WO2021060367A1 - SiC基板の製造方法 - Google Patents
SiC基板の製造方法 Download PDFInfo
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- WO2021060367A1 WO2021060367A1 PCT/JP2020/036002 JP2020036002W WO2021060367A1 WO 2021060367 A1 WO2021060367 A1 WO 2021060367A1 JP 2020036002 W JP2020036002 W JP 2020036002W WO 2021060367 A1 WO2021060367 A1 WO 2021060367A1
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- KWYUFKZDYYNOTN-UHFFFAOYSA-M Potassium hydroxide Chemical compound [OH-].[K+] KWYUFKZDYYNOTN-UHFFFAOYSA-M 0.000 claims description 18
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- WGTYBPLFGIVFAS-UHFFFAOYSA-M tetramethylammonium hydroxide Chemical compound [OH-].C[N+](C)(C)C WGTYBPLFGIVFAS-UHFFFAOYSA-M 0.000 claims description 6
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- H01L21/0445—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 crystalline silicon carbide
- H01L21/0475—Changing the shape of the semiconductor body, e.g. forming recesses
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- 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
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- H01L21/302—Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to change their surface-physical characteristics or shape, e.g. etching, polishing, cutting
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- H—ELECTRICITY
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- 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
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- Y02P80/30—Reducing waste in manufacturing processes; Calculations of released waste quantities
Definitions
- the present invention relates to a method for manufacturing a SiC substrate.
- the SiC (silicon carbide) substrate is formed by slicing a single crystal SiC ingot.
- a surface layer hereinafter, referred to as a processed alteration layer
- distortions and scratches of crystals introduced at the time of slicing.
- machining has been performed in order to remove this processing alteration layer and obtain an epiready SiC substrate capable of epitaxial growth for manufacturing a SiC device.
- This machining includes a rough grinding process using abrasive grains such as diamond, a finish grinding process using abrasive grains having a smaller particle size than the abrasive grains used in the rough grinding process, and the mechanical action of the polishing pad.
- CMP chemical mechanical polishing
- the processed alteration layer has a crack layer having a large number of cracks (scratches) and a strain layer in which the crystal lattice is distorted.
- This strain layer is introduced at a position deeper in the SiC substrate than the crack layer. Therefore, in order to remove the strain layer, it is necessary to remove single crystal SiC having a size of several tens of ⁇ m to several hundreds of ⁇ m. As a result, there is a problem that a lot of material loss occurs.
- an object to be solved by the present invention is to provide a new technique for manufacturing a SiC substrate capable of reducing the amount of material loss when removing the strain layer.
- the present invention that solves the above-mentioned problems is a method for manufacturing a SiC substrate, which includes a strain layer thinning step of thinning the strain layer by moving the strain layer of the SiC substrate body to the surface side.
- a strain layer thinning step of thinning the strain layer by moving the strain layer of the SiC substrate body to the surface side.
- a preferred embodiment of the present invention includes a strain layer removing step of removing the strain layer.
- the strain layer thinning step when the depth of the strain layer before the strain layer thinning step is set as a reference depth, the strain layer after the strain layer thinning step is moved to the surface side of the reference depth. It ’s a process,
- the strain layer removing step is a step of removing at least a part of the surface side of the reference depth. In this way, the amount of material loss of the SiC substrate can be reduced by moving and removing the strain layer to the surface side of the reference depth that has been conventionally removed.
- the strain layer removing step is chemical mechanical polishing.
- the strain layer removing step is chemical mechanical polishing.
- the strain layer removing step is a thermal etching method. As described above, by adopting the thermal etching method in the strain layer removing step, the strain layer can be moved and the strain layer can be removed at the same time. That is, the strain layer thinning step and the strain layer removing step can be performed at the same time.
- a preferred embodiment of the present invention further includes a slicing step of slicing an ingot to obtain a SiC substrate, and the slicing step is a thickness obtained by adding a thickness of 100 ⁇ m or less to the thickness of the SiC substrate after the strain layer removing step.
- This is a step of obtaining a SiC substrate body having the above.
- the slicing step is a step of obtaining a SiC substrate having a thickness obtained by adding a thickness of 50 ⁇ m or less to the thickness of the SiC substrate after the strain layer removing step.
- a preferred embodiment of the present invention further includes an etching step of etching the surface of the SiC substrate body, and the etching step is wet etching.
- the etching step is selected from the group consisting of a potassium hydroxide melt, a chemical solution containing hydrofluoric acid, a potassium permanganate-based chemical solution, and tetramethylammonium hydroxide as the etching solution. Includes one or more.
- a preferred embodiment of the present invention includes a slicing step of slicing an ingot to obtain a SiC substrate, and includes the slicing step, the etching step, and the strain layer thinning step in this order.
- the strain layer thinning step is a step of heating a SiC substrate in an environment containing Si elements.
- the strain layer thinning step is a step of heating the SiC substrate in a semi-closed space including a Si element supply source and a C element supply source.
- the strain layer thinning step is a step of heating the SiC substrate in a main body container made of a SiC material.
- the strain layer thinning step is a step of making the SiC substrate and the SiC material relative to each other and heating the SiC substrate so that a temperature gradient is formed between the SiC substrate and the SiC material. ..
- the strain layer thinning step is a step of heating a SiC substrate body in a Si vapor pressure environment.
- the strain layer thinning step is a metastable solvent epitaxy method.
- the heating temperature in the strain layer thinning step is 1400 ° C. or higher and 1600 ° C. or lower.
- FIG. 1 shows an embodiment in which the strain layer 12 is thinned and removed with respect to the SiC substrate body 10 having the strain layer 12.
- FIG. 2 shows an embodiment in which a SiC substrate 30 having a substrate thickness D is obtained from an ingot I having a thickness D0.
- the strain layer 12 is moved (concentrated) to the surface side of the strain layer 12 of the SiC substrate body 10.
- This is a method for manufacturing a SiC substrate 30, which includes a strain layer thinning step S1 for thinning.
- the strain layer 12 after the strain layer thinning step is set to the reference depth. This is a step of moving the surface to the surface side of the 20th.
- the present invention is a method for manufacturing a SiC substrate 30, which includes a strain layer removing step S2 for removing the strain layer 12 moved by the strain layer thinning step S1.
- This strain layer removing step S2 is a step of removing at least a part of the surface side of the reference depth 20.
- FIG. 1A shows an embodiment in which the strain layer 12 is moved to the surface side while maintaining the substrate thickness of the SiC substrate body 10.
- FIG. 1B shows an embodiment in which the strain layer 12 is moved to the surface side while the SiC substrate body 10 is crystal-grown.
- FIG. 1C shows an embodiment in which the strain layer 12 is moved to the surface side while etching the SiC substrate body 10.
