WO2011055537A1 - スパッタリングターゲット及びその製造方法 - Google Patents
スパッタリングターゲット及びその製造方法 Download PDFInfo
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- WO2011055537A1 WO2011055537A1 PCT/JP2010/006481 JP2010006481W WO2011055537A1 WO 2011055537 A1 WO2011055537 A1 WO 2011055537A1 JP 2010006481 W JP2010006481 W JP 2010006481W WO 2011055537 A1 WO2011055537 A1 WO 2011055537A1
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- powder
- naf
- sputtering target
- sputtering
- target
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- 238000005477 sputtering target Methods 0.000 title claims abstract description 64
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 39
- 238000000034 method Methods 0.000 title abstract description 39
- 239000000843 powder Substances 0.000 claims abstract description 50
- 238000005245 sintering Methods 0.000 claims abstract description 31
- 239000011812 mixed powder Substances 0.000 claims abstract description 25
- 239000002184 metal Substances 0.000 claims abstract description 15
- 229910052751 metal Inorganic materials 0.000 claims abstract description 15
- PXGOKWXKJXAPGV-UHFFFAOYSA-N Fluorine Chemical compound FF PXGOKWXKJXAPGV-UHFFFAOYSA-N 0.000 claims abstract description 12
- 229910052731 fluorine Inorganic materials 0.000 claims abstract description 12
- 239000011737 fluorine Substances 0.000 claims abstract description 12
- 239000011261 inert gas Substances 0.000 claims abstract description 9
- -1 NaF compound Chemical class 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 239000002245 particle Substances 0.000 claims description 32
- 239000000758 substrate Substances 0.000 claims description 18
- 229910002056 binary alloy Inorganic materials 0.000 claims description 10
- 238000001513 hot isostatic pressing Methods 0.000 claims description 9
- 238000007731 hot pressing Methods 0.000 claims description 8
- 238000004544 sputter deposition Methods 0.000 abstract description 48
- 239000000203 mixture Substances 0.000 abstract description 14
- 229910052733 gallium Inorganic materials 0.000 abstract description 6
- 230000002829 reductive effect Effects 0.000 abstract 1
- 239000010408 film Substances 0.000 description 52
- 230000000052 comparative effect Effects 0.000 description 22
- 230000002159 abnormal effect Effects 0.000 description 16
- 238000003754 machining Methods 0.000 description 12
- 230000031700 light absorption Effects 0.000 description 11
- 229910000807 Ga alloy Inorganic materials 0.000 description 10
- 238000010438 heat treatment Methods 0.000 description 9
- 238000002844 melting Methods 0.000 description 9
- 230000008018 melting Effects 0.000 description 9
- 238000010248 power generation Methods 0.000 description 9
- 229910002059 quaternary alloy Inorganic materials 0.000 description 9
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 8
- 239000002994 raw material Substances 0.000 description 6
- 238000005336 cracking Methods 0.000 description 5
- 238000004453 electron probe microanalysis Methods 0.000 description 5
- 238000009835 boiling Methods 0.000 description 4
- 238000000227 grinding Methods 0.000 description 4
- 239000000155 melt Substances 0.000 description 4
- 238000002156 mixing Methods 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 238000010521 absorption reaction Methods 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 238000009616 inductively coupled plasma Methods 0.000 description 3
- 239000010935 stainless steel Substances 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 239000010409 thin film Substances 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 239000002826 coolant Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000001704 evaporation Methods 0.000 description 2
- 230000008020 evaporation Effects 0.000 description 2
- 239000003925 fat Substances 0.000 description 2
- 238000010304 firing Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 238000001755 magnetron sputter deposition Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000011164 primary particle Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 239000000523 sample Substances 0.000 description 2
- 239000011163 secondary particle Substances 0.000 description 2
- 239000004065 semiconductor Substances 0.000 description 2
- 239000005361 soda-lime glass Substances 0.000 description 2
- 229910000679 solder Inorganic materials 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000007740 vapor deposition Methods 0.000 description 2
- 230000000007 visual effect Effects 0.000 description 2
