Patent Grant
10357343
The invention relates to glass-ceramics based on the lithium disilicate system which can be mechanically machined easily in an intermediate step of crystallisation and, after complete crystallisation, represent a very strong, highly-translucent and chemically-stable glass-ceramic. Likewise, the invention relates to a method for the production of these glass-ceramics. The glass-ceramics according to the invention are used as dental material.
Lithium disilicate glass-ceramics are well known from the literature and several patents are based on this glass-ceramic system. Thus, for example, self-glazed lithium disilicate glass-ceramic objects for the production of tableware are described in EP-B-536 479, in EP-B-536 572 lithium disilicate glass-ceramics which can be used, by scattering fine-particle coloured glass on the surface thereof, as lining elements for building purposes.
The main focus of patented lithium disilicate glass-ceramics is on dental applications. This is due to the fact that the crystallisation of lithium disilicate crystals is effected via a phase of lesser strength (lithium metasilicate) and the material system is consequently amenable inter alia to chair-side methods (see S. D. Stookey: “Chemical Machining of Photosensitive Glass”, Ind. Eng. Chem., 45, pp. 115-118 (1993) and S. D. Stookey: “Photosensitively Opacifiable Glass” U.S. Pat. No. 2,684,911 (1954)). Investigations by Borom, e.g. M.-P Borom, A. M. Turkalo, R. H. Doremus: “Strength and Microstructure in Lithium Disilicate Glass-Ceramics”, J. Am. Ceram. Soc., 58, No. 9-10, pp. 385-391 (1975) and M.-P. Borom, A. M. Turkalo, R. H. Doremus: “Verfahren zum Herstellen von Glaskeramiken” (Method for the production of glass-ceramics), DE-A-24 51 121 (1974) show that glass-ceramics which comprise lithium metasilicate as main phase have reduced strength in comparison with glass-ceramics which comprise lithium disilicate as single crystalline phase.
This principle was used in order firstly to produce a glass-ceramic, in a two-step crystallisation process, which can be machined well mechanically, e.g. by means of CAD/CAM methods, and to process this subsequently in a second crystallisation step to form dental glass-ceramic. This method is suitable for being able to use dental restorations according to the so-called chair-side method. In the case of this method, an individually adapted crown/onlay/inlay is milled out of a glass-ceramic block after the first crystallisation step by means of CAD/CAM in the dentist's surgery, this is subjected to the second crystallisation step in a special oven and used directly in the first and only dental appointment for the patient (DE 10 2005 028 637).
In addition, in WO-A-95/32678 and U.S. Pat. No. 5,507,981, lithium disilicate glass-ceramics were described, which can be processed to form shaped dental products by means of hot-pressing by using a special compressible crucible. Furthermore, there are known, from DE-C-14 21 886, glass-ceramics based on SiO2 and Li2O which contain large quantities of physiologically very questionable arsenic oxide. Also in U.S. Pat. No. 4,515,634 and in FR-A-2 655 264, lithium disilicate glass-ceramics which are suitable for the production of dental crowns and bridges are disclosed.
All known lithium disilicate glass-ceramics display inadequacies in the processing thereof to shaped products and/or in mechanical or visual properties and/or in chemical stability. In particular when used in the dental field, equally high requirements for all the mentioned properties must be fulfilled.
Starting herefrom, it was the object of the present invention to provide a glass-ceramic which has improved mechanical and optical properties and also improved chemical stability relative to the (glass-) ceramics known from the state of the art.
This object is achieved by the described lithium disilicate glass-ceramic, by the method for the production of this glass-ceramic, and the shaped dental product. Advantageous developments and uses of the invention are also described.
The present invention provides a lithium disilicate glass-ceramic comprising at least 10% by weight of a stabiliser in order to increase the chemical and mechanical stability, the stabiliser being present essentially in the amorphous phase.
In the above lithium disilicate glass-ceramic embodiment, the stabiliser is selected from the group consisting of zirconium oxide, hafnium oxide and mixtures thereof.
Embodiments of the above lithium disilicate glass-ceramic have the following composition:
55 to 70% by weight of SiO2,
10 to 15% by weight of Li2O,
10 to 20% by weight of the stabiliser selected from the group consisting of ZrO2, HfO2 or mixtures hereof,
0.1 to 5% by weight of K2O,
0.1 to 5% by weight of Al2O3,
0 to 10% by weight of additives and also
0 to 10% by weight of colourants.
