is performed in which the object to be treated is heat-treated in an atmosphere containing elements Si and C to etch the object to be processed.
- the present invention can manufacture a high-quality SiC wafer while eliminating or suppressing the occurrence of distortion, crystal defects, BPD and MSB, and then manufacture a SiC semiconductor device.
- the etching step heat-treats the object to be treated in a semi-closed space where the SiC material is exposed.
- the present invention can manufacture a high-quality SiC wafer while eliminating or suppressing the occurrence of distortion, crystal defects, BPD and MSB, and then manufacture a SiC semiconductor device.
- the preferred embodiment of the present invention includes the separation step, the etching step, and the growth step in this order. With such a configuration, the present invention can repeatedly manufacture a higher quality SiC wafer including at least a part of the SiC semiconductor device, and thus can manufacture a highly economical SiC semiconductor device. It can be realized.
- the separation step and the growth step are included in this order.
- the present invention can repeatedly manufacture a high-quality SiC wafer including at least a part of the SiC semiconductor device, thereby realizing the manufacture of a highly economical SiC semiconductor device. can do.
- the present invention includes a growth layer having a basal dislocation density of ⁇ 100 / cm 2 , and the growth layer is an n-type or p-type substrate.
- the present invention can realize a high-quality SiC semiconductor device capable of suppressing the generation of stacking defects that cause deterioration of forward characteristics.
- the dopant concentration of the growth layer is 1.0 ⁇ 10 17 / cm 3 or more.
- the present invention can realize, for example, a high-quality SiC semiconductor device capable of suppressing the generation of stacking defects that cause deterioration of forward characteristics.
- the SiC semiconductor device 12 in the growth step S1 for forming the growth layer 10 on the object 1 containing the SiC single crystal, at least a part of the SiC semiconductor device 12 is formed in the growth layer 10.
- the device forming step S2 and the separating step S3 for separating at least a part of the formed SiC semiconductor device 12 from the object 1 to be processed are included.
- the "SiC semiconductor device 12" in the description of the present specification refers to a semiconductor device containing at least a SiC material including a SiC device.
- the object to be processed 1 includes a raw substrate 11 made of a SiC single crystal.
- the original substrate 11 may be a SiC ingot produced by a known crystal growth method such as a sublimation method, or may be a SiC wafer sliced into a disk shape from the SiC ingot.
- the "polytype of SiC single crystal" in the description in this specification refers to a known polytype such as 3C, 4H, 6H and the like.
- the cross-sectional size of the object 1 to be processed is several centimeters square, 2 inches, 3 inches, 4 inches, 6 inches, 8 inches, or 12 inches. There is no limit to the cross-sectional size.
- the surface of the object 1 to be processed may be configured to have an off angle of several degrees (for example, 0.4 to 8.0 °) from the (0001) plane or the (000-1) plane.
- "-" in the description of this specification refers to a bar in the notation of the Miller index.
- the manufacturing method of the SiC semiconductor device 12 can be grasped as follows. 1) In the growth step S1, the growth layer 10 is formed on the original substrate 11. 2) In the device forming step S2, the growth layer 10 is processed to form at least a part of the SiC semiconductor device 12. 3) In the separation step S3, at least a part of the SiC semiconductor device 12 formed in the device forming step S2 is separated from the object to be processed 1.
- FIG. 2 illustrates a SiC semiconductor device 12 having a field effect transistor (FET) structure.
- FET field effect transistor
- the epitaxial growth step S11 forms a growth layer 10 having the step 102a and the terrace 102b exhibiting the elongated terrace length W2 on the surface of the original substrate 11 having the step 101a and the terrace 101b exhibiting the reduced terrace length W1. Crystal growth is carried out so as to form a growth layer 10 having a bunched (bunched) surface.
- a growth layer having a basal dislocation density (BPD density) of ⁇ 100 / cm 2 is formed, or the BPD in the object 1 is subjected to through-blade dislocation (TED). Crystal growth is performed to form at least a part of the growth layer 10 so as to be converted into other defects / dislocations including.
- BPD density basal dislocation density
- the growth layer 10 having the step 103a and the terrace 103b exhibiting the reduced terrace length W3 is formed or flattened on the surface of the growth layer 10 having the step 102a and the terrace 102b.
- the MSB on the surface of the object to be processed 1 is decomposed and the object to be processed 1 is crystal-grown so as to form a bunching-free surface.
- the surface of the growth layer 10 is terminated by a step exhibiting the height of the full unit in the SiC single crystal.
- the "flattened bunching-free surface” in the description herein refers to the SiC surface from which the MSB has been decomposed.
- the term "MSB” in the description of the present specification refers to a step on the surface of SiC that bunches to form a height exceeding the full unit of each polytype. That is, the MSB is a step of bunching beyond 4 molecular layers (5 molecular layers or more) in the case of 4H-SiC, and exceeds 6 molecular layers (7 molecular layers or more) in the case of 6H-SiC. It is a bunched step.
- the thickness of the growth layer 10 formed in one embodiment of the present invention is preferably 500 ⁇ m or less, more preferably 350 ⁇ m or less, more preferably 200 ⁇ m or less, still more preferably 150 ⁇ m or less, still more preferable. Is 120 ⁇ m or less, more preferably 100 ⁇ m or less, still more preferably 50 ⁇ m or less, still more preferably 20 ⁇ m or less. The thickness is preferably 20 ⁇ m or more, more preferably 50 ⁇ m or more, more preferably 100 ⁇ m or more, more preferably 150 ⁇ m or more, still more preferably 200 ⁇ m or more, still more preferably 350 ⁇ m or more. Is.
- the growth step S1 is based on a known film formation method such as a physical vapor deposition method (PVD method) or a chemical vapor deposition method (CVD method) after forming a growth layer having a BPD density of ⁇ 100 / cm 2. Further SiC epitaxial growth may be carried out. Further, a part of the growth layer 10 having a BPD density of ⁇ 100 / cm 2 formed in the growth step S1 may be treated as the substrate 111. As an example, the substrate 111 has a dopant concentration of 1.0 ⁇ 10 17 / cm 3 or more.
- the “processed body 1" in the description in the present specification refers to the processed body 1 including the growth layer 10 in the case of the growth step S1 or later. Further, it can be understood that the "various treatments on the object 1 to be processed” by the device forming step S2 and the separation step S3, which will be described later, are “various processes on the growth layer 10 contained in the object 1 to be processed”.
- Device forming process S2 performs a patterning step S21 for forming the circuit pattern 211 on the object 1 on which the growth layer 10 is formed.
- the patterning step S21 includes, for example, a resist coating step of applying a photoresist, an exposure step of exposing the photoresist through a photomask, and a developing step of developing the exposed photoresist.
- a known photoresist containing a base resin that selectively reacts with the wavelength of a light source that can be adopted in the exposure step described later is coated on the object to be processed 1.
- the photoresist is, for example, a polymer material containing a novolak resin and a 1,2-naphthoquinonediazide sulfonic acid ester (NQD) -based compound when the light source is g-ray (wavelength: 436 nm).
- the photoresist is, for example, a polymer material containing a base resin having an alicyclic group such as norbornene that can suppress light absorption near a wavelength of 200 nm when the light source is an ArF laser (wavelength: 193 nm). is there.
- a photoresist is applied onto the object 1 to be treated by using a known resist coating device such as spin coating or spray coating.
- the resist coating step sets or optimizes the process conditions such as the rotation speed and the dropping amount related to the spin coating so that a desired film thickness and the like related to the photoresist can be obtained.
- a silicifying agent such as hexamethyldisilazane (HMDS) that removes hydroxyl groups is applied so that the surface of the object 1 to be treated is provided with hydrophobicity. It may be applied to the surface of the treated body 1.
- HMDS hexamethyldisilazane
- the photoresist and the object to be processed 1 are heat-treated to perform prebaking. Further, in the resist coating step, the process conditions such as the heating temperature and the heating time related to prebaking are preferably transferred so that the desired film thickness and surface roughness related to the photoresist can be obtained, or the circuit pattern 211 is preferably transferred. Set or optimize.
- the exposure step is applied onto the object 1 to be processed by using a known exposure device such as a close contact exposure device including a known light source, an optical system and a stage, a reduced projection exposure device, and a photomask exhibiting a circuit pattern 211. A part of the photoresist is exposed.
- a known projection method such as a lens method or a mirror method can be adopted.
- the exposure apparatus may perform exposure in the form of maskless exposure without using a tangible photomask. Further, in the exposure step, process conditions such as exposure time are appropriately set or optimized so that the circuit pattern 211 is suitably transferred.
- g-ray (436 nm wavelength), i-ray (365 nm wavelength), KrF laser (248 nm wavelength), ArF laser (193 nm wavelength), F 2 laser (157 nm wavelength), Kr 2 laser (146 nm wavelength) , Ar 2 laser (126 nm wavelength), soft X-ray (EUV: Extreme Ultraviolet, ⁇ 13.5 nm wavelength), electron beam, X-ray and the like can be adopted.
- pure water may be inserted between the projection optical system and the object 1 to be processed to improve the refractive index in the mode of immersion lithography.
- the photoresist may be heat-treated after the exposure to perform baking (PEB: Post Exposure Bakering). Further, in the exposure step, the process conditions such as the heating temperature and the heating time related to the baking are set or optimized so that the circuit pattern 211 is suitably transferred.
- PEB Post Exposure Bakering
- the developing step a part of the exposed photoresist is removed (developed) with a developing solution.
- the material of the developing solution can be appropriately selected according to the material of the photoresist.
- the developer contains, for example, tetramethylammonium hydroxide (TMAH).
- TMAH tetramethylammonium hydroxide
- the process conditions such as the developer temperature and the developing time are set or optimized so that the circuit pattern 211 is suitably transferred.
- the developing step is post-baking of the developed photoresist. Further, in the developing step, the process conditions such as the heating temperature and the heating time related to the baking are set or optimized so that the circuit pattern 211 is suitably transferred.
- a hard mask used as a sacrificial layer is formed on the object 1 to be processed based on a known film forming method such as a PVD method or a CVD method. The process may be performed.
- Hard mask formation step and SiO 2, TEOS-SiO 2 such as silicon oxide, SiN, Si 3 N 4 such as silicon nitride or, or silicon oxynitride such as SiON, or boron nitride such as BN, TiN A material exhibiting high hardness and low stress such as titanium nitride and a mixture thereof can be used as a hard mask.
- the hard mask may be configured to appropriately add element B or the like.
- the hard mask and the photoresist may be formed in this order, or the antireflection film such as the hard mask and the carbon film and the photoresist may be formed in this order, and the multilayer structure may be formed. You may perform the film formation which exhibits.
- the photoresist may be formed on the object to be processed 1, the photoresist may be treated as a hard mask having heat resistance, etching resistance, and ion stopping ability, and the circuit pattern 211 may be transferred.
- the circuit pattern 211 may be transferred to the object 1 to be processed by using a mold containing a SiO 2 material as an example in the form of nanoimprint.
- the line width of the circuit pattern 211 formed in one embodiment of the present invention is preferably 10 ⁇ m or less, more preferably 5.0 ⁇ m or less, more preferably 2.0 ⁇ m or less, and more preferably 1. It is 0 ⁇ m or less, more preferably 0.5 ⁇ m or less, further preferably 0.2 ⁇ m or less, still more preferably 0.1 ⁇ m or less, still more preferably 50 nm or less, still more preferably 20 nm or less. , More preferably 10 nm or less.