- 229910004613 CdTe Inorganic materials 0.000 description 1
- 239000004698 Polyethylene Substances 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000007580 dry-mixing Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000011521 glass Substances 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 239000012212 insulator Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 229920000573 polyethylene Polymers 0.000 description 1
- 239000002243 precursor Substances 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 238000004445 quantitative analysis Methods 0.000 description 1
- 229910002058 ternary alloy Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
- C23C14/3407—Cathode assembly for sputtering apparatus, e.g. Target
- C23C14/3414—Metallurgical or chemical aspects of target preparation, e.g. casting, powder metallurgy
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0425—Copper-based alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L31/00—Semiconductor devices sensitive to infrared radiation, light, electromagnetic radiation of shorter wavelength or corpuscular radiation and specially adapted either for the conversion of the energy of such radiation into electrical energy or for the control of electrical energy by such radiation; Processes or apparatus specially adapted for the manufacture or treatment thereof or of parts thereof; Details thereof
- H01L31/0248—Semiconductor devices sensitive to infrared radiation, light, electromagnetic radiation of shorter wavelength or corpuscular radiation and specially adapted either for the conversion of the energy of such radiation into electrical energy or for the control of electrical energy by such radiation; Processes or apparatus specially adapted for the manufacture or treatment thereof or of parts thereof; Details thereof characterised by their semiconductor bodies
- H01L31/0256—Semiconductor devices sensitive to infrared radiation, light, electromagnetic radiation of shorter wavelength or corpuscular radiation and specially adapted either for the conversion of the energy of such radiation into electrical energy or for the control of electrical energy by such radiation; Processes or apparatus specially adapted for the manufacture or treatment thereof or of parts thereof; Details thereof characterised by their semiconductor bodies characterised by the material
- H01L31/0264—Inorganic materials
- H01L31/032—Inorganic materials including, apart from doping materials or other impurities, only compounds not provided for in groups H01L31/0272 - H01L31/0312
- H01L31/0322—Inorganic materials including, apart from doping materials or other impurities, only compounds not provided for in groups H01L31/0272 - H01L31/0312 comprising only AIBIIICVI chalcopyrite compounds, e.g. Cu In Se2, Cu Ga Se2, Cu In Ga Se2
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E10/00—Energy generation through renewable energy sources
- Y02E10/50—Photovoltaic [PV] energy
- Y02E10/541—CuInSe2 material PV cells
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
- Y02P70/50—Manufacturing or production processes characterised by the final manufactured product
Definitions
- the present invention relates to a sputtering target used for forming a Cu—In—Ga—Se quaternary alloy film for forming a light absorption layer of a solar cell and a method for manufacturing the same.
- a Mo electrode layer serving as a positive electrode is formed on a soda lime glass substrate.
- a light absorption layer made of a Cu—In—Ga—Se quaternary alloy film is formed on the light absorption layer made of this Cu—In—Ga—Se quaternary alloy film.
- a buffer layer is formed, and a transparent electrode layer serving as a negative electrode is formed on the buffer layer.
- Non-Patent Document 1 proposes that the Na content in the precursor film (Cu—In—Ga—Se quaternary alloy film) is generally about 0.1%.
- the sputtering method has a problem that it is very difficult to add Na to the sputtering target.
- a Cu—Ga target is used to form a Cu—Ga film, but Na does not dissolve in Cu,
- the metal Na has a very low melting point (98 ° C.) and boiling point (883 ° C.), and the metal Na is very easy to oxidize, so it is difficult to add the metal Na to the Cu—Ga target. was there. *
- the present invention has been made in view of the above-described problems, and an object of the present invention is to provide a sputtering target capable of forming a Cu—Ga film doped with Na satisfactorily by a sputtering method and a manufacturing method thereof.
