WO2012172316A2 - Matériau de restauration dentaire en céramique - Google Patents

Matériau de restauration dentaire en céramique Download PDF

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Publication number
WO2012172316A2
WO2012172316A2 PCT/GB2012/051311 GB2012051311W WO2012172316A2 WO 2012172316 A2 WO2012172316 A2 WO 2012172316A2 GB 2012051311 W GB2012051311 W GB 2012051311W WO 2012172316 A2 WO2012172316 A2 WO 2012172316A2
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WIPO (PCT)
Prior art keywords
ceramic
glass frit
glass
weight
leucite
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PCT/GB2012/051311
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WO2012172316A3 (fr
Inventor
Richard Van Noort
Pannapa SINTHUPRASIRT
Sarah Pollington
Emad Abdel-Salaam Mostafa EL-MELIEGY
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University of Sheffield
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University of Sheffield
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    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61K—PREPARATIONS FOR MEDICAL, DENTAL OR TOILETRY PURPOSES
    • A61K6/00—Preparations for dentistry
    • A61K6/80—Preparations for artificial teeth, for filling teeth or for capping teeth
    • A61K6/802—Preparations for artificial teeth, for filling teeth or for capping teeth comprising ceramics
    • A61K6/827—Leucite
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61K—PREPARATIONS FOR MEDICAL, DENTAL OR TOILETRY PURPOSES
    • A61K6/00—Preparations for dentistry
    • A61K6/80—Preparations for artificial teeth, for filling teeth or for capping teeth
    • A61K6/802—Preparations for artificial teeth, for filling teeth or for capping teeth comprising ceramics
    • A61K6/807—Preparations for artificial teeth, for filling teeth or for capping teeth comprising ceramics comprising magnesium oxide

Definitions

  • the present invention relates to a ceramic dental restoration material, to a method of making such a material, and to use of such a material in restorative dentistry.
  • the present invention relates to a ceramic dental restoration material having a multiple phase structure, to a method of making the same, and to use of the same in dentistry, especially aesthetic restorative dentistry.
  • Aesthetic leucite-feldspar ceramic veneers have been widely used in dentistry for many years. They are used in metal-ceramic restorations, i.e. restorations based upon a metallic core on which a ceramic veneer is applied, for ceramic restorations which are based on a high strength ceramic core, and/or can be resin-bonded to the enamel and/or dentine of an existing tooth. Restorations include both anterior and posterior crowns, veneers, onlays and inlays.
  • leucite otherwise known as potassium aluminium tectosilicate: K[AISi 2 0 6 ]
  • feldspar belonging to a group of tectosilicate minerals comprising: K[AISi 3 0 8 ], Na[AISi 3 0 8 ] and Ca[AISi 3 0 8 ] 2
  • K[AISi 3 0 8 ] potassium aluminium tectosilicate minerals
  • Ca[AISi 3 0 8 ] 2 feldspar
  • a dental ceramic composition including exhibition of pleasing aesthetics to enable matching to a range of tooth shades, including colour stability, translucency (that is similar in range to that of enamel and dentine) and surface finish, possession of a minimum level of abrasion resistance, inherent strength and toughness, tissue compatibility, chemical stability, and, in the case of application to an artificial core material (i.e. a metallic core or a ceramic core), ideally have a coefficient of thermal expansion which is as closely matched as possible to the underlying core material to which the ceramic composition is applied to minimise any effects of thermal shock during preparation of the restoration.
  • an artificial core material i.e. a metallic core or a ceramic core
  • a non-optimised composition can lead to brittle fracture of the ceramic, which involves the rapid, uninterrupted propagation of cracks, usually beginning at a flaw in the ceramic itself, and also increases the risk of abrasive wear of surrounding, and particularly opposing, tooth structure(s). Furthermore, once in situ, a restoration formed from a non-optimised composition may undesirably fracture and/or easily chip.