- the line width is preferably 1.0 nm or more, more preferably 10 nm or more, more preferably 20 nm or more, more preferably 50 nm or more, and even more preferably 0.1 ⁇ m or more. It is more preferably 0.2 ⁇ m or more, more preferably 0.5 ⁇ m or more, more preferably 1.0 ⁇ m or more, still more preferably 2.0 ⁇ m or more, still more preferably 5.0 ⁇ m or more.
- a photoresist exhibiting the circuit pattern 211 is used to perform a selective etching step of etching the exposed surface below the photoresist.
- the selective etching step etches the exposed surface on the object 1 to be processed so as to exhibit material selectivity.
- “Exhibiting material selectivity” in the description herein refers to, for example, that the etching rates of the photoresist and the SiC single crystal are different.
- the selective etching step for example, etches the exposed surface on the object 1 to be processed by wet etching.
- the selective etching step sets or optimizes the process conditions such as etchant, etching time, and etching temperature so as to realize desired material selectivity, plane orientation dependence, etching rate, and the like.
- the solution containing the etchant include a TMAH solution, a potassium hydroxide (KOH) solution, a potassium permanganate (KMnO 4 ) solution, a hydrogen fluoride (HF) solution, and the like.
- the selective etching step etches the exposed surface on the object 1 to be processed by, for example, a known thermal etching such as reactive gas etching.
- the process conditions such as the partial pressure and heat treatment temperature related to the etchant (reaction gas) and the reaction gas are set so as to realize the desired material selectivity, plane orientation dependence, etching rate, and the like. Or optimize.
- the etchant as an example, a H 2, HCl, a mixture of such Cl 2, O 2, CIF 3 .
- the selective etching step etches the exposed surface on the object 1 to be processed by, for example, a known dry etching such as reactive ion etching (RIE).
- RIE reactive ion etching
- Reactive ion etching forms plasma by a known method such as ICP or CCP, and Ar gas, O 2 gas, NF 3 gas, PF 3 gas, BF 3 gas, CF 4 gas, CHF 3 gas, SF 6 gas , XeF 2, and other known gases are combined as appropriate.
- the selective etching step sets or optimizes process conditions such as bias power, gas type, gas partial pressure, and discharge time so as to realize desired anisotropy, etching rate, and the like.
- anisotropic etching or deep etching may be performed so as to form a three-dimensional shape such as a U groove or a V groove on the object 1 to be processed.
- ⁇ Doping step S22> As shown in FIG. 3, in the device forming step S2, a dopant atom is introduced into the object 1 to be processed so as to form an n-type and / or p-type region in the object 1 or to form a pn junction region. Doping step S22 is performed.
- an ion implantation step of irradiating the object 1 to be treated with a dopant ion which is an ionized dopant atom, and a step of heat-treating the object 1 to be treated to be irradiated with the dopant ion to activate the object 1. includes activation steps to be performed.
- the ion injection step is, for example, a beam extraction step of drawing an ion beam from an ion source containing a dopant element, a mass analysis step of mass-separating a desired ion species among the ion species contained in the ion beam, and mass separation.
- An acceleration step of imparting acceleration energy to an ion beam containing an ion species and a scanning step of scanning the ion beam to which the acceleration energy is applied and irradiating the object 1 to be processed are performed.
- the circuit pattern 211 which is a sacrificial layer having an ion stopping ability, is used to irradiate a desired region with dopant ions.
- the ion implantation step for example, known dopant elements such as N element, P element, Al element and B element are ionized and irradiated onto the object 1 to be processed.
- the N element and the P element are added to the SiC single crystal so as to form the n-type region
- the Al element and the B element are added to the SiC single crystal so as to form the p-type region.
- An element that forms an n-type or p-type region in the SiC single crystal can be appropriately adopted as the dopant ion.
- non-dopant elements such as C element, Si element, Cl element, and Ar element can be similarly ionized and irradiated onto the object to be processed 1.
- the beam extraction step extracts an ion beam containing dopant ions from an ion source containing dopant elements installed in a vacuum chamber so that a desired mean free path can be obtained. Further, in the beam extraction step, as an example, the ion beam is extracted by applying an extraction voltage to the ion source. Further, in the beam extraction step, for example, the ion source is ionized in a plasma environment to extract the ion beam.
- the ion source may be a solid material, a gaseous material, a liquid metal ion source (LMIS), or for forming a plasma environment that promotes ionization.
- the support gas and the solid material may be combined.
- the plasma environment is appropriately formed based on a known method using a DC power source, an AC power source, or the like.
- the mass spectrometry step analyzes the mass-to-charge ratio (m / z) of the ion beam containing the dopant ions extracted by the beam extraction step so as to mass-separate the desired ion species.
- a magnetic field is passed while applying a voltage to the ion beam, the voltage and / or the magnetic field strength is adjusted, and m / z corresponding to the ion species is selected.
- the mass spectrometry step can be appropriately adopted as long as it is a known mass spectrometry such as a fan-shaped magnetic field, a quadrupole magnet, a time-of-flight (TOF), and an ion trap type.
- the acceleration step applies acceleration energy to the ion beam containing the dopant ions so as to achieve the desired ion implantation depth or the desired dopant profile.
- the acceleration step may be performed after the mass spectrometry step, or may be performed before and after the mass spectrometry step.
- the scanning step scans an ion beam containing the dopant ions on at least a part of the surface of the target object 1 to be processed, which is a target installed in the vacuum chamber, so that the dopant ions are given an injection angle.
- the beam current of the ion beam irradiated to the target may be evaluated by using a Faraday cup or the like.
- the beam current and the beam irradiation time are used for evaluating the dose amount related to the ion beam.
- the process conditions such as the acceleration energy, the implantation angle, and the dose amount are set or optimized so that a desired dopant profile is formed.
- coion implantation may be performed so as to irradiate two or more types of ions.
- the two or more ion species may be, for example, a plurality of types of dopant ions, C ions and dopant ions, and the combination thereof is not limited.
- the dopant ion may be irradiated to the object 1 to be processed a plurality of times so that a desired dopant profile is formed, or the dopant ion is irradiated while changing the acceleration energy in a plurality of steps.
- the processed body 1 may be irradiated, or the dopant ion may be irradiated to the processed body 1 while heating the processed body 1.
- the dopant ion may be irradiated to the object 1 to be processed so as to form a box profile such that the dopant concentration is constant.
- the "desired dopant profile" in the description of the present specification may be appropriately changed depending on the structure of the SiC semiconductor device to be manufactured.
- the object 1 irradiated with the dopant ion is heat-treated in an inert atmosphere such as an Ar atmosphere so as to recover the crystal damage caused by the irradiation of the dopant ion and activate the dopant ion.
- the process conditions such as heating temperature, heating time, and partial pressure are set or optimized so that a desired dopant profile is formed or the activation rate of the dopant ion is increased. ..
- a passivation film such as a carbon layer or SiO 2 is formed on the surface strip of the object to be treated 1 so as to prevent carbonization of the surface of the object 1 to be processed.
- the doping step S22 forms an n-type or p-type drift region 220 to form an n + and / or n - region, a p + and / or p -region, and an n-type or p-type.
- Form n-type or p-type pillar regions to form n-type or p-type collector regions, n-type or p-type field stop regions to form type or p-type source regions, and n-type or p-type pillar regions.
- n-type or p-type buffer region To form an n-type or p-type buffer region, to form an n-type or p-type recombination promoting region, to form an n-type or p-type embedded region, and to form a hallo structure.
- Dopant atoms are introduced into the object 1 to form a shallow junction structure or a super junction structure.
- the doping step S22 introduces a dopant atom into the object 1 to be treated so as to form an n-type or p-type region having a profile as seen in known Si-based electronic devices.
- the "region" included in the n-type region, the drift region, and the like in the description in the present specification is the same as the "layer” included in the n-type layer, the drift layer, and the like.
- the dopant concentration in the n-type or p-type region formed by the doping step S22 is preferably 1.0 ⁇ 10 21 / cm 3 or less, more preferably 1.0 ⁇ 10 20 / cm 3 or less, and more preferably. Is 1.0 ⁇ 10 19 / cm 3 or less, more preferably 1.0 ⁇ 10 18 / cm 3 or less, still more preferably 1.0 ⁇ 10 17 / cm 3 or less, still more preferably 1 It is 0.0 ⁇ 10 16 / cm 3 or less.
- the dopant concentration is preferably 1.0 ⁇ 10 15 / cm 3 or more, more preferably 1.0 ⁇ 10 16 / cm 3 or more, and more preferably 1.0 ⁇ 10 17 / cm 3 or more.
- the dopant concentration may differ between different regions such as an n-type contact region and a drift region, for example.
- a dopant atom may be introduced into the object 1 to be processed after the patterning step S21 each time SiC epitaxial growth is performed.
- the SiC epitaxial growth may be carried out by the growth step S1 or by a known film forming method such as the PVD method or the CVD method.
- the device forming step S2 may repeat the patterning step S21 and the doping step S22. Further, in the device forming step S2, the SiC epitaxial growth, the patterning step S21 and the doping step S22 may be repeated based on the plurality of circuit patterns 211. Further, in the device forming step S2, the SiC epitaxial growth and doping step S22 may be performed without performing the patterning step S21. The device forming step S2 etches the photoresist and / or the hard mask exhibiting the circuit pattern 211 each time the doping step S22 is performed.
- the device forming step S2 performs an insulating film forming step S23 for introducing the insulating film 230 into the object to be processed 1.
- the insulating film 230 functions as, for example, a gate insulating film, an interlayer insulating film for element separation, or a cap layer for adjusting a flat band voltage in the gate electrode 240 in a SiC semiconductor device having an FET structure or the like. ..
- the EOT (Equivalent Oxide Pickness) of the insulating film 230 formed by the insulating film forming step S23 is preferably 100 nm or less, more preferably 50 nm or less, more preferably 20 nm or less, still more preferably 10 nm or less. , More preferably 5.0 nm or less, still more preferably 2.0 nm or less.
- the EOT is preferably 1.0 nm or more, more preferably 2.0 nm or more, more preferably 5.0 nm or more, more preferably 10 nm or more, still more preferably 20 nm or more. , More preferably 50 nm or more.
- the object to be treated 1 is thermally oxidized using a known oxidizing furnace and an oxidizing species such as dry oxygen (O 2 ) and steam (H 2 O), and the thermally oxidized SiO 2 film is formed.
- the insulating film forming step S23 sets the process conditions such as the oxidation temperature, the oxidation time, and the partial pressure of the oxide gas to the SiC / SiO 2 interface roughness so that the interface state density at the SiC / SiO 2 interface is reduced. Is set or optimized so that carbon residue in the thermally oxidized SiO 2 film is suppressed, or CO gas generation in the thermal oxidation reaction is promoted.
- a heat treatment or a dry process utilizing a plasma environment may be performed after the insulating film 230 is formed so as to reduce the interface state density at the insulating film interface.
- the nitriding treatment may be performed after forming the thermal oxide SiO 2 film so that the interface state density at the SiC / SiO 2 interface is reduced.
- the nitriding treatment may be a heat treatment in a nitric oxide (NO) atmosphere, or may be a treatment using a plasma environment in which nitrogen oxide such as NO is excited.
- the insulating film 230 may be formed based on a known film forming method such as a CVD method or ALD (Atomic Layer Deposition). At this time, the insulating film 230, in addition to the Si oxide film such as thermal oxide SiO 2 film, Al 2 O 3 film may be configured to include a metal oxide film such as AlON film.
- a known film forming method such as a CVD method or ALD (Atomic Layer Deposition).
- the insulating film 230 in addition to the Si oxide film such as thermal oxide SiO 2 film, Al 2 O 3 film may be configured to include a metal oxide film such as AlON film.