- the present inventors have studied to produce a Cu—Ga target to which Na is well added. As a result, it was ascertained that Na could be added satisfactorily if it was added to the target as compound-state NaF instead of metal Na. Therefore, the present invention has been obtained from the above findings, and the following configuration has been adopted in order to solve the above problems. That is, the sputtering target of the present invention contains Ga: 20 to 40 at%, Na: 0.05 to 1 at% as a metal component excluding fluorine (F) of the sputtering target, with the balance being Cu and inevitable impurities. And Na is contained in the state of a NaF compound. *
- the metal component excluding fluorine (F) of the sputtering target contains Ga: 20 to 40 at%, Na: 0.05 to 1 at%, and the balance is composed of Cu and inevitable impurities, Since Na is contained in the form of a NaF compound, a Cu—Ga film containing a good Na content with a high melting point (993 ° C.) and boiling point (1700 ° C.) and effective in improving power generation efficiency is obtained by sputtering. A film can be formed. Note that fluorine (F) in this Na-containing Cu—Ga film is removed from the film by high-temperature heat treatment (below the temperature at which soda lime glass is softened, that is, about 550 ° C.
- the reason why the amount of Na added is set within the above range is that when the Na content in the Cu—Ga target exceeds Na: 1 at%, a large amount of fluorine (F) is taken into the film, and the subsequent solar This is because it becomes difficult to remove in the battery manufacturing process and, at the same time, a large amount of Na is contained in the film, so that the denseness of the Cu—In—Ga—Se film is lowered and the power generation characteristics are deteriorated.
- the Na content in the Cu—Ga target is less than 0.05 at%, the amount of Na in the film is insufficient and the effect of improving the power generation efficiency cannot be obtained.
- a preferable amount of Na content in the Cu—Ga target is 0.1 to 0.5 at%. *
- the sputtering target of the present invention has a structure in which NaF is dispersed in the target substrate, and the average particle diameter of the NaF is 5 ⁇ m or less.
- NaF in a compound state having no conductivity is added to the conductive Cu—Ga target, abnormal discharge caused by NaF occurs frequently when direct current sputtering is performed in the same manner as the conventional Cu—Ga target.
- the light absorption layer of the solar cell is very thick (for example, 1000 to 2000 nm), and therefore the film thickness of Cu—Ga is very thick.
- the sputtering target of the present invention can optimize the particle size of NaF in the target substrate to enable the direct current sputtering similar to the conventional Cu—Ga target. That is, the sputtering target of the present invention has a structure in which NaF is dispersed in the target substrate, and the average particle diameter of NaF is 5 ⁇ m or less, thereby suppressing abnormal discharge caused by NaF and stable direct current sputtering. It becomes possible.
- the contained NaF is an insulator, if the average particle diameter exceeds 5 ⁇ m, abnormal discharge occurs frequently and DC sputtering becomes unstable. Therefore, in the present invention, by setting the average particle size of NaF to 5 ⁇ m or less, abnormal discharge is suppressed and stable direct current sputtering becomes possible.
- NaF particles in a 0.1 mm 2 visual field when observing a target cross section with an SEM are present when large NaF particles having a particle diameter of 10 to 40 ⁇ m are present.
- the number is preferably 3 or less.
- the sputtering target of the present invention is characterized in that Ga in the target substrate is contained in the form of a Cu—Ga binary alloy.
- the present inventors have found that when NaF is added, the presence of Ga alone in the target substrate affects the spatter crack resistance of the target. That is, it has been found that when Ga is contained alone in the target, the Cu—Ga target containing NaF is very susceptible to cracking and processing defects such as chips during machining after sintering.
