WO2019131782A1 - 歯科用に好適なジルコニア仮焼体 - Google Patents
歯科用に好適なジルコニア仮焼体 Download PDFInfo
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- WO2019131782A1 WO2019131782A1 PCT/JP2018/047904 JP2018047904W WO2019131782A1 WO 2019131782 A1 WO2019131782 A1 WO 2019131782A1 JP 2018047904 W JP2018047904 W JP 2018047904W WO 2019131782 A1 WO2019131782 A1 WO 2019131782A1
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- zirconia
- point
- less
- calcined body
- body according
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- XDTMQSROBMDMFD-UHFFFAOYSA-N C1CCCCC1 Chemical compound C1CCCCC1 XDTMQSROBMDMFD-UHFFFAOYSA-N 0.000 description 1
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- A61C13/00—Dental prostheses; Making same
- A61C13/08—Artificial teeth; Making same
- A61C13/083—Porcelain or ceramic teeth
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Definitions
- the present invention relates to a zirconia calcined body. Furthermore, the present invention relates to a method for producing a zirconia sintered body comprising the zirconia calcined body and a dental product.
- Zirconia is a compound in which phase transition occurs between a plurality of crystal systems. Therefore, partially-stabilized zirconia (PSZ; Partially-Stabilized Zirconia) and fully-stabilized zirconia in which the phase transition is suppressed by dissolving a stabilizer such as yttria (yttrium oxide; Y 2 O 3 ) in zirconia and suppressing the phase transition are various fields.
- PSZ partially-stabilized zirconia
- yttria yttrium oxide
- Y 2 O 3 yttrium oxide
- Patent Document 1 discloses a colored zirconia sintered body having high transparency and suitable for dental use (in particular, front teeth).
- the colored translucent zirconia sintered body described in Patent Document 1 is produced by sintering a pressed compact of zirconia powder at 1450 ° C., a temperature rising rate of 600 ° C./hr, and a holding time of 2 hours. .
- the zirconia powder contains more than 4.0 mol% and up to 6.5 mol% of yttria and less than 0.1 wt% of alumina, and has a BET specific surface area of 8 to 15 m 2 / g and an average particle size of 0. It is 40 to 0.50 ⁇ m, and the total proportion of tetragonal crystals and cubic crystals contained in the crystals is 80% or more.
- the holding time at the maximum temperature is 2 hours, and the entire firing step including cooling is required for about 7 to 8 hours.
- the patient can not receive treatment with the dental prosthesis on the day of the examination, and visit the hospital again on another day Must.
- the colored translucent zirconia sintered body is manufactured by shortening the holding time at the maximum temperature, it becomes cloudy and the light transmitting property of the sintered body is lowered, and a color tone suitable for dental use can not be reproduced There is a problem called.
- a zirconia calcined body that exhibits a color tone suitable for dental use (particularly in dental clinics) even after firing for a short time.
- a zirconia calcined body capable of maintaining the light transmitting property of the sintered body after firing even for a short time firing is required.
- the inventor of the present invention has made it possible to use a zirconia calcined body whose main crystal system is a monoclinic crystal and the L * a * b * values of each layer after firing.
- the inventors have found that the above-mentioned problems can be solved by appropriately setting the zirconia calcined body, and have further studied based on this finding and completed the present invention.
- the present invention includes the following inventions.
- L1-L2 is more than 0 and 12.0 or less, a2-a1 is more than 0 and 6.0 or less, The zirconia calcined body according to the above [1], wherein b2-b1 is more than 0 and not more than 12.0.
- L1-L2 is more than 0 and not more than 8.0, a2-a1 is more than 0 and not more than 5.0, The zirconia calcined body according to the above [1] or [2], wherein b2-b1 is more than 0 and not more than 10.0.
- L1-L2 is 1.0 or more and 7.0 or less
- a2-a1 is 0.5 or more and 3.0 or less
- the third point is at a distance of 45% of the total length from the one end
- the zirconia calcined body according to [7] wherein the fourth point is at a distance of 55% of the total length from the one end.
- the pigment further contains a pigment, and the pigment is Ti, V, Cr, Mn, Fe, Co, Ni, Zn, Y, Zr, Sn, Sb, Bi, Ce, Pr, Sm, Eu, Gd, and Tb.
- I m (111) and I m (11-1) indicate peak intensities of (111) plane and (11-1) plane of the monoclinic system of zirconia in the X-ray diffraction pattern
- I t (111) represents the peak intensity of the (111) plane of the tetragonal system of zirconia in the X-ray diffraction pattern
- I c (111) shows the peak intensity of the (111) plane of the cubic system of zirconia in the X-ray diffraction pattern.
- a first translucent property of a first sintered body produced by firing the zirconia calcined body for 30 minutes at a proper firing temperature When comparing the second light transmitting property of the second sintered body produced by firing the zirconia calcined body at the appropriate firing temperature for 120 minutes, The zirconia calcined body according to any one of the above [1] to [21], wherein the first light transmitting property is 85% or more of the second light transmitting property.
- a first light transmitting property of a first sintered body produced by firing the zirconia calcined body for 15 minutes at a proper firing temperature When comparing the second light transmitting property of the second sintered body produced by firing the zirconia calcined body at the appropriate firing temperature for 120 minutes, The zirconia calcined body according to any one of the above [1] to [22], wherein the first light transmittance is 85% or more of the second light transmittance.
- a method for producing a zirconia sintered body comprising firing the zirconia calcined body according to any one of the above [1] to [23] at a maximum firing temperature of 1400 ° C. to 1600 ° C.
- a method for producing a dental product comprising cutting and processing the zirconia calcined body according to any one of the above [1] to [23].
- a zirconia calcined body in which a sintered body after firing exhibits a color tone suitable for dental use (particularly, use in a dental clinic) even in a short time firing. Further, according to the present invention, it is possible to provide a zirconia calcined body capable of maintaining the light transmittance of the sintered body after firing even for a short time.
- FIG. 1 is an X-ray diffraction pattern of a calcined body produced in Example 1.
- FIG. 7 is an X-ray diffraction pattern of a calcined body produced in Example 3.
- 7 is an X-ray diffraction pattern of a calcined body produced in Comparative Example 4; It is a graph which shows the change of the light transmission retention rate with respect to the holding time in the suitable calcination temperature. It is a photograph of the external appearance of the zirconia sintered compact regarding judgment of appropriate calcination temperature.
- the zirconia calcined body of the present invention will be described.
- the zirconia calcined body can be a precursor (intermediate product) of a zirconia sintered body.
- a zirconia calcined body can be, for example, one obtained by blocking zirconia particles (powder) in a state in which they are not completely sintered.
- the density of the zirconia calcined body is preferably 2.7 g / cm 3 or more.
- the density of the zirconia calcined body is preferably 4.0 g / cm 3 or less, more preferably 3.8 g / cm 3 or less, 3.6 g / cm 3 or less is more preferred. If it is in this density range, molding can be easily performed.
- the zirconia calcined body of the present invention contains zirconia and a stabilizer capable of suppressing the phase transition of zirconia.
- the stabilizer is preferably one capable of forming partially stabilized zirconia.
- the stabilizer include oxides such as calcium oxide (CaO), magnesium oxide (MgO), yttria, cerium oxide (CeO 2 ), scandium oxide (Sc 2 O 3 ) and the like.
- the content ratio of the stabilizer in the zirconia calcined body of the present invention and the sintered body thereof can be measured, for example, by inductively coupled plasma (ICP; Inductively Coupled Plasma) emission spectroscopy, fluorescent X-ray analysis, or the like.
- ICP inductively coupled plasma
- the content of the stabilizer is preferably 0.1 to 18 mol%, more preferably 1 to 15 mol%, based on the total mol of zirconia and the stabilizer. preferable.
- the main crystal system of zirconia in the zirconia calcined body of the present invention needs to be a monoclinic system.
- the main crystal system is a monoclinic system
- the ratio f m of the monoclinic system in the zirconia, which is calculated in the above) represents a ratio of 50% or more.
- the ratio f m of the monoclinic system in zirconia calculated by the following formula (2) is 55 with respect to the total amount of monoclinic system, tetragonal system and cubic system.