In accordance with embodiments of the invention, the colourants are glass-colouring oxides and/or pigments.
In accordance with embodiments of the invention, the glass-colouring oxides are selected from the group of the oxides of iron, titanium, cerium, copper, chromium, cobalt, nickel, manganese, selenium, silver, indium, gold, rare earth metals, in particular neodymium, praseodymium, samarium and europium.
In any of the above embodiments, the pigments are doped spinels.
In any of the above embodiments, the additives are selected from the group consisting of boron oxide, phosphorus oxide, fluorine, sodium oxide, barium oxide, strontium oxide, magnesium oxide, zinc oxide, calcium oxide, yttrium oxide, titanium oxide, niobium oxide, tantalum oxide, lanthanum oxide and mixtures thereof.
In accordance with an embodiment, the lithium disilicate glass-ceramic has the following composition:
58 to 64% by weight of SiO2,
11 to 13% by weight of Li2O,
10 to 15% by weight of the stabiliser selected from the group consisting of ZrO2, HfO2 or mixtures thereof,
2 to 5% by weight of K2O,
2 to 5% of Al2O3,
2 to 5% of P2O5 and also
0 to 5% by weight of additives and also
0 to 10% by weight of colourants.
In a specific embodiment, the invention provides a lithium disilicate glass-ceramic having the following composition:
55 to 70% by weight of SiO2,
10 to 15% by weight of Li2O,
10 to 20% by weight of the stabiliser selected from the group consisting of ZrO2, HfO2 and mixtures thereof,
0.1 to 5% by weight of K2O,
0.1 to 5% by weight of Al2O3,
0 to 10% by weight of additives selected from the group consisting of boron oxide, phosphorus oxide, fluorine, sodium oxide, barium oxide, strontium oxide, magnesium oxide, zinc oxide, calcium oxide, yttrium oxide, titanium oxide, niobium oxide, tantalum oxide, lanthanum oxide and mixtures thereof, and
0 to 10% by weight of colourants.
In a further specific embodiment, the invention provides a lithium disilicate glass-ceramic having the following composition:
58 to 64% by weight of SiO2,
11 to 13% by weight of Li2O,
10 to 15% by weight of the stabiliser selected from the group consisting of ZrO2, HfO2 and mixtures thereof,
2 to 5% by weight of K2O,
2 to 5% of Al2O3,
2 to 5% of P2O5 and
0 to 5% by weight of additives selected from the group consisting of boron oxide, phosphorus oxide, fluorine, sodium oxide, barium oxide, strontium oxide, magnesium oxide, zinc oxide, calcium oxide, yttrium oxide, titanium oxide, niobium oxide, tantalum oxide, lanthanum oxide and mixtures thereof, and
0 to 10% by weight of colourants.
The present invention further provides a method for the production of a lithium disilicate glass-ceramic as described above, in which
a) an initial glass is produced which comprises the components of the glass-ceramic,
b) the initial glass is subjected to a first heat treatment in order to produce a glass-ceramic which has lithium metasilicate as main crystal phase,
c) the glass-ceramic of b) is subjected to a second heat treatment in which the lithium metasilicate is converted with SiO2 from the initial glass phase into lithium disilicate and subsequently lithium disilicate is present as main crystal phase.
In an embodiment of the above method, the first heat treatment is effected at a temperature of 620° C. to 800° C. over a period of time of 1 to 200 min, in particular, at a temperature of 650° C. to 750° C. over a period of time of 10 to 60 min.
In an embodiment of the above method, the second heat treatment is effected at a temperature of 800° C. to 1,040° C. over a period of time of 5 to 200 min, in particular at a temperature of 650° C. to 750° C. over a period of time of 5 to 30 min.
In accordance with an embodiment, the rare earth metals of the glass-colouring oxides are selected from the group consisting of neodymium, praseodymium, samarium and europium.
The lithium disilicate glass-ceramic as described above find use as dental material or as component of a dental material.
The present invention further provides a shaped dental product comprising a lithium disilicate glass-ceramic as described above, in particular in the form of an inlay, an onlay, a bridge, a pin construction, a veneer, a (partial) crown.
Within the scope of the present invention, glass compositions have been developed which can be prepared in a two-step production process, are easy to machine after the first crystallisation step, in particular by means of CAD/CAM, and, after a very short second crystallisation step, are both highly-transparent and very strong and have better chemical stabilities than the known lithium disilicate glass-ceramics.