- Electrode forming step S24 As shown in FIGS. 4 and 5, the device forming step S2 performs an electrode forming step S24 for forming an electrode on the object 1 to be processed.
- the collector electrode is formed so as to form the gate electrode 240, the source electrode 241 is formed, the drain electrode 242 is formed, the base electrode is formed, the emitter electrode is formed, and the emitter electrode is formed.
- An electrode is formed on the object 1 to be processed, such as forming an anode electrode, forming a cathode electrode, forming an ohmic electrode, or forming a Schottky electrode.
- the electrode forming step S24 for example, poly-Si is formed on the object 1 to be processed by a film forming process based on a known method such as a CVD method.
- the poly-Si is processed as a gate electrode 240 adjacent to the insulating film 230 by, for example, a patterning step S21, a doping step S22, and a selective etching step.
- a metal material other than poly-Si can be used as the gate electrode 240 in place of / in addition to poly-Si.
- a metal film such as Ni is formed on the object 1 by the PVD method.
- the metal film is formed by, for example, a patterning step S21, a doping step S22, and a selective etching step. It is formed as a source electrode 241 or a drain electrode 242, which is an ohmic electrode adjacent to an n-type or p-type contact region 222.
- the silicidation reaction may be carried out by heat-treating the object 1 to be treated after forming the metal film.
- a barrier metal such as TiN or TaN may be laminated on an electrode such as a source electrode 241 or a drain electrode 242.
- the electrode forming step S24 sets or optimizes the process conditions such as the heat treatment temperature and the heat treatment time in the silicidation reaction so that the Schottky electrode is formed or the ohmic electrode is formed by the dopant segregation effect. To do.
- a metal film such as Ni is formed on the object 1 to be processed by the PVD method, and the ohmic electrode adjacent to the n-type or p-type region is used.
- a certain drain electrode 242 may be formed as a back surface electrode.
- the insulating film 23 or the electrode formed by the insulating film forming step S23 or the electrode forming step S24 may be used as the hard mask.
- the "CVD method" in the description in this specification refers to a known CVD method such as thermal CVD, PECVD (Plasma-Enhanced CVD), MOCVD (Metal Organic CVD), and various types constituting the SiC semiconductor device 12. It can be adopted as a film forming method for introducing any of the materials.
- PVD method in the description of the present specification refers to a known PVD method such as vacuum deposition, DC sputtering, RF sputtering, magnetron sputtering, reactive sputtering, molecular beam epitaxy (MBE), etc., and is a SiC semiconductor device 12 It can be appropriately adopted as a film forming method in introducing any of the various materials constituting the above.
- a doping step S22, an insulating film forming step S23, or an electrode forming step S24 may be performed after the selective etching step so as to manufacture the SiC semiconductor device 12 having a trench gate structure.
- the device forming step S2 at least a part of the insulating film forming step S23 may be performed after the electrode forming step S24.
- each step included in the device forming step S2 is performed in no particular order so that a desired structure of the SiC semiconductor device 12 is realized according to the structure of the SiC semiconductor device 12. obtain.
- the device forming step S2 may form a wiring region.
- Separation step S3 a part of the object to be processed 1 is separated.
- a multi-wire saw cutting method for cutting by reciprocating a plurality of wires, an electric discharge machining method for cutting by intermittently generating plasma discharge, and a layer to be a base point for cutting by irradiating a laser are formed. The method can be adopted.
- the step S32 is included.
- ⁇ Separation layer forming step S31> a laser having a wavelength that is transparent in the object to be processed 1 is applied so that the inside of the object to be processed 1 is focused as a depth corresponding to the thickness of the SiC semiconductor device 12 to be separated from the upper surface.
- the treated body 1 is irradiated with light to collect light to form a separation layer 300.
- the separation layer forming step S31 preferably irradiates the surface of the object to be processed 1 on which the SiC semiconductor device 12 is not formed with a laser.
- the separation layer forming step S31 includes a holding means capable of holding the object 1 to be processed based on a conventional method such as an adsorption chuck, a light source 311 capable of irradiating a pulse-oscillating laser, a lens capable of condensing the laser, and the like.
- the separation layer 300 is formed by using the conventional light collecting means 312. Further, in the separation layer forming step S31, an infrared laser is adopted as the laser as an example.
- the wavelength of the laser may be a wavelength similar to ultraviolet light or a wavelength similar to visible light, and there is no limitation.
- the process conditions such as the laser wavelength, the laser output, the laser scanning speed, the beam spot diameter, the pulse width, and the pitch width can be suitably separated from the object 1 to be processed by the SiC semiconductor device 12. Set or optimize.
- ⁇ Peeling step S32> the SiC semiconductor device 12 which is a part of the object to be processed 1 is peeled off from the separation layer 300 as a starting point.
- mechanical vibration is applied to the object to be processed 1 by reciprocating the wire along the separation layer 300 or generating ultrasonic vibration, and the separation layer 300 is used as a starting point.
- the SiC semiconductor device 12 is peeled off from the processing body 1.
- a holding means capable of holding the object 1 to be processed based on a conventional method such as a suction chuck, a vibrating means formed of piezoelectric ceramics or the like and capable of generating conventional mechanical vibration including ultrasonic vibration, and pure
- the SiC semiconductor device 12 is peeled from the object to be processed 1 starting from the separation layer 300 by using at least a part of the liquid supply means capable of supplying a liquid such as water.
- a polymer layer which is a stress generating layer, may be formed on the object 1 to be processed prior to the separation layer forming step S31 or prior to the peeling step S32.
- the peeling step S32 induces crack propagation in the separation layer 300 by cooling the object 1 including the polymer layer, and peels the SiC semiconductor device 12 from the object 1 to be processed starting from the separation layer 300. It's okay.
- the process conditions such as the composition and film thickness of the polymer layer, the cooling temperature, the cooling rate, and the cooling time are set or set so that the SiC semiconductor device 12 can be suitably separated from the object 1 to be processed.
- the separation step S3 preferably forms the polymer layer on the surface of the object to be processed 1 on which the SiC semiconductor device 12 is not formed so as to suppress the generation of stress in the SiC semiconductor device 12.
- the separation step S3 is an apparatus described in patent documents such as Japanese Patent Application Laid-Open No. 2013-49161, Japanese Patent Application Laid-Open No. 2018-207834, Japanese Patent Application Laid-Open No. 2017-500725, and Japanese Patent Application Laid-Open No. 2017-526161. And methods can be adopted at least in part. Further, in the separation step S3, for example, Japanese Patent Application Laid-Open No. 2017-526161, Japanese Patent Application Laid-Open No. 2017-500725, Japanese Patent Application Laid-Open No. 2018-152582, Japanese Patent Application Laid-Open No. 2019-500220, and Japanese Patent Application Laid-Open No. 2019-511122 At least a part of the devices and methods described in the patent documents such as the above can be adopted.
- Etching process S4 etches the object 1 to be processed so as to form a flattened, bunching-free surface exhibiting a reduced terrace length W3.
- the mechanism related to the etching step S4 will be described later.
- the object to be processed 1 separated by the separation step S3 is heat-treated, and the surface layer including the separation layer 300 remaining in the object to be processed 1 is etched.
- the separation layer 300 includes crystal dislocations 301 and damaged regions 302.
- the surface of the growth layer 10 can be terminated by a step exhibiting the height of the full unit in the SiC single crystal.
- the separation layer 300 is also understood as a strain layer or a damage layer.
- the etching step S4 includes a strain layer removing step S41 in which the object to be processed 1 is installed in a semi-closed space having an atomic number ratio Si / C of 1 or less and heated to etch the object 1 to be processed. Further, the etching step S4 includes a bunching decomposition step S42 in which the object to be processed 1 is installed in a semi-closed space having an atomic number ratio Si / C of more than 1 and heated to etch the object 1 to be etched.
- the separation layer 300 is etched, and the object to be processed 1 is etched so that the bunched (bunched) surface is exposed.
- the bunching decomposition step S42 etches the object to be processed 1 so as to form a flattened bunching-free surface, and decomposes the MSB on the surface of the object to be processed 1. At this time, the surface is terminated by a step exhibiting the height of the full unit in the SiC single crystal.
- a plurality of steps including at least a growth step S1, a device forming step S2, and a separation step S3 may be repeated so as to form a ring.
- the growth step S1, the device forming step S2, the separation step S3, and the etching step S4 may be repeated so as to form a ring.
- at least a part of each step of the device forming step S2 may be performed after the separation step S3.
- One embodiment of the present invention is a SiC semiconductor device 12 having a known device structure including, for example, a Schottky barrier diode (SBD), a bipolar junction transistor (BJT), a FET, an insulated gate bipolar transistor (IGBT) and a combination thereof. Can be manufactured.
- SBD Schottky barrier diode
- BJT bipolar junction transistor
- IGBT insulated gate bipolar transistor
- one embodiment of the present invention manufactures a SiC semiconductor device 12 including an n-type or p-type substrate 111 that is adjacent to an electrode surface such as a drain electrode, an anode electrode, and a collector electrode. be able to.
- one embodiment of the present invention includes an n-type or p-type substrate 111, an n-type or p-type drift region 220, an n-type or p-type well region 221 or n-type or.
- a SiC semiconductor device 12 having an FET structure including a p-type contact region 222, an insulating film 230, a gate electrode 240, a source electrode 241 and a drain electrode 242 can be manufactured.
- one embodiment of the present invention is a SiC semiconductor device having an SBD structure including an n-type or p-type substrate 111, a low concentration region 226, an anode electrode 244, and a cathode electrode 245. 12 can be manufactured.
- the thickness of the n-type or p-type substrate 111 is not limited within the range of the thickness of the growth layer 10.
- the n-type or p-type substrate 111 contributes to the realization of an ohmic electrode as an example.
- One embodiment of the present invention can manufacture a SiC semiconductor device 12 having a planar gate type structure.
- the SiC semiconductor device 12 may have a known device structure such as an FET structure or an IGBT structure.
- the SiC semiconductor device 12 having a trench gate type structure can be manufactured so that the JFET resistance during device operation is reduced.
- the SiC semiconductor device 12 may have a known device structure such as an FET structure or an IGBT structure.
- a known SiC semiconductor device 12 having a super junction structure including an n-type or p-type pillar region can be manufactured so that the drift resistance during device operation is reduced.
- the SiC semiconductor device 12 may have a known device structure such as an FET structure or an IGBT structure.
- the SiC semiconductor device 12 including an n-type or p-type embedded region can be manufactured so that the electric field concentration effect during device operation is alleviated.
- the n-type or p-type embedded region in the SiC semiconductor device 12 may be installed below the gate electrode 240 along the film thickness direction as an example, or the source electrode 241 may be installed along the film thickness direction. It may be installed below, or it may be installed so as to exhibit a guard ring aligned with an n-type or p-type well region along a direction orthogonal to the film thickness direction.
- One embodiment of the present invention includes a growth layer having a basal dislocation density (BPD density) of ⁇ 100 / cm 2 and a growth layer having a BPD density of ⁇ 10 / cm 2 or ⁇ 1.0.
- a SiC semiconductor device 12 including a growth layer of / cm 2 can be manufactured.
- the growth layer is at least a part of the growth layer 10.
- the growth layer refers to at least a part of the SiC structure constituting the SiC semiconductor device 12 including the n-type or p-type region. Further, the growth layer refers to an n-type or p-type substrate 111 as an example.
- the growth layer is, for example, 1.0 ⁇ 10 17 / cm 3 or more, 2.0 ⁇ 10 17 / cm 3 or more, 5.0 ⁇ 10 17 / cm 3 or more, 1.0 ⁇ 10 18 /.
