WO2016038711A1 - Ta-Nb合金粉末および固体電解コンデンサ用陽極素子 - Google Patents
Ta-Nb合金粉末および固体電解コンデンサ用陽極素子 Download PDFInfo
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- 239000000843 powder Substances 0.000 title claims abstract description 144
- 229910001257 Nb alloy Inorganic materials 0.000 title claims abstract description 64
- 239000003990 capacitor Substances 0.000 title claims abstract description 48
- 239000007787 solid Substances 0.000 title claims abstract description 14
- 238000000034 method Methods 0.000 claims abstract description 47
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- 239000010955 niobium Substances 0.000 description 82
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- 229910052715 tantalum Inorganic materials 0.000 description 8
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 8
- 229910052751 metal Inorganic materials 0.000 description 7
- 239000002184 metal Substances 0.000 description 7
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 description 6
- 239000010405 anode material Substances 0.000 description 5
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- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 4
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- URLJKFSTXLNXLG-UHFFFAOYSA-N niobium(5+);oxygen(2-) Chemical compound [O-2].[O-2].[O-2].[O-2].[O-2].[Nb+5].[Nb+5] URLJKFSTXLNXLG-UHFFFAOYSA-N 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
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- NUJOXMJBOLGQSY-UHFFFAOYSA-N manganese dioxide Chemical compound O=[Mn]=O NUJOXMJBOLGQSY-UHFFFAOYSA-N 0.000 description 2
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- MIVBAHRSNUNMPP-UHFFFAOYSA-N manganese(2+);dinitrate Chemical compound [Mn+2].[O-][N+]([O-])=O.[O-][N+]([O-])=O MIVBAHRSNUNMPP-UHFFFAOYSA-N 0.000 description 1
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- ZKATWMILCYLAPD-UHFFFAOYSA-N niobium pentoxide Chemical compound O=[Nb](=O)O[Nb](=O)=O ZKATWMILCYLAPD-UHFFFAOYSA-N 0.000 description 1
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- 238000007254 oxidation reaction Methods 0.000 description 1
- BPUBBGLMJRNUCC-UHFFFAOYSA-N oxygen(2-);tantalum(5+) Chemical compound [O-2].[O-2].[O-2].[O-2].[O-2].[Ta+5].[Ta+5] BPUBBGLMJRNUCC-UHFFFAOYSA-N 0.000 description 1
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Images
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
- C22C27/02—Alloys based on vanadium, niobium, or tantalum
-
- 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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
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- 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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/05—Metallic powder characterised by the size or surface area of the particles
- B22F1/054—Nanosized particles
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- 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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/05—Metallic powder characterised by the size or surface area of the particles
- B22F1/054—Nanosized particles
- B22F1/056—Submicron particles having a size above 100 nm up to 300 nm
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- 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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
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- 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
- B22F3/10—Sintering only
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- 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
- B22F3/24—After-treatment of workpieces or articles
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- 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
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
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- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/16—Making metallic powder or suspensions thereof using chemical processes
- B22F9/18—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds
- B22F9/20—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds starting from solid metal compounds
- B22F9/22—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds starting from solid metal compounds using gaseous reductors
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01G—CAPACITORS; CAPACITORS, RECTIFIERS, DETECTORS, SWITCHING DEVICES, LIGHT-SENSITIVE OR TEMPERATURE-SENSITIVE DEVICES OF THE ELECTROLYTIC TYPE
- H01G9/00—Electrolytic capacitors, rectifiers, detectors, switching devices, light-sensitive or temperature-sensitive devices; Processes of their manufacture
- H01G9/004—Details
- H01G9/04—Electrodes or formation of dielectric layers thereon
- H01G9/042—Electrodes or formation of dielectric layers thereon characterised by the material
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01G—CAPACITORS; CAPACITORS, RECTIFIERS, DETECTORS, SWITCHING DEVICES, LIGHT-SENSITIVE OR TEMPERATURE-SENSITIVE DEVICES OF THE ELECTROLYTIC TYPE
- H01G9/00—Electrolytic capacitors, rectifiers, detectors, switching devices, light-sensitive or temperature-sensitive devices; Processes of their manufacture
- H01G9/004—Details
- H01G9/04—Electrodes or formation of dielectric layers thereon
- H01G9/048—Electrodes or formation of dielectric layers thereon characterised by their structure
- H01G9/052—Sintered electrodes
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- 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
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/241—Chemical after-treatment on the surface
- B22F2003/242—Coating
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B22F2301/20—Refractory metals
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01G—CAPACITORS; CAPACITORS, RECTIFIERS, DETECTORS, SWITCHING DEVICES, LIGHT-SENSITIVE OR TEMPERATURE-SENSITIVE DEVICES OF THE ELECTROLYTIC TYPE
- H01G9/00—Electrolytic capacitors, rectifiers, detectors, switching devices, light-sensitive or temperature-sensitive devices; Processes of their manufacture
- H01G9/15—Solid electrolytic capacitors
Definitions
- the present invention relates to a Ta—Nb alloy powder suitable for use as an anode element of a small-sized and large-capacity solid electrolytic capacitor mainly used in electronic devices such as personal computers and mobile phones, and a solid electrolytic capacitor using the alloy powder.