- the conventional method includes a strain layer removing step S2 for removing all of the strain layer 12. That is, in order to remove the strain layer 12, it is necessary to remove the SiC single crystal at least to a position reaching the reference depth 20. In this way, when all of the introduced strain layer 12 is removed, a large amount of material loss L will occur.
- the strain layer 12 is moved (concentrated) to the surface side of the SiC substrate body 10 before the strain layer 12 is removed (or while the strain layer 12 is removed).
- the strain layer thinning step S1 for thinning 12 is included. As a result, the amount of material loss L of the SiC substrate body 10 can be reduced as compared with the conventional method.
- the amount of material loss L can be reduced by the strain layer thinning step S1. Therefore, the SiC substrate body 10 can be sliced with a substrate thickness D1 thinner than that of the conventional method.
- FIG. 2A shows how four SiC substrates 30 having a substrate thickness D are obtained from an ingot I having a thickness D0.
- the conventional method includes a strain layer removing step S2 for removing all of the strain layers 12 introduced into the SiC substrate body 10. Therefore, in order to manufacture the SiC substrate 30 having a substrate thickness D produced in the present invention, it is necessary to slice with a substrate thickness D2 thicker than the substrate thickness D1. In FIG. 2B, it is shown that three SiC substrates 30 having a substrate thickness D are obtained from an ingot I having a thickness D0.
- the present invention including the strain layer thinning step S1 and the conventional method not including the strain layer thinning step S1.
- the number of SiC substrates 30 obtained differs from that of the above.
- the strain layer thinning step S1 for thinning the strain layer 12 by moving (concentrating) the strain layer 12 of the SiC substrate body 10 to the surface side is included, so that from one ingot.
- the number of SiC substrates 30 to be taken can be increased, and the unit price per substrate can be lowered.
- the slicing step S3, the etching step S4, the strain layer thinning step S1, and the strain layer removing step S2 will be described in detail in this order.
- the slicing step S3 is a step of slicing the SiC substrate body 10 from the ingot I.
- a multi-wire saw cutting method for cutting the ingot I at predetermined intervals by reciprocating a plurality of wires an electric discharge machining method for intermittently generating a plasma discharge to cut the ingot, and an ingot. Examples thereof include cutting using a laser that irradiates and condenses a laser in I to form a layer serving as a base point for cutting.
- the substrate thickness of the SiC substrate body 10 is determined by the interval of cutting in this slicing step S3. This substrate thickness is set in consideration of the single crystal SiC (material loss L) that will be removed in a future process. As described above, since the slice thickness from Ingot I is set in consideration of the amount of material loss L after all the processing steps, the specific numerical values thereof have been described for all the steps. It will be described later.
- the etching step S4 is a step of etching the surface of the SiC substrate body 10 after the slicing step S3.
- the etching method of the etching step S4 includes a thermal etching method such as a SiVE method or a hydrogen etching method, a potassium hydroxide melt, a chemical solution containing hydrofluoric acid, a potassium permanganate-based chemical solution, and tetramethylammonium hydroxide.
- An example is a wet etching method using a chemical solution or the like. Normally, any chemical solution used in wet etching can be used.
- etching step S4 it is preferable to etch the surface of the SiC substrate body 10 with a potassium hydroxide melt.
- a potassium hydroxide melt By etching the surface of the SiC substrate body 10 by so-called KOH etching, the surface can be flattened while removing impurities adhering in the slicing step S3.
- the SiC substrate 10 after the slicing step S3 may be subjected to an etching step S4 using a potassium hydroxide melt, and then a strain layer thinning step S1 and a strain layer removing step S2. good.
- the strain layer thinning step S1 is a step of heating the SiC substrate 10 to at least 1400 ° C. or higher in an environment containing Si elements. By heating the SiC substrate 10 in such an environment, the strain layer 12 can be moved and concentrated on the surface side of the SiC substrate 10 without carbonizing the surface of the SiC substrate 10.
- a semi-stable solvent epitaxy that grows a single crystal SiC crystal by heating a sandwich structure in which a polycrystalline SiC and a single crystal SiC are arranged via the single crystal Si.
- MSE Metal Organic Chemical Vapor Deposition
- SiVE Si vapor pressure etching
- the heat treatment environment of the SiC substrate 10 in the strain layer thinning step S1 is a vapor phase environment containing a Si element or a liquid phase environment containing a Si element.
- the following methods can be exemplified.
- the strain layer thinning step S1 is a step of heating the SiC substrate body 10 in a semi-closed space including a Si element supply source and a C element supply source.
- the SiC substrate body 10 is arranged in the main body container 50 in which the SiC material 40 (Si element supply source and C element supply source) is exposed.
- the SiC material 40 Si element supply source and C element supply source
- the "quasi-closed space” in the present specification means a space in which the inside of the container can be evacuated, but at least a part of the vapor generated in the container can be confined.
- This semi-closed space can be formed in the main body container 50 or the melting point container 70, which will be described later.
- the SiC substrate body 10 can be exemplified by processing a single crystal SiC into a plate shape. Specifically, a SiC wafer or the like sliced into a disk shape from a SiC ingot produced by a sublimation method or the like can be exemplified. As the crystal polymorphism of single crystal SiC, any polymorphism can be adopted.
- the SiC substrate body 10 that has undergone mechanical processing (for example, slicing, grinding / polishing) or laser processing has a strain layer 12 in which the crystal lattice is distorted due to processing damage and such processing damage is introduced. It has a bulk layer 11 and no bulk layer 11 (see FIG. 1). In order to manufacture a high-quality SiC substrate 30, it is preferable to remove the strain layer 12 and expose the bulk layer 11 to which no processing damage has been introduced.
- a crack layer having a large number of cracks is introduced in addition to the strain layer 12 due to processing damage, but it is omitted because it is introduced at a position shallower than the strain layer 12.
- the crack layer and the strain layer 12 are collectively referred to as a processed alteration layer.
- the presence or absence and depth of the strain layer 12 can be confirmed by the SEM-EBSD method, TEM, ⁇ XRD, Raman spectroscopy, or the like.
- the SiC material 40 includes a SiC substrate and a SiC container (main body container 50 itself). That is, it is possible to exemplify a form in which a SiC substrate, which is a SiC material 40, is arranged in a container separately from the SiC substrate body 10 (see FIGS. 4 and 5). In addition, a form in which at least a part of the container accommodating the SiC substrate body 10 is formed of the SiC material 40 can be exemplified (see FIG. 7). In this case, the entire container may be formed of the SiC material 40, or the portion facing the SiC substrate 10 may be formed of the SiC material 40. When single crystal SiC is used for the SiC material 40, any polytype can be used.
- the heated semi-enclosed space be a vapor pressure environment of a mixed system of gas phase species containing Si element and gas phase species containing 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 include Si 2 C, SiC 2 , SiC and C. That is, it is preferable that the SiC gas is present in the semi-closed space.
- the heating temperature in the strain layer thinning step S1 is preferably set in the range of 1400 to 2300 ° C. Further, it is more preferably set in the range of 1400 to 1600 ° C.