- n + or p + region having a dopant concentration of cm 3 or greater, 2.0 ⁇ 10 18 / cm 3 or greater, or 5.0 ⁇ 10 18 / cm 3 or greater.
- the cell pitch of the SiC semiconductor device 12 manufactured in one embodiment of the present invention is preferably 10 ⁇ m or less, more preferably 5.0 ⁇ m or less, more preferably 2.0 ⁇ m or less, and more preferably 1. It is 0 ⁇ m or less, more preferably 0.5 ⁇ m or less, further preferably 0.2 ⁇ m or less, still more preferably 0.1 ⁇ m or less, still more preferably 50 nm or less, still more preferably 20 nm or less. , More preferably 10 nm or less.
- the cell pitch is preferably 1.0 nm or more, more preferably 10 nm or more, more preferably 20 nm or more, more preferably 50 nm or more, more preferably 0.1 ⁇ m or more, and more. It is preferably 0.2 ⁇ m or more, more preferably 0.5 ⁇ m or more, more preferably 1.0 ⁇ m or more, still more preferably 2.0 ⁇ m or more, still more preferably 5.0 ⁇ m or more.
- the heat treatment step heat-treats the object to be processed 1 and the SiC raw material 4 so that a temperature difference is formed between the object to be processed 1 and the SiC raw material 4.
- the body 1 to be treated is placed on the low temperature side to grow crystals of the body 1 to be treated, and the growth layer 10 is formed on the surface of the body 1 to be treated.
- the object to be processed 1 is placed on the high temperature side to etch the object to be processed 1, for example, to remove the separation layer 300.
- the formation of the growth layer 10 on the back surface 1a and the etching of the SiC raw material 4 (main surface 4a) are performed at the same time.
- the object to be treated 1 and the SiC raw material 4 are heat-treated in a semi-closed space in an atmosphere containing Si element and C element.
- the "quasi-closed space” in the description of the present specification refers to a space in which the inside of the space can be evacuated, but at least a part of the vapor generated inside the space can be confined.
- the raw material is continuously transported based on the following reactions 1) to 5), and the growth layer 10 is formed.
- Si atoms (Si (v)) are desorbed from the surface of the SiC raw material 4 by thermally decomposing the surface of the SiC raw material 4.
- the C atom (C (s)) remaining on the surface of the SiC raw material 4 due to the desorption of the Si atom (Si (v)) is the Si vapor (Si (v)) in the raw material transport space. )), It becomes Si 2 C or SiC 2 or the like and sublimates into the raw material transport space.
- the growth step S1 includes a Si atom sublimation step of thermally sublimating the Si atom from the SiC raw material 4, and a C atom that sublimates the C atom remaining on the main surface 4a of the SiC raw material 4 by combining it with the Si atom in the raw material transport space. Including the sublimation process.
- the growth layer 10 is formed on the back surface 1a of the object 1 to be processed based on the step flow growth.
- Each step included in the growth step S1 is sequentially performed.
- the growth step S1 is understood to be a step based on PVT (physical vapor phase transport) because the transported Si 2 C or SiC 2 or the like becomes supersaturated and condenses to form the growth layer 10. Further, with such a configuration, the growth step S1 can suppress the formation of MSB on the surface of the object to be treated 1 and obtain a flattened SiC surface exhibiting a reduced terrace length.
- the etching step S4 includes a Si atom sublimation step of thermally sublimating Si atoms from the surface of the object to be processed 1 and a C atom to sublimate the C atoms remaining on the surface of the object to be processed 1 by combining them with Si atoms in the raw material transport space. Including a sublimation step, the surface of the object to be treated 1 is etched. With such a configuration, the etching step S4 can decompose the MSB on the surface of the object to be processed 1 to obtain a flattened SiC surface exhibiting a reduced terrace length.
- the mechanism related to each of the growth step S1 and the etching step S4 is the transportation of the raw material containing the Si element and the C element.
- the driving force for transporting the raw material is the vapor pressure difference between the object to be processed 1 and the SiC raw material 4 due to the formed temperature gradient. Therefore, not only the temperature difference on the surfaces of the object to be processed 1 and the SiC raw material 4 but also the chemical potential difference due to the crystal structure between the object to be processed 1 and the SiC raw material 4 can be a driving force for the transportation of the raw materials. Can be grasped.
- the SiC raw material 4 may be a SiC ingot produced by a sublimation method or the like, or may be a SiC wafer sliced into a disk shape from the SiC ingot. It may be a SiC polycrystal. Further, the SiC raw material 4 may be a processed product such as a sintered body containing SiC polycrystals. Further, in each of the growth step S1 and the etching step S4, the SiC material forming the semi-closed space and the SiC material exposed in the semi-closed space can be the SiC raw material 4.
- the dopant concentration in the growth layer 10 can be adjusted by supplying the dopant gas into the semi-closed space by the dopant gas supply means. It can be understood that when the dopant gas is not supplied, the growth layer 10 inherits the dopant concentration in the semi-closed space.
- the raw material transport in each of the growth step S1 and the etching step S4 is preferably carried out in an environment having a gas phase species containing a Si element and a gas phase species containing a C element. Further, the raw material transportation in each of the growth step S1 and the etching step S4 is performed in a SiC-Si or SiC-C equilibrium vapor pressure environment.
- the "SiC-Si vapor pressure environment" in the description in the present specification refers to the vapor pressure environment when SiC (solid) and Si (liquid phase) are in a phase equilibrium state via a gas phase.
- the SiC-Si equilibrium vapor pressure environment is formed by heat-treating a semi-closed space having an atomic number ratio of Si / C of more than 1.
- the "SiC-C equilibrium vapor pressure environment” in the description in the present specification refers to the vapor pressure environment when SiC (solid phase) and C (solid phase) are in a phase equilibrium state via a gas phase. Point to.
- the SiC-C equilibrium vapor pressure environment is formed by heat-treating a semi-closed space having an atomic number ratio of Si / C of 1 or less.
- the heat treatment temperature in each of the growth step S1 and the etching step S4 is preferably 1400 ° C. or higher, more preferably 1500 ° C. or higher, more preferably 1600 ° C. or higher, more preferably 1700 ° C. or higher, and more. It is preferably 1800 ° C. or higher, more preferably 1900 ° C. or higher, still more preferably 2000 ° C. or higher, still more preferably 2100 ° C. or higher, still more preferably 2200 ° C. or higher.
- the heat treatment temperature is preferably 2300 ° C. or lower, more preferably 2200 ° C. or lower, more preferably 2100 ° C. or lower, more preferably 2000 ° C. or lower, and even more preferably 1900 ° C.
- the growth rate or etching rate related to each of the growth step S1 and the etching step S4 is determined by the heat treatment temperature.
- the temperature gradient between the object to be treated 1 and the SiC raw material 4 in each of the growth step S1 and the etching step S4 is preferably 0.1 ° C./mm or more, more preferably 0.2 ° C./mm or more, and more. It is preferably 0.5 ° C./mm or more, more preferably 1.0 ° C./mm or more, and even more preferably 2.0 ° C./mm or more.
- the temperature gradient is preferably 5.0 ° C./mm or less, more preferably 2.0 ° C./mm or less, more preferably 2.0 ° C./mm or less, and more preferably 1. It is 0 ° C./mm or less, more preferably 0.5 ° C./mm or less, still more preferably 0.2 ° C./mm or less.
- the temperature gradient may be uniform or may have a distribution.
- the manufacturing apparatus includes a main body container 141, a melting point container 142, and a heating furnace 143.
- the main body container 141 is made of a material containing SiC polycrystals, for example. Therefore, at least a part of the main body container 141 can be a transport source (SiC raw material 4) in raw material transportation.
- the environment in the heated main body container 141 is, for example, a vapor pressure environment of a mixed system of a gas phase species containing a Si element and a gas phase species containing a C element.
- the vapor phase species containing the Si element include Si, Si 2 , Si 3 , Si 2 C, SiC 2 , and SiC.
- the gas phase species containing the C element Si 2 C, SiC 2 , SiC, C and the like can be exemplified.
- the dopant and dopant concentration of the main body container 141 can be selected according to the dopant and dopant concentration of the growth layer 10 to be formed.
- the structure is such that the vapor pressure of the vapor phase species containing Si element and the vapor phase species containing C element is generated in the internal space during the heat treatment of the main body container 141, the structure can be adopted.
- a configuration in which the SiC polycrystal is exposed on a part of the inner surface a configuration in which the SiC polycrystal is separately installed in the main body container 141, and the like can be shown.
- the main body container 141 is provided with an installation tool 141a on which the object to be processed 1 can be installed. Further, the main body container 141 is a fitting container including an upper container 141c and a lower container 141b that can be fitted to each other. A minute gap is formed in the fitting portion between the upper container 141c and the lower container 141b, and the inside of the main container 141 can be exhausted (evacuated) from this gap.
- the main body container 141 has a Si steam supply source.
- the Si steam supply source is used for the purpose of adjusting the atomic number ratio Si / C of the semi-closed space in the main container 141 so as to exceed 1.
- Examples of the Si vapor supply source include solid Si (Si pellets such as Si pieces and Si powder) and Si compounds.
- the atomic number ratio Si / in the main body container 141 C exceeds 1.
- the object to be treated 1 and the SiC raw material 4 satisfying the stoichiometric ratio 1: 1 and the Si steam supply source are placed in the main body container 141 of the SiC polycrystal satisfying the stoichiometric ratio 1: 1.
- the atomic number ratio Si / C in the main body container 141 will exceed 1.
- the SiC-Si equilibrium vapor pressure environment according to the embodiment of the present invention is formed by heating a semi-closed space having an atomic number ratio Si / C of more than 1. Further, the SiC-C equilibrium vapor pressure environment according to the embodiment of the present invention is formed by heating a semi-closed space having an atomic number ratio of Si / C of 1 or less.
- the main body container 141 according to the embodiment of the present invention may be configured to appropriately accommodate predetermined members so as to have a SiC-Si equilibrium vapor pressure environment or a SiC-C equilibrium vapor pressure environment, respectively.
- the heating furnace 143 is configured to heat so as to form a temperature gradient so that the temperature decreases / increases from the upper container 141c of the main container 141 toward the lower container 141b. As a result, a temperature gradient is formed in the thickness direction of the object 1 to be processed.
- the heating furnace 143 preserves the main heating chamber 143c capable of heating the object to be processed 1 and the like to a temperature of 1000 ° C. or higher and 2300 ° C. or lower, and the object to be processed to a temperature of 500 ° C. or higher.
- a spare chamber 143a capable of heating, a melting point container 142 capable of accommodating the main body container 141, and a moving means 143b (moving table) capable of moving the melting point container 142 from the spare chamber 143a to the main heating chamber 143c are provided. ing.
- the main heating chamber 143c is formed in a regular hexagon in a plan sectional view, and a melting point container 142 is installed inside the heating chamber 143c.
- a heating heater 143d (mesh heater) is provided in the heating chamber 143c.
- a multilayer heat-reflecting metal plate is fixed to the side wall and ceiling of the main heating chamber 143c (not shown). The multilayer heat-reflecting metal plate is configured to reflect the heat of the heating heater 143d toward the substantially central portion of the main heating chamber 143c.
- the heating heater 143d is installed in the main heating chamber 143c so as to surround the high melting point container 142 in which the object to be processed is housed. At this time, by installing the multilayer heat-reflecting metal plate on the outside of the heating heater 143d, it is possible to raise the temperature in the temperature range of 1000 ° C. or higher and 2300 ° C. or lower.