- the sputtering target of the present invention is characterized by containing Ga in the target substrate in the form of a Cu—Ga binary alloy. That is, by using Ga as a solid solution of Cu—Ga or an intermetallic compound, stable sputtering can be realized without cracking after sintering, after machining, and during sputtering. *
- the manufacturing method of the sputtering target of the present invention is performed by preparing a mixed powder of NaF powder and Cu—Ga powder or a mixed powder of NaF powder, Cu—Ga powder and Cu powder in advance and using this mixed powder. It is characterized by these three manufacturing methods. That is, (1) A method for producing a sputtering target, comprising a step of forming a molded body from the above mixed powder and then sintering in a vacuum, an inert gas or a reducing atmosphere. (2) A method for producing a sputtering target, comprising a step of hot pressing the mixed powder in a vacuum or an inert gas atmosphere. (3) A method for producing a sputtering target, comprising a step of sintering the mixed powder by a hot isostatic pressing method (HIP method). *
- these sputtering target manufacturing methods can uniformly disperse and distribute NaF by sintering the mixed powder by a powder sintering method.
- NaF melts at 993 ° C. or higher, and the specific gravity is lower than Cu or Ga. Difficult to disperse.
- NaF evaporates vigorously when heated to 1000 ° C. or higher at normal pressure, the composition of the sputtering target using the melting method manufactured at a temperature of 1000 ° C. or higher greatly varies due to evaporation of the added NaF.
- the sputtering target of the present invention produced by the powder sintering method of the above (1) to (3), NaF is dispersed in a substrate made of Cu—Ga alloy or Cu—Ga alloy and Cu. Stable sputtering without cracking can be achieved after sintering, machining after sintering, and also during sputtering.
- the method for producing a sputtering target of the present invention is characterized in that, in the production method (1), the sintering after forming the molded body is performed at 700 to 950 ° C.
- the method for producing a sputtering target of the present invention is characterized in that, in the production method (2), the hot pressing temperature is 500 to 800 ° C.
- the sputtering target production method of the present invention is characterized in that, in the production method (3), the hot isostatic pressing is performed at a temperature of 500 to 800 ° C. and a pressure of 30 to 150 MPa. *
- the reason for setting the sintering temperature within the above range in the manufacturing method of (1) above is that the target density is not sufficiently increased when the temperature is lower than 700 ° C., and abnormal discharge is increased when sputtering the sputtering target. Because. On the other hand, when the firing temperature exceeds 950 ° C., evaporation of NaF starts and the composition of the target deviates from the target composition. A more preferable temperature is in the range of 700 to 750 ° C. *
- the reason for setting the hot press temperature within the above range in the production method of (2) above is that the target density is not sufficiently increased when the temperature is less than 500 ° C., and abnormal discharge is increased when sputtering the sputtering target. Because. On the other hand, when the hot press temperature exceeds 800 ° C, NaF moves to the grain boundary of Cu-Ga alloy and Cu particles, the strength of the sintered body decreases, and cracks and chips occur during machining and sputtering. It is because it becomes easy to do.
- a more preferable hot press temperature is in the range of 650 to 750 ° C. *
- the reason for setting the sintering temperature and pressure of the hot isostatic pressing (3) in the above range is that the target density is not sufficiently increased when the temperature is less than 500 ° C. or less than 30 MPa, and the sputtering target is This is because abnormal discharge increases during sputtering.
- the sintering temperature exceeds 800 ° C., the strength of the sputtering target is lowered, and cracks and chips are likely to occur during machining and during sputtering.
- a more preferable firing temperature is in the range of 550 ° C. to 650 ° C.
- the present invention has the following effects. That is, according to the sputtering target and the manufacturing method thereof according to the present invention, the sputtering target contains Ga: 20 to 40 at%, Na: 0.05 to 1 at% as a metal component excluding fluorine (F), and the balance is Cu. In addition, since Na is contained in the state of a NaF compound, a Cu—Ga film containing Na effective in improving power generation efficiency can be formed by sputtering. . Therefore, by forming a light absorption layer by sputtering using the sputtering target of the present invention, Na can be added satisfactorily and a solar cell with high power generation efficiency can be manufactured.
- the sputtering target of the present embodiment contains Ga: 20 to 40 at%, Na: 0.05 to 1 at% as a metal component excluding fluorine (F) of the sputtering target, and the balance is composed of Cu and inevitable impurities.