  • full ceramic restorations are preferred over metal-ceramic restorations because of the inherent shrinkage (and consequential poor fit) that often occurs due to a mis-match in linear coefficient of thermal expansion between the metal core and the applied ceramic, the reduced light transmission through a metal-ceramic restoration (making the restoration appear undesirably darkened as compared to the surrounding teeth), discolouration of the ceramic due to metal-ion migration from the metal core and possible allergic reaction to the metal core.
  • the preferred full ceramic restorations must however possess the necessary mechanical strength to properly function.
  • the process for manufacturing high strength full ceramic restorations can involve many firing cycles (unless other formation processes such as hot-pressing or computer-aided design and computer-aided manufacturing (CAD-CAM) are used).
  • CAD-CAM computer-aided design and computer-aided manufacturing
  • ceramics change in length and volume, and as such it is important that the core and veneering ceramic are thermally compatible to prevent thermal stress formation in restorations during ceramic processing, otherwise this may lead to crazing, cracking, delamination or fracture and contribute to the failure of the restorations.
  • failures are still too often observed. It would therefore be desirable to produce a ceramic dental restoration composition which does not suffer from the problems outlined above, or at least the effect of these problems are minimised insofar as is possible, which exist despite the wealth of teaching that clearly exists in this field.
  • the present invention provides a ceramic dental restoration material having a composition a diopside crystalline phase and a leucite crystalline phase, preferably forming a dual crystalline phase structure.
  • a composition appears to be particularly compatible with precious metal alloy cores, e.g. dental gold alloy cores, such that the aforementioned benefits are achievable, as will be discussed in more detail below.
  • Said diopside-crystalline phase and leucite-crystalline phase containing composition according to the first aspect of the invention may yet further comprise a feldspathic glassy matrix having both the leucite crystalline phase and the diopside crystalline phase dispersed therein.
  • the feldspathic glassy matrix is typically an amorphous phase in which each of the leucite and diopside crystalline phases are dispersed, which is determinable by both x- ray diffraction (XRD) and scanning electron microscopy (SEM).
  • XRD x- ray diffraction
  • SEM scanning electron microscopy
  • the coefficient of thermal expansion of the restoration material is irrelevant.
  • the restoration material must be (and is believed to be) compatible with resin technologies commonly used in dentistry.
  • the ceramic dental restoration material of the invention is preferably treatable with silane, prior to being resin-bonded.
  • the composition of the invention may be formed from the following combinations of glass frits:
  • the sum total of the glass frits in said composition is 100 %.
  • Inclusion of a leucite crystalline phase in the ceramic restoration material of the invention is particularly advantageous because it acts to control the coefficient of thermal expansion of the material and the translucency of the material, and it can improve the inherent strength of the material.
  • composition of the invention may further comprise one or more ingredients, which may comprise any one or more oxides of the following: titanium (e.g. Ti0 2 ), cerium (e.g. Ce0 2 ), tin (e.g. Sn0 2 ) and vanadium (e.g. V 2 0 5 ) in a total amount of from 0 to 20 % by weight, preferably from 0.0001 to 10 % by weight and more preferably from 0.0005 to 5% by weight.
  • titanium e.g. Ti0 2
  • cerium e.g. Ce0 2
  • tin e.g. Sn0 2
  • vanadium e.g. V 2 0 5
  • each of the leucite, diopside and feldspar glass frits together these preferably comprise one or more oxides of the following: silicon (e.g. Si0 2 ), aluminium (e.g. Al 2 0 3 ), sodium (e.g. Na 2 0), calcium (e.g. CaO), magnesium (e.g. MgO) and potassium (e.g. K 2 0), which are typical glass-forming ingredients and which therefore contribute to attainment of the desirable properties of the composition hereinbefore described.