- the heating heater 143d a resistance heating type heater or a high frequency induction heating type heater can be adopted as an example.
- the heating heater 143d may adopt a configuration capable of forming a temperature gradient in the melting point container 142.
- the heating heater 143d may be configured so that many heaters are installed on the upper side (or lower side). Further, the heating heater 143d may be configured so that the width increases toward the upper side (or the lower side). Alternatively, the heating heater 143d may be configured so that the electric power supplied can be increased toward the upper side (or the lower side).
- the main heating chamber 143c includes a vacuum forming valve 143f for exhausting the inside of the main heating chamber 143c, an inert gas injection valve 143e for introducing an inert gas into the main heating chamber 143c, and the main heating chamber 143c.
- a vacuum gauge of 143 g for measuring the degree of vacuum is connected.
- the vacuum forming valve 143f is connected to a vacuum drawing pump that exhausts the inside of the main heating chamber 143c to create a vacuum (not shown).
- the degree of vacuum in the main heating chamber 143c is preferably adjusted to 10 Pa or less, more preferably 1.0 Pa or less, and most preferably 10-3 Pa or less by the vacuum forming valve 143f and the vacuum pulling pump. Can be done.
- a turbo molecular pump can be exemplified.
- the inert gas injection valve 143e is connected to the inert gas supply source (not shown). ). With the inert gas injection valve 143e and the inert gas supply source, the inert gas can be introduced into the heating chamber 143c in the range of 10-5 to 10 4 Pa. As this inert gas, Ar or the like can be selected.
- the inert gas injection valve 143e is a dopant gas supply means capable of supplying the dopant gas into the main body container 141. That is, the dopant concentration of the growth layer 10 can be increased by selecting the dopant gas (for example, N 2 or the like) as the inert gas.
- the dopant gas for example, N 2 or the like
- the spare chamber 143a is connected to the main heating chamber 143c, and the melting point container 142 can be moved by the moving means 143b.
- the spare chamber 143a of the present embodiment is configured so that the temperature can be raised by the residual heat of the heating heater 143d of the main heating chamber 143c. As an example, when the temperature of the main heating chamber 143c is raised to 2000 ° C., the temperature of the spare chamber 143a is raised to about 1000 ° C. Degassing treatment can be performed.
- the moving means 143b is configured to be movable between the main heating chamber 143c and the spare chamber 143a by placing the melting point container 142.
- the transfer between the main heating chamber 143c and the spare chamber 143a by the moving means 143b is completed in about 1 minute at the shortest, it is possible to realize the temperature rise / fall at 1.0 to 1000 ° C./min. As a result, rapid temperature rise and rapid temperature decrease can be performed, so that it is possible to observe a surface shape that does not have a history of low temperature growth during temperature rise and temperature decrease.
- the spare chamber 143a is installed below the main heating chamber 143c, but the spare chamber 143a is not limited to this and may be installed in any direction.
- the moving means 143b is a moving table on which the high melting point container 142 is placed.
- the contact portion between the moving table and the melting point container 142 serves as a heat propagation path.
- a temperature gradient can be formed in the high melting point container 142 so that the contact portion side between the moving table and the high melting point container 142 is on the low temperature side.
- the heating furnace 143 of the present embodiment since the bottom of the melting point container 142 is in contact with the moving table, a temperature gradient is provided so that the temperature decreases from the upper container 142b of the melting point container 142 toward the lower container 142a. ..
- the direction of the temperature gradient can be set to any direction by changing the position of the contact portion between the moving table and the melting point container 142.
- the temperature gradient is provided so that the temperature rises from the upper container 142b of the high melting point container 142 toward the lower container 142a. It is desirable that this temperature gradient is formed along the thickness direction of the object to be treated 1 and the SiC raw material 4. Further, as described above, the temperature gradient may be formed by the configuration of the heater 143d.
- the vapor pressure environment of the vapor phase species containing the Si element in the heating furnace 143 is formed by using the high melting point container 142 and the Si steam supply material.
- any method capable of forming a vapor pressure environment of a vapor phase species containing a Si element around the main body container 141 can be adopted in one embodiment of the present invention.
- the high melting point container 142 is preferably composed of a high melting point material having a melting point equal to or higher than the melting point of the material constituting the main body container 141.
- Refractory vessel 142 as an example, a general purpose heat-resistant member C, W is a refractory metal, Re, Os, Ta, Mo , Ta 9 C 8 is a carbide, HfC, TaC, NbC, ZrC , Ta 2 C , illustrated TiC, WC, MoC, a nitride HfN, TaN, BN, Ta 2 N, ZrN, TiN, the HfB 2, TaB 2, ZrB 2 , NB 2, TiB 2, SiC polycrystal like borides can do.
- the melting point container 142 is a fitting container including an upper container 142b and a lower container 142a that can be fitted to each other, like the main body container 141, and can accommodate the main body container 141. It is configured.
- a minute gap 43 is formed in the fitting portion between the upper container 142b and the lower container 142a, and the inside of the high melting point container 142 can be exhausted (evacuated) from the gap 43.
- the high melting point container 142 has a Si steam supply material capable of supplying the vapor pressure of a vapor phase species containing a Si element in the high melting point container 142.
- the Si vapor supply material may have a configuration in which Si vapor is generated in the refractory container 142 during heat treatment, and examples thereof include solid Si (Si pellets such as Si pieces and Si powder) and Si compounds. Can be done. Further, the Si steam supply material is, for example, a thin film that covers the inner wall of the melting point container 142.
- the Si steam supply material is, for example, a metal atom and a silidic material of Si atoms constituting the refractory vessel 142.
- the Si steam supply material inside the high melting point container 142, it is possible to maintain the vapor pressure environment of the vapor phase species containing the Si element in the main body container 141. It can be understood that this is because the vapor pressure of the vapor phase species containing the Si element inside the main body container 141 and the vapor pressure of the vapor phase species containing the Si element outside the main body container 141 are balanced.
- Reference example 1 Under the following conditions, the SiC single crystal substrate E10 is housed in the main body container 141, and the main body container 141 is housed in the high melting point container 142.
- SiC polycrystalline container Size Diameter (60mm), Height (4.0mm) Distance between SiC single crystal substrate E10 and SiC material: 2.0 mm Atomic number ratio in the container Si / C: 1 or less
- TaC Container size diameter (160 mm), height (60 mm) Si vapor supply material (Si compound): TaSi 2
- the SiC single crystal substrate E10 installed under the above conditions is heat-treated under the following conditions. Heating temperature: 1700 ° C Heating time: 300 min Temperature gradient: 1.0 ° C / mm Growth rate: 5.0 nm / min Vacuum degree of this heating chamber 143c: 10-5 Pa
- FIG. 13 is an explanatory diagram of a method for obtaining a conversion rate obtained by converting BPD into other defects / dislocations (TED, etc.) in the growth layer E11.
- FIG. 13A shows how the growth layer E11 was grown by the heating step.
- the BPD existing in the SiC single crystal substrate E10 is converted into TED with a certain probability. Therefore, TED and BPD are mixed on the surface of the growth layer E11 unless 100% conversion is performed.
- FIG. 13B shows how defects in the growth layer E11 were confirmed using the KOH dissolution etching method.
- a SiC single crystal substrate E10 is immersed in a molten salt (KOH, etc.) heated to about 500 ° C. to form etch pits in dislocations and defective portions, and dislocations occur depending on the size and shape of the etch pits.
- KOH molten salt
- FIG. 13 (c) shows how the growth layer E11 is removed after KOH dissolution etching.
- the surface of the SiC single crystal substrate E10 is exposed by removing the growth layer E11 by thermal etching after flattening to the depth of the etch pit by mechanical polishing, CMP, or the like.
- FIG. 13 (d) shows a state in which defects in the SiC single crystal substrate E10 were confirmed by using the KOH dissolution etching method on the SiC single crystal substrate E10 from which the growth layer E11 was removed. By this method, the number of BPDs existing on the surface of the SiC single crystal substrate E10 is evaluated.
- the number of BPDs present on the surface of the growth layer E11 (see FIG. 13B) and the number of BPDs present on the surface of the SiC single crystal substrate E10 (FIG. 13D).
- the BPD conversion rate converted from BPD to other defects / dislocations by heat treatment can be obtained.
- the number of BPDs present on the surface of the growth layer E11 of Reference Example 1 was about 0 / cm 2
- the number of BPDs present on the surface of the SiC single crystal substrate E10 was 1000 / cm 2 . That is, it can be understood that the BPD is reduced or removed by installing the SiC single crystal substrate E10 having no MSB on the surface in a semi-closed space having an atomic number ratio of Si / C of 1 or less and heating the substrate.
- SiC polycrystalline container Size Diameter (60mm), Height (4.0mm) Distance between SiC single crystal substrate E10 and SiC material: 2.0 mm
- Si steam source Si piece Exceeds the atomic number ratio Si / C: 1 in the container
- the atomic number ratio Si / C in the container exceeds 1.
- TaC Container size diameter 160 mm x height 60 mm Si vapor supply material (Si compound): TaSi 2
- the SiC single crystal substrate E10 installed under the above conditions is heat-treated under the following conditions. Heating temperature: 1800 ° C Heating time: 60 min Temperature gradient: 1.0 ° C / mm Growth rate: 68 nm / min Vacuum degree of this heating chamber 143c: 10-5 Pa
- FIG. 14 is an SEM image of the surface of the SiC single crystal substrate E10 before the growth of the growth layer E11.
- FIG. 14A is an SEM image observed at a magnification of ⁇ 1000
- FIG. 14B is an SEM image observed at a magnification of ⁇ 100,000. It can be seen that the MSB is formed on the surface of the SiC single crystal substrate E10 before the growth of the growth layer E11, and the steps having a height of 3.0 nm or more are arranged with a terrace width of 42 nm on average. it can. The step height was measured by AFM.
- FIG. 15 is an SEM image of the surface of the SiC single crystal substrate E10 after the growth layer E11 has grown.
- FIG. 15A is an SEM image observed at a magnification of ⁇ 1000
- FIG. 15B is an SEM image observed at a magnification of ⁇ 100,000. It can be seen that the MSB is not formed on the surface of the growth layer E11 of Reference Example 2, and the steps of 1.0 nm (full unit cell) are regularly arranged with a terrace width of 14 nm. The step height was measured by AFM.
- the growth layer E11 in which the MSB is decomposed is formed by installing the SiC single crystal substrate E10 having the MSB on the surface in a semi-closed space having an atomic number ratio Si / C of more than 1 and heating it. be able to.
- FIG. 16 is a graph showing the relationship between the heating temperature and the growth rate grown by the method for producing a SiC single crystal substrate according to the present invention.
- the horizontal axis of this graph is the reciprocal of temperature, and the vertical axis of this graph is the logarithmic representation of the growth rate.
- the results of growing the growth layer E11 on the SiC single crystal substrate E10 by installing the SiC single crystal substrate E10 in a space where the atomic number ratio Si / C exceeds 1 (inside the main body container 141) are indicated by ⁇ .
- the result of growing the growth layer E11 on the SiC single crystal substrate E10 by installing the SiC single crystal substrate E10 in a space where the atomic number ratio Si / C is 1 or less (inside the main body container 141) is indicated by a cross. ing.
- the graph of FIG. 16 shows the result of the thermodynamic calculation of the SiC substrate growth in the SiC-Si equilibrium vapor pressure environment by a broken line (Arenius plot), and shows the thermodynamic calculation of the SiC substrate growth in the SiC-Si equilibrium vapor pressure environment. The results are shown by the alternate long and short dash line (Arenius plot).