- the proportion f m of the monoclinic system can be calculated from the following formula (2) based on the peak of the X-ray diffraction (XRD; X-Ray Diffraction) pattern by CuK ⁇ ray.
- the main crystal system in the zirconia calcined body may contribute to increasing the shrinkage temperature and shortening the sintering time.
- the ratio f m of the monoclinic system can be made 100%.
- I m (111) and I m (11-1) indicate peak intensities of the (111) plane and the (11-1) plane of the monoclinic system of zirconia, respectively.
- I t (111) indicates the peak intensity of the (111) plane of tetragonal zirconia.
- I c (111) shows the peak intensity of the cubic (111) plane of zirconia.
- the stabilizer is present such that at least a part of crystals of zirconia is monoclinic. That is, it is preferable that at least a part of the stabilizer is not solid-solved in zirconia. It can be confirmed by, for example, an XRD pattern that part of the stabilizer is not solid-solved in zirconia. When the peak derived from the stabilizer is confirmed in the XRD pattern of the zirconia calcined body, the stabilizer which is not solid-solved in the zirconia is present in the zirconia calcined body.
- the stabilizer When the entire amount of the stabilizer is solid-solved, basically, no peak derived from the stabilizer is confirmed in the XRD pattern. However, depending on conditions such as the crystal state of the stabilizer, the stabilizer may not be solid-solved in zirconia even if the peak of the stabilizer does not exist in the XRD pattern.
- the main crystal system of zirconia is tetragonal and / or cubic and there is no stabilizer peak in the XRD pattern, most (essentially all) of the stabilizer is solid solution in zirconia It is thought that it is doing.
- all of the stabilizers may not be in solid solution in zirconia.
- that the stabilizer is in solid solution means, for example, that an element (atom) contained in the stabilizer is in solid solution in zirconia.
- the stabilizer is preferably yttria from the viewpoint of the strength and light transmittance of the zirconia sintered body produced from the zirconia calcined body of the present invention.
- the content of yttria is preferably 3 mol% or more, more preferably 3.5 mol% or more, and still more preferably 4.0 mol% or more based on the total mol of zirconia and yttria.
- the content of yttria is 3 mol% or more, the light transmittance of the zirconia sintered body can be enhanced.
- 7.5 mol% or less is preferable with respect to the sum total mol of a zirconia and a yttria, as for the content rate of yttria, 7.0 mol% or less is more preferable, 6.5 mol% or less is still more preferable, 6.0 mol% or less Particularly preferred.
- the content rate of yttria is 7.5 mol% or less, strength reduction of the zirconia sintered body can be suppressed.
- the abundance ratio f y of yttria (hereinafter sometimes referred to as “undissolved yttria”) not solid-solved in zirconia is calculated based on the following equation (1) Can.
- the abundance ratio f y of undissolved yttria is preferably greater than 0%, more preferably 1% or more, and still more preferably 2% or more.
- the upper limit of the abundance ratio f y of undissolved yttria may be, for example, 15% or less, but preferably depends on the content of yttria in the zirconia calcined body.
- f y When the content of yttria is 3 mol% or more and less than 4.5 mol%, f y can be 7% or less. When the content of yttria is 4.5 mol% or more and less than 5.8 mol%, f y can be 11% or less. When the content of yttria is 5.8 mol% or more and less than 7.5 mol%, f y can be 15% or less.
- f y is preferably 0.5% or more, more preferably 1.0% or more, and 2.0% The above is more preferable.
- f y is preferably at least 1%, more preferably at least 2%, more preferably 3% or more.
- f y is preferably 2% or more, more preferably 3% or more, and still more preferably 4% or more.
- f m / f y is preferably 20 to 200, more preferably 25 to 100, still more preferably 30 to 60, when the content of yttria is 3 mol% or more and less than 4.5 mol%. preferable.
- f m / f y is preferably 5 to 45, more preferably 10 to 40, and still more preferably 15 to 35.
- f m / f y is preferably 2 to 40, more preferably 5 to 35, and still more preferably 10 to 30.
- I m (111) and I m (11-1) indicate peak intensities of (111) plane and (11-1) plane of a monoclinic system of zirconia.
- I t (111) indicates the peak intensity of the (111) plane of tetragonal zirconia.
- I c (111) shows the peak intensity of the cubic (111) plane of zirconia.
- the bending strength of the zirconia calcined body of the present invention is preferably 15 MPa or more in order to secure the strength that enables mechanical processing. Moreover, in order to make mechanical processing easy, 70 Mpa or less is preferable and, as for the bending strength of a calcination body, 60 Mpa or less is more preferable.
- the bending strength can be measured in accordance with ISO 6872: 2015 (Dentistry-Ceramic materials), but a test piece with a size of 5 mm ⁇ 10 mm ⁇ 50 mm, changing only the condition of the test piece size. Measure using.
- the face of the test piece and the C-face (the face of the corner of the test piece beveled at an angle of 45 °) are longitudinally face finished with a No. 600 sandpaper.
- the test piece is disposed so that the widest surface is in the vertical direction (load direction).
- the distance between supporting points (span) is 30 mm
- the crosshead speed is 0.5 mm / min.
- the zirconia calcined body of the present invention may contain additives other than zirconia and a stabilizer as long as the effects of the present invention are exhibited.
- the additive include colorants (including pigments, composite pigments and fluorescent agents), alumina (Al 2 O 3 ), titanium oxide (TiO 2 ), silica (SiO 2 ) and the like.
- Examples of the pigment include Ti, V, Cr, Mn, Fe, Co, Ni, Y, Zr, Sn, Sb, Bi, Ce, Pr, Sm, Eu, Gd, Tb and Er.
- Examples thereof include oxides of at least one selected element (specifically, NiO, Cr 2 O 3 and the like), Ti, V, Cr, Mn, Fe, Co, Ni, Zn, Y, Zr, Sn, An oxide of at least one element selected from the group consisting of Sb, Bi, Ce, Pr, Sm, Eu, Gd, and Tb is preferable, and Ti, V, Cr, Mn, Fe, Co, Ni, Zn, Y is preferable.
- the zirconia calcined body of the present invention may not contain erbium oxide (Er 2 O 3 ).
- the composite pigment include (Zr, V) O 2 , Fe (Fe, Cr) 2 O 4 , (Ni, Co, Fe) (Fe, Cr) 2 O 4 .ZrSiO 4 , (Co, Zn) Al 2 O 4 and the like can be mentioned.
- Y 2 SiO 5 Ce
- Y 2 SiO 5 Tb
- (Y, Gd, Eu) BO 3 Y 2 O 3
- Eu Eu
- YAG Ce
- ZnGa 2 O 4 Zn
- BaMgAl 10 O 17 Eu
- the zirconia calcined body of the present invention can be produced, for example, by the following method. First, a raw material powder is manufactured. Using a monoclinic zirconia powder and a powder of stabilizer (eg, yttria powder), a mixture is made to have a desired content of stabilizer (eg, yttria). The mixture is then added to water to make a slurry and wet milled mixed in a ball mill until the desired particle size is achieved. The crushed slurry is dried by a spray drier and granulated. The obtained powder is fired at a temperature (for example, 800 to 1200 ° C.) at which the zirconia particles do not reach sintering to produce a powder (primary powder).
- a temperature for example, 800 to 1200 ° C.
- the obtained primary powder is divided into at least two (preferably four).
- a pigment is added to each of the powders as first to fourth powders.
- each powder to which the pigment is added is added to water to prepare a slurry, and wet grinding and mixing are carried out with a ball mill until the desired particle size is achieved.
- Additives such as a binder are added to the crushed slurry as required, and then dried by a spray drier to prepare four types of powders (secondary powders) of first to fourth powders.
- the first powder of the secondary powder is filled in a predetermined mold, the upper surface is rubbed to flatten the upper surface of the first powder, and then the second powder is filled on the first powder. And scrape the top surface to flatten the top surface of the second powder.
- the third powder is filled on the second powder, and the upper surface is scraped to flatten the upper surface of the third powder.
- the fourth powder is filled on the third powder, and the upper surface is rubbed to flatten the upper surface of the fourth powder.