  • silicon e.g. Si0 2
  • aluminium e.g. Al 2 0 3
  • sodium e.g. Na 2 0
  • calcium e.g. CaO
  • magnesium e.g. MgO
  • potassium e.g. K 2 0
  • each of the leucite, diopside and feldspar glass frits may additionally further comprise one or more oxides of the following: aluminium (e.g. Al 2 0 3 ), barium (e.g. BaO), boron (e.g. B 2 0 3 ), cobalt (e.g. CoO, Co 2 0 3 , Co 3 0 4 ), chromium (e.g. CrO, Cr 2 0 3 , Cr0 2 , Cr0 3 ), indium (e.g. ln 2 0 3 ), nickel (e.g. NiO, Ni 2 0 3 ), rubidium (e.g. Rb 2 0) titanium (e.g. Ti0 2 ) and zirconium (e.g. Zr0 2 ), and optionally also magnesium fluoride (MgF 2 ), to enable subtle changes in the colour of the final ceramic material to be achieved.
  • aluminium e.g. Al 2 0 3
  • barium e.g. BaO
  • the ceramic material of the present invention possesses and exhibits a number of desirable properties, including preferably having a linear coefficient of thermal expansion (a) in the range of from 5 to 15 ppm/°C, further preferably in the range of from 7 to 12 ppnVO, and most preferably in the range of from 9.5 to 10 ppm/°C, as measured using dilatometry over the temperature range 300- 400 °C.
  • a linear coefficient of thermal expansion
  • the ceramic material of the invention may exhibit a percentage difference in linear coefficient of thermal expansion, as compared to a core material to which it may be applied, of less than 10 %, preferably less than 5 % and most preferably of less than 1 % (when measured over the temperature range 300-400 °C).
  • a percentage difference may equate to a difference of less than 1 ppnVO and preferably of less than 0.5 ppm/°C (when measured over the temperature range 300-400 °C).
  • a ceramic material according to the invention may additionally possess a biaxial flexural strength of at least 80 MPa, preferably of at least 90 MPa, further preferably at least 100 MPa and possibly up to around 120 MPa.
  • Biaxial flexural strength is measured as follows: prepare a fired disc of the ceramic material of the invention of 12 mm diameter and 2 mm thickness. Grind and polish this disc down to a thickness of 1 .2 mm using silicon carbide grinding papers. A Lloyds LRX tensometer (available from Lloyds Instruments Ltd, UK) with a 2500 N load cell and a cross-head speed of 1 mm/min was used to determine the biaxial flexural strength. The disc was fractured using a ball on ring arrangement.
  • a max [P / h 2 ] ⁇ (1 + v)[0.485 x ln(a / h) + 0.52] + 0.48 ⁇
  • a max the maximum tensile strength
  • P the measured load at fracture in Newtons
  • h the sample thickness in millilmetres
  • v Poisson's ratio for the material (a value of 0.25 was substituted for the glass-ceramics)
  • a is the radius of the support ring in millimetres. In all cases, fracture was observed to have originated at the centre of the disc.
  • a ceramic material according to the invention may register a Vickers hardness (H v ) of at least 550 kg/mm 2 , preferably of at least 555 kg/mm 2 and further preferably up to around 570 kg/mm 2 .
  • Vickers hardness is measured as follows: prepare a fired disc of the ceramic material of the invention of 12 mm diameter and 2 mm thickness. Grind and polish this disc down to a thickness of 1 .2 mm using silicon carbide grinding papers and diamond paste.
  • the ceramic material of the invention may exhibit an indentation fracture toughness (K, c ) of at least 1 .25 MPa-m /2 , preferably of at least 1 .3 MPa-m /2 and preferably up to around 1 .55 MPa-m /2 .
  • Fracture toughness is measured as follows: prepare a 1 .2 mm thick fired disc of the ceramic material of the invention and make an indentation in the same manner as for measuring Vickers hardness. Take readings of the radial crack length using the same equipment as used for measuring Vickers hardness and calculated the fracture toughness using the following equation:
  • the ceramic material of the invention preferably also exhibits resistance to thermal shock up to a temperature of at least 235 °C, preferably at least 250 ' ⁇ and further preferably up to around 265 ' ⁇ . This means that the material (when applied onto a chosen core material) can be heated to this temperature for 30 minutes before being quenched in ice water, dried, reheated to the same temperature and cooled to room temperature without showing signs of failure.