- the chemical potential difference and the temperature gradient are used as the growth driving force.
- the SiC single crystal substrate E10 is grown. This chemical potential difference can exemplify the difference in voltage division of gas phase species generated on the surface of a SiC polycrystal and a SiC single crystal.
- the SiC growth rate can be obtained by the following equation 1.
- T is the temperature of the SiC raw material side
- k is Boltzmann's constant.
- P transported original i -P transport destination i is the raw material gas becomes a supersaturated state, a growth amount deposited as SiC, as a raw material gas SiC, Si 2 C, SiC 2 is assumed.
- the broken line indicates when a SiC single crystal is grown from a SiC polycrystal as a raw material in a vapor pressure environment when SiC (solid) and Si (liquid phase) are in a phase equilibrium state via a gas phase. It is the result of the thermodynamic calculation of. Specifically, the result was obtained by thermodynamic calculation under the following conditions (i) to (iv) using Equation 1.
- the growth driving force is the temperature gradient in the main body container 141 and the difference in vapor pressure (chemical potential difference) between the SiC polycrystal and the SiC single crystal.
- the raw material gas is SiC, SiC 2 C, SiC 2.
- the adsorption coefficient at which the raw material is adsorbed on the step of the SiC single crystal substrate E10 is 0.001.
- the two-point chain wire grows a SiC single crystal from a SiC polycrystal as a raw material in a vapor pressure environment when SiC (solid phase) and C (solid phase) are in a phase equilibrium state via a gas phase. It is the result of thermodynamic calculation when it is made to. Specifically, the result was obtained by thermodynamic calculation under the following conditions (i) to (iv) using Equation 1.
- the growth driving force is the temperature gradient in the main body container 141 and the vapor pressure difference (chemical potential difference) between the SiC polycrystal and the SiC single crystal (i).
- the raw material gas is SiC, SiC 2 C, SiC 2.
- the adsorption coefficient at which the raw material is adsorbed on the step of the SiC single crystal substrate E10 is 0.001.
- the values in the JANAF thermochemical table were adopted.
- the SiC single crystal substrate E10 was placed in a space where the atomic number ratio Si / C exceeds 1 (inside the main body container 141), and the growth layer E11 was grown on the SiC single crystal substrate E10. It can be grasped that the result (marked with ⁇ ) is in agreement with the result of the thermodynamic calculation of SiC growth in the SiC-Si equilibrium vapor pressure environment.
- a growth rate of 1.0 ⁇ m / min or more is achieved at a heating temperature of 1960 ° C. Further, it can be understood that a growth rate of 2.0 ⁇ m / min or more is achieved at a heating temperature of 2000 ° C. or higher.
- a growth rate of 1.0 ⁇ m / min or more is achieved at a heating temperature of 2000 ° C. Further, it can be understood that a growth rate of 2.0 ⁇ m / min or more is achieved at a heating temperature of 2030 ° C. or higher.
- the present invention it is possible to provide a high-quality SiC semiconductor device by combining the growth step S1, the device forming step S2, and the separation step S3.
- Processed object 1a Back surface 4: SiC raw material 4a: Main surface 10: Growth layer 11: Original substrate 12: SiC semiconductor device formed on the growth layer 10 23: Insulation film 43: Gap 101a: Step 101b: Terrace 102a : Step 102b: Terrace 103a: Step 103b: Terrace 111: Substrate 141: Main body container 141a: Installation tool 141b: Lower container 141c: Upper container 142: High melting point container 142a: Lower container 142b: Upper container 143: Heating furnace 143a: Spare Chamber 143b: Transportation means 143c: Main heating chamber 143d: Heating heater 143e: Inert gas injection valve 143f: Vacuum forming valve 143g: Vacuum gauge 211: Circuit pattern 220: Drift region 221: Well region 222: Contact region 226: Low concentration region 230: Insulation film 240: Gate electrode 241: Source electrode 242: Drain electrode 244: Anode electrode 245: Cathode electrode 300: Separat
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Abstract
Description
このような構成とすることで、本発明は、歪、結晶欠陥、BPD及びMSBを解消又はその発生を抑止しながら高品質なSiCウェハを製造した上でSiC半導体装置を製造することができる。
本発明の技術的範囲は、添付図面に示した実施形態に限定されるものではなく、特許請求の範囲に記載された範囲内において、適宜変更が可能である。
なお、本明細書中の説明における「SiC半導体装置12」は、SiCデバイスを含むSiC材料を少なくとも含む半導体装置のことを指す。
1)成長工程S1は、原基板11上に成長層10を形成する。
2)デバイス形成工程S2は、成長層10を加工しSiC半導体装置12の少なくとも一部を形成する。
3)分離工程S3は、デバイス形成工程S2により形成された、SiC半導体装置12の少なくとも一部を、被処理体1から分離する。
図2に示すように、成長工程S1は、エピタキシャル成長工程S11及びバンチング分解工程S12を行い、原基板11上に成長層10を形成する。なお、本明細書では、成長工程S1に係る機構を後述する。また、図2では、電界効果トランジスタ(FET)構造を有するSiC半導体装置12を例示する。
なお、本明細書中の説明における「MSB」は、SiC表面上のステップの内、バンチングすることで各ポリタイプのフルユニットを超えた高さを形成するようなステップを指す。
すなわち、MSBとは、4H-SiCの場合には4分子層を超えて(5分子層以上)バンチングしたステップであり、6H-SiCの場合には6分子層を超えて(7分子層以上)バンチングしたステップである。
また、当該厚みは、好ましくは20μm以上であり、より好ましくは50μm以上であり、より好ましくは100μm以上であり、より好ましくは150μm以上であり、さらに好ましくは200μm以上であり、さらに好ましくは350μm以上である。
また、成長工程S1により形成された、<100/cm2のBPD密度を有する成長層10の一部は、基板111として扱われてよい。基板111は、例として、1.0×1017/cm3以上のドーパント濃度を有する。
図3に示すように、デバイス形成工程S2は、成長層10が形成された被処理体1上に回路パターン211を形成するパターニング工程S21を行う。
パターニング工程S21は、例として、フォトレジストを塗布するレジスト塗布工程、フォトマスクを介してフォトレジストを露光する露光工程、及び、露光されたフォトレジストを現像する現像工程を含む。
フォトレジストは、例として、当該光源がg線(波長:436nm)である場合、ノボラック樹脂及び1,2‐ナフトキノンジアジドスルホン酸エステル(NQD)系化合物を含む高分子材料である。また、フォトレジストは、例として、当該光源がArFレーザ(波長:193nm)である場合、ノルボルネン等の200nm波長付近の光吸収を抑えられるような脂環基を有するベース樹脂を含む高分子材料である。
このとき、レジスト塗布工程は、スピンコーティングに係る回転速度や滴下量等のプロセス条件を、フォトレジストに係る所望の膜厚等が得られるよう、設定又は最適化する。
なお、レジスト塗布工程は、フォトレジストの塗布に先行して、被処理体1表面に疎水性が付与されるよう、ヘキサメチルジシラザン(HMDS)等の水酸基を除去するようなシリカ化剤を被処理体1表面に塗布してもよい。
また、レジスト塗布工程は、プリベーキングに係る加熱温度や加熱時間等のプロセス条件を、フォトレジストに係る所望の膜厚や表面粗さが得られるよう、又は、回路パターン211が好適に転写されるよう、設定又は最適化する。
また、露光工程は、露光時間等のプロセス条件を、回路パターン211が好適に転写されるよう適宜、設定又は最適化する。
また、露光工程は、当該ベーキングに係る加熱温度や加熱時間等のプロセス条件を、回路パターン211が好適に転写されるよう、設定又は最適化する。
また、現像工程は、現像液温度や現像時間等のプロセス条件を、回路パターン211が好適に転写されるよう、設定又は最適化する。
また、現像工程は、当該ベーキングに係る加熱温度や加熱時間等のプロセス条件を、回路パターン211が好適に転写されるよう、設定又は最適化する。
このとき、選択的エッチング工程は、エッチャント、エッチング時間、エッチング温度等のプロセス条件を、所望の材料選択性や面方位依存性やエッチングレート等を実現するよう、設定又は最適化する。当該エッチャントを含む溶液は、例として、TMAH溶液、水酸化カリウム(KOH)溶液、過マンガン酸カリウム(KMnO4)溶液、フッ化水素(HF)溶液等である。
このとき、選択的エッチング工程は、エッチャント(反応ガス)や反応ガスに係る分圧や熱処理温度等のプロセス条件を、所望の材料選択性や面方位依存性やエッチングレート等を実現するよう、設定又は最適化する。当該エッチャントは、例として、H2、HCl、Cl2、O2、CIF3等の混合物である。