- the sputtering target of this embodiment has a structure in which NaF is dispersed in the target substrate, and the average particle diameter of the NaF is 5 ⁇ m or less.
- the number of NaF particles in a 0.1 mm 2 visual field is preferably 3 or less when large NaF particles having a particle diameter of 10 to 40 ⁇ m are present.
- Ga in the target substrate is contained in the form of a Cu—Ga binary alloy.
- the sputtering target of the present embodiment is prepared by preparing a mixed powder of NaF powder and Cu—Ga alloy powder or a mixed powder of NaF powder, Cu—Ga alloy powder and Cu powder in advance.
- the above mixed powder is filled in a molding mold with or without pressure molding, and tapped to form a molded body having a certain bulk density, which is 700 ° C. or higher in a vacuum, an inert gas or a reducing atmosphere.
- a manufacturing method of sintering at 950 ° C. (2) A manufacturing method in which the mixed powder is hot pressed in a temperature range of 500 ° C. to 800 ° C. in a vacuum or an inert gas atmosphere.
- a production method in which the mixed powder is sintered at a temperature of 500 ° C. to 800 ° C. and a pressure of 30 MPa to 150 MPa by a hot isostatic pressing method. *
- the mixed powder is prepared by any one of the following methods (1) to (3), for example.
- NaF preferably has a purity of 3N or more and a primary particle size of 0.3 ⁇ m or less, and this is averaged by using a pulverizer (eg, ball mill, jet mill, Henschel mixer, attritor, etc.). Crush to 5 ⁇ m or less.
- this pulverized powder is mixed and pulverized with a Cu—Ga alloy powder having a target composition using a mixing and pulverizing apparatus (for example, a ball mill, a Henschel mill, a jet mill, a V-type mixer, etc.), and prepared as a raw material powder. Since NaF dissolves in water, it is preferable to use a dry mixing and grinding apparatus that does not use water rather than a wet mixing and grinding apparatus that uses water. *
- NaF preferably has a purity of 3N or more and a primary particle size of 0.3 ⁇ m or less, and this is mixed with a previously prepared Cu—Ga alloy powder having a target composition at the same time as a mixing and grinding device (for example, ball mill, jet mill, Henschel). Mixer, attritor, V-type mixer, etc.), mixing and crushing NaF at the same time, finishing crushing when the average secondary particle size of NaF becomes 5 ⁇ m or less, and preparing as raw material powder .
- a mixing and grinding device for example, ball mill, jet mill, Henschel.
- a Cu—Ga alloy powder prepared in advance is made into a Cu—Ga alloy powder having a content greater than the Ga content of the target composition, and this is mixed with NaF. Or pure Cu powder) is added and mixed so as to have a target sputtering target composition, and prepared as a raw material powder.
- the raw material powder prepared by any one of the methods (1) to (3) is preferably stored in a dry environment. This is to prevent moisture absorption by NaF and aggregation of NaF particles due to moisture absorption.
- atmospheric pressure sintering, hot pressing, and hot isostatic pressing are performed in a vacuum, an inert gas atmosphere, or a reducing atmosphere.
- the presence of hydrogen in the atmosphere is advantageous for improving the sinterability, and the hydrogen content in the atmosphere is preferably 1% or more.
- the hot press since the pressure of the hot press affects the density of the target sintered body, the preferable pressure is 100 to 500 kgf / cm 2 . Further, the pressurization may be performed before the start of temperature increase, or may be performed after reaching a certain temperature.
- the sintered Cu—Ga—NaF sintered body is processed into a specified shape of the target by using ordinary electric discharge machining, cutting or grinding.
- a dry method that does not use a coolant or a wet method that uses a coolant that does not contain water is preferable during processing.
- the surface may be further processed by a dry method.
- the processed target is bonded to a backing plate made of Cu or SUS (stainless steel) or other metal (for example, Mo) using In as solder, and is subjected to sputtering.