  • a second aspect of the invention provides a method of making a ceramic dental restoration material as hereinbefore described, said method comprising the steps of:
  • step (b) grinding each glass frit of step (a) to produce glass frits powder(s) having an optimum particle size, preferably of less than 100 ⁇ ;
  • each glass frit in step (b) may be achieved by milling, e.g. planetary ball milling, although any other suitable milling or particle size reduction technique may be used.
  • the ground glass frits may then be sieved using appropriate sieving apparatus to achieve glass frit powders of optimum particle size.
  • the glass frit powders in step (c) may be blended in an appropriate ratio, especially as hereinbefore described, so as to enable production of a desired ceramic restoration material.
  • step (d) above may be any one of the following processes: 1 ) sintering, whereby the glass frit powder mixture may be made into a slurry by addition of water or other liquid (e.g. ethanol), applied to an appropriate metallic or high strength ceramic core, allowed to dry and subsequently fired at a sufficiently high temperature (e.g. in the range of from 900-1000 'C, especially 930 °C, for at least 5 minutes) in an appropriate firing oven (e.g. a Programat P300 IPS vacuum furnace available from Ivoclar Vivadent AG, Schaan, Liechtenstein) to ensure that the particles fuse together to form the desired crystalline phases;
  • a sufficiently high temperature e.g. in the range of from 900-1000 'C, especially 930 °C, for at least 5 minutes
  • an appropriate firing oven e.g. a Programat P300 IPS vacuum furnace available from Ivoclar Vivadent AG, Schaan, Liechtenstein
  • the glass frit powder mixture may firstly be pelletized by filling pellet moulds (e.g. 1 1 mm diameter and 8 mm height) with the powder mixture, pressing the powder mixture in the mould to form pellets, removing the pellets from the mould and subsequently firing them at a sufficiently high temperature (e.g. in the range of from 900-1000 'C, especially 930 'C, for at least 5 minutes) in an appropriate firing oven (e.g. a Programat P300 IPS vacuum furnace available from Ivoclar Vivadent AG, Schaan, Liechtenstein) to ensure that the particles in the pellets fuse together to form the desired crystalline phases - the resultant fully crystallized solid pellets are then ready for use in hot-pressing;
  • pellet moulds e.g. 1 1 mm diameter and 8 mm height
  • an appropriate firing oven e.g. a Programat P300 IPS vacuum furnace available from Ivoclar Vivadent AG, Schaan, Liechtenstein
  • the glass frit powder mixture may firstly be formed into a block by filling, e.g. a stainless steel cuboid mould with the powder mixture, pressing the powder mixture in the cuboid mould to form a block, removing the block from the mould and subsequently firing it at a sufficiently high temperature (e.g. in the range of from 900-1000 °C, especially 930 'C, for at least 5 minutes) in an appropriate firing oven (e.g.
  • a sufficiently high temperature e.g. in the range of from 900-1000 °C, especially 930 'C, for at least 5 minutes
  • an appropriate firing oven e.g.
  • a third aspect of the invention consequently provides a ceramic dental restoration precursor material for use in making a ceramic dental restoration material as hereinbefore described in the form of:
  • composition of the diopside glass frit used in the invention preferably comprises the following ingredients:
  • all of the ingredients specified for inclusion in a glass frit used in the present invention are reagent grade raw materials.
  • composition of the diopside glass frit comprises the following ingredients:
  • composition of the leucite glass frit used in the invention preferably comprises the following ingredients:
  • composition of the leucite glass frit comprises the following ingredients:
  • composition of the feldspar glass frit used in the invention preferably comprises the following ingredients:
  • the summed total of Na 2 0, K 2 0 and CaO present in the composition is at least 5 %, and preferably at least 7 %, by weight.
  • composition of the feldspar glass frit comprises the following ingredients:
  • a ceramic dental restoration material according to the invention is suitable for (and especially designed for) use in dentistry, particularly aesthetic restorative dentistry, and especially as a veneering ceramic for dental crowns (both anterior and posterior), dental bridges, onlays and inlays.