- the upper mold is set and primary press molding is performed by a uniaxial press molding machine.
- the obtained primary press-formed product is CIP-formed to produce a four-layered formed product.
- the resulting shaped body can be fired at a temperature at which the zirconia particles do not reach sintering to produce a zirconia calcined body.
- the zirconia calcined body of the present invention may be prepared by firing (i.e., calcining) a zirconia molded body formed from a raw material powder containing zirconia particles and a stabilizer at a temperature at which the zirconia particles do not reach sintering. Can be done (calcining process).
- the calcination temperature is preferably, for example, 800 ° C. or more, more preferably 900 ° C. or more, and still more preferably 950 ° C. or more, in order to ensure blocking.
- the firing temperature is, for example, preferably 1200 ° C. or less, more preferably 1150 ° C. or less, and still more preferably 1100 ° C.
- the temperature is preferably 800 ° C. to 1200 ° C. It is thought that solid solution of a stabilizer does not advance if it is such a calcination temperature.
- the zirconia calcined body of the present invention may be a molded body having a predetermined shape.
- the zirconia calcined body can have a disc (disk) shape, a rectangular solid shape, or a dental product shape (for example, a crown shape).
- a dental product (for example, a crown-shaped prosthesis) obtained by processing a calcined zirconia disk by a CAD-CAM (Computer-Aided Design / Computer-Aided Manufacturing) system is also included in the calcined body.
- CAD-CAM Computer-Aided Design / Computer-Aided Manufacturing
- the zirconia calcined body of the present invention can produce a highly translucent sintered body even by firing for a short time.
- a sintered body produced by firing the zirconia calcined body of the present invention for a given time which is a proper firing temperature is taken as a first sintered body.
- a sintered body produced by firing the zirconia calcined body of the present invention at an appropriate firing temperature for 120 minutes is used as a second sintered body.
- the light transmitting property of the first sintered body is the second The light transmittance of the sintered body is preferably 85% or more, more preferably 90% or more, still more preferably 95% or more, and particularly preferably substantially equal. Furthermore, when the baking time of the first sintered body is 15 minutes, the light transmitting property of the first sintered body is preferably 85% or more of the light transmitting property of the second sintered body, and is 90% or more. Is more preferable, 95% or more is more preferable, and it is particularly preferable to be substantially the same.
- the zirconia calcined body of the present invention has the advantages relating to the above-mentioned short time sintering.
- the details, such as an evaluation method, are demonstrated in the below-mentioned Example.
- the zirconia calcined body of the present invention has a total length of 25 from the one end on a straight line extending in a first direction from one end of the zirconia calcined body to the other end from the viewpoint of reproducing a color tone suitable for dental use.
- L1 is 68.0 or more and 90.0 or less
- a1 is -3.0 or more and 4.5 or less
- b1 is 0.0 or more and 24.0 or less
- L2 is 60.0 or more and 85.0 or less
- a2 is -2.0 or more and 7.0 or less
- b2 is 4.0 or more and 28.0 or less
- L1 is 69.0 or more and 89.0 or less, a1 is -2.7 or more and 4.0 or less, b1 is 1.0 or more and 23.5 or less, L2 is 61.5 or more and 84.5 or less, a2 is -1.5 or more and 6.5 or less, b2 is 5.5 or more and 26.0 or less. More preferably, L1 is 70.0 or more and 87.0 or less, a1 is -2.5 or more and 3.7 or less, b1 is 2.0 or more and 23.0 or less, L2 is 63.0 or more and 84.0 or less, a2 is -1.2 or more and 6.0 or less, b2 is 7.0 or more and 24.0 or less.
- the color tone of an average natural tooth can be matched.
- the zirconia calcined body of the present invention is L1-L2 is more than 0 and 12.0 or less, a2-a1 is greater than 0 and less than or equal to 6.0, It is preferable that b2-b1 is more than 0 and 12.0 or less. More preferably, L1-L2 is more than 0 and not more than 10.0, a2-a1 is greater than 0 and not more than 5.5, b2-b1 is more than 0 and 11.0 or less. More preferably, L1-L2 is more than 0 and not more than 8.0, a2-a1 is more than 0 and not more than 5.0, b2-b1 is greater than 0 and less than or equal to 10.0.
- L1-L2 is 1.0 or more and 7.0 or less, a2-a1 is 0.5 or more and 3.0 or less, b2-b1 is 1.6 or more and 6.5 or less. Most preferably, L1-L2 is 1.5 or more and 6.4 or less, a2-a1 is 0.8 or more and 2.6 or less, b2-b1 is 1.7 or more and 6.0 or less. By satisfying the above range, the color tone of natural teeth can be more suitably reproduced.
- the zirconia sintered body obtained by firing the zirconia calcined body of the present invention preferably changes in color from one end connecting the two ends to the other end.
- FIG. 1 a schematic diagram of a zirconia sintered compact.
- the L * value, the a * value and the b * value tend to increase or decrease in the opposite direction It is preferable not to change to That is, when the L * value tends to decrease on the straight line from one end P to the other end Q, it is preferable that there is no section in which the L * value substantially increases.
- FIG. 1 a schematic diagram of a zirconia sintered compact.
- a section in which the a * value decreases by 1 or more It is preferable not to exist, and it is more preferable that there is no section decreasing by 0.5 or more.
- the b * value tends to increase on a straight line from one end P to the other end Q, it is preferable that there is no section in which the b * value substantially decreases.
- a section in which the b * value decreases by 1 or more It is preferable not to exist, and it is more preferable that there is no section decreasing by 0.5 or more.
- the color change direction in the zirconia sintered body 10 is preferably such that the a * value and the b * value tend to increase when the L * value tends to decrease from one end P to the other end Q. For example, from one end P to the other end Q, it changes from white to light yellow, light orange or light brown.
- a point between the first point A and the second point D is taken as a third point B as a point on a straight line connecting one end P to the other end Q.
- L3 is 66.0 or more and 89.0 or less
- a3 is -2.5 or more and 6.0 or less
- b3 is 1.5 or more and 25.0 or less
- L1>L3> L2 a1 ⁇ a3 ⁇ a2 and b1 ⁇ b3 ⁇ b2, Is preferred.
- a point between the third point B and the second point D is referred to as a fourth point C.
- L4 is 62.0 or more and 86.0 or less
- a4 is -2.2 or more and 7.0 or less
- b4 is 3.5 or more and 27.0 or less
- b1 ⁇ b3 ⁇ b4 ⁇ b2 Is preferred.
- the first point A is preferably in a section from one end P to 25% of the length between the one end P and the other end Q (hereinafter referred to as “total length”).
- the third point B is preferably in a section from 30% of the full length from one end P to 70% of the full length from one end P, for example, 45% of the full length from one end P It is also good.
- the second point D is preferably in the section from the other end Q to 25% of the total length.
- the fourth point C is preferably in a section from 30% of the total length away from the other end Q to 70% of the total length from the other end Q, for example, 45% of the total length from the other end Q (ie one end P And 55% of the total length).
- a zirconia calcined body and its sintered compact have crown shape, for example, said "one end” and "the other end", It is preferable to indicate one point at the end on the incisal side and one point on the end at the root side.
- the one point may be a point on the end face or a point on the cross section.
- the point in the section from one end or the other end to 25% of the total length means, for example, a point separated from the one end or the other end by a distance corresponding to 10% of the height of the crown.
- the “one end” and the “other end” preferably indicate one point on the upper surface and the lower surface (bottom surface).
- the one point may be a point on the end face or a point on the cross section.
- the point in the section from one end or the other end to 25% of the total length means, for example, a point separated from the one end or the other end by a distance corresponding to 10% of the thickness of the hexahedron or the disc.
- the “first direction from one end to the other” means a direction in which the color is changing.
- the first direction is preferably a direction in which the powder is laminated in a manufacturing method described later.
- the first direction is preferably a direction connecting the incisal side and the root side.
- the zirconia sintered body of the present invention will be described.
- the zirconia sintered body can be said to be, for example, one in which zirconia particles (powder) are in a sintered state.
- the zirconia sintered body of the present invention refers to one prepared from the zirconia calcined body of the present invention.