- a backing plate made of Cu or SUS (stainless steel) or other metal (for example, Mo) using In as solder, and is subjected to sputtering.
- there are a method of applying fats and oils to the entire surface of the target and removing the fat after measurement and a method of covering the target with a waterproof sheet.
- a DC magnetron sputtering apparatus For sputtering of the Cu—Ga—NaF target thus produced, a DC magnetron sputtering apparatus is used, and Ar gas is used as the sputtering gas.
- the direct current (DC) sputtering at this time may use a pulsed DC power supply to which a pulse voltage is applied or a DC power supply without a pulse.
- the input power during sputtering is preferably 1 to 10 W / cm 2 .
- the thickness of the film formed using the Cu—Ga—NaF target is set to 1000 to 2000 nm.
- the metal component excluding fluorine (F) of the sputtering target contains Ga: 20 to 40 at%, Na: 0.05 to 1 at%, and the balance is composed of Cu and inevitable impurities. Therefore, by sputtering, a Cu—Ga film having a high melting point (993 ° C.) and boiling point (1700 ° C.) and containing Na which is effective for improving power generation efficiency can be formed. In addition, by having a structure in which NaF is dispersed in the target substrate and setting the average particle size of NaF to 5 ⁇ m or less, it is possible to suppress abnormal discharge due to NaF and perform stable DC sputtering. *
- the target substrate in the form of a Cu—Ga binary alloy
- NaF can be dispersed more uniformly than the melting method by using the above-described powder sintering method using the mixed powder.
- Examples Cu—Ga binary alloy powders or Cu powders (purity 4N) No. 1 having the component compositions and particle sizes shown in Table 1 were used. 1 to 15 were prepared, and NaF powder having a purity of 3N and a primary average particle size of 0.2 ⁇ m was added as shown in Table 1. These raw materials were put in a polyethylene pot having a volume of 10 L, and further ZrO 2 balls having a diameter of 5 mm were placed, and mixed and ground by a ball mill until the secondary particle diameter of NaF became 5 ⁇ m or less. The obtained mixed powder was sintered by the sintering method and sintering conditions specified in Table 2.
- the mixed powder was filled in a mold and pressed at room temperature at a pressure of 1500 kg / cm 2 to prepare a molded body.
- vacuum hot pressing was performed using a graphite mold at a pressure of 20 MPa.
- hot isostatic pressing the mixed powder is first filled in a mold, and pressure-molded at 1500 kgf / cm 2 at room temperature. The obtained molded body was charged into a 0.5 mm-thick stainless steel container and then subjected to hot isostatic pressing through vacuum deaeration. These sintered sintered bodies were subjected to dry cutting to prepare targets (Examples 1 to 15) of ⁇ 125 (mm) ⁇ 5 (mm) T.
- the average size of NaF particles can be measured, for example, by the following procedures (a) to (c).
- (A) Take 10 500 ⁇ COMPO images (60 ⁇ m ⁇ 80 ⁇ m) by field emission EPMA.
- the image analysis software for example, WinRoof Ver 5.6.2 (manufactured by Mitani Corporation) can be used as the image analysis software.
- a certain “threshold value” is set for the luminance (brightness) of each pixel of an image, and “0” is set if the threshold value is less than the threshold value, and “1” is set if the threshold value is greater. , To differentiate areas. *
- the maximum threshold value that does not select all the images is set to 100%, and a black side region is selected using a threshold value of 30 to 35%. Then, the selected region is contracted 4 times, and the region when expanded 3 times is NaF particle, and the size of each particle is measured.
- the shrinkage and expansion magnification is, for example, 2.3%. By this operation, a diameter corresponding to a circle is obtained from the area of each particle, and is defined as a particle size.
- quantitative analysis was performed using the ICP method (high frequency inductively coupled plasma method) with the Ga and Na contents in the prepared Cu—Ga—NaF target as a metal component excluding fluorine. *
- the target was formed into a 1000 nm-thick film on a 3.2 mm-thick blue glass coated with a Mo sputtered film by direct current sputtering at 5 W / cm 2 using a magnetron sputtering apparatus.