- the heating time in the strain layer thinning step S1 can be set to an arbitrary time so as to have a desired strain layer 12 depth.
- the strain layer 12 By heating the SiC substrate 10 in such an environment, the strain layer 12 can be moved (concentrated) to the surface side, and the strain layer 12 can be thinned (see FIG. 3).
- the SiC substrate body 10 and the SiC material 40 are arranged so as to face each other, and a temperature gradient is formed between the SiC substrate body 10 and the SiC material 40.
- the strain layer 12 can be thinned while the SiC substrate body 10 is crystal-grown or etched.
- [Strain layer thinning step S1 with crystal growth] 1 (b) and 4 are explanatory views showing an outline of the strain layer thinning step S1 accompanied by crystal growth.
- the SiC substrate body 10 and the SiC material 40 are arranged so as to face each other, and a temperature gradient is provided between them for heating, so that the raw material (Si element) is transferred from the SiC material 40 to the SiC substrate body 10. And C element) can be transported to grow single crystal SiC.
- the SiC substrate body 10 is placed in the semi-closed space where the SiC material 40 is exposed and heated in a temperature range of 1400 ° C. or higher and 2300 ° C. or lower. It is considered that the reaction is carried out continuously, and as a result, crystal growth proceeds (see FIG. 4 (b)).
- the strain layer thinning step S1 accompanied by crystal growth involves a Si atom sublimation step of thermally sublimating Si atoms from the surface of the SiC material 40 and a reaction of the SiC material 40 with Si vapor in the semi-closed space.
- the raw material reaches the steps of the SiC substrate body 10, a C atom sublimation step of sublimating the C atom remaining on the surface, a raw material transportation step of transporting the raw material to the surface of the SiC substrate body 10 using a temperature gradient or a chemical potential difference as a driving force. Includes a step-flow growth process to grow.
- the SiC substrate body 10 and the SiC material 40 are arranged so as to face each other, and the SiC substrate body 10 is heated to the low temperature side and the SiC material 40 to the high temperature side. Is.
- a crystal growth space X is formed between the SiC substrate body 10 and the SiC material 40, the SiC substrate body 10 can be crystal-grown by using the temperature gradient as a driving force, and the strain layer 12 is formed on the SiC substrate body 10. Can be moved to the surface side of.
- [Strain layer thinning step S1 with etching] 1 (c) and 5 are explanatory views showing an outline of the strain layer thinning step S1 accompanied by etching.
- the SiC substrate body 10 and the SiC material 40 are arranged so as to face each other, and a temperature gradient is provided between them to heat the SiC substrate body 10 to the SiC material 40 as a raw material (Si element). And C element) can be transported to etch the SiC substrate body 10.
- the SiC substrate body 10 is placed in the semi-closed space where the SiC material 40 is exposed and heated in a temperature range of 1400 ° C. or higher and 2300 ° C. or lower. It is considered that the reaction is carried out continuously and the etching proceeds as a result (see FIG. 5 (b)).
- the strain layer thinning step S1 accompanied by etching includes a Si atom sublimation step of thermally sublimating Si atoms from the surface of the SiC substrate body 10 and a C atom remaining on the surface of the SiC substrate body 10 and the inside of the semi-closed space. It includes a C atom sublimation step of sublimating from the surface of the SiC substrate body 10 by reacting the Si vapor of.
- the strain layer thinning step S1 accompanied by etching is a step of arranging the SiC substrate body 10 and the SiC material 40 so as to face each other and heating the SiC substrate body 10 on the high temperature side and the SiC material 40 on the low temperature side. is there.
- an etching space Y is formed between the SiC substrate body 10 and the SiC material 40, the SiC substrate body 10 is etched using the temperature gradient as a driving force, and the strain layer 12 is moved to the surface side of the SiC substrate body 10. Can be made to.
- the strain layer removing step S2 is a step of removing the strain layer 12 thinned by the strain layer thinning step S1. Specifically, it is a step of removing the strain layer 12 that has moved to the surface side from the reference depth 20 which is the depth of the strain layer 12 before the strain layer thinning step S1, and is a step of removing the surface from the reference depth 20. This is a step of removing at least a part of the side (FIGS. 1 (a) to 1 (c)).
- strain layer removing step S2 examples include the CMP method, the SIVE method, the hydrogen etching method, and the etching method described in the above-mentioned [Strain layer thinning step S1 accompanied by etching].
- the strain layer removing step S2 in the conventional method includes a rough grinding step using abrasive grains such as diamond, a finish grinding step using abrasive grains having a smaller particle size than the abrasive grains used in the rough grinding step, and polishing.
- the process of polishing is performed by combining the mechanical action of the pad and the chemical action of the slurry.
- the strain layer 12 after the strain layer thinning step S1 is removed. Therefore, the strain layer 12 can be removed with a removal amount smaller than the strain layer depth (reference depth 20) conventionally introduced. As a result, the amount of the SiC substrate 10 removed in the strain layer removing step S2 of the present invention can be reduced as compared with the conventional method.
- the strain layer thinning step S1 for thinning the strain layer 12 by moving the strain layer 12 of the SiC substrate body 10 to the surface side is included.
- the amount of material loss L in the strain layer removing step S2 can be reduced.
- the cost and processing time in the strain layer removing step S2 can be reduced.
- the strain layer 12 depth (reference depth 20) of the SiC substrate body 10 before the strain layer thinning step S1 is 5 ⁇ m and the strain layer 12 depth is 1 ⁇ m by the strain layer thinning step S1.
- 1 ⁇ m of the SiC substrate body 10 may be removed. That is, in the conventional method, it is necessary to remove the SiC substrate body 10 for 5 ⁇ m, but by including the strain layer thinning step S1, the material loss L for 4 ⁇ m can be reduced.
- consumables grindstones, blades, abrasive grains, etc.
- machining time required for machining can be reduced. Therefore, the cost in the strain layer removing step S2 can be significantly reduced.
- the method for manufacturing a SiC substrate according to the present embodiment by adopting chemical mechanical polishing (CMP) in the strain layer removing step S2, an epiready surface can be obtained while reducing material loss L, cost, and processing time.
- CMP chemical mechanical polishing
- the SiC substrate 30 having the same can be manufactured.
- the burden of CMP which is the finishing process of the conventional method, can be reduced.
- the desired substrate thickness can be adjusted by adopting the strain layer thinning step S1 accompanied by crystal growth.
- the strain layer thinning step S1 by adopting the strain layer thinning step S1 accompanied by etching, the strain layer thinning step S1 and the strain layer removing step S2 can be performed at the same time.
- the introduction cost of the process and the equipment and the outsourcing cost can be reduced, and the cost can be reduced.
- the heating temperature in the strain layer thinning step S1 is 1400 ° C. or higher and 1600 ° C. or lower.