- the present invention relates to an anode element.
- Capacitors are a type of electronic component used in various electronic devices such as personal computers and mobile phones, and basically have a structure in which a dielectric is sandwiched between two opposing electrode plates. When applied, charge is stored in each electrode by the polarization action of the dielectric.
- capacitors There are a wide variety of capacitors, but at present, aluminum electrolytic capacitors, multilayer ceramic capacitors, tantalum electrolytic capacitors, and film capacitors are mainly used.
- Ta tantalum solid electrolytic capacitor
- This Ta capacitor utilizes the fact that tantalum pentoxide (Ta 2 O 5 ), which is an anodic oxide film of Ta, is excellent as a dielectric, and compresses and molds Ta powder as an anode material in a high vacuum. Sintering to produce a porous element, then subjecting it to chemical conversion treatment (anodic oxidation treatment), an oxide film (amorphous Ta 2 O 5 film) excellent in corrosion resistance and insulation on the Ta powder surface, That is, a dielectric film is formed as an anode, and then the porous element is impregnated with a manganese nitrate solution and thermally decomposed to form a MnO 2 layer (electrolyte) on the anodized film as a cathode.
- Ta 2 O 5 tantalum pentoxide
- Ta 2 O 5 an anodic oxide film of Ta
- a CV value ( ⁇ F ⁇ V / g), which is a product of capacitance and formation voltage, is used.
- a CV value ( ⁇ F ⁇ V / g)
- commercially available Ta powder has a CV value of about 50 to 100 kF / V / g
- even a high-capacity product has a CV value of about 100 to 200 kF / V / g. Therefore, development of a tantalum powder for a capacitor having a higher CV value, specifically 250 k ⁇ F ⁇ V / g or more, is strongly desired.
- S electrode area (m 2 )
- t distance between electrodes (m)
- ⁇ dielectric constant (F / m)
- ⁇ ⁇ s ⁇ ⁇ 0
- ⁇ s relative permittivity of dielectric (Ta Oxide film: about 25)
- ⁇ 0 vacuum induction rate (8.855 ⁇ 10 ⁇ 12 F / m)
- the anode area S that is, the surface area of the Ta powder constituting the anode is increased, or the interelectrode distance t, that is, the film thickness of the anodic oxide film Ta 2 O 5 is decreased.
- the interelectrode distance t that is, the film thickness of the anodic oxide film Ta 2 O 5 is decreased.
- the primary particle diameter of Ta powder has been miniaturized as the capacity has increased in recent years.
- the primary particle size is reduced, the bonded portion (neck portion) of the metal particles when sintered is reduced, and the bonded portion is disconnected by the oxide film formed by chemical conversion treatment, resulting in a decrease in capacitance.
- miniaturization of primary particles causes an increase in the content of gas components such as oxygen, nitrogen, and hydrogen adsorbed on the surface, and other impurity components, which adversely affects the characteristics as a capacitor. Therefore, it is desirable that the Ta powder has a size of a certain level or more, specifically, a size of 30 nm or more.
- the Ta powder used for the above Ta capacitor is industrially produced by a Na reduction method in which K 2 TaF 7 is reduced with Na (see Patent Document 1), and a Mg reduction method in which Ta 2 O 5 is reduced with Mg.
- Patent Document 2 pulverization method in which Ta ingot is hydrogenated and pulverized
- Patent Document 3 thermal CVD method in which TaCl 5 is vaporized and reduced with H 2 (gas phase reduction method)
- Patent Documents 4 and 5 thermal CVD method described in Patent Documents 4 and 5 has an advantage that a fine Ta powder can be easily obtained.
- most of the Ta powders for capacitors currently used are manufactured by the Na reduction method (see Patent Document 6).
- this Na reduction method has a problem that it is difficult to efficiently produce fine and high-capacity Ta powder.
- the film thickness of the anodized film can be adjusted by the chemical conversion voltage, but reducing this film thickness causes various problems.