また、選択的エッチング工程は、バイアスパワー、ガス種、ガス分圧、放電時間等のプロセス条件を、所望の異方性やエッチングレート等を実現するよう、設定又は最適化する。
なお、選択的エッチング工程は、被処理体1上にU溝やV溝等の三次元形状を形成するよう、異方性エッチング又は深堀りエッチングを行ってよい。
図3に示すように、デバイス形成工程S2は、被処理体1においてn型及び/又はp型領域を形成するよう、又は、pn接合領域を形成するよう、被処理体1にドーパント原子を導入するドーピング工程S22を行う。
なお、SiC単結晶中においてn型又はp型の領域を形成するような元素は、当該ドーパントイオンとして適宜、採用され得る。
なお、イオン注入工程は、C元素、Si元素、Cl元素、Ar元素等の非ドーパント元素も同様にイオン化し被処理体1上に照射し得る。
また、ビーム引出工程は、例として、引出電圧を当該イオン源に印加することで当該イオンビームを引き出す。また、ビーム引出工程は、例として、当該イオン源をプラズマ環境下でイオン化させ当該イオンビームを引き出す。
当該イオン源は、固体材料であってもよいし、気体材料であってもよいし、液体金属イオン源(LMIS)であってもよいし、イオン化を促進するようなプラズマ環境を形成するためのサポートガスと固体材料とを組み合わせる構成としてもよい。なお、当該プラズマ環境は、直流電源や交流電源等を利用する既知の方式に基づき適宜、形成される。
質量分析工程は、扇形磁場、四重極、飛行時間(TOF)、イオントラップ型等の既知の質量分析であれば適宜、採用することができる。
また、イオン注入工程は、上記加速エネルギー、注入角度、ドーズ量等のプロセス条件を、所望のドーパントプロファイルが形成されるよう、設定又は最適化する。
当該2以上のイオン種は、例として、複数種のドーパントイオンであってもよいし、Cイオン及びドーパントイオンであってもよく、その組み合わせに制限はない。
また、イオン注入工程は、ドーパント濃度が一定となるようなボックスプロファイルを形成するよう、ドーパントイオンを被処理体1に対して照射してもよい。なお、本明細書中の説明における「所望のドーパントプロファイル」とは、製造対象であるSiC半導体装置の構造に応じて適宜、変化し得る。
また、活性化工程は、加熱温度、加熱時間、分圧等のプロセス条件を、所望のドーパントプロファイルが形成されるよう、又は、当該ドーパントイオンの活性化率が高まるよう、設定又は最適化される。
活性化工程は、例として、被処理体1表面のカーボン化を防ぐよう、被処理体1表面条にカーボン層やSiO2等のパッシベーション膜を成膜する。
また、ドーピング工程S22は、既知のSi系電子デバイスにおいてみられるようなプロファイルを呈するn型又はp型領域を形成するよう、被処理体1に対してドーパント原子を導入する。
なお、本明細書中の説明におけるn型領域やドリフト領域等に含まれる「領域」は、n型層やドリフト層等に含まれる「層」と同一である、と把握することができる。
なお、当該ドーパント濃度は、例として、n型コンタクト領域及びドリフト領域等の異なる領域間で相違する場合がある。
また、デバイス形成工程S2は、複数の回路パターン211に基づき、SiCエピタキシャル成長、パターニング工程S21及びドーピング工程S22を繰り返してよい。
また、デバイス形成工程S2は、パターニング工程S21を行わず、SiCエピタキシャル成長及びドーピング工程S22を行ってよい。
なお、デバイス形成工程S2は、ドーピング工程S22が行われる都度、回路パターン211を呈するフォトレジスト及び/又はハードマスクをエッチングする。
図4に示すように、デバイス形成工程S2は、被処理体1に絶縁膜230を導入する絶縁膜形成工程S23を行う。
当該絶縁膜230は、例として、FET構造等を有するSiC半導体装置においてゲート絶縁膜、素子分離用の層間絶縁膜、又は、ゲート電極240におけるフラットバンド電圧等を調整するためのキャップ層として機能する。
このとき、絶縁膜形成工程S23は、酸化温度、酸化時間、酸化種ガスの分圧等のプロセス条件を、SiC/SiO2界面における界面準位密度が低減されるよう、SiC/SiO2界面ラフネスが低減されるよう、熱酸化SiO2膜中のカーボン残留が抑えられるよう、又は、熱酸化反応におけるCOガス発生を促進させるよう、設定又は最適化する。
絶縁膜形成工程S23は、例として、SiC/SiO2界面における界面準位密度が低減されるよう、上記熱酸化SiO2膜を形成した後に窒化処理を行ってもよい。当該窒化処理は、一酸化窒素(NO)雰囲気下での熱処理であってよいし、NO等の酸化窒素を励起させたプラズマ環境を利用した処理であってもよい。
図4及び図5に示すように、デバイス形成工程S2は、被処理体1上に電極を形成する電極形成工程S24を行う。
また、電極形成工程S24は、シリサイド化反応における熱処理温度や熱処理時間等のプロセス条件を、ショットキー電極が形成されるよう、又は、ドーパント偏析効果によりオーミック電極が形成されるよう、設定又は最適化する。
分離工程S3は、被処理体1の一部を分離する。
分離工程S3は、複数本のワイヤを往復運動させることで切断するマルチワイヤソー切断や、プラズマ放電を断続的に発生させて切断する放電加工法、レーザを照射し切断の基点となる層を形成する手法を、採用することができる。
分離層形成工程S31は、上面から分離すべきSiC半導体装置12の厚みに相当する深さとして被処理体1の内部が焦点となるよう、被処理体1において透過性を有する波長のレーザを被処理体1に対して照射し集光させ分離層300を形成する。
このとき、分離層形成工程S31は、好ましくは、SiC半導体装置12が形成されていない被処理体1の表面に対してレーザを照射する。
また、分離層形成工程S31は、例として、赤外レーザを当該レーザとして採用する。
なお、当該レーザの波長は、紫外光に類される波長であってもよいし、可視光に類される波長であってもよく、制限はない。
また、分離層形成工程S31は、レーザ波長、レーザ出力、レーザ走査速度、ビームスポット径、パルス幅、ピッチ幅等のプロセス条件を、被処理体1からSiC半導体装置12を好適に分離できるよう、設定又は最適化する。
剥離工程S32は、分離層300を起点に被処理体1の一部であるSiC半導体装置12を剥離する。このとき、剥離工程S32は、分離層300に沿ってワイヤを往復運動させる、又は、超音波振動を発生させる等することで被処理体1に機械振動を付与し、分離層300を起点に被処理体1からSiC半導体装置12を剥離する。
このとき、剥離工程S32は、当該ポリマー層を含む被処理体1を冷却することで分離層300における亀裂伝播を誘起し、分離層300を起点に被処理体1からSiC半導体装置12を剥離してよい。
また、このとき、剥離工程S32は、ポリマー層の組成や膜厚、冷却温度、冷却速度、冷却時間等のプロセス条件を、被処理体1からSiC半導体装置12を好適に分離できるよう、設定又は最適化する。
また、このとき、分離工程S3は、好ましくは、SiC半導体装置12における応力発生を抑えるよう、当該ポリマー層をSiC半導体装置12が形成されていない被処理体1の表面上に形成する。
また、分離工程S3は、例えば、特開2013-49161号公報、特開2018-207034号公報、特表2017-500725号公報、及び、特表2017-526161号公報等の特許文献に記載の装置や方法等の少なくとも一部を採用することができる。
また、分離工程S3は、例えば、特表2017-526161号公報、特表2017-500725号公報、特開2018-152582号公報、特表2019-500220号公報、及び、特表2019-511122号公報等の特許文献に記載の装置や方法等の少なくとも一部を採用することができる。
図7に示すように、エッチング工程S4は、低減されたテラス長W3を呈する、平坦化されたバンチングフリーな表面を形成するよう、被処理体1をエッチングする。なお、エッチング工程S4に係る機構は、後述される。
また、本発明の一実施形態は、成長工程S1、デバイス形成工程S2、分離工程S3及びエッチング工程S4が、円環をなすよう、繰り返し行われてよい。
また、本発明の一実施形態は、デバイス形成工程S2の各工程の少なくとも一部が、分離工程S3の後に行われてもよい。
図9(a)に示すように、本発明の一実施形態は、n型又はp型の基板111、n型又はp型のドリフト領域220、n型又はp型のウェル領域221、n型又はp型のコンタクト領域222、絶縁膜230、ゲート電極240、ソース電極241及びドレイン電極242を含むFET構造を有するSiC半導体装置12を製造することができる。
また、図9(b)に示すように、本発明の一実施形態は、n型又はp型の基板111、低濃度領域226、アノード電極244及びカソード電極245を含むSBD構造を有するSiC半導体装置12を製造することができる。
n型又はp型の基板111の厚みは、成長層10の厚みの範囲で制限はない。n型又はp型の基板111は、例として、オーミック電極の実現に寄与する。
なお、当該SiC半導体装置12におけるn型又はp型の埋込み領域は、例として、膜厚方向に沿ってゲート電極240の下方に設置されてもよいし、膜厚方向に沿ってソース電極241の下方に設置されてもよいし、膜厚方向と直交する方向に沿ってn型又はp型のウェル領域と並ぶガードリングを呈するよう設置されてもよい。
当該成長層は、上記n型又はp型領域を含むSiC半導体装置12を構成するSiC構造の少なくとも一部を指す。
また、当該成長層は、例として、n型又はp型の基板111を指す。
また、当該成長層は、例として、1.0×1017/cm3以上、2.0×1017/cm3以上、5.0×1017/cm3以上、1.0×1018/cm3以上、2.0×1018/cm3以上、又は、5.0×1018/cm3以上のドーパント濃度を有するn+又はp+領域を指す。
本明細書は、以下、成長工程S1又はエッチング工程S4である熱処理工程に係る原料輸送機構を説明する。
成長工程S1としての熱処理工程は、被処理体1を低温側に設置することで、被処理体1を結晶成長させ、被処理体1表面に成長層10を形成する。
エッチング工程S4としての熱処理工程は、被処理体1を高温側に設置することで、被処理体1をエッチングし、例えば分離層300を除去する。
なお、本明細書中の説明における「準閉鎖空間」は、空間内部の真空引きは可能であるが、空間内部で発生した蒸気の少なくとも一部を閉じ込め可能な空間のことを指す。
2) 2C(s)+Si(v)→SiC2(v)
3) C(s)+2Si(v)→Si2C(v)
4) Si(v)+SiC2(v)→2SiC(s)
5) Si2C(v)→Si(v)+SiC(s)
2)及び3)の説明:Si原子(Si(v))が脱離することでSiC原料4表面に残存したC原子(C(s))は、原料輸送空間内のSi蒸気(Si(v))と反応することで、Si2C又はSiC2等となって原料輸送空間内に昇華する。
4)及び5)の説明:昇華したSi2C又はSiC2等が、温度勾配によって被処理体1の裏面1aのテラスに到達・拡散し、ステップに到達することで裏面1aの多形を引き継ぎ、ステップフロー成長の様相を呈しながら、成長層10が形成される。
なお、成長工程S1は、輸送されたSi2C又はSiC2等が過飽和となり凝結することで成長層10を形成するため、PVT(物理気相輸送)に基づく工程と解される。
また、このような構成とすることで、成長工程S1は、被処理体1表面上のMSBの形成を抑止し、低減されたテラス長を呈する平坦化されたSiC表面を得ることができる。
原料輸送の駆動力は、形成された温度勾配に起因する被処理体1及びSiC原料4間の蒸気圧差である、と把握することができる。よって、被処理体1及びSiC原料4のそれぞれの表面における温度差のみならず、被処理体1及びSiC原料4間の結晶構造等に起因する化学ポテンシャル差も原料輸送の駆動力となり得る、と把握することができる。
また、成長工程S1及びエッチング工程S4のそれぞれにおいて、準閉鎖空間を形成するSiC材料や、準閉鎖空間内で露出したSiC材料は、SiC原料4となり得る。
ドーパントガスを供給しない場合、成長層10は準閉鎖空間内のドーパント濃度を引き継ぐ、と把握することができる。
また、成長工程S1及びエッチング工程S4のそれぞれにおける原料輸送は、SiC‐Si又はSiC‐C平衡蒸気圧環境下で行われる。
本明細書中の説明における「SiC‐C平衡蒸気圧環境」は、SiC(固相)とC(固相)とが気相を介して相平衡状態となっているときの蒸気圧の環境を指す。SiC‐C平衡蒸気圧環境は、原子数比Si/Cが1以下である準閉鎖空間が熱処理されることで形成される。
また、当該熱処理温度は、好ましくは2300℃以下であり、より好ましくは2200℃以下であり、より好ましくは2100℃以下であり、より好ましくは2000℃以下であり、より好ましくは1900℃以下であり、さらに好ましくは1800℃以下であり、さらに好ましくは1700℃以下であり、さらに好ましくは1600℃以下であり、さらに好ましくは1500℃以下である。
なお、成長工程S1及びエッチング工程S4のそれぞれに係る、成長レート又はエッチングレートは、当該熱処理温度によって決定される。
なお、当該温度勾配は、一様であってもよいし、分布をもってもよい。
本明細書は、以下、成長工程S1及びエッチング工程S4において用いられる装置について、詳細に説明する。なお、先の製造方法に示した構成と基本的に同一の構成要素については、同一の符号を付してその説明を簡略化する。
また、C元素を含む気相種としては、Si2C、SiC2、SiC、C等を例示することができる。
本体容器141は、Si蒸気供給源を有する。Si蒸気供給源は、本体容器141内の準閉鎖空間の原子数比Si/Cを、1を超えるよう調整する目的で用いられる。Si蒸気供給源としては、固体のSi(Si片やSi粉末等のSiペレット)やSi化合物を例示することができる。
)。この不活性ガス注入用バルブ143e及び不活性ガス供給源により、本加熱室143c内に不活性ガスを10‐5~104Paの範囲で導入することができる。この不活性ガスとしては、Ar等を選択することができる。
また、図12において、予備室143aは本加熱室143cの下方に設置されているが、予備室143aはこれに限られず何れの方向に設置されてもよい。
また、Si蒸気供給材料は、例として、高融点容器142の内壁を被覆する薄膜である。
《参考例1》
以下の条件で、SiC単結晶基板E10は本体容器141に収容され、本体容器141は高融点容器142に収容されている。