- the relative density of the zirconia sintered body is preferably 99.5% or more. The relative density can be calculated as a ratio of the actual density measured by the Archimedes method to the theoretical density.
- the zirconia sintered body of the present invention is not only a sintered body obtained by sintering molded zirconia particles under normal pressure or non-pressurization, as well as HIP (Hot Isostatic Pressing) treatment, etc.
- a sintered body densified by high temperature pressure treatment is also included.
- the content of zirconia and the stabilizer in the zirconia sintered body of the present invention is the same as the content in the calcined body before preparation of the sintered body.
- the ratio f m of monoclinic system is preferably 10% or less, more preferably 5% or less, and substantially not contained (0%) preferable.
- Crystal systems other than monoclinic system are tetragonal and / or cubic.
- the solid solution proportion of the stabilizer in the zirconia sintered body of the present invention it is preferable that 95% or more of the contained stabilizer is solid-solved in zirconia, and substantially all the stabilizers are It is more preferable that it is in solid solution.
- the stabilizer is yttria
- the abundance ratio f y of undissolved yttria in the zirconia sintered body of the present invention is preferably 5% or less, more preferably 1% or less, and substantially all solid solution (0%) is more preferable.
- a stabilizer for example, yttria
- a stabilizer is considered to be solid solution in zirconia.
- the zirconia sintered body of the present invention can be produced by firing a zirconia calcined body at a temperature at which the zirconia particles reach sintering (sintering step). 1400 degreeC or more is preferable, for example, and, as for the calcination temperature in a sintering process, 1450 degreeC or more is more preferable. Moreover, 1650 degrees C or less is preferable, and, as for this calcination temperature, for example, 1600 degrees C or less is more preferable.
- the temperature raising rate and the temperature lowering rate are preferably 300 ° C./min or less.
- the holding time at a sinterable temperature is preferably less than 120 minutes, more preferably 90 minutes or less, still more preferably 75 minutes or less, still more preferably 60 minutes or less, 45 Minutes or less are particularly preferred and 30 minutes or less are most preferred. Furthermore, it can also be 25 minutes or less, 20 minutes or less, or 15 minutes or less.
- the holding time is preferably 1 minute or more, more preferably 5 minutes or more, and still more preferably 10 minutes or more. According to the zirconia calcined body of the present invention, it is possible to suppress the decrease in light transmittance of the produced zirconia sintered body even with such a short baking time. In addition, shortening the firing time can improve production efficiency and reduce energy costs.
- the temperature raising rate and the temperature lowering rate in the sintering step can be set to reach the maximum firing temperature in the shortest time depending on the performance of the firing furnace.
- the temperature rising rate to the maximum firing temperature is, for example, 10 ° C./min or more, 50 ° C./min or more, 100 ° C./min or more, 120 ° C./min or more, 150 ° C./min or more, or 200 ° C./min or more be able to.
- the temperature drop rate is preferably set so as not to cause defects such as cracks in the sintered body. For example, after completion of heating, the sintered body can be allowed to cool at room temperature.
- the highest firing temperature means the highest temperature in the sintering process.
- the zirconia sintered body obtained by firing the zirconia calcined body of the present invention can be suitably used for dental products.
- dental products for example, coping, framework, crown, crown bridge, abutment, implant, implant screw, implant fixture, implant bridge, implant bar, bracket, denture base, inlay, onlay, orthodontic wire And laminate veneers.
- a suitable method can be selected as the manufacturing method according to each application, for example, a dental product can be obtained by cutting the zirconia calcined body of the present invention and then sintering it. it can.
- a CAD / CAM system is used in the cutting process.
- the present invention includes embodiments in which the above-described configurations are variously combined within the scope of the technical idea of the present invention as long as the effects of the present invention are exhibited.
- Examples 1 to 8 and Comparative Examples 1 to 2 [Preparation of zirconia calcined body and sintered body]
- the zirconia calcined bodies and the sintered bodies thereof of the respective examples and comparative examples were produced by the following procedure.
- the method of producing the raw material powder used to produce the zirconia calcined body will be described.
- a mixture was prepared to have the yttria content described in Table 1.
- this mixture was added to water to prepare a slurry, which was wet-ground and mixed in a ball mill until the average particle size became 0.13 ⁇ m or less.
- the pulverized slurry was dried by a spray drier, and the obtained powder was calcined at 950 ° C. for 2 hours to produce a powder (primary powder).
- the average particle size can be determined by a laser diffraction scattering method.
- the laser diffraction scattering method can be measured, for example, with a laser diffraction type particle size distribution measuring apparatus (SALD-2300: manufactured by Shimadzu Corporation) using a 0.2% aqueous sodium hexametaphosphate solution as a dispersion medium. .
- SALD-2300 manufactured by Shimadzu Corporation
- the obtained primary powder was divided into four as first to fourth powders, and to each powder, a pigment was added with a composition shown in Table 1.
- the numerical values shown in Table 1 are the pigment content relative to the mixed powder (100% by mass) of zirconia and yttria.
- each powder to which the pigment was added was added to water to prepare a slurry, and wet grinding and mixing were carried out with a ball mill until the average particle diameter becomes 0.13 ⁇ m or less.
- the binder was added to the pulverized slurry, it was dried by a spray drier to prepare four types of powders (secondary powders) of first to fourth powders.
- the upper mold was set, and primary pressing was performed for 90 seconds at a surface pressure of 300 kg / cm 2 using a uniaxial press molding machine.
- the obtained primary press-formed product was CIP-formed at 1700 kg / cm 2 for 5 minutes to produce a four-layered formed product.
- the obtained molded body was fired at 1000 ° C. for 2 hours to prepare a zirconia calcined body.
- a zirconia calcined body was formed into a crown shape using a CAD / CAM system ("Katana (registered trademark) CAD / CAM system", Kurare Noritake Dental Co., Ltd.).
- the zirconia calcined body was fired at 1500 ° C. in Example 1, and at 1550 ° C. in Examples 2 to 8 and Comparative Examples 1 to 2 to prepare a zirconia sintered body.
- the lengths of the zirconia sintered bodies in the stacking direction of the first to fourth powders were all about 8 mm.
- any of the zirconia sintered bodies is yellowish white to pale yellow from the area corresponding to the first layer derived from the first powder to the area corresponding to the fourth layer derived from the fourth powder.
- a changing gradation was formed and had the same appearance as a natural tooth.
- Comparative Example 1 had strong redness and Comparative Example 2 had strong yellowishness, and the color tone was unnatural as compared to that of the natural teeth, and it could not be said that the same appearance as natural teeth was exhibited.
- the (L *, a *, b *) of the zirconia sintered body produced independently from each of these powders is the (L *, a) of each point in the zirconia sintered body produced from the laminate of the above four powders. It corresponds to *, b *).
- the first powder corresponds to a first point A
- the second powder to a third point B
- the third powder to a fourth point C
- the fourth powder to a second point D.
- the XRD patterns of the zirconia calcined bodies of Examples 1 to 3 were measured using CuK ⁇ radiation to calculate f y and f m .
- the XRD pattern of the zirconia calcined body produced in Example 1 is shown in FIG.
- the XRD pattern of the zirconia calcined body produced in Example 3 is shown in FIG.
- Comparative Examples 3 to 4 zirconia calcined bodies were produced by the method described later using commercially available partially stabilized zirconia powders, and the XRD patterns were respectively measured to calculate f y and f m .
- Zpex registered trademark
- Comparative Example 4 Zpex (registered trademark) Smile manufactured by Tosoh Corporation was used.
- 100 g of the zirconia powder is filled in a mold having an inner size of 82 mm ⁇ 25 mm, the upper surface is scraped to be flat, the upper mold is set, and 90 with a surface pressure of 300 kg / cm 2 by a uniaxial press molding machine. Primary press molding for 2 seconds.
- the obtained primary press molded product was CIP molded at 1700 kg / cm 2 for 5 minutes to produce a molded product.
- the formed body was fired at 1000 ° C. for 2 hours to prepare a zirconia calcined body.
- the XRD pattern of the zirconia calcined body produced in Comparative Example 4 is shown in FIG.