- a crystalline natural oxide film having a thickness of several nanometers formed during the production of the powder exists on the surface of the Ta powder.
- This oxide film often contains a large amount of impurities, and is inferior in quality and adhesion as a dielectric layer, so that electrical characteristics are deteriorated.
- This problem is not particularly apparent when the chemical conversion treatment is performed at a high voltage because it is buried in a thick anodic oxide film.
- the anodized film becomes thin, the crystalline oxide film is exposed on the surface.
- the reduction of the film thickness of the oxide film makes the impurities adsorbed on the surface of the powder and the film defects resulting therefrom more obvious.
- the leakage current (LC) is increased or the life of the capacitor is adversely affected. Therefore, there is a limit to reducing the film thickness of the anodized film Ta 2 O 5 to increase the capacity.
- Ta is a rare metal with a small reserve, it is difficult to stably supply, and is expensive and has a large price fluctuation. Therefore, there is an increasing need for solid electrolytic capacitors using metals other than Ta. Therefore, development and research of a niobium solid electrolytic capacitor using Nb, which has similar chemical and physical properties to Ta, has abundant reserves, and is inexpensive, has been partly put into practical use (for example, (See Patent Documents 7 to 10, Non-Patent Documents 1 and 2).
- JP 2002-206105 A Special Table 2002-544375 Japanese Patent Laid-Open No. 02-310301 Japanese Examined Patent Publication No. 64-073009 Japanese Patent Application Laid-Open No. 06-025701 JP 2007-335883 A Japanese Patent No. 3624898 Japanese Patent No. 4213222 Japanese Patent No. 4552732 Patent No. 4202609
- Niobium powder for capacitors metal, vol. 72 (2002) No. 3, p. 221-226 “Nb powder for electrolytic capacitors”; 8 (June 2005) p. 63-65
- the dielectric of the niobium solid electrolytic capacitor (hereinafter also referred to as “Nb capacitor”) is an oxide (niobium pentoxide Nb 2 O 5 ), and its dielectric constant is tantalum. Since it is 41, which is about 1.5 times that of the oxide Ta 2 O 5, a higher CV value can be obtained than a Ta capacitor.
- the niobium oxide film has low thermal stability and has problems such as a change in capacitance after mounting and deterioration of leakage current LC due to thermal stress in component mounting (reflow mounting). Even after commercialization, it has not been widely adopted.
- an object of the present invention is to provide a Ta—Nb alloy powder having a higher capacity than a Ta capacitor and an oxide film having a thermal stability superior to that of an Nb capacitor, and an anode element for a solid electrolytic capacitor using the alloy powder. Is to provide.
- the inventors have intensively studied to solve the above problems. As a result, by using Ta—Nb alloy powder manufactured by a thermal CVD method and controlling the Nb content within an appropriate range as an anode material, the CV value ( ⁇ F ⁇ V / g) per unit mass is higher than that of a Ta capacitor.
- the inventors have found that an anode element for a solid electrolytic capacitor that is high and excellent in thermal stability of an oxide film can be obtained, and the present invention has been completed.
- the present invention based on the above findings is a Ta—Nb alloy powder produced by a thermal CVD method, wherein the Nb content is 1 to 50 mass%, and the average primary particle size is 30 to 200 nm. It is a powder.
- the Ta—Nb alloy powder of the present invention is characterized in that the CV value ( ⁇ F ⁇ V / g) per unit mass when an anode element is used is 250 k ⁇ F ⁇ V / g or more.
- the Ta—Nb alloy powder of the present invention is characterized in that the CV value ( ⁇ F ⁇ V / mm 3 ) per unit volume when used as an anode element is 900 ⁇ F ⁇ V / mm 3 or more.
- R Nb Nb content in alloy (mass%) It is a value when in the anode element being defined [rho c.
- the Ta—Nb alloy powder of the present invention has an anode element, and the leakage current when the reflow treatment is performed at 260 ° C. for 30 minutes in an Ar atmosphere is not more than 8 times that before the reflow treatment. It is characterized by that.
- the present invention is an anode element for a solid electrolytic capacitor using the Ta—Nb alloy powder described above.
- the present invention it is possible to provide a Ta—Nb alloy powder suitable for use in a solid electrolytic capacitor having a higher CV value per unit volume and superior oxide film characteristics than an Nb capacitor. It greatly contributes to miniaturization and large capacity.