- the burden on the apparatus can be reduced.
- the lower the temperature of the heat treatment apparatus the easier it can be introduced.
- Table 1 summarizes an example of manufacturing a SiC substrate 30 having a substrate thickness of 350 ⁇ m in each of the methods for manufacturing a SiC substrate according to the present embodiment and the conventional method.
- the amount of material loss L in the method for manufacturing the SiC substrate of the present embodiment is 50 ⁇ m as shown in Table 1. As described above, according to the present embodiment, it is possible to significantly reduce the amount of material loss L in the manufacture of the SiC substrate.
- the substrate thickness D1 of the SiC substrate body 10 cut out from the ingot I in the slicing step S3 is set using this material loss L amount as an index. That is, the thickness obtained by adding the amount of material loss L to the substrate thickness D (thickness of the SiC substrate 30 at the end of surface processing) of the SiC substrate 30 to be finally obtained is set as the substrate thickness D1 at the time of slicing.
- the amount of material loss L is added to the thickness of the SiC substrate 30 after the surface processing is completed to determine the substrate thickness D1 at the time of slicing.
- surface processing refers to processing that reduces the thickness of the SiC substrate body 10, such as the etching step S4 and the strain layer removing step S2. That is, the substrate thickness D1 at the time of slicing is set by adding the amount of material loss L to the thickness of the SiC substrate 30 that has reached the point where the thickness does not decrease any more in the subsequent step.
- the thickness D of the SiC substrate 30 is preferable to add to the lower limit of 37 ⁇ m or more, more preferably 40 ⁇ m or more, as the substrate thickness D1 at the time of slicing.
- a thickness of 100 ⁇ m or less, more preferably 90 ⁇ m or less, still more preferably 80 ⁇ m or less, still more preferably 70 ⁇ m or less, still more preferably 60 ⁇ m or less, still more preferably 50 ⁇ m or less is added to the substrate thickness D of the SiC substrate 30. It is preferable to set the substrate thickness D1 at the time of slicing. This makes it possible to manufacture more SiC substrates 30 from one Ingot I.
- the thickness D of the SiC substrate 30 it is common to remove 100 ⁇ m or more per 30 SiC substrates. Therefore, it is preferable to add the thickness D of the SiC substrate 30 to the upper limit of 100 ⁇ m or less, more preferably less than 100 ⁇ m, as the substrate thickness D1 at the time of slicing. As a result, more SiC substrates 30 can be manufactured as compared with the case where the conventional method generally used is used.
- the substrate thickness D of the SiC substrate 30 that has undergone the slicing step S3 to the strain layer removing step S2 is typically 100 to 600 ⁇ m, more typically 150 to 550 ⁇ m, more typically 200 to 500 ⁇ m, and further. Typically 250-450 ⁇ m, more typically 300-400 ⁇ m can be exemplified. That is, it is preferable to add the amount of material loss L according to the method for manufacturing the SiC substrate of the present invention to the substrate thickness of these typical SiC substrates 30 to set the substrate thickness D1 at the time of slicing.
- the substrate thickness D1 at the time of slicing is set to 387 ⁇ m or more as a lower limit. It is preferable to obtain the SiC substrate 30 having a thickness of preferably 390 ⁇ m or more, more preferably 400 ⁇ m or more in the slicing step S3.
- the upper limit of the substrate thickness D1 at the time of slicing is 450 ⁇ m or less, more preferably 440 ⁇ m or less, still more preferably 430 ⁇ m or less, still more preferably 420 ⁇ m or less, still more preferably 410 ⁇ m or less, still more preferably 400 ⁇ m or less. It is preferable to obtain the substrate 30 in the slicing step S3.
- a temperature gradient is formed between the main body container 50 capable of accommodating the SiC substrate body 10 and the SiC substrate body 10 and the SiC material 40.
- a heating furnace 60 capable of heating is provided.
- the main body container 50 is a fitting container including an upper container 51 and a lower container 52 that can be fitted to each other.
- a minute gap 53 is formed in the fitting portion between the upper container 51 and the lower container 52, and the inside of the main container 50 can be exhausted (evacuated) from the gap 53.
- the upper container 51 and the lower container 52 according to the present embodiment are made of polycrystalline SiC. Therefore, the main body container 50 itself may be the SiC material 40. Further, only the portion of the main body container 50 facing the SiC substrate body 10 may be made of the SiC material 40. In that case, a high melting point material (a material similar to the high melting point container 70 described later) can be used for the portion other than the SiC material 40.
- a configuration in which the substrate-shaped SiC material 40 is separately accommodated may be adopted.
- a spacer (a substrate holder 54 or the like) may be arranged between the substrate-shaped SiC material 40 and the SiC substrate body 10 to form a crystal growth space X or an etching space Y. It is desirable that the substrate holder 54 is made of the same high melting point material as the high melting point container 70.
- the main body container 50 is configured to generate an atmosphere containing Si element and C element in the internal space when heated while accommodating the SiC substrate body 10.
- the SiC material 40 composed of polycrystalline SiC is heated to form an atmosphere containing Si element and C element in the internal space.
- the space in the heated main body container 50 becomes 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 include Si 2 C, SiC 2 , SiC and C. That is, it is preferable that the SiC gas is present in the semi-closed space.
- the crystal growth space X or the etching space Y is a space for transporting raw materials from the SiC substrate 10 to the SiC material 40 by using a temperature gradient provided between the SiC substrate 10 and the SiC material 40 as a driving force. This is a space for transporting raw materials from the SiC material 40 to the SiC substrate body 10.
- the temperature of the SiC substrate 10 is low and the temperature of the SiC material 40 is high.
- the body 10 is arranged (see FIG. 4).
- the SiC substrate body 10 and the SiC material 40 are arranged so as to face each other and heated so that the SiC substrate body 10 is on the low temperature side and the SiC material 40 is on the high temperature side, the SiC substrate body 40 to the SiC substrate body are heated.
- the raw material is transported to No. 10, and single crystal SiC grows on the SiC substrate body 10. That is, a crystal growth space X is formed between the SiC material 40 and the SiC substrate body 10.
- the temperature on the side of the SiC substrate 10 is high and the temperature of the SiC material 40 is low.
- the substrate 10 is arranged (see FIG. 5).
- the SiC substrate body 10 and the SiC material 40 are arranged so as to face each other and heated so that the SiC substrate body 10 is on the high temperature side and the SiC material 40 is on the low temperature side, the SiC substrate body 10 to the SiC material 40 are heated.
- the raw material is transported to 40, and the SiC substrate body 10 is etched. That is, an etching space Y is formed between the SiC material 40 and the SiC substrate body 10.
- the heating furnace 60 includes a main heating chamber 61 capable of heating an object to be processed (SiC substrate body 10 or the like) to a temperature of 1000 ° C. or higher and 2300 ° C. or lower, and a heating object at 500 ° C.