- Example 9 and Comparative Example 5 [Measurement of translucent retention rate to firing time] A zirconia sintered body was produced using each of the zirconia calcined bodies of the examples and comparative examples described later, and the relationship between the retention time at the appropriate firing temperature and the light transmittance was examined.
- the first powder of the secondary powder of Example 2 was used.
- the secondary powder is prepared by adjusting the size in advance and press-forming so that a zirconia sintered body having a thickness of 1.2 mm can be obtained after # 600 polishing of both surfaces of the obtained zirconia sintered body.
- a molded body was produced, and the molded body was fired at 1000 ° C. for 2 hours to produce a zirconia calcined body.
- the sample (zirconia calcined body) was fired for 120 minutes at 1550 ° C., which is the proper firing temperature specified by the method described later, to produce a sintered body.
- Both sides of the obtained zirconia sintered body were polished by # 600, and a zirconia sintered body having a thickness of 1.2 mm was used for light transmittance measurement.
- the translucency of the obtained zirconia sintered body was measured by the below-mentioned method.
- a sintered body was produced by changing the holding time at the appropriate firing temperature (1550 ° C.) to 60 minutes, 30 minutes, and 15 minutes.
- Translucency was similarly measured about each zirconia sintered compact.
- the temperature raising rate and the temperature lowering rate were set to the same conditions as the firing for 120 minutes.
- the change of the light transmittance ( ⁇ L * x ) of the sintered body fired for the holding time x min to the light transmittance ( ⁇ L * 120 ) of the sintered body fired at the proper firing temperature for 120 minutes is taken as the light transmittance Calculated by
- Comparative Example 5 the same measurement as in Example 9 was performed using Zpex (registered trademark) Smile made by Tosoh Corporation as Comparative Example 4.
- the appropriate firing temperature of zirconia refers to the firing temperature specified by the manufacturer when using commercially available zirconia.
- the specified baking temperature it can be defined as follows. First, the zirconia calcined body was fired at various temperatures for 120 minutes, and then both surfaces were polished by # 600 to obtain a sample of a zirconia sintered body having a thickness of 1.2 mm. The appearance of the obtained sample was visually observed, and the appropriate firing temperature of each zirconia calcined body was determined based on the following criteria based on the transparency of the sample. As in the sample on the left side of FIG.
- the state in which the transparency is high and the background is transmitted can be regarded as the zirconia calcined body being sufficiently fired.
- the state of low transparency or the state of white turbidity is insufficient for firing.
- the lowest temperature that can be regarded as being sufficiently fired as in the sample on the left side of FIG. 6 was judged as the proper firing temperature of the zirconia calcined body.
- the appropriate firing temperature of the zirconia used in each of the examples and comparative examples is 1500 ° C.
- the light transmittance of the zirconia sintered body was measured with a D65 light source using a spectrocolorimeter CM-3610A manufactured by Konica Minolta Co., Ltd., L * a * b * color system (JIS Z 8781-4: 2013 It was calculated using the L * value of lightness (color space) in colorimetry-part 4: CIE 1976 L * a * b * color space).
- the L * value measured with the sample background white is the first L * value
- the L * value measured with the sample background black for the same sample whose first L * value was measured is the second A value ( ⁇ L *) obtained by subtracting the second L * value from the first L * value is used as a numerical value indicating translucency.
- Example 9 In Comparative Example 5, as the holding time at the appropriate firing temperature decreases, the light transmittance decreases, and in 60 minutes firing, 91% of the light transmittance in 120 minutes firing, and in 30 minutes firing, the light transmittance in 120 minutes firing The lightness was 74%, and the light for 15 minutes was 63% of the light transmission for 120 minutes. On the other hand, in Example 9, even if the holding time at the proper firing temperature was shortened, the same light transmission as that for the firing for 120 minutes could be secured. In the 30-minute firing, it can be made almost 100% of the 120-minute firing, and in the 15-minute firing it can be made 95% or more of the 120 ° C. firing.