- the thickness of the Mo sputtered film was 500 nm.
- the Ar pressure during sputtering was 1.3 Pa, and the target-substrate distance was 70 mm. Note that the substrate is not heated during film formation.
- the number of occurrences of abnormal discharge during continuous sputtering for 10 minutes under the above conditions was automatically recorded by an arcing counter attached to the sputtering power source.
- “Comparative Example” Cu—Ga powder having the component composition and particle size shown in Table 5, or Cu powder and Ga metal were prepared, and NaF similar to Table 1 was prepared. These raw materials were mixed in the same manner as in the examples of the present invention. The mixture thus obtained was sintered by hot pressing, normal pressure sintering, or hot isostatic pressing under the conditions shown in Table 6. Note that the targets of the comparative examples all have a Na content outside the range of 0.05 to 1 at%. *
- the comparative example was evaluated in the same manner as in the above example.
- the evaluation results are shown in Table 7 and Table 8.
- Comparative Example 8 in which the content of Na is as high as 1.5 at%, the number of NaF aggregates having a particle size of 10 to 40 ⁇ m is as large as 6, and the metallic Ga phase is present, and Comparative Example 9 by the melt casting method , 10 are cracked or chipped during machining.
- Comparative Example 1 having a high Na content of 1.5 at% and a high hot press temperature of 950 ° C., and a Comparative Example having a high Na content of 1.5 at% and a large average particle size of NaF of 10 ⁇ m 2, Comparative Example 3 having a high Na content of 1.5 at% and a hot press temperature as low as 300 ° C., Comparative Example 11 in which atmospheric pressure sintering in the atmosphere did not sufficiently increase the density, and sintering Compared with Comparative Example 12, which has a temperature of 400 ° C., a pressure of 80 MPa, and is sintered by a hot isostatic press and has a low density, cracks and chips are generated during sputtering. *
- the number of abnormal discharges during sputtering was 50 or less, while in Comparative Examples 1, 2, 3, and 4, all occurred 100 times or more. That is, Comparative Example 1 with a high Na content of 1.5 at% and a high hot press temperature of 950 ° C., and Comparative Example 2 with a high Na content of 1.5 at% and a large NaF average particle size of 10 ⁇ m In Comparative Example 3 with a high Na content of 1.5 at% and a low hot press temperature of 300 ° C., and Comparative Example 4 with a high Na content of 3 at%, many abnormal discharges occurred. Yes. *
- Na in the film before the heat treatment is contained at 0.05 at% or more, and Na in the film after the heat treatment is contained at 0.3 at% or more.
- F (fluorine) in the film after heat treatment is 0 at%, and it can be seen that F is removed from the film by heat treatment.
- no metal Ga single phase is observed in XRD, and it can be seen that all of Ga in the target substrate is contained in the form of a Cu—Ga binary alloy.