- a preheating chamber 62 capable of preheating to the above temperature
- a refractory container 70 capable of accommodating the main body container 50
- a moving means 63 capable of moving the refractory container 70 from the preheating chamber 62 to the main heating chamber 61. It is equipped with a moving table).
- the heating chamber 61 is formed in a regular hexagonal shape in a plan sectional view, and the melting point container 70 is arranged inside the heating chamber 61.
- a heater 64 (mesh heater) is provided inside the heating chamber 61.
- a multilayer heat-reflecting metal plate is fixed to the side wall or ceiling of the heating chamber 61 (not shown). The multilayer heat-reflecting metal plate is configured to reflect the heat of the heating heater 64 toward the substantially central portion of the main heating chamber 61.
- the heating heater 64 is arranged so as to surround the melting point container 70 in which the object to be processed is housed, and further, the multilayer heat-reflecting metal plate is arranged outside the heating heater 64, so that the temperature is 1000 ° C.
- the temperature can be raised to 2300 ° C. or lower.
- a resistance heating type heater or a high frequency induction heating type heater can be used as the heating heater 64.
- the heating heater 64 may adopt a configuration capable of forming a temperature gradient in the melting point container 70.
- the heating heater 64 may be configured so that many heaters are arranged on the upper side. Further, the heating heater 64 may be configured so that the width increases toward the upper side. Alternatively, the heater 64 may be configured so that the electric power supplied can be increased toward the upper side.
- a vacuum forming valve 65 for exhausting the inside of the main heating chamber 61
- an inert gas injection valve 66 for introducing an inert gas into the main heating chamber 61
- a vacuum gauge 67 for measuring the degree of vacuum inside is connected.
- the vacuum forming valve 65 is connected to a vacuum drawing pump that exhausts the inside of the main heating chamber 61 to create a vacuum (not shown). With the vacuum forming valve 65 and the vacuum pulling pump, the degree of vacuum in the main heating chamber 61 can be adjusted to , for example, 10 Pa or less, more preferably 1 Pa or less, still more preferably 10 -3 Pa or less. As this evacuation pump, a turbo molecular pump can be exemplified.
- the Inert gas injection valve 66 is connected to the Inactive gas supply source (not shown). With the inert gas injection valve 66 and the inert gas supply source, the inert gas can be introduced into the heating chamber 61 in the range of 10-5 to 10000 Pa. As the inert gas, Ar, He, N 2, or the like can be selected.
- the inert gas injection valve 66 is a dopant gas supply means capable of supplying the dopant gas into the main body container 50. That is, the doping concentration of the growth layer can be adjusted by selecting a dopant gas (for example, N 2 or the like) as the inert gas.
- a dopant gas for example, N 2 or the like
- the preheating chamber 62 is connected to the main heating chamber 61, and the high melting point container 70 can be moved by the moving means 63.
- the preheating chamber 62 of the present embodiment is configured so that the temperature can be raised by the residual heat of the heating heater 64 of the main heating chamber 61. For example, when the temperature of the main heating chamber 61 is raised to 2000 ° C., the temperature of the preheating chamber 62 is raised to about 1000 ° C. Degassing treatment can be performed.
- the moving means 63 is configured to be movable between the main heating chamber 61 and the preheating chamber 62 on which the melting point container 70 is placed. Since the transfer between the main heating chamber 61 and the preheating chamber 62 by the moving means 63 is completed in about 1 minute at the shortest, the temperature can be raised or lowered at 1 to 1000 ° C./min. Since the rapid temperature rise and the rapid temperature decrease can be performed in this way, it is possible to observe a surface shape having no history of low temperature growth during temperature rise and temperature reduction, which was difficult with conventional devices. Further, in FIG. 6, the preheating chamber 62 is arranged below the main heating chamber 61, but the present invention is not limited to this, and the preheating chamber 62 may be arranged in any direction.
- the moving means 63 is a moving table on which the melting point container 70 is placed. A small amount of heat is released from the contact portion between the moving table and the melting point container 70. Thereby, a temperature gradient can be formed in the high melting point container 70 (and in the main body container 50). That is, in the heating furnace 60 of the present embodiment, since the bottom of the melting point container 70 is in contact with the moving table, the temperature gradient is such that the temperature decreases from the upper container 71 to the lower container 72 of the melting point container 70. Is provided. It is desirable that this temperature gradient is formed along the front and back directions of the SiC substrate body 10. Further, as described above, a temperature gradient may be formed by the configuration of the heater 64. Further, the heating heater 64 may be configured so that the temperature gradient can be reversed.
- the heating furnace 60 forms an atmosphere containing a Si element, and the main body container 50 can be heated in this atmosphere.
- the atmosphere containing the Si element in the heating furnace 60 according to the present embodiment is formed by using the high melting point container 70 and the Si steam supply source 74. As long as the method can form an atmosphere containing Si element around the main body container 50, it can be naturally adopted.
- the high melting point container 70 is configured to contain a high melting point material.
- 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, TiC, WC, MoC, a nitride HfN, TaN, BN, Ta 2 N, ZrN, TiN, HfB 2, TaB 2, ZrB 2, NB 2, TiB 2 is a boride, it can be exemplified polycrystalline SiC.
- the high melting point container 70 is a fitting container including an upper container 71 and a lower container 72 that can be fitted to each other, and is configured to be able to accommodate the main body container 50.
- a minute gap 73 is formed in the fitting portion between the upper container 71 and the lower container 72, and the inside of the high melting point container 70 can be exhausted (evacuated) from the gap 73.
- the high melting point container 70 preferably has a Si steam supply source 55 capable of supplying the vapor pressure of a vapor phase species containing a Si element in the high melting point container 70.
- the Si vapor supply source 55 may have a configuration in which Si vapor is generated in the melting point container 70 at the time of heating, and examples thereof include solid Si (Si pellets such as single crystal Si pieces and Si powder) and Si compounds. be able to.
- the SiC substrate manufacturing apparatus employs TaC as the material of the melting point container 70 and tantalum Silicide as the Si vapor supply source 55. That is, as shown in FIGS. 4 and 5, a tantalum Silicide layer is formed inside the melting point container 70, and Si vapor is supplied into the container from the tantalum Silicide layer during heating, so that the Si vapor pressure environment Is configured to form. In addition to this, any configuration can be adopted as long as the vapor pressure of the vapor phase species containing the Si element is formed in the melting point container 70 during heating.
- Example 1 Movement of strain layer>
- the SiC substrate body 10 after the slicing step S3 was housed in the main body container 50 and the melting point container 70 (see FIG. 7), and heat-treated under the following heat treatment conditions.
- the main body container 50 is formed of polycrystalline SiC so that the main body container 50 itself functions as a SiC material 40 (Si element supply source and C element supply source).
- the depth of the strain layer 12 was confirmed by the SEM-EBSD method.
- the strain layer 12 can also be confirmed by TEM, ⁇ XRD, or Raman spectroscopy.