It was shown surprisingly that the addition of ZrO2 to certain glass compositions leads to glass-ceramics which can be machined very readily in an intermediate crystallisation step and, in the end state, have excellent strength values, exceptional translucence and significantly increased chemical stabilities.
It was shown that up to 20% by weight of a stabiliser selected from the group consisting of ZrO2, HfO2 or mixtures hereof can be incorporated in the glass without having a significant influence on the structure. Contrary to all expectations, the stabiliser does not hereby crystallise out as a separate crystal phase but remains in the remaining glass phase. As a result of the high proportion in the amorphous phase, the mechanical and chemical stabilities in this phase are hugely improved, which also leads to improved properties in the end product.
In particular the chemical stability can be improved via the composition of the remaining glass phase since the glass phase has a significantly higher solubility than the lithium disilicate and hence represents the weak point with respect to chemical attack. The extremely high solubility of the stabiliser (ZrO2) in the glass phase is in particular remarkable since e.g. zirconium oxide acts in many silicate glass-ceramics as nucleation agent, i.e. crystallises out as first phase during a temperature treatment, and the actually sought crystal phase is facilitated and is deposited in a fine-crystalline manner on these ZrO2 crystals.
As a result of the high proportions of stabiliser which remain essentially in the amorphous phase, the crystalline proportion is correspondingly restricted. As a result, and due to the low crystallite size of the lithium disilicate crystals, good translucence of the materials is produced after the second crystallisation. The translucence is however also further improved by the refractive index of the glass phase being increased in turn by the stabiliser and, consequently, being adapted to the refractive index of the lithium disilicate. In the case of glass-ceramics in which the refractive index of the amorphous matrix phase corresponds to the refractive index of the crystalline phase/phases, very good translucence properties are found, relatively irrespective of the crystallite size. In the glass-ceramics according to the invention, therefore all three points for the production of an extremely translucent glass-ceramic are fulfilled:
The high proportion of stabiliser has the effect therefore in the glass-ceramic of
The glass-ceramics according to the invention can be produced preferably by means of a method, in which
a) an initial glass is produced which comprises the components of the glass-ceramic,
b) the initial glass is subjected to a first heat treatment at a first temperature in order to produce a glass-ceramic which has lithium metasilicate as single or main crystal phase and
c) this glass-ceramic is subjected to a second heat treatment in which the lithium metasilicate is converted with SiO2 from the glass phase into lithium disilicate and subsequently lithium disilicate is present as single or main crystal phase.
The crystallisation to form lithium metasilicate preferably takes place at temperatures between 620° C. and 800° C., with times between 1 and 200 minutes, preferably between 650° C. and 750° C. for 10 to 60 minutes.
The crystallisation to form lithium disilicate preferably takes place at temperatures between 800° C. and 1,040° C., with times of 5 to 200 minutes, preferably between 800° C. and 870° C. for 5 to 30 minutes.
The subject according to the invention is intended to be explained in more detail with reference to the subsequent examples without wishing to restrict said subject to the special embodiments shown here.
In examples 1 to 6, compositions of glasses with a high zirconium oxide content are indicated, which are converted by a two-step temperature treatment firstly into readily mechanically machinable lithium metasilicate glass-ceramics and subsequently into highly-translucent, very strong and chemically-stable lithium disilicate glass-ceramics.
The compositions with their components are represented in Table 1.
The glasses were melted at 1,500° C. and poured into metal moulds to form blocks. The blocks were stress-relieved at 560° C. in the furnace and cooled slowly. For the different characterisation processes, the glass blocks were divided up and subjected to a first crystallisation treatment. For this purpose, the glasses were aged for 10 to 120 minutes at 600° C. to 750° C. As a result, glass-ceramics with strength values of 150 MPa to 220 MPa were produced. Exclusively lithium metasilicate was hereby established as crystal phase. In this state, machining by means of CAD/CAM methods is very readily possible.
With a second short crystallisation at 800° C. to 950° C. for 3 to 15 minutes, recrystallisation of the lithium metasilicate with amorphous SiO2 from the glass phase takes place to form lithium disilicate and the result is an increase in strength to 300 MPa to 450 MPa. In addition to the lithium disilicate phase, a subsidiary crystal phase with a zirconium oxide content can hereby be produced. In addition, also small residues of lithium metasilicate can be present. The unequivocal main crystal phase is lithium disilicate.