  • the ceramic dental restoration material may be applied to either a metallic core material or a ceramic core material (especially to a high strength ceramic core material), or it may be resin-bonded directly to the enamel and/or dentine of an existing tooth. Because of the desirability of ceramic cores over metallic cores, it is especially preferred that the material be used in combination with a high strength ceramic core material. The primary benefit of such a combination lies in the optimised matching of linear coefficients of thermal expansion that can be achieved, thereby resulting in fewer (if any) failures of the final restoration.
  • Suitable metallic core materials for use with the ceramic material of the invention include: titanium, gold and precious metal alloys, and base metal alloys.
  • Suitable ceramic core materials suitable for use with the ceramic material of the invention include: densely-sintered alumina (e.g. ProceraTM), zirconia-based materials, lithium disilicate (l- ⁇ O-A ⁇ C SiC ⁇ ) and fluorocanasite (AlaC CaO-F-KaO-NagO-SiOg) glass- ceramic core materials, and other of the materials listed in Table I.
  • Figure 1 is a Differential Thermal Analysis (DTA) trace of a leucite glass ceramic material
  • Figure 2 is a DTA trace of a diopside glass ceramic material
  • Figure 3 is an X-Ray Diffraction (XRD) trace of the leucite glass ceramic of Figure 1 ;
  • Figure 4 is an XRD trace of the diopside glass ceramic of Figure 2.
  • a diopside glass was prepared (by melting the following reagent grade raw materials) having a composition (% by weight): Si0 2 55.7 %; Al 2 0 3 2 %; Na 2 0 1 .6 %; K 2 0 2.4 %; MgO 1 1 .8 %; CaO 16.5 %; Zr0 2 3 %; Ti0 2 3 %; B 2 0 3 2 %; MgF 2 2 %.
  • the molten glass was cooled quickly to make a diopside glass frit, which was then ground into a powder using planetary ball milling.
  • a leucite glass was prepared (by melting the following reagent grade raw materials) having a composition (% by weight): Si0 2 58 %; Al 2 0 3 15 %; Na 2 0 8 %; K 2 0 13 %; MgO 1 %; CaO 2 %; BaO 3 %.
  • the molten glass was cooled quickly to make a leucite glass frit, which was then ground into a powder using planetary ball milling.
  • a feldspar glass was prepared (by melting the following reagent grade raw materials) having a composition (% by weight): Si0 2 73 %; Al 2 0 3 8 %; Na 2 0 5.5 %; K 2 0 4 %; MgO 0.5 %; CaO 1 .5 %; B 2 0 3 7.5 %.
  • the molten glass was cooled quickly to make a feldspar glass frit, which was then ground into a powder using planetary ball milling.
  • Powder Mixture 1 (PM1 ): leucite 58 %; diopside 22 %; feldspar 20 %
  • Powder Mixture 2 (PM2): leucite 60 %; diopside 20 %; feldspar 20 %.
  • Each of PM1 and PM2 were formed into glass ceramic rods (of 30 mm length and 6 m diameter) so as to enable determination of their linear coefficients of thermal expansion (a) using the following slip-moulding / slip-casting technique.
  • a suspension (a "slip") of each of PM1 and PM2 was made by dispersing each of the mixtures into water. Each slip was then poured into a rod-shaped, silicone rubber mould and water drawn out of the mould so as to compact the powder particles within. Once fully dried, the rods (of type R1 and R2 made from PM1 and PM2 respectively) were removed from their moulds and subsequently sintered (at 930 °C for 5 minutes).
  • Each rod was then smoothed and square cut at both ends by trimming and paralleling with a rotary diamond cutting machine (LECO VC-50 available from LECO Corporation, Michigan, USA) with a diamond watering blade (available from Buehler, Illinois, USA) and was fired following the recommended firing procedure.