- Heating treatment conditions The SiC substrate body 10 arranged under the above-mentioned conditions was heat-treated under the following conditions. Heating temperature: 1500 ° C Heating time: 10h Etching amount: 40 nm Temperature gradient: 1 ° C / mm This heating chamber vacuum degree: 10-5 Pa
- the lattice strain of the SiC substrate 10 can be obtained by comparing with a reference crystal lattice as a reference.
- the SEM-EBSD method can be used as a means for measuring this lattice strain.
- the SEM-EBSD method is a method (Electron Backscattering Diffraction) that enables strain measurement of a minute region based on the Kikuchi line diffraction pattern obtained by electron backscattering in a scanning electron microscope (SEM). : EBSD).
- the amount of lattice strain can be obtained by comparing the diffraction pattern of the reference crystal lattice as a reference with the diffraction pattern of the measured crystal lattice.
- a reference point is set in a region where lattice distortion is not considered to occur. That is, it is desirable to arrange the reference point in the region of the bulk layer 11. It is a well-established theory that the depth of the strain layer 12 is usually about 10 ⁇ m. Therefore, the reference point may be set at a position having a depth of about 20 to 35 ⁇ m, which is considered to be sufficiently deeper than the strain layer 12.
- the diffraction pattern of the crystal lattice at this reference point is compared with the diffraction pattern of the crystal lattice in each measurement region measured at a pitch on the order of nanometers. This makes it possible to calculate the amount of lattice strain in each measurement region with respect to the reference point.
- the presence or absence of the strain layer 12 can be determined. That is, when strain is introduced due to processing damage, lattice strain is generated in the SiC substrate body 10, so that stress is observed by the SEM-EBSD method.
- the strain layer 12 existing in the SiC substrate body 10 of Example 1 before and after the strain layer thinning step S1 was observed by the SEM-EBSD method. The results are shown in FIGS. 8 (a) and 8 (b).
- the cross section of the SiC substrate 10 before and after the strain layer thinning step S1 of Example 1 was measured using a scanning electron microscope under the following conditions.
- FIG. 8A is a cross-sectional SEM-EBSD imaging image of the SiC substrate body 10 before the strain layer thinning step S1 in Example 1.
- a lattice strain having a depth of 3.5 ⁇ m was observed in the SiC substrate body 10. This is the lattice strain introduced at the time of the slicing step S3, and it can be seen that the strain layer 12 is provided.
- compressive stress is observed.
- FIG. 8B is a cross-sectional SEM-EBSD imaging image of the SiC substrate body 10 after the strain layer thinning step S1 in Example 1.
- a lattice strain having a depth of 1.3 ⁇ m was observed in the SiC substrate body 10. Since the etching amount during the heat treatment is 40 nm, it can be seen that the strain layer 12 has moved and concentrated on the surface side by about 2.2 ⁇ m. Further, by lengthening the heating time, the strain layer 12 can be further moved to the surface side. In this way, by heat-treating the SiC substrate body 10 in the semi-closed space including the Si element supply source and the C element supply source, the strain layer 12 can be moved and concentrated on the surface side of the SiC substrate body 10. ..
- the region removed as the material loss in the conventional method can be reduced or reduced.
- SiC substrate body 11
- Bulk layer 12
- Strain layer 20
- Reference depth 30
- SiC substrate 40
- SiC material 50
- Main body container 51
- Upper container 52
- Lower container 53
- Gap 54
- Substrate holder 55
- Si steam supply source 60
- Heating furnace 61
- Heating chamber 62
- Preheating Room 63
- Transportation means 64
- Heating heater 65
- Vacuum forming valve 66