- the sputtering target of the present invention contains Ga: 20 to 40 at%, and further contains Na: 0.05 to 1 at% in the state of NaF compound, with the balance being Cu and inevitable impurities. Therefore, by sputtering, a Cu—Ga film having a high melting point and boiling point and containing Na which is effective for improving power generation efficiency can be formed. Therefore, by forming a light absorption layer by sputtering using the sputtering target of the present invention, Na can be added well into the film, and a solar cell with high power generation efficiency can be produced. *
Abstract
Description
トをスパッタする際の異常放電が多くなるためである。一方、上記焼結温度が800℃を越えると、スパッタリングターゲットの強度が低下し、機械加工時や、スパッタ中に割れや欠けが発生しやすくなる。なお、より好ましい焼成温度は、550℃~650℃の範囲内である。
ガラスに1000nm成膜した。なお、Moスパッタ膜の厚みは500nmとした。 また、スパッタ時のAr圧力は1.3Paとし、ターゲット-基板間距離は70mmとした。なお、成膜時の基板加熱は行っていない。さらに、以上の条件において10分間の連続スパッタ中での、異常放電の発生回数をスパッタ電源に付属したアーキングカウンターにより自動的に記録した。
Claims (9)
- スパッタリングターゲットのフッ素(F)を除く金属成分としてGa:20~40at%、Na:0.05~1at%を含有し、残部がCu及び不可避不純物からなる成分組成を有し、NaはNaF化合物の状態で含有されていることを特徴とするスパッタリングターゲット。
- 請求項1に記載のスパッタリングターゲットにおいて、 ターゲット素地中にNaFが分散している組織を有すると共に、前記NaFの平均粒径が5μm以下であることを特徴とするスパッタリングターゲット。
- 請求項1に記載のスパッタリングターゲットにおいて、 ターゲット素地中のGaがCu-Ga二元合金の形態で含有されていることを特徴とするスパッタリングターゲット。
- 請求項1に記載のスパッタリングターゲットを作製する方法であって、 NaF粉末とCu-Ga粉末との混合粉末、又はNaF粉末とCu-Ga粉末とCu粉末との混合粉末からなる成形体を形成し、その後、真空、不活性ガスまたは還元雰囲気中で焼結する工程を有していることを特徴とするスパッタリングターゲットの製造方法。
- 請求項1に記載のスパッタリングターゲットを作製する方法であって、 NaF粉末とCu-Ga粉末との混合粉末、又はNaF粉末とCu-Ga粉末とCu粉末との混合粉末を、真空または不活性ガス雰囲気中でホットプレスにて焼結する工程であることを特徴とするスパッタリングターゲットの製造方法。
- 請求項1に記載のスパッタリングターゲットを作製する方法であって、 NaF粉末とCu-Ga粉末との混合粉末、又はNaF粉末とCu-Ga粉末とCu粉末との混合粉末を、熱間静水圧プレスにより焼結する工程であることを特徴とするスパッタリングターゲットの製造方法。
- 請求項4に記載のスパッタリングターゲットの製造方法において、 前記成形体形成後の焼結を、700~950℃で行うことを特徴とするスパッタリングターゲットの製造方法。
- 請求項5に記載のスパッタリングターゲットの製造方法において、 ホットプレス温度を、500~800℃で行うことを特徴とするスパッタリングターゲットの製造方法。
- 請求項6に記載のスパッタリングターゲットの製造方法において、 前記熱間静水圧プレスを、温度:500~800℃で、かつ圧力:30~150MPaの圧力で行うことを特徴とするスパッタリングターゲットの製造方法。
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JP2017500438A (ja) * | 2013-09-27 | 2017-01-05 | プランゼー エスエー | 銅−ガリウムスパッタリングターゲット |
WO2016047556A1 (ja) * | 2014-09-22 | 2016-03-31 | 三菱マテリアル株式会社 | スパッタリングターゲット及びその製造方法 |
CN108603283A (zh) * | 2016-02-08 | 2018-09-28 | 三菱综合材料株式会社 | 溅射靶及溅射靶的制造方法 |
CN108603283B (zh) * | 2016-02-08 | 2020-06-23 | 三菱综合材料株式会社 | 溅射靶及溅射靶的制造方法 |
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IN2012DN03820A (ja) | 2015-08-28 |
EP2402482B1 (en) | 2014-07-02 |
CN102395702A (zh) | 2012-03-28 |
EP2402482A4 (en) | 2012-03-28 |
JP4793504B2 (ja) | 2011-10-12 |
US8795489B2 (en) | 2014-08-05 |
KR20110113213A (ko) | 2011-10-14 |
JP2011117077A (ja) | 2011-06-16 |
CN102395702B (zh) | 2013-04-10 |
TWI360583B (ja) | 2012-03-21 |
EP2402482A1 (en) | 2012-01-04 |
KR101099416B1 (ko) | 2011-12-27 |
TW201126002A (en) | 2011-08-01 |
US20120217157A1 (en) | 2012-08-30 |
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