- 6 is a graph showing the influence of Nb content on CV value ( ⁇ F ⁇ V / g) per unit mass of Ta—Nb alloy powder. 6 is a graph showing the influence of Nb content on CV value ( ⁇ F ⁇ V / mm 3 ) per unit volume of Ta—Nb alloy powder. 6 is a graph showing the influence of Nb content on leakage current of Ta—Nb alloy powder. It is a graph which shows the influence of the reflow process on the CV value ( ⁇ F ⁇ V / mm 3 ) per unit volume of the Ta—Nb alloy powder. It is a graph which shows the influence of the reflow process which has on the leakage current of Ta-Nb alloy powder.
- the Ta—Nb alloy powder of the present invention is produced by a thermal CVD method (vapor phase reduction method).
- the thermal CVD method is suitable for producing fine metal powder, and at present, it is the only method that can stably produce fine Ta—Nb alloy powder. This is because an alloy having an easy composition and a narrow composition range can be produced.
- the specific method and conditions of the thermal CVD method are not particularly limited, but for example, any method disclosed in Japanese Patent Application Laid-Open No. 2004-52026 can be suitably used.
- the Ta—Nb alloy powder (primary particles) of the present invention must have an average particle size in the range of 30 to 200 nm.
- the average particle size is less than 30 nm, the strength of the joint part (neck part) between the particles formed when the Ta—Nb alloy powder is sintered is weak, and the joint part is broken by the anodic oxide film formed by the chemical conversion treatment. In addition, the conductivity and the electrostatic capacity are reduced.
- the average particle size exceeds 200 nm, the primary particle size is too large, so the surface area of the Ta—Nb alloy powder is reduced, and the target CV value (250 k ⁇ F ⁇ V / g or more) must be stably secured. Because it becomes difficult.
- the primary particles of the Ta—Nb alloy powder preferably have an average particle size in the range of 50 to 150 nm, preferably 60 to 120 nm. A range is more preferable.
- the average particle size of the Ta—Nb alloy powder is obtained by calculating the particle size of 1000 particles or more from a particle image taken with a scanning electron microscope SEM or the like. It is the number-based average particle diameter measured using -View).
- the Ta—Nb alloy powder of the present invention needs to have a Nb content in the range of 1 to 50 mass%.
- metal powders (hereinafter, the above three types of powders are collectively referred to as “metal powders”) in which the Ta powder, the Nb powder, and the Nb content were variously produced were manufactured by a thermal CVD method.
- the production conditions were adjusted so that the average particle diameter of the primary particles was in the range of 60 to 120 nm.
- the metal powder was pressure-molded to obtain pellets having a diameter of 3 mm ⁇ ⁇ length of 4 mm.
- the molding density is a value excluding the wire.
- the true density of varies depending on the composition. Therefore, the proper forming density (mass per unit volume) of the Ta—Nb alloy also varies depending on the composition, and the proper forming density decreases as the Nb content increases.
- it exceeds +0.20 g / cm 3 with respect to ⁇ c obtained from the above equation (1) cracks are likely to occur after molding or after sintering.
- the molded pellets were sintered at a temperature of 900 to 1200 ° C. in a vacuum atmosphere to obtain an anode element.
- the element was subjected to a chemical conversion treatment at a voltage of 10 V for 2 hr in a 0.05 mass% phosphoric acid solution at a temperature of 80 ° C. to form an anodic oxide film serving as a dielectric on the surface of the metal particles, and then the EIAJ RC
- the capacitance CV and the leakage current LC were measured.
- the capacitance CV was measured in a 40 mass% sulfuric acid solution at a voltage of 1 V, a bias voltage of 1.5 Vdc, and a frequency of 120 Hz.
- the leakage current LC was measured by applying a 7V voltage and measuring the leakage current after 2 minutes had elapsed.
- the capacitance CV and leakage current LC were also measured under the same conditions as described above for a Ta—Nb mixed powder in which Ta powder and Nb powder were blended so that the Nb content was 30 mass%. The measurement results are shown in Table 1.
- the leakage current was shown by the leakage current per unit capacity (nA / ⁇ F ⁇ V).
- FIG. 1 shows the relationship between the Nb content in the metal powder and the CV value per unit mass ( ⁇ F ⁇ V / g).
- the CV value of the element using Nb powder (also referred to as “Nb powder element”) is about 1.6 times the CV value of the element using Ta powder (also referred to as “Ta powder element”).
- the CV value of an element using a Ta—Nb mixed powder in which 30 mass% of Nb powder is mixed in Ta powder also referred to as “Ta—Nb mixed powder element” is the value of the Nb powder element and the Ta powder element.