- the baking time can be shortened while maintaining high translucency.
- the production efficiency of the zirconia sintered body can be enhanced, and the energy cost can be reduced.
- the time burden on the patient can be reduced.
- the crystal system of the calcined zirconia body of Comparative Example 4 used in Comparative Example 5 is tetragonal and cubic, and monoclinic crystals can not be detected substantially. It is considered that all yttria is dissolved in zirconia.
- the crystal system of zirconia is mainly monoclinic, and undissolved yttria is present. It is considered that these differences affect the possibility of sintering for a short time.
- the zirconia calcined body of the present invention and the sintered body thereof can be used for dental products such as a prosthesis.
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Abstract
Description
ジルコニアの相転移を抑制可能な安定化剤と、を含有し、
ジルコニアの主たる結晶系が単斜晶であるジルコニア仮焼体であって、
前記ジルコニア仮焼体の一端から他端に向かう第1方向に延在する直線上において、
前記一端から全長の25%までの区間にある第1点のL*a*b*表色系による焼結後の(L*,a*,b*)を(L1,a1,b1)とし、
前記他端から全長の25%までの区間にある第2点のL*a*b*表色系による焼結後の(L*,a*,b*)を(L2,a2,b2)としたとき、
L1が68.0以上90.0以下であり、
a1が-3.0以上4.5以下であり、
b1が0.0以上24.0以下であり、
L2が60.0以上85.0以下であり、
a2が-2.0以上7.0以下であり、
b2が4.0以上28.0以下であり、
L1>L2であり、
a1<a2であり、
b1<b2であり、
前記第1点から前記第2点に向かってL*a*b*表色系による焼結後の(L*,a*,b*)の増減傾向が変化しない、ジルコニア仮焼体。
[2]L1-L2が0超12.0以下であり、
a2-a1が0超以上6.0以下であり、
b2-b1が0超12.0以下である、前記[1]に記載のジルコニア仮焼体。
[3]L1-L2が0超8.0以下であり、
a2-a1が0超5.0以下であり、
b2-b1が0超10.0以下である、前記[1]又は[2]に記載のジルコニア仮焼体。
[4]L1-L2が1.0以上7.0以下であり、
a2-a1が0.5以上3.0以下であり、
b2-b1が1.6以上6.5以下である、前記[1]~[3]のいずれかに記載のジルコニア仮焼体。
[5]前記第1点と前記第2点とを結ぶ直線上において、
前記第1点から前記第2点に向かって焼結後のL*値が1以上増加する区間が存在せず、
前記第1点から前記第2点に向かって焼結後のa*値が1以上減少する区間が存在せず、
前記第1点から前記第2点に向かって焼結後のb*値が1以上減少する区間が存在しない、前記[1]~[4]のいずれかに記載のジルコニア仮焼体。
[6]前記第1点から前記第2点を結ぶ直線上において、前記第1点と前記第2点の間にある第3点のL*a*b*表色系による焼結後の(L*,a*,b*)を(L3,a3,b3)としたとき、
L3が66.0以上89.0以下であり、
a3が-2.5以上6.0以下であり、
b3が1.5以上25.0以下であり、
L1>L3>L2であり、
a1<a3<a2であり、
b1<b3<b2である、前記[1]~[5]のいずれかに記載のジルコニア仮焼体。
[7]前記第1点から前記第2点を結ぶ直線上において、前記第3点と前記第2点の間にある第4点のL*a*b*表色系による焼結後の(L*,a*,b*)を(L4,a4,b4)としたとき、
L4が62.0以上86.0以下であり、
a4が-2.2以上7.0以下であり、
b4が3.5以上27.0以下であり、
L1>L3>L4>L2であり、
a1<a3<a4<a2であり、
b1<b3<b4<b2である、前記[6]に記載のジルコニア仮焼体。
[8]前記第3点は前記一端から全長の45%の距離にあり、
前記第4点は前記一端から全長の55%の距離にある、前記[7]に記載のジルコニア仮焼体。
[9]前記ジルコニアの55%以上が単斜晶である、前記[1]~[8]のいずれかに記載のジルコニア仮焼体。
[10]前記安定化剤の少なくとも一部がジルコニアに固溶されていない、前記[1]~[9]のいずれかに記載のジルコニア仮焼体。
[11]密度が2.7~4.0g/cm3である、前記[1]~[10]のいずれかに記載のジルコニア仮焼体。
[12]曲げ強さが15~70MPaである、前記[1]~[11]のいずれかに記載のジルコニア仮焼体。
[13]さらに顔料を含み、前記顔料が、Ti、V、Cr、Mn、Fe、Co、Ni、Zn、Y、Zr、Sn、Sb、Bi、Ce、Pr、Sm、Eu、Gd、及びTbからなる群から選択される少なくとも1つの元素の酸化物である、前記[1]~[12]のいずれかに記載のジルコニア仮焼体。
[14]前記安定化剤がイットリアである、前記[1]~[13]のいずれかに記載のジルコニア仮焼体。
[15]前記ジルコニアと前記イットリアの合計molに対して、前記イットリアを3~7.5mol%含有する、前記[14]に記載のジルコニア仮焼体。
[16]X線回折パターンにおいてイットリアのピークが存在する、前記[14]又は[15]に記載のジルコニア仮焼体。
[17]以下の数式(1)に基づいて算出したfyが0%超である、前記[14]~[16]のいずれかに記載のジルコニア仮焼体。
Im(111)及びIm(11-1)は、前記X線回折パターンにおけるジルコニアの単斜晶系の(111)面及び(11-1)面のピーク強度を示し、
It(111)は、前記X線回折パターンにおけるジルコニアの正方晶系の(111)面のピーク強度を示し、
Ic(111)は、前記X線回折パターンにおけるジルコニアの立方晶系の(111)面のピーク強度を示す。
[18]前記fyが15%以下である、前記[17]に記載のジルコニア仮焼体。
[19]前記ジルコニア仮焼体におけるイットリアの含有率が3mol%以上4.5mol%未満であり、前記fyが0.5%以上である、前記[17]又は[18]に記載のジルコニア仮焼体。
[20]前記ジルコニア仮焼体におけるイットリアの含有率が4.5mol%以上5.8mol%未満であり、前記fyが1%以上である、前記[17]又は[18]に記載のジルコニア仮焼体。
[21]前記ジルコニア仮焼体におけるイットリアの含有率が5.8mol%以上7.5mol%以下であり、前記fyが2%以上である、前記[17]又は[18]に記載のジルコニア仮焼体。
[22]前記ジルコニア仮焼体を適正焼成温度で30分間焼成して作製された第1の焼結体の第1の透光性と、
前記ジルコニア仮焼体を該適正焼成温度で120分間焼成して作製された第2の焼結体の第2の透光性と、を比較したとき、
前記第1の透光性が前記第2の透光性の85%以上である、前記[1]~[21]のいずれかに記載のジルコニア仮焼体。
[23]前記ジルコニア仮焼体を適正焼成温度で15分間焼成して作製された第1の焼結体の第1の透光性と、
前記ジルコニア仮焼体を該適正焼成温度で120分間焼成して作製された第2の焼結体の第2の透光性と、を比較したとき、
前記第1の透光性が前記第2の透光性の85%以上である、前記[1]~[22]のいずれかに記載のジルコニア仮焼体。
[24]ジルコニア粒子と安定化剤と含む原料粉末から形成されたジルコニア成形体を800℃~1200℃で仮焼する、前記[1]~[23]のいずれかに一項に記載のジルコニア仮焼体の製造方法。
[25]前記[1]~[23]のいずれかに記載のジルコニア仮焼体を最高焼成温度1400℃~1600℃で焼成する、ジルコニア焼結体の製造方法。
[26]最高焼成温度での保持時間が120分未満である、前記[25]に記載のジルコニア焼結体の製造方法。
[27]前記[1]~[23]のいずれかに記載のジルコニア仮焼体を切削加工した後に焼結する、歯科用製品の製造方法。
[28]前記ジルコニア仮焼体を、CAD/CAMシステムを用いて切削加工した後に焼結した状態である、前記[27]に記載の歯科用製品の製造方法。
L1が68.0以上90.0以下であり、
a1が-3.0以上4.5以下であり、
b1が0.0以上24.0以下であり、
L2が60.0以上85.0以下であり、
a2が-2.0以上7.0以下であり、
b2が4.0以上28.0以下であり、
L1>L2であり、
a1<a2であり、
b1<b2であり、
前記第1点から前記第2点に向かってL*a*b*表色系による焼結後の(L*,a*,b*)の増減傾向が変化しないことが重要である。好ましくは、
L1が69.0以上89.0以下であり、
a1が-2.7以上4.0以下であり、
b1が1.0以上23.5以下であり、
L2が61.5以上84.5以下であり、
a2が-1.5以上6.5以下であり、
b2が5.5以上26.0以下である。より好ましくは、
L1が70.0以上87.0以下であり、
a1が-2.5以上3.7以下であり、
b1が2.0以上23.0以下であり、
L2が63.0以上84.0以下であり、
a2が-1.2以上6.0以下であり、
b2が7.0以上24.0以下である。
上記の範囲を満たすことにより、平均的な天然歯の色調に適合させることができる。
L1-L2が0超12.0以下であり、
a2-a1が0超6.0以下であり、
b2-b1が0超12.0以下であることが好ましい。より好ましくは、
L1-L2が0超10.0以下であり、
a2-a1が0超5.5以下であり、
b2-b1が0超11.0以下である。さらに好ましくは、
L1-L2が0超8.0以下であり、