In Table 2, the crystallisation conditions of individual glasses and also the resulting crystal phases and strength values are displayed.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10 2009 060 274 | Dec 2009 | DE | national |
This patent application is a continuation of U.S. patent application Ser. No. 14/586,229, filed Dec. 30, 2014, now U.S. Pat. No. 9,604,873, which is a continuation of U.S. patent application Ser. No. 13/518,765, filed Aug. 15, 2012, now U.S. Pat. No. 8,956,987, which is the U.S. national phase of International Application No. PCT/EP2010/007918, filed on Dec. 23, 2010, which claims the benefit of German Patent Application No. DE 10 2009 060 274.7, filed on Dec. 23, 2009, the disclosures of which are incorporated by reference in their entireties for all purposes.
| Number | Name | Date | Kind |
|---|---|---|---|
| 2684911 | Stookey | Jul 1954 | A |
| 3238085 | Hayami et al. | Mar 1966 | A |
| 4515634 | Wu et al. | May 1985 | A |
| 5507981 | Petticrew | Apr 1996 | A |
| 5698482 | Frank et al. | Dec 1997 | A |
| 5925180 | Frank et al. | Jul 1999 | A |
| 5968856 | Schweiger et al. | Oct 1999 | A |
| 6268303 | Aitken et al. | Jul 2001 | B1 |
| 6420286 | Goto et al. | Jul 2002 | B1 |
| 6420288 | Schweiger et al. | Jul 2002 | B2 |
| 6426311 | Goto et al. | Jul 2002 | B1 |
| 6524982 | Nagata et al. | Feb 2003 | B1 |
| 6703332 | Peng et al. | Mar 2004 | B2 |
| 7166548 | Apel et al. | Jan 2007 | B2 |
| 7452836 | Apel et al. | Nov 2008 | B2 |
| 7867930 | Apel et al. | Jan 2011 | B2 |
| 7867931 | Apel et al. | Jan 2011 | B2 |
| 7867933 | Apel et al. | Jan 2011 | B2 |
| 7871948 | Apel et al. | Jan 2011 | B2 |
| 7892995 | Castillo | Feb 2011 | B2 |
| 7993137 | Apel et al. | Aug 2011 | B2 |
| 8162664 | Apel et al. | Apr 2012 | B2 |
| 8536078 | Ritzberger et al. | Sep 2013 | B2 |
| 8546280 | Apel et al. | Oct 2013 | B2 |
| 8557150 | Ritzberger et al. | Oct 2013 | B2 |
| 8592330 | Johannes et al. | Nov 2013 | B2 |
| 8759237 | Ritzberger et al. | Jun 2014 | B2 |
| 8778075 | Ritzberger et al. | Jul 2014 | B2 |
| 8956987 | Durschang et al. | Feb 2015 | B2 |
| 9125812 | Durschang et al. | Sep 2015 | B2 |
| 9206077 | Durschang et al. | Dec 2015 | B2 |
| 9604873 | Durschang | Mar 2017 | B2 |
| 9730863 | Durschang | Aug 2017 | B2 |
| 20020010063 | Schweiger et al. | Jan 2002 | A1 |
| 20050098064 | Schweiger et al. | May 2005 | A1 |
| 20050209082 | Apel et al. | Sep 2005 | A1 |
| 20070042889 | Apel et al. | Feb 2007 | A1 |
| 20090038344 | Apel et al. | Feb 2009 | A1 |
| 20090038508 | Apel et al. | Feb 2009 | A1 |
| 20090042713 | Apel et al. | Feb 2009 | A1 |
| 20090042714 | Apel et al. | Feb 2009 | A1 |
| 20090256274 | Castillo | Oct 2009 | A1 |
| 20100083706 | Castillo | Apr 2010 | A1 |
| 20110030423 | Johannes et al. | Feb 2011 | A1 |
| 20110059836 | Apel et al. | Mar 2011 | A1 |
| 20110252831 | Apel et al. | Oct 2011 | A1 |
| 20110256409 | Ritzberger et al. | Oct 2011 | A1 |
| 20110257000 | Ritzberger et al. | Oct 2011 | A1 |
| 20110259053 | Apel et al. | Oct 2011 | A1 |
| 20120248642 | Ritzberger et al. | Oct 2012 | A1 |
| 20120309607 | Durschang et al. | Dec 2012 | A1 |
| 20130295523 | Durschang et al. | Nov 2013 | A1 |
| 20130296156 | Apel et al. | Nov 2013 | A1 |
| 20130323404 | Ritzberger et al. | Dec 2013 | A1 |
| 20140000314 | Ritzberger et al. | Jan 2