- Ta—Nb alloy powder element An element using Ta—Nb alloy powder (also referred to as “Ta—Nb alloy powder element”) whereas it is almost the same as the CV value obtained by interpolation from the CV value (also referred to as “interpolated value”). It can be seen that the CV value is higher than the CV value obtained by the above interpolation. Therefore, it can be seen that the capacitance of the Ta—Nb alloy powder element has different capacitance characteristics from those of the Ta powder element, Ta powder element, and Ta—Nb mixed powder element in which only Ta powder and Nb powder are mixed. However, it is difficult to say that the CV value ( ⁇ F ⁇ V / g) per unit mass of the Ta—Nb alloy powder element is better than that of the Nb powder element.
- FIG. 2 shows the CV value per unit mass ( ⁇ F ⁇ V / g) in FIG. 1 converted to the CV value per unit volume ( ⁇ F ⁇ V / mm 3 ).
- the CV value of the Ta—Nb mixed powder element is on a straight line connecting the CV values of the Ta powder element and the Nb powder element, and the interpolation value obtained from the CV values of the Nb powder element and the Ta powder element. Is the same.
- the CV value of the Ta—Nb alloy powder element having the Nb content in the range of 14 to 62 mass% is about 17 to 30 than the interpolated value obtained from the CV value of the Nb powder element and the Ta powder element. %, And even a Ta—Nb alloy containing only 1.7 mass% of Nb has a CV value as high as about 8% compared to the interpolated value.
- the Ta—Nb alloy produced by the thermal CVD method exhibits different capacity characteristics from Ta and Nb single powder, and Ta—Nb mixed powder obtained by simply mixing Ta powder and Nb powder, It can be seen that this is a material capable of producing a capacitor having a higher capacity than before.
- Patent Document 10 of the prior art discloses a Ta—Nb alloy having an Nb content of about 75 mass% and a primary particle diameter of about 400 nm manufactured by the Mg reduction method.
- the CV value per unit mass is disclosed. Is 290 kF / V / g. This value is 250 k ⁇ F ⁇ V / g or more, but is only a value lower than the interpolated value of the Ta—Nb mixed powder having the same composition shown in FIG. Therefore, it is considered difficult to produce a high-capacity Ta—Nb alloy powder by a method other than the CVD method.
- the Ta—Nb alloy powder produced by the thermal CVD method has a problem of poor fluidity because it is a fine powder, but this can be solved by improving the granulation technique described later.
- FIG. 3 shows the relationship between the Nb content per unit volume and the leakage current LC in the Ta powder element, the Nb powder element and the Ta—Nb alloy powder element.
- the leakage current of the Nb powder element is about twice or more that of the Ta powder element, that is, 2.0 nA / ⁇ F ⁇ V or more, which is not preferable for a capacitor.
- the leakage current of the Ta—Nb mixed powder element is also shown in the figure, but is similar to that of the Ta—Nb alloy powder element.
- the Ta—Nb alloy powder with the Nb content in the range of 1 to 62 mass% manufactured by the thermal CVD method has a CV value ( ⁇ F) per unit volume from the Ta powder, Nb powder, and Ta—Nb mixed powder.
- V / mm 3 is excellent, and it can be seen that the anode material is suitable for downsizing and increasing the capacity of the capacitor.
- FIG. 4 shows a comparison of CV values ( ⁇ F ⁇ V / mm 3 ) per unit volume before and after the reflow treatment. From this figure, the CV value per unit volume after the reflow treatment increases as the Nb content increases, and the increase rate (%) with respect to the CV value before the reflow treatment is less than 47 mass% for the Nb content. It is about 20%. However, it can be seen that when the Nb content is 62 mass%, the Nb content has risen to nearly 40%, which is inferior in thermal stability.
- the CV value after the reflow treatment of the Ta—Nb mixed powder element is still on a straight line connecting the CV values of the Ta powder element and the Nb powder element, and is obtained from the CV values of the Nb powder element and the Ta powder element. Same as inset value.
- FIG. 5 shows a comparison of the leakage current LC before and after the reflow process.
- the increase ratio defined by (LC after reflow treatment / LC before reflow treatment) is 8 or less, but when the Nb content is 62 mass% or more, it will be 10 or more and deteriorate to the same extent as Nb powder. I understand.
- the leakage current after the reflow treatment of the Ta—Nb mixed powder element is greatly increased as compared with the Ta—Nb alloy powder element, and the increase ratio is deteriorated to the same level as that of the Nb powder element.
- the Ta—Nb alloy powder of the present invention can obtain the CV value ( ⁇ F ⁇ V / mm 3 ) per unit volume from the CV value of Nb powder and Ta powder.