a2-a1が0超5.0以下であり、
b2-b1が0超10.0以下である。特に好ましくは、
L1-L2が1.0以上7.0以下であり、
a2-a1が0.5以上3.0以下であり、
b2-b1が1.6以上6.5以下である。最も好ましくは、
L1-L2が1.5以上6.4以下であり、
a2-a1が0.8以上2.6以下であり、
b2-b1が1.7以上6.0以下である。
上記の範囲を満たすことにより、天然歯の色調をより好適に再現することができる。
L3が66.0以上89.0以下であり、
a3が-2.5以上6.0以下であり、
b3が1.5以上25.0以下であり、
L1>L3>L2であり、
a1<a3<a2であり、
b1<b3<b2である、
ことが好ましい。
L4が62.0以上86.0以下であり、
a4が-2.2以上7.0以下であり、
b4が3.5以上27.0以下であり、
L1>L3>L4>L2であり、
a1<a3<a4<a2であり、
b1<b3<b4<b2である、
ことが好ましい。
[ジルコニア仮焼体及び焼結体の作製]
各実施例及び比較例のジルコニア仮焼体及びその焼結体を以下の手順により作製した。
各実施例及び比較例のジルコニア焼結体について、天然歯の外観との比較の観点で、目視により色調を評価した。
各実施例及び比較例のジルコニア焼結体の色調について、以下の方法で定量的に評価した。各例における二次粉末の第1粉末、第2粉末、第3粉末、及び第4粉末について、それぞれ単独のジルコニア焼結体を作製し、L*a*b*表色系(JIS Z 8781-4:2013 測色-第4部:CIE 1976 L*a*b*色空間)による(L*,a*,b*)を測定した。これらの各粉末から単独で作製したジルコニア焼結体の(L*,a*,b*)は、上記の4つの粉末の積層体から作製したジルコニア焼結体における各点の(L*,a*,b*)に相当する。具体的には、第1粉末は第1点A、第2粉末は第3点B、第3粉末は第4点C、第4粉末は第2点Dに相当する。(L*,a*,b*)は、各粉末単独で製造したジルコニア焼結体を直径14mm、厚さ1.2mmの円板となるように加工(両面は#600研磨)した後、コニカミノルタ株式会社製の分光測色計CM-3610Aを用いて、D65光源、測定モードSCI、測定径/照明径=φ8mm/φ11mm、白背景にて測定した。評価結果を表1に示す。
[ジルコニア仮焼体の作製及びXRD測定]
ジルコニアの結晶系及び安定化剤がジルコニアに固溶されていない程度を確認した。結果を表2に示す。
[焼成時間に対する透光性保持率の測定]
後述の実施例及び比較例の各ジルコニア仮焼体を用いてジルコニア焼結体を作製し、適正焼成温度における保持時間と透光性との関係を調べた。
実施例9においては実施例2の二次粉末の第1粉末を用いた。まず、得られるジルコニア焼結体の両面を#600研磨加工後に厚さ1.2mmのジルコニア焼結体が得られるように、予めサイズを調整してプレス成形を行うことで、該二次粉末からなる成形体を作製し、成形体を1000℃で2時間焼成してジルコニア仮焼体を作製した。次に、後述の方法により特定した適正焼成温度である、1550℃に設定して、120分間、試料(ジルコニア仮焼体)を焼成して焼結体を作製した。得られたジルコニア焼結体の両面を#600研磨加工し、厚さ1.2mmのジルコニア焼結体を透光性の測定に用いた。得られたジルコニア焼結体の透光性を後述の方法により測定した。次に、同じ方法で作製したジルコニア仮焼体の試料について、適正焼成温度(1550℃)での保持時間を60分、30分、15分と変更して焼結体を作製し、得られた各ジルコニア焼結体について同様に透光性を測定した。なお、昇温速度と降温速度は、120分間の焼成と同一条件とした。適正焼成温度で120分間焼成した焼結体の透光性(ΔL*120)に対する、保持時間x分間で焼成した焼結体の透光性(ΔL*x)の変化を透光性として下記式により算出した。一方、比較例5として、比較例4の東ソー株式会社製Zpex(登録商標)Smileを用いて、実施例9と同様の測定を実施した。表3及び図5に結果を示す。
透光性保持率(%)=(ΔL*x)/(ΔL*120)×100
なお、各実施例及び比較例で用いたジルコニアの適正焼成温度は、上記の測定によりイットリア含有率が4.0mol%のジルコニア仮焼体(実施例1)では1500℃、イットリア含有率が5.5mol%及び6.0mol%のジルコニア仮焼体(実施例2~9、比較例1及び2)ではいずれも1550℃という結果となった一方、東ソー株式会社製Zpex(登録商標)及びZpex(登録商標)Smile(比較例3及び4)は製造元の指定する焼成温度が1450℃である。
A 第1点
B 第3点
C 第4点
D 第2点
P 一端
Q 他端
L 全長
Y 第1方向
Claims (28)
- ジルコニアと、
ジルコニアの相転移を抑制可能な安定化剤と、を含有し、
ジルコニアの主たる結晶系が単斜晶であるジルコニア仮焼体であって、
前記ジルコニア仮焼体の一端から他端に向かう第1方向に延在する直線上において、
前記一端から全長の25%までの区間にある第1点のL*a*b*表色系による焼結後の(L*,a*,b*)を(L1,a1,b1)とし、
前記他端から全長の25%までの区間にある第2点のL*a*b*表色系による焼結後の(L*,a*,b*)を(L2,a2,b2)としたとき、
L1が68.0以上90.0以下であり、
a1が-3.0以上4.5以下であり、
b1が0.0以上24.0以下であり、
L2が60.0以上85.0以下であり、
a2が-2.0以上7.0以下であり、
b2が4.0以上28.0以下であり、
L1>L2であり、
a1<a2であり、
b1<b2であり、
前記第1点から前記第2点に向かってL*a*b*表色系による焼結後の(L*,a*,b*)の増減傾向が変化しない、ジルコニア仮焼体。 - L1-L2が0超12.0以下であり、
a2-a1が0超以上6.0以下であり、
b2-b1が0超12.0以下である、請求項1に記載のジルコニア仮焼体。 - L1-L2が0超8.0以下であり、
a2-a1が0超5.0以下であり、
b2-b1が0超10.0以下である、請求項1又は2に記載のジルコニア仮焼体。 - L1-L2が1.0以上7.0以下であり、
a2-a1が0.5以上3.0以下であり、
b2-b1が1.6以上6.5以下である、請求項1~3のいずれか一項に記載のジルコニア仮焼体。 - 前記第1点と前記第2点とを結ぶ直線上において、
前記第1点から前記第2点に向かって焼結後のL*値が1以上増加する区間が存在せず、
前記第1点から前記第2点に向かって焼結後のa*値が1以上減少する区間が存在せず、
前記第1点から前記第2点に向かって焼結後のb*値が1以上減少する区間が存在しない、請求項1~4のいずれか一項に記載のジルコニア仮焼体。 - 前記第1点から前記第2点を結ぶ直線上において、前記第1点と前記第2点の間にある第3点のL*a*b*表色系による焼結後の(L*,a*,b*)を(L3,a3,b3)としたとき、
L3が66.0以上89.0以下であり、
a3が-2.5以上6.0以下であり、
b3が1.5以上25.0以下であり、
L1>L3>L2であり、
a1<a3<a2であり、
b1<b3<b2である、請求項1~5のいずれか一項に記載のジルコニア仮焼体。 - 前記第1点から前記第2点を結ぶ直線上において、前記第3点と前記第2点の間にある第4点のL*a*b*表色系による焼結後の(L*,a*,b*)を(L4,a4,b4)としたとき、
L4が62.0以上86.0以下であり、
a4が-2.2以上7.0以下であり、
b4が3.5以上27.0以下であり、
L1>L3>L4>L2であり、
a1<a3<a4<a2であり、
b1<b3<b4<b2である、請求項6に記載のジルコニア仮焼体。 - 前記第3点は前記一端から全長の45%の距離にあり、
前記第4点は前記一端から全長の55%の距離にある、請求項7に記載のジルコニア仮焼体。 - 前記ジルコニアの55%以上が単斜晶である、請求項1~8のいずれか一項に記載のジルコニア仮焼体。
- 前記安定化剤の少なくとも一部がジルコニアに固溶されていない、請求項1~9のいずれか一項に記載のジルコニア仮焼体。
- 密度が2.7~4.0g/cm3である、請求項1~10のいずれか一項に記載のジルコニア仮焼体。
- 曲げ強さが15~70MPaである、請求項1~11のいずれか一項に記載のジルコニア仮焼体。
- さらに顔料を含み、前記顔料が、Ti、V、Cr、Mn、Fe、Co、Ni、Zn、Y、Zr、Sn、Sb、Bi、Ce、Pr、Sm、Eu、Gd、及びTbからなる群から選択される少なくとも1つの元素の酸化物であり、酸化エルビウムを含まない、請求項1~12のいずれか一項に記載のジルコニア仮焼体。
- 前記安定化剤がイットリアである、請求項1~13のいずれか一項に記載のジルコニア仮焼体。
- 前記ジルコニアと前記イットリアの合計molに対して、前記イットリアを3~7.5mol%含有する、請求項14に記載のジルコニア仮焼体。
- X線回折パターンにおいてイットリアのピークが存在する、請求項14又は15に記載のジルコニア仮焼体。
- 前記fyが15%以下である、請求項17に記載のジルコニア仮焼体。
- 前記イットリアの含有率が3mol%以上4.5mol%未満であり、前記fyが0.5%以上である、請求項17又は18に記載のジルコニア仮焼体。
- 前記イットリアの含有率が4.5mol%以上5.8mol%未満であり、前記fyが1%以上である、請求項17又は18に記載のジルコニア仮焼体。
- 前記イットリアの含有率が5.8mol%以上7.5mol%以下であり、前記fyが2%以上である、請求項17又は18に記載のジルコニア仮焼体。
- 前記ジルコニア仮焼体を適正焼成温度で30分間焼成して作製された第1の焼結体の第1の透光性と、
前記ジルコニア仮焼体を該適正焼成温度で120分間焼成して作製された第2の焼結体の第2の透光性と、を比較したとき、
前記第1の透光性が前記第2の透光性の85%以上である、請求項1~21のいずれか一項に記載のジルコニア仮焼体。 - 前記ジルコニア仮焼体を適正焼成温度で15分間焼成して作製された第1の焼結体の第1の透光性と、
前記ジルコニア仮焼体を該適正焼成温度で120分間焼成して作製された第2の焼結体の第2の透光性と、を比較したとき、
前記第1の透光性が前記第2の透光性の85%以上である、請求項1~22のいずれか一項に記載のジルコニア仮焼体。 - ジルコニア粒子と安定化剤と含む原料粉末から形成されたジルコニア成形体を800℃~1200℃で仮焼する、請求項1~23のいずれかに一項に記載のジルコニア仮焼体の製造方法。
- 請求項1~23のいずれか一項に記載のジルコニア仮焼体を最高焼成温度1400℃~1600℃で焼成する、ジルコニア焼結体の製造方法。