  • a rotary diamond cutting machine LECO VC-50 available from LECO Corporation, Michigan, USA
  • a diamond watering blade available from Buehler, Illinois, USA
  • ceramic rods were produced from each of the following commercially available ceramics in the same manner as outlined above: VITA VM 9 (PM3) (available from Vita Zahnfabrik, Switzerland) forming rod type 3 (R3) and IPS e.max Ceram (PM4) (available from Ivoclar Vivadent AG, Liechtenstein) forming rod type 4 (R4).
  • VITA VM 9 PM3 (available from Vita Zahnfabrik, Switzerland) forming rod type 3 (R3)
  • IPS e.max Ceram PM4 (available from Ivoclar Vivadent AG, Liechtenstein) forming rod type 4 (R4).
  • ceramic rods were also fabricated from both fluorocanasite (i.e. AI 2 0 3 -CaO- F-K 2 0-Na 2 0-Si0 2 ) (R5) VITA In-Ceram YZ (R6), a partially yttrium-stabilized zirconium dioxide high strength ceramic core material (also available from Vita Zahnfabrik, Switzerland).
  • fluorocanasite i.e. AI 2 0 3 -CaO- F-K 2 0-Na 2 0-Si0 2
  • VITA In-Ceram YZ R6
  • a partially yttrium-stabilized zirconium dioxide high strength ceramic core material also available from Vita Zahnfabrik, Switzerland.
  • glass ceramic R1 has a mean linear coefficient of thermal expansion that substantially matches that of core material R5 (unlike prior art glass ceramics R3 and R4 which have lower coefficients).
  • glass ceramic R2 has a mean linear coefficient of thermal expansion that substantially matches that of core material R6 (again unlike prior art glass ceramics R3 and R4 which have lower coefficients).
  • Each batch of ten D1 discs was provided with a 0.7 mm thick veneering layer of one of each of the PM1 , PM3 and PM4 glass ceramics used in Example 1
  • each batch of ten D2 was provided with a 0.7 mm thick veneering layer of one of each of the PM2, PM3 and PM4 glass ceramics used in Example 1 .
  • Each veneered disc was subsequently preheated to 90 ' ⁇ for 30 minutes, quenched in ice cold water, dried, reheated to 90 ' ⁇ and finally cooled back to room temperature. Each veneered disc was then inspected for crazing using optical microscopy (Wild M3Z microscope available from Wild Heerbrugg, Switzerland) at 40x magnification with fibre optic transillumination (Intralux 4000, Switzerland). The results are as follows.
  • a leucite glass was prepared (by melting the following reagent grade raw materials) having a composition (% by weight): Si0 2 58 %; Al 2 0 3 15 %; Na 2 0 8 %; K 2 0 13 %; MgO 1 %; CaO 2 %; BaO 3 %.
  • the molten glass was cooled quickly to make a leucite glass frit, which was then ground into a powder using planetary ball milling. This powder was used to produce discs (of 12 mm diameter and 2 mm thickness) which were then heat treated in an air furnace at 830 °C for 30 minutes in order to produce leucite glass ceramic discs.
  • a diopside glass was prepared (by melting the reagent grade raw materials) having a composition (% by weight): Si0 2 55.7 %; Al 2 0 3 2 %; Na 2 0 1 .6 %; K 2 0 2.4 %; MgO 1 1 .8 %; CaO 16.5 %; Zr0 2 3 %; Ti0 2 3 %; B 2 0 3 2 %; MgF 2 2 %.
  • the molten glass was cooled quickly to make a glass frit, which was then ground into a powder using planetary ball milling. This powder was again used to produce discs (of 12 mm diameter and 2 mm thickness) which were then heat treated in an air furnace at 930 'C for 60 minutes in order to produce the diopside glass ceramic discs.
  • each powder was characterised using DTA - the results are shown in Figures 1 and 2.
  • the leucite glass ceramic exhibited a glass transition temperature (T g ) of 653 °C and a crystallisation temperature (T x ) of 780 °C.
  • the diopside glass ceramic exhibited a exhibited a glass transition temperature (T g ) of 720 °C and crystallisation temperatures (T x ) of 847 ⁇ ⁇ and 917 °C.