- the Nb content is set to 1 mass% or more, and from the viewpoint of making the capacitance CV and leakage current LC deterioration due to reflow processing smaller than that of the Nb powder, the Nb content is set to 50 mass% or less. It was decided to limit to.
- the preferred Nb content is in the range of 1 to 40 mass%.
- the reflow treatment causes oxygen in the niobium oxide film to diffuse and disappear, the thickness of the oxide film forming the dielectric decreases, and the disappearance of the oxygen causes the oxide film to become thinner. This is thought to be due to the fact that defects become obvious or that insulating Nb 2 O 5 is transformed into conductive NbO.
- the Ta—Nb alloy powder When Ta—Nb alloy powder is used as an anode material for a capacitor, the Ta—Nb alloy powder is generally compression-molded into the shape of an anode element with an automatic molding machine or the like.
- the Ta—Nb alloy powder (primary particles) produced by the thermal CVD method has a fine particle diameter, a low bulk density, and a large pushing allowance, the density of the molded body serving as the anode element is not uniform. Easy to be.
- the particles after granulation preferably have a fluidity measured in accordance with JIS Z2502 in the range of 0.5 to 5 g / second.
- the fluidity is less than 0.5 g / second, the fluidity is poor and the amount of the material charged into the molding machine mold is not stable, so that the dispersion of the anode element weight after compression molding becomes large.
- the fluidity exceeds 5 g / second, the particle size becomes too large, and it becomes difficult to obtain an anode element having a uniform density by compression molding.
- the range is preferably 1 to 4 g / sec.
- liquidity in this invention is the value which divided
- the granulated Ta—Nb alloy powder (secondary particles) preferably has a size in the range of 10 to 500 ⁇ m in terms of volume-based median diameter d 50 .
- the d 50 of less than 10 [mu] m, it is difficult to flowability and moldability is molded deteriorated. On the other hand, when d 50 exceeds 500 ⁇ m, it is difficult to uniformly fill the molding die, and the density of the molded body becomes non-uniform.
- a more preferable median diameter d 50 is in the range of 15 to 300 ⁇ m.
- the volume-based median diameter d 50 is a value obtained by measuring a particle image captured at 100 times using a scanning electron microscope, using image analysis type particle size distribution software, like the primary particles.
- the Ta—Nb alloy powder (secondary particles) after granulation preferably has a powder bulk density in the range of 1.00 to 4.00 g / cm 3 .
- the powder bulk density is less than 1.00 g / cm 3 , it is difficult to increase the density of the molded body, and the electrostatic capacity per unit volume when the anode element is formed decreases.
- the powder bulk density exceeds 4.00 g / cm 3 , it becomes difficult to impregnate manganese dioxide MnO 2 serving as a cathode or a conductive polymer material after sintering.
- a more preferable bulk density is in the range of 1.50 to 3.80 g / cm 3 .
- the above-mentioned powder bulk density in the present invention refers to a “relaxed bulk density” measured according to JIS Z2504.
- the method for obtaining Ta—Nb granulated powder (secondary particles) from Ta—Nb alloy powder (primary particles) produced by thermal CVD is not particularly limited as long as the granulated powder satisfying the above conditions is obtained.
- the granulated powder satisfying the above conditions is obtained.
- acrylic, polyvinyl alcohol (PVA), polyvinyl butyral (PVB), methyl cellulose, carboxyl cellulose, etc. as a granulating agent (binder) to Ta—Nb alloy particles, it is rolled on a rotating drum or the like.
- a granulation method, a high-speed rotary granulation method, a fluidized bed granulation method, a spray drying method, or the like can be used.
- the heat granulation method which heats and sinters, grind
- the granulated powder of Ta—Nb alloy powder whose bulk density, particle size distribution, and median diameter are adjusted to appropriate ranges by the above various granulation methods, is usually dry-formed, debindered, fired, and then subjected to chemical conversion treatment.
- the molding density at the time of dry molding may be appropriately selected according to required electrostatic characteristics.
- a method of directly molding from the primary powder without using the dry molding process described above may be employed.
- a solvent such as a binder or water is added to the primary powder, kneaded to form a dough, formed into a sheet with an extrusion molding machine, the sheet is removed from the binder, vacuum fired, and then the wire is welded or the like It is good also as an anode element by joining.
- the alloy powder was washed with water, dried and after addition of binder cellulosic, granulated using a rotary drum, and the granulated particles of 30 ⁇ 50 [mu] m in median diameter d 50 (secondary particles).