- Inactive gas injection valve 67
- Vacuum gauge 70
- Refrigerating container 71
- Lower container 72
- Gap 74
- Si Steam supply source
- X Crystal growth space Y Etching space
- S1 Strain layer thin Chemicalization process S2
- S3 Slicing process
- S4 Etching process I Ingot
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Abstract
Description
このように、歪層を表面側に移動させる(集中させる)工程を含むことで、後に行う歪層を除去する歪層除去工程での、SiC基板体の素材ロス量を低減することができる。さらには、歪層除去工程おける加工コストや加工時間を低減することができる。
前記歪層薄化工程は、前記歪層薄化工程前の歪層の深さを基準深さとした場合において、前記歪層薄化工程後の歪層を前記基準深さよりも表面側に移動させる工程であり、
前記歪層除去工程は、前記基準深さよりも表面側の少なくとも一部を除去する工程である。
このように、従来除去されていた基準深さよりも表面側へ歪層を移動させ、除去することにより、SiC基板体の素材ロス量を低減することができる。
このように、SiC基板体の歪層を表面側に移動させることで前記歪層を薄くした後に化学機械研磨を施すことにより、素材ロス量とコストを低減しつつ、エピレディな表面を形成することができる。
このように、歪層除去工程に熱エッチング法を採用することで、歪層の移動と、歪層の除去と、を同時に行うことができる。すなわち、歪層薄化工程と歪層除去工程を同時に行うことができる。
また、前記スライス工程は、前記歪層除去工程後におけるSiC基板体の厚みに、50μm以下の厚みを加算した厚みを有するSiC基板体を得る工程である。
このような厚みでSiC基板体をスライスすることで、1インゴットからのSiC基板体の取り枚数を増やすことができ、1枚当たりの単価を下げることができる。
このように、SiC基板体をウェットエッチングすることにより、スライス工程にて付着した不純物を除去しつつ表面を平坦化することができる。
図1および図2は、本発明の実施の形態にかかるSiC基板の製造方法と、従来法にかかるSiC基板の製造方法と、を比較する説明図である。
図1は、歪層12を有するSiC基板体10に対し、歪層12を薄くして除去する実施の形態を示している。一方、図2は、厚みD0のインゴットIから、基板厚みDのSiC基板30を得る実施の形態を示している。
スライス工程S3は、インゴットIからSiC基板体10をスライスする工程である。スライス工程S3のスライス手法としては、複数本のワイヤーを往復運動させることでインゴットIを所定の間隔で切断するマルチワイヤーソー切断や、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、インゴットI中にレーザーを照射・集光させて切断の基点となる層を形成するレーザーを用いた切断、等を例示できる。
エッチング工程S4は、スライス工程S3後のSiC基板体10の表面をエッチングする工程である。エッチング工程S4のエッチング手法としては、SiVE法や水素エッチング法等の熱エッチング法、水酸化カリウム溶融液、フッ化水素酸を含む薬液、過マンガン酸カリウム系の薬液、水酸化テトラメチルアンモニウムを含む薬液等を用いたウェットエッチング法を例示できる。なお、通常、ウェットエッチングで用いられる薬液であれば採用することができる。
歪層薄化工程S1は、Si元素を含む環境下で、SiC基板体10を少なくとも1400℃以上に加熱する工程である。このような環境下でSiC基板体10を加熱することにより、SiC基板体10表面を炭化させることなく、歪層12をSiC基板体10の表面側に移動・集中させることができる。
上述したSiVE法やMSE法の他に、以下の手法を例示することができる。
具体的には、図3に示すように、SiC材料40(Si元素供給源およびC元素供給源)を露出させた本体容器50内に、SiC基板体10を配置する。この本体容器50を加熱することにより、容器内にSi元素を含む気相環境を形成することができる。
また、SiC基板体10を収容する容器の少なくとも一部を、SiC材料40で形成する形態を例示することができる(図7参照)。この場合、容器全体をSiC材料40で形成しても良いし、SiC基板体10と相対する部分をSiC材料40で形成しても良い。
なお、SiC材料40に単結晶SiCを採用する場合には、何れのポリタイプのものも採用することができる。
歪層薄化工程S1における加熱時間は、所望の歪層12深さとなるよう任意の時間に設定することができる。
以下、エッチングを伴う場合と結晶成長を伴う場合に分けて詳細に説明する。
図1(b)および図4は、結晶成長を伴う歪層薄化工程S1の概要を示す説明図である。図4に示すように、SiC基板体10とSiC材料40とを相対させて配置し、これらの間に温度勾配を設けて加熱することで、SiC材料40からSiC基板体10へ原料(Si元素およびC元素)を輸送し、単結晶SiCを成長させることが可能である。
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)および3)の説明:Si原子(Si(v))が脱離することで残存したC原子(C(s))は、準閉鎖空間内のSi蒸気(Si(v))と反応する。その結果、C原子(C(s))は、Si2C又はSiC2等となって準閉鎖空間内に昇華する。
4)および5)の説明:昇華したSi2C又はSiC2等が、温度勾配(又は化学ポテンシャル差)によってSiC基板体10のテラスに到達・拡散しステップに到達することで、下地のSiC基板体10の多型を引き継いで成長する(ステップフロー成長)。
図1(c)および図5は、エッチングを伴う歪層薄化工程S1の概要を示す説明図である。図5に示すように、SiC基板体10とSiC材料40とを相対させて配置し、これらの間に温度勾配を設けて加熱することで、SiC基板体10からSiC材料40へ原料(Si元素およびC元素)を輸送し、SiC基板体10をエッチングさせることが可能である。
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)および3)の説明:Si原子(Si(v))が脱離することで、SiC基板体10表面に残存したC(C(s))は、準閉鎖空間内のSi蒸気(Si(v))と反応する。その結果、C(C(s))は、Si2C又はSiC2等となってSiC基板体10表面から昇華する(C原子昇華工程)。
4)および5)の説明:昇華したSi2C又はSiC2等が、温度勾配によって準閉鎖空間内のSiC材料40に到達し、結晶成長する。
これにより、SiC基板体10とSiC材料40との間にエッチング空間Yが形成され、温度勾配を駆動力としてSiC基板体10をエッチングすると共に、歪層12をSiC基板体10の表面側に移動させることができる。
歪層除去工程S2は、歪層薄化工程S1により薄くされた歪層12を除去する工程である。具体的には、歪層薄化工程S1前の歪層12の深さである基準深さ20よりも、表面側に移動した歪層12を除去する工程であり、基準深さ20よりも表面側の少なくとも一部を除去する工程である(図1(a)~図1(c))。
表1に、本実施の形態と従来法とのそれぞれのSiC基板の製造法において、基板厚み350μmのSiC基板30を製造する場合の一例についてまとめる。
一方、本実施の形態のSiC基板の製造方法における素材ロスL量は、表1に示すように50μmである。この通り、本実施の形態によれば、SiC基板の製造における素材ロスL量を大幅に低減することが可能である。
つまり、後行の工程により厚みがそれ以上減少しない時点にまで至ったSiC基板30の厚さに対して、素材ロスL量を加算して、スライス時の基板厚みD1を設定する。
つまり、これら典型的なSiC基板30の基板厚みに、本発明のSiC基板の製造方法による素材ロスL量を加算して、スライス時の基板厚みD1を設定することが好ましい。
また、この場合、スライス時の基板厚みD1は、上限として450μm以下、より好ましくは440μm以下、さらに好ましくは430μm以下、さらに好ましくは420μm以下、さらに好ましくは410μm以下、さらに好ましくは400μm以下であるSiC基板30をスライス工程S3において得ることが好ましい。
以下、本発明にかかるSiC基板の製造方法を実現する製造装置について詳細に説明する。なお、この実施の形態において、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。
本体容器50は、互いに嵌合可能な上容器51および下容器52と、を備える嵌合容器である。上容器51と下容器52の嵌合部には、微小な間隙53が形成されており、この間隙53から本体容器50内の排気(真空引き)が可能なよう構成されている。