多型:4H‐SiC
基板サイズ:横幅(10mm)、縦幅(10mm)、厚み(0.3mm)
オフ方向及びオフ角:<11‐20>方向4°オフ
成長面:(0001)面
MSBの有無:無し
分離層又は歪層:無し
容器サイズ:直径(60mm)、高さ(4.0mm)
SiC単結晶基板E10とSiC材料との距離:2.0mm
容器内の原子数比Si/C:1以下
容器サイズ:直径(160mm)、高さ(60mm)
Si蒸気供給材料(Si化合物):TaSi2
加熱温度:1700℃
加熱時間:300min
温度勾配:1.0℃/mm
成長速度:5.0nm/min
本加熱室143cの真空度:10‐5Pa
以下の条件で、SiC単結晶基板E10を本体容器141に収容し、さらに本体容器141を高融点容器142に収容した。
多型:4H‐SiC
基板サイズ:横幅(10mm)、縦幅(10mm)、厚み(0.3mm)
オフ方向及びオフ角:<11‐20>方向4°オフ
成長面:(0001)面
MSBの有無:有り
容器サイズ:直径(60mm)、高さ(4.0mm)
SiC単結晶基板E10とSiC材料との距離:2.0mm
Si蒸気供給源:Si片
容器内の原子数比Si/C:1を超える
容器サイズ:直径160mm×高さ60mm
Si蒸気供給材料(Si化合物):TaSi2
加熱温度:1800℃
加熱時間:60min
温度勾配:1.0℃/mm
成長速度:68nm/min
本加熱室143cの真空度:10‐5Pa
参考例2の成長層E11表面には、MSBは形成されておらず、1.0nm(フルユニットセル)のステップが、14nmのテラス幅で規則正しく配列していることが把握することができる。なお、ステップ高さは、AFMにより測定した。
図16は、本発明に係るSiC単結晶基板の製造方法にて成長させた加熱温度と成長速度の関係を示すグラフである。このグラフの横軸は温度の逆数であり、このグラフの縦軸は成長速度を対数表示している。SiC単結晶基板E10を原子数比Si/Cが1を超える空間(本体容器141内)に設置して、SiC単結晶基板E10に成長層E11を成長させた結果を〇印で示す。また、SiC単結晶基板E10を原子数比Si/Cが1以下である空間(本体容器141内)に設置して、SiC単結晶基板E10に成長層E11を成長させた結果を×印で示している。
(i)体積一定のSiC‐Si平衡蒸気圧環境であること
(ii)成長駆動力は、本体容器141内の温度勾配と、SiC多結晶とSiC単結晶の蒸気圧差(化学ポテンシャル差)であること
(iii)原料ガスは、SiC,Si2C,SiC2である
(iv)原料がSiC単結晶基板E10のステップに吸着する吸着係数は0.001である
(i)体積一定のSiC‐C平衡蒸気圧環境である
(ii)成長駆動力は、本体容器141内の温度勾配と、SiC多結晶とSiC単結晶の蒸気圧差(化学ポテンシャル差)である
(iii)原料ガスはSiC,Si2C,SiC2である
(iv)原料がSiC単結晶基板E10のステップに吸着する吸着係数は0.001である
なお、熱力学計算に用いた各化学種のデータはJANAF熱化学表の値を採用した。
1a :裏面
4 :SiC原料
4a :主面
10 :成長層
11 :原基板
12 :成長層10に形成されたSiC半導体装置
23 :絶縁膜
43 :間隙
101a :ステップ
101b :テラス
102a :ステップ
102b :テラス
103a :ステップ
103b :テラス
111 :基板
141 :本体容器
141a :設置具
141b :下容器
141c :上容器
142 :高融点容器
142a :下容器
142b :上容器
143 :加熱炉
143a :予備室
143b :移動手段
143c :本加熱室
143d :加熱ヒータ
143e :不活性ガス注入用バルブ
143f :真空形成用バルブ
143g :真空計
211 :回路パターン
220 :ドリフト領域
221 :ウェル領域
222 :コンタクト領域
226 :低濃度領域
230 :絶縁膜
240 :ゲート電極
241 :ソース電極
242 :ドレイン電極
244 :アノード電極
245 :カソード電極
300 :分離層
301 :結晶転位
302 :損傷領域
311 :光源
312 :集光手段
E10 :SiC単結晶基板
E11 :成長層
S1 :成長工程
S11 :エピタキシャル成長工程
S12 :バンチング分解工程
S2 :デバイス形成工程
S21 :パターニング工程
S22 :ドーピング工程
S23 :絶縁膜形成工程
S24 :電極形成工程
S3 :分離工程
S31 :分離層形成工程
S32 :剥離工程
S4 :エッチング工程
W1 :テラス長
W2 :テラス長
W3 :テラス長
Claims (15)
- SiC単結晶を含む被処理体上に成長層を形成する成長工程、前記成長層においてSiC半導体装置の少なくとも一部を形成するデバイス形成工程、及び、前記SiC半導体装置の少なくとも一部を前記被処理体から分離する分離工程を含むSiC半導体装置の製造方法。
- 前記成長工程は、Si元素及びC元素を含む雰囲気下で前記被処理体を熱処理する請求項1に記載の製造方法。
- 前記成長工程は、SiC材料が露出した準閉鎖空間内で前記被処理体を熱処理する請求項2に記載の製造方法。
- 前記デバイス形成工程は、前記成長層上に回路パターンを形成するパターニング工程を行う請求項1~3の何れか一項に記載の製造方法。
- 前記デバイス形成工程は、前記成長層にドーパント原子を導入するドーピング工程を行う請求項1~4の何れか一項に記載の製造方法。
- 前記デバイス形成工程は、前記成長層に絶縁膜を導入する絶縁膜形成工程を行う請求項1~5の何れか一項に記載の製造方法。
- 前記デバイス形成工程は、前記成長層上に電極を形成する電極形成工程を行う請求項1~6の何れか一項に記載の製造方法。
- 前記分離工程は、前記成長層を含む前記被処理体の内部に分離層を形成する分離層形成工程、及び、前記分離層を起点に前記成長層を含む前記被処理体の一部を剥離する剥離工程を含む請求項1~7の何れか一項に記載の製造方法。
- 前記分離層形成工程は、前記内部が焦点となるよう前記被処理体にレーザを照射し前記分離層を形成する請求項8に記載の製造方法。
- 前記被処理体をSi元素及びC元素を含む雰囲気下で熱処理し前記被処理体をエッチングするエッチング工程を行う請求項1~9の何れか一項に記載の製造方法。
- 前記エッチング工程は、SiC材料が露出した準閉鎖空間内で前記被処理体を熱処理する請求項10に記載の製造方法。
- 前記分離工程、エッチング工程及び成長工程をこの順で含む請求項10又は請求項11に記載の製造方法。
- 前記分離工程及び成長工程をこの順で含む請求項1~11の何れか一項に記載の製造方法。
- 基底面転位密度が<100/cm2である成長層を含み、
前記成長層は、n型又はp型の基板であるSiC半導体装置。 - 前記成長層のドーパント濃度は、1.0×1017/cm3以上である請求項14に記載のSiC半導体装置。
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Citations (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2013049161A (ja) | 2011-08-30 | 2013-03-14 | Hamamatsu Photonics Kk | 加工対象物切断方法 |
JP2013189323A (ja) * | 2012-03-12 | 2013-09-26 | Sumitomo Electric Ind Ltd | 炭化珪素単結晶の製造方法 |
JP2014179605A (ja) * | 2013-03-08 | 2014-09-25 | Infineon Technologies Austria Ag | 半導体デバイスおよびそれを製造するための方法 |
JP2015024932A (ja) | 2013-07-24 | 2015-02-05 | トヨタ自動車株式会社 | SiC基板の製造方法 |
JP2017500725A (ja) | 2013-10-08 | 2017-01-05 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | レーザー処理及び温度誘導ストレスを用いた複合ウェハー製造方法 |
JP2017526161A (ja) | 2014-11-27 | 2017-09-07 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | 物質変化による固体分離 |
WO2017188381A1 (ja) * | 2016-04-28 | 2017-11-02 | 学校法人関西学院 | 気相エピタキシャル成長方法及びエピタキシャル層付き基板の製造方法 |
JP2018207034A (ja) | 2017-06-08 | 2018-12-27 | 株式会社ディスコ | ウエーハ生成装置 |
JP2019500220A (ja) | 2016-01-05 | 2019-01-10 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | 固体状物における改質の平面生成のための装置及び方法 |
WO2019044029A1 (ja) * | 2017-09-01 | 2019-03-07 | 住友電気工業株式会社 | 炭化珪素エピタキシャル基板および炭化珪素半導体装置の製造方法 |
JP2019511122A (ja) | 2016-03-22 | 2019-04-18 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | 分離されるべき固体物の複合レーザ処理 |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5353800B2 (ja) * | 2010-04-07 | 2013-11-27 | 新日鐵住金株式会社 | 炭化珪素エピタキシャル膜の製造方法 |
US9406551B2 (en) * | 2012-09-27 | 2016-08-02 | Infineon Technologies Austria Ag | Method for manufacturing a semiconductor substrate, and method for manufacturing semiconductor devices integrated in a semiconductor substrate |
CN109234804B (zh) * | 2018-11-02 | 2020-01-14 | 山东天岳先进材料科技有限公司 | 一种碳化硅单晶生长方法 |
-
2020
- 2020-09-24 JP JP2021548980A patent/JPWO2021060366A1/ja active Pending
- 2020-09-24 CN CN202080065954.4A patent/CN114423890A/zh active Pending
- 2020-09-24 WO PCT/JP2020/036001 patent/WO2021060366A1/ja active Application Filing
- 2020-09-24 US US17/761,176 patent/US20220375749A1/en active Pending
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Patent Citations (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2013049161A (ja) | 2011-08-30 | 2013-03-14 | Hamamatsu Photonics Kk | 加工対象物切断方法 |
JP2013189323A (ja) * | 2012-03-12 | 2013-09-26 | Sumitomo Electric Ind Ltd | 炭化珪素単結晶の製造方法 |
JP2014179605A (ja) * | 2013-03-08 | 2014-09-25 | Infineon Technologies Austria Ag | 半導体デバイスおよびそれを製造するための方法 |
JP2015024932A (ja) | 2013-07-24 | 2015-02-05 | トヨタ自動車株式会社 | SiC基板の製造方法 |
JP2017500725A (ja) | 2013-10-08 | 2017-01-05 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | レーザー処理及び温度誘導ストレスを用いた複合ウェハー製造方法 |
JP2017526161A (ja) | 2014-11-27 | 2017-09-07 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | 物質変化による固体分離 |
JP2018152582A (ja) | 2014-11-27 | 2018-09-27 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | 物質変化による固体分離 |
JP2019500220A (ja) | 2016-01-05 | 2019-01-10 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | 固体状物における改質の平面生成のための装置及び方法 |
JP2019511122A (ja) | 2016-03-22 | 2019-04-18 | シルテクトラ ゲゼルシャフト ミット ベシュレンクター ハフトゥング | 分離されるべき固体物の複合レーザ処理 |
WO2017188381A1 (ja) * | 2016-04-28 | 2017-11-02 | 学校法人関西学院 | 気相エピタキシャル成長方法及びエピタキシャル層付き基板の製造方法 |
JP2018207034A (ja) | 2017-06-08 | 2018-12-27 | 株式会社ディスコ | ウエーハ生成装置 |
WO2019044029A1 (ja) * | 2017-09-01 | 2019-03-07 | 住友電気工業株式会社 | 炭化珪素エピタキシャル基板および炭化珪素半導体装置の製造方法 |
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