- the granulated particles were sintered according to the test conditions of 100 kCV powder specified in Table 1 of the Annex of the Japan Electronic Machinery Manufacturers Association Standard EIAJ RC-2361A “Testing Method for Tantalum Sintered Elements for Tantalum Electrolytic Capacitors”.
- a sintered element was produced.
- the molding density of the element (pellet) is adjusted so as to be within ⁇ 0.10 g / cm 3 with respect to ⁇ c obtained by the above-described equation (1). Since the temperature depends on the particle size and becomes higher as the particle size becomes larger, preliminary experiments were conducted in the temperature range of 950 to 1150 ° C., and the temperature at which the highest capacitance was obtained was adopted.
- the device was subjected to a chemical conversion treatment at a voltage of 10 V for 2 hr in a 0.05 mass% phosphoric acid solution at a temperature of 80 ° C. to form an anodized film on the surface of the metal particles, and then described in EIAJ RC-2361A
- the capacitance CV and the leakage current LC were measured according to the method.
- the capacitance CV was measured in a 40 mass% sulfuric acid solution at a voltage of 1 V, a bias voltage of 1.5 Vdc, and a frequency of 120 Hz.
- 7V voltage was applied for the leakage current LC, and the leakage current after 2 minutes passed was measured.
- the element after the above measurement was subjected to a heat treatment simulating a reflow process of 260 ° C. ⁇ 30 min in an Ar gas atmosphere, and the capacitance CV and the leakage current LC were measured under the same conditions as described above.
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Abstract
Description
C=(ε・S)/t
ここで、S:電極面積(m2)、t:電極間距離(m)、ε:誘電率(F/m)、ε=εs・ε0、εs:誘電体の比誘電率(Taの酸化皮膜:約25)、ε0:真空誘導率(8.855×10-12F/m)
で表わされ、電極面積Sが大きいほど、電極間距離tが小さいほど、また、誘電率εが高いほど、大きくなる。したがって、CV値を高めるためには、陽極面積S、即ち、陽極を構成しているTa粉末の表面積を大きくするか、電極間距離t、即ち、陽極酸化皮膜Ta2O5の膜厚を薄くするか、誘電率εの高い材料を利用する必要がある。
ρc(g/cm3)=-0.012RNb+3.57 ・・・(1)
ここで、RNb:合金中のNb含有量(mass%)
で定義されるρcの陽極素子としたときの値である。
<実験1>
熱CVD法で、Ta粉末、Nb粉末およびNb含有量を種々に変えたTa-Nb合金粉末(以降、上記3種類の粉末を「金属粉末」と総称する)を製造した。なお、上記金属粉末の製造するに際しては、一次粒子の平均粒径が60~120nmの範囲内となるよう製造条件を調整した。次いで、上記金属粉末を加圧成形して直径3mmφ×長さ4mmのペレットとした。この際、上記加圧成形後のペレットの成形密度ρ(g/cm3)は、Ta-Nb合金中のNbの含有量RNb(mass%)に応じて、下記(1)式;
ρc=-0.012RNb+3.57 ・・・(1)
から求められるρcに対して±0.10g/cm3の範囲に収まるよう調整した。なお、上記成形密度は、ワイヤを除いた値である。
実際、上記実験における成形において、上記(1)式から得られるρcに対して+0.20g/cm3を超えると、成形後や焼結後にクラック(割れ)が発生し易くなり、逆に、上記(1)式から得られるρcに対して-0.20g/cm3を下回ると、成形体としての強度を確保することが困難であった。また、より好ましい成形密度は、(1)式から得られるρcに対して±0.10g/cm3の範囲であった。