- 最高焼成温度での保持時間が120分未満である、請求項25に記載のジルコニア焼結体の製造方法。
- 請求項1~23のいずれか一項に記載のジルコニア仮焼体を切削加工した後に焼結する、歯科用製品の製造方法。
- 前記ジルコニア仮焼体を、CAD/CAMシステムを用いて切削加工した後に焼結した状態である、請求項27に記載の歯科用製品の製造方法。
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Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2021020582A1 (ja) * | 2019-08-01 | 2021-02-04 | クラレノリタケデンタル株式会社 | ジルコニア焼結体の製造方法 |
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CN113753948A (zh) * | 2021-09-09 | 2021-12-07 | 浙江大学 | 一种超高压/高温相变法制备纳米多晶氧化锆的方法 |
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WO2022065448A1 (ja) | 2020-09-25 | 2022-03-31 | クラレノリタケデンタル株式会社 | 歯科用被加工体 |
WO2023127945A1 (ja) | 2021-12-28 | 2023-07-06 | クラレノリタケデンタル株式会社 | 歯科用に好適なジルコニア仮焼体 |
WO2024127664A1 (ja) | 2022-12-16 | 2024-06-20 | クラレノリタケデンタル株式会社 | 高透光性アルミナ焼結体となる歯科用アルミナ仮焼体 |
WO2024127666A1 (ja) | 2022-12-16 | 2024-06-20 | クラレノリタケデンタル株式会社 | 歯科用アルミナ被加工体 |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010528731A (ja) * | 2007-06-07 | 2010-08-26 | ノベル バイオケア サーヴィシィズ アーゲー | 歯科ブリッジを形成するための方法及び装置 |
WO2014181828A1 (ja) * | 2013-05-10 | 2014-11-13 | クラレノリタケデンタル株式会社 | ジルコニア焼結体、ジルコニア組成物及びジルコニア仮焼体並びにこれらの製造方法、及び歯科用補綴物 |
CN104844200A (zh) * | 2015-04-30 | 2015-08-19 | 浙江大学 | 多种氧化物掺杂的渐变色氧化锆牙科修复体及其制备方法 |
WO2015199018A1 (ja) | 2014-06-23 | 2015-12-30 | 東ソー株式会社 | 着色透光性ジルコニア焼結体と粉末、及びその用途 |
JP2017127431A (ja) * | 2016-01-19 | 2017-07-27 | クラレノリタケデンタル株式会社 | ジルコニア焼結体及び歯科用製品 |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102875147B (zh) * | 2012-10-17 | 2013-11-20 | 安泰科技股份有限公司 | 氧化锆陶瓷材料及其制备方法 |
JP6352593B2 (ja) | 2013-05-02 | 2018-07-04 | クラレノリタケデンタル株式会社 | ジルコニア焼結体、ジルコニア組成物及びジルコニア仮焼体、並びに歯科用補綴物 |
WO2014181827A1 (ja) | 2013-05-10 | 2014-11-13 | クラレノリタケデンタル株式会社 | ジルコニア焼結体、ジルコニア組成物及びジルコニア仮焼体、並びに歯科用補綴物 |
EP2829251B1 (en) * | 2013-07-22 | 2019-04-10 | Ivoclar Vivadent AG | Controlling of sintering kinetics of oxide ceramics |
EP3214057A4 (en) * | 2014-10-31 | 2018-06-06 | Kuraray Noritake Dental Inc. | Zirconia composition, zirconia calcined body and zirconia sintered body, and dental product |
JP6741592B2 (ja) * | 2014-12-26 | 2020-08-19 | クラレノリタケデンタル株式会社 | ジルコニア組成物、ジルコニア仮焼体及びジルコニア焼結体、並びに歯科用製品 |
-
2018
- 2018-12-26 EP EP18897850.6A patent/EP3733630A4/en active Pending
- 2018-12-26 US US16/957,924 patent/US11795110B2/en active Active
- 2018-12-26 CN CN201880083764.8A patent/CN111511702B/zh active Active
- 2018-12-26 WO PCT/JP2018/047904 patent/WO2019131782A1/ja unknown
- 2018-12-26 JP JP2019562118A patent/JP7213829B2/ja active Active
- 2018-12-26 KR KR1020207018541A patent/KR20200093617A/ko not_active Application Discontinuation
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010528731A (ja) * | 2007-06-07 | 2010-08-26 | ノベル バイオケア サーヴィシィズ アーゲー | 歯科ブリッジを形成するための方法及び装置 |
WO2014181828A1 (ja) * | 2013-05-10 | 2014-11-13 | クラレノリタケデンタル株式会社 | ジルコニア焼結体、ジルコニア組成物及びジルコニア仮焼体並びにこれらの製造方法、及び歯科用補綴物 |
WO2015199018A1 (ja) | 2014-06-23 | 2015-12-30 | 東ソー株式会社 | 着色透光性ジルコニア焼結体と粉末、及びその用途 |
CN104844200A (zh) * | 2015-04-30 | 2015-08-19 | 浙江大学 | 多种氧化物掺杂的渐变色氧化锆牙科修复体及其制备方法 |
JP2017127431A (ja) * | 2016-01-19 | 2017-07-27 | クラレノリタケデンタル株式会社 | ジルコニア焼結体及び歯科用製品 |
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JPWO2021020582A1 (ja) * | 2019-08-01 | 2021-12-02 | クラレノリタケデンタル株式会社 | ジルコニア焼結体の製造方法 |
JP7005819B2 (ja) | 2019-08-01 | 2022-01-24 | クラレノリタケデンタル株式会社 | ジルコニア焼結体の製造方法 |
CN114144389A (zh) * | 2019-08-01 | 2022-03-04 | 可乐丽则武齿科株式会社 | 氧化锆烧结体的制造方法 |
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WO2022004862A1 (ja) * | 2020-07-01 | 2022-01-06 | クラレノリタケデンタル株式会社 | 歯科用に好適なジルコニア仮焼体 |
JP7001310B1 (ja) * | 2020-07-01 | 2022-01-19 | クラレノリタケデンタル株式会社 | 歯科用に好適なジルコニア仮焼体 |
CN115802980A (zh) * | 2020-07-01 | 2023-03-14 | 可乐丽则武齿科株式会社 | 适用于牙科的氧化锆预烧体 |
WO2022065448A1 (ja) | 2020-09-25 | 2022-03-31 | クラレノリタケデンタル株式会社 | 歯科用被加工体 |
KR20230074109A (ko) | 2020-09-25 | 2023-05-26 | 쿠라레 노리타케 덴탈 가부시키가이샤 | 치과용 피가공체 |
CN113753948B (zh) * | 2021-09-09 | 2023-03-21 | 浙江大学 | 一种超高压/高温相变法制备纳米多晶氧化锆的方法 |
CN113753948A (zh) * | 2021-09-09 | 2021-12-07 | 浙江大学 | 一种超高压/高温相变法制备纳米多晶氧化锆的方法 |
WO2023127945A1 (ja) | 2021-12-28 | 2023-07-06 | クラレノリタケデンタル株式会社 | 歯科用に好適なジルコニア仮焼体 |
WO2024127664A1 (ja) | 2022-12-16 | 2024-06-20 | クラレノリタケデンタル株式会社 | 高透光性アルミナ焼結体となる歯科用アルミナ仮焼体 |
WO2024127666A1 (ja) | 2022-12-16 | 2024-06-20 | クラレノリタケデンタル株式会社 | 歯科用アルミナ被加工体 |
Also Published As
Publication number | Publication date |
---|---|
CN111511702A (zh) | 2020-08-07 |
EP3733630A4 (en) | 2021-09-22 |
KR20200093617A (ko) | 2020-08-05 |
EP3733630A1 (en) | 2020-11-04 |
US20210061715A1 (en) | 2021-03-04 |
JP7213829B2 (ja) | 2023-01-27 |
JPWO2019131782A1 (ja) | 2021-01-14 |
US11795110B2 (en) | 2023-10-24 |
CN111511702B (zh) | 2022-11-29 |
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