加熱炉60は、図6に示すように、被処理物(SiC基板体10等)を1000℃以上2300℃以下の温度に加熱することが可能な本加熱室61と、被処理物を500℃以上の温度に予備加熱可能な予備加熱室62と、本体容器50を収容可能な高融点容器70と、この高融点容器70を予備加熱室62から本加熱室61へ移動可能な移動手段63(移動台)と、を備えている。
本加熱室61の内部には、加熱ヒータ64(メッシュヒーター)が備えられている。また、本加熱室61の側壁や天井には多層熱反射金属板が固定されている(図示せず。)。この多層熱反射金属板は、加熱ヒータ64の熱を本加熱室61の略中央部に向けて反射させるように構成されている。
なお、加熱ヒータ64としては、例えば、抵抗加熱式のヒータや高周波誘導加熱式のヒータを用いることができる。
このように急速昇温および急速降温が行えるため、従来の装置では困難であった、昇温中および降温中の低温成長履歴を持たない表面形状を観察することが可能である。
また、図6においては、本加熱室61の下方に予備加熱室62を配置しているが、これに限られず、何れの方向に配置しても良い。
すなわち、本実施の形態の加熱炉60は、高融点容器70の底部が移動台と接触しているため、高融点容器70の上容器71から下容器72に向かって温度が下がるように温度勾配が設けられる。この温度勾配は、SiC基板体10の表裏方向に沿って形成されていることが望ましい。
また、上述したように、加熱ヒータ64の構成により、温度勾配を形成してもよい。また、この加熱ヒータ64により、温度勾配を逆転可能に構成しても良い。
加熱炉60は、Si元素を含む雰囲気を形成し、この雰囲気内で本体容器50を加熱可能であることが好ましい。本実施の形態にかかる加熱炉60内のSi元素を含む雰囲気は、高融点容器70およびSi蒸気供給源74を用いて形成している。
なお、本体容器50の周囲にSi元素を含む雰囲気を形成可能な方法であれば、当然に採用することができる。
この他にも、加熱時に高融点容器70内にSi元素を含む気相種の蒸気圧が形成される構成であれば採用することができる。
スライス工程S3後のSiC基板体10を、本体容器50および高融点容器70に収容し(図7参照)、以下の熱処理条件で熱処理した。なお、この実施例1においては、本体容器50を多結晶SiCで形成することにより、本体容器50自体がSiC材料40(Si元素供給源およびC元素供給源)として機能するよう構成されている。
多型:4H-SiC
基板サイズ:横幅10mm×縦幅10mm×厚み0.45mm
オフ方向およびオフ角:<11-20>方向4°オフ
熱処理面:(0001)面
歪層12深さ:3.5μm
材料:多結晶SiC
容器サイズ:直径60mm×高さ4mm
基板保持具54の材料:単結晶SiC
SiC基板体10と本体容器50の底面の距離:2mm
材料:TaC
容器サイズ:直径160mm×高さ60mm
Si蒸気供給源74(Si化合物):TaSi2
上述した条件で配置したSiC基板体10を、以下の条件で熱処理した。
加熱温度:1500℃
加熱時間:10h
エッチング量:40nm
温度勾配:1℃/mm
本加熱室真空度:10-5Pa
SiC基板体10の格子歪みは、基準となる基準結晶格子と比較することにより求めることができる。この格子歪みを測定する手段としては、例えば、SEM-EBSD法を用いることができる。SEM-EBSD法は、走査電子顕微鏡(Scanning Electron Microscope:SEM)の中で、電子線後方散乱により得られる菊池線回折図形をもとに、微小領域の歪み測定が可能な手法(Electron Back Scattering Diffraction:EBSD)である。この手法では、基準となる基準結晶格子の回折図形と測定した結晶格子の回折図形を比較することで、格子歪み量を求めることができる。
SEM装置:Zeiss製Merline
EBSD解析:TSLソリューションズ製OIM結晶方位解析装置
加速電圧:15kV
プローブ電流:15nA
ステップサイズ:200nm
基準点R深さ:20μm
この図8(a)に示すように、歪層薄化工程S1の前においては、SiC基板体10内に深さ3.5μmの格子歪みが観察された。これは、スライス工程S3時により導入された格子歪みであり、歪層12を有していることがわかる。なお、この図8(a)では圧縮応力が観測されている。
この図8(b)に示すように、歪層薄化工程S1の後においては、SiC基板体10内に深さ1.3μmの格子歪みが観測された。熱処理時のエッチング量は40nmであるため、歪層12は、2.2μm程表面側に移動・集中したことがわかる。また、加熱時間を長くすることで、さらに表面側へ歪層12を移動させることができる。
このように、Si元素供給源およびC元素供給源を含む準閉鎖空間内で、SiC基板体10を熱処理することにより、SiC基板体10の表面側に歪層12が移動・集中させることができる。
11 バルク層
12 歪層
20 基準深さ
30 SiC基板
40 SiC材料
50 本体容器
51 上容器
52 下容器
53 間隙
54 基板保持具
55 Si蒸気供給源
60 加熱炉
61 本加熱室
62 予備加熱室
63 移動手段
64 加熱ヒータ
65 真空形成用バルブ
66 不活性ガス注入用バルブ
67 真空計
70 高融点容器
71 上容器
72 下容器
73 間隙
74 Si蒸気供給源
X 結晶成長空間
Y エッチング空間
S1 歪層薄化工程
S2 歪層除去工程
S3 スライス工程
S4 エッチング工程
I インゴット
Claims (16)
- SiC基板体の歪層を表面側に移動させることで前記歪層を薄くする歪層薄化工程を含む、SiC基板の製造方法。
- 前記歪層を除去する歪層除去工程を含み、
前記歪層薄化工程は、前記歪層薄化工程前の歪層の深さを基準深さとした場合において、前記歪層薄化工程後の歪層を前記基準深さよりも表面側に移動させる工程であり、
前記歪層除去工程は、前記基準深さよりも表面側の少なくとも一部を除去する工程である、請求項1に記載のSiC基板の製造方法。 - 前記歪層除去工程は、化学機械研磨である、請求項2に記載のSiC基板の製造方法。
- 前記歪層除去工程は、熱エッチング法である、請求項2に記載のSiC基板の製造方法。
- インゴットをスライスしてSiC基板体を得るスライス工程をさらに含み、
前記スライス工程は、前記歪層除去工程後におけるSiC基板体の厚みに、100μm以下の厚みを加算した厚みを有するSiC基板体を得る工程である、請求項2~4の何れか一項に記載のSiC基板の製造方法。 - 前記スライス工程は、前記歪層除去工程後におけるSiC基板体の厚みに、50μm以下の厚みを加算した厚みを有するSiC基板体を得る工程である、請求項5に記載のSiC基板の製造方法。
- 前記SiC基板体の表面をエッチングするエッチング工程をさらに含み、
前記エッチング工程は、ウェットエッチングである、請求項1~6の何れか一項に記載のSiC基板の製造方法。 - 前記エッチング工程は、エッチング液として、水酸化カリウム溶融液、フッ化水素酸を含む薬液、過マンガン酸カリウム系の薬液及び水酸化テトラメチルアンモニウムからなる群から選択される1種又は2種以上を含む、請求項7に記載のSiC基板の製造方法。
- インゴットをスライスしてSiC基板体を得るスライス工程を含み、
前記スライス工程、前記エッチング工程、前記歪層薄化工程をこの順で含む、請求項8に記載のSiC基板の製造方法。 - 前記歪層薄化工程は、Si元素を含む環境下でSiC基板体を加熱する工程である、請求項1~9の何れか一項に記載のSiC基板の製造方法。
- 前記歪層薄化工程は、Si元素供給源およびC元素供給源を含む準閉鎖空間内で、前記SiC基板体を加熱する工程である、請求項1~10の何れか一項に記載のSiC基板の製造方法。
- 前記歪層薄化工程は、SiC材料で構成された本体容器内で前記SiC基板体を加熱する工程である、請求項1~11の何れか一項に記載のSiC基板の製造方法。
- 前記歪層薄化工程は、SiC基板体とSiC材料とを相対させて配置し、SiC基板体とSiC材料との間に温度勾配が形成されるように加熱する工程である、請求項1~12の何れか一項に記載のSiC基板の製造方法。
- 前記歪層薄化工程は、Si蒸気圧環境下でSiC基板体を加熱する工程である、請求項1~13の何れか一項に記載のSiC基板の製造方法。
- 前記歪層薄化工程は、準安定溶媒エピタキシー法である、請求項1~14の何れか一項に記載のSiC基板の製造方法。
- 前記歪層薄化工程の加熱温度は、1400℃以上1600℃以下である、請求項1~15の何れか一項に記載のSiC基板の製造方法。
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TW202129097A (zh) | 2021-08-01 |
US20220344152A1 (en) | 2022-10-27 |
CN114424322A (zh) | 2022-04-29 |
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