  • the discs were ground down to powders once more and characterised using XRD - the results are shown in Figures 3 and 4.
  • Blend A the fully crystallized (i.e. fired) form of the leucite glass ceramic pellets with the fully crystallized (i.e. fired) form of the diopside glass ceramic pellets
  • Blend B the non-fired leucite glass ceramic pellets with the non-fired diopside glass ceramic pellets
  • Blend A three different mixtures of fully crystallized pellets were used:
  • Blend A1 90 % leucite pellets and 10 % diopside pellets
  • Blend A2 80 % leucite pellets and 20 % diopside pellets
  • Blend A3 70 % leucite pellets and 30 % diopside pellets.
  • Blend B three different mixtures of non-fired pellets were used:
  • Blend B1 70 % leucite pellets and 30 % diopside pellets
  • Blend B2 60 % leucite pellets and 40 % diopside pellets
  • Blend B3 50 % leucite pellets and 50 % diopside pellets.
  • Blends A1 , A2, A3 and B1 , B2, B3 were subsequently heated in a vacuum furnace at 930 °C and characterized using XRD and optical microscopy.
  • Figures 5 and 6 show XRD traces for each of Blends A1 (upper trace), A2 (centre trace), A3 (lower trace) and B1 (upper trace), B2 (centre trace), B3 (lower trace) respectively; all showing the presence of both leucite crystallites and diopside crystallites.
  • Blends A1 , A2, A3 in Figure 5
  • Blends B1 , B2, B3 in Figure 6
  • Example 4 optical microscopy of the two blends shows Blends A1 , A2, A3 (in Figure 5) as having crystal grains but undesirable porosity within the material, making it (and therefore its method of making) less attractive as compared to Blends B1 , B2, B3 (in Figure 6) which again show crystal grains, but pleasingly no porosity.
  • the ceramic formed from PM2 outperforms the ceramic formed from PM3 in all aspects (apart from chemical solubility where the two are equally matched), illustrating the benefit of such a multi-phase structure as compared to prior art two-phase structures, with the attendant performance and longevity benefits described above.

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  • Health & Medical Sciences (AREA)
  • Oral & Maxillofacial Surgery (AREA)
  • Epidemiology (AREA)
  • Ceramic Engineering (AREA)
  • Engineering & Computer Science (AREA)
  • Plastic & Reconstructive Surgery (AREA)
  • Chemical & Material Sciences (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Animal Behavior & Ethology (AREA)
  • General Health & Medical Sciences (AREA)
  • Public Health (AREA)
  • Veterinary Medicine (AREA)
  • Glass Compositions (AREA)
  • Dental Preparations (AREA)

Abstract

La présente invention concerne un matériau de restauration dentaire en céramique ayant une composition comprenant : une phase cristalline de diopside et une phase cristalline de leucite, les deux pouvant être dispersées dans une matrice vitreuse feldspathique. La présente invention concerne en outre un procédé de fabrication associé et un procédé d'utilisation associé.
PCT/GB2012/051311 2011-06-11 2012-06-11 Matériau de restauration dentaire en céramique Ceased WO2012172316A2 (fr)

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GB1109812.6 2011-06-11
GBGB1109812.6A GB201109812D0 (en) 2011-06-11 2011-06-11 Ceramic dental restoration material

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WO2012172316A2 true WO2012172316A2 (fr) 2012-12-20
WO2012172316A3 WO2012172316A3 (fr) 2013-03-14

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EP3050856A1 (fr) 2015-01-30 2016-08-03 Ivoclar Vivadent AG Vitrocéramique en diopside-lithium-silice
CN116177884A (zh) * 2023-03-13 2023-05-30 爱迪特（秦皇岛）科技股份有限公司 一种玻璃陶瓷基体及其制备方法与应用
CN116730623A (zh) * 2023-06-20 2023-09-12 青岛融合新材料科技有限公司 可切削复合相云母微晶玻璃及其制备工艺

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