次いで、上記素子に、温度が80℃の0.05mass%のリン酸溶液中で、電圧10Vで2hrの化成処理を施して金属粒子表面に誘電体となる陽極酸化被膜を形成した後、EIAJ RC-2361Aに記載の方法に準拠して、静電容量CVおよび漏れ電流LCを測定した。なお、静電容量CVの測定は、40mass%の硫酸溶液中で、電圧1V,バイアス電圧1.5Vdc、周波数120Hzで測定した。また、漏れ電流LCの測定は、7V電圧を印加し、2min経過後の漏れ電流を測定した。
また、参考として、Ta粉末およびNb粉末をNb含有量が30mass%となるよう配合したTa-Nb混合粉末についても、上記と同じ条件で、静電容量CVおよび漏れ電流LCを測定した。
上記の測定結果を、表1に示した。なお、漏れ電流は、単位容量当たりの漏れ電流(nA/μF・V)で示した。
この図から、単位体積当たりのCV値(μF・V/mm3)では、Ta粉末素子とNb粉末素子の差は大きく縮まり、9%弱の差しかない。この差は、体積サイズが一定としてTa粉末およびNb粉末をそれぞれ同条件で充填して素子を作製したときの静電容量の差に相当し、実用上、コンデンサを設計する上で重要な指標となる。また、この場合でも、Ta-Nb混合粉末素子のCV値は、Ta粉末素子とNb粉末素子のCV値を結ぶ直線上にあり、Nb粉末素子およびTa粉末素子のCV値から得られる内挿値と同じである。
なお、熱CVD法で製造したTa-Nb合金粉末は、微粉であるが故に、流動性が悪いという問題点を有するが、この点については、後述する造粒技術の改善によって解決可能である。
次に、発明者らは、Ta-Nb合金粉末の熱的安定性を調査するため、上記実験に用いた化成処理後の素子に、実装時のリフロー処理を模擬して、260℃×30分の熱処理をアルゴンガス雰囲気中で施し、CV値(μF・V/mm3)および漏れ電流LCの変化を調査した。なお、CV値および漏れ電流LCの測定は、前述した<実験1>と同条件で行った。なお、参考として、Ta-Nb混合粉末についても同様の調査を行った。
また、バインダとして水、リン酸水などの無機物を使用して造粒した後、加熱して焼結し、粉砕し、その後、酸素等の不純物を除去する熱造粒法も適宜用いることができる。
また、陽極素子の作製には、上記の乾式成形プロセスを用いずに、一次粉末から直接成形する方法を採用してもよい。例えば、一次粉末にバインダや水等の溶媒を添加し、混練して練土とし、押し出し成形機でシートに成形した後、該シートを脱バインダし、真空焼成し、その後、ワイヤを溶接等で接合して陽極素子としてもよい。
次いで、上記造粒粒子を、日本電子機械工業会規格EIAJ RC-2361A「タンタル電解コンデンサ用タンタル焼結素子の試験方法」附属書の表1に規定された100kCV粉末の試験条件に準拠して焼結素子を作製した。この際、素子(ペレット)の成形密度は、前述した(1)式で得られるρcに対して±0.10g/cm3以内に収まるように調整し、また、一般に、素子の最適焼結温度は粒径に依存し、粒径が大きくなるほど高くなるため、950~1150℃の温度範囲で予備実験し、最も高い静電容量が得られる温度を採用した。
さらに、上記測定後の素子に対して、Arガス雰囲気中で、260℃×30minのリフロー処理を模した熱処理を施し、上記と同条件で、静電容量CVおよび漏れ電流LCを測定した。
Claims (5)
- 熱CVD法で製造したTa-Nb合金粉末であって、
Nbの含有量が1~50mass%で、一次粒子の平均粒径が30~200nmであるTa-Nb合金粉末。 - 陽極素子としたときの単位質量当たりのCV値(μF・V/g)が250kμF・V/g以上であることを特徴とする請求項1に記載のTa-Nb合金粉末。
- 陽極素子としたときの単位体積当たりのCV値(μF・V/mm3)が900μF・V/mm3以上であることを特徴とする請求項1または2に記載のTa-Nb合金粉末。ここで、上記CV値は、成形密度ρ(g/cm3)を下記(1)式で定義されるρcの陽極素子としたときの値である。
記
ρc(g/cm3)=-0.012RNb+3.57 ・・・(1)
ここで、RNb:合金中のNb含有量(mass%) - 陽極素子とした後、Ar雰囲気下で260℃×30分間保持するリフロー処理を施したときの漏れ電流が、リフロー処理前の8倍以下であることを特徴とする請求項1~3のいずれか1項に記載のTa-Nb合金粉末。
- 請求項1~4のいずれか1項に記載のTa-Nb合金粉末を用いた固体電解コンデンサ用陽極素子。
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Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2019198191A1 (ja) * | 2018-04-12 | 2019-10-17 | 石原ケミカル株式会社 | Ta-Nb合金粉末とその製造方法ならびに固体電解コンデンサ用の陽極素子 |
Also Published As
Publication number | Publication date |
---|---|
JP6353912B2 (ja) | 2018-07-04 |
EP3192595B1 (en) | 2019-04-17 |
JPWO2016038711A1 (ja) | 2017-06-29 |
US20170283916A1 (en) | 2017-10-05 |
EP3192595A4 (en) | 2018-04-04 |
EP3192595A1 (en) | 2017-07-19 |
US10329644B2 (en) | 2019-06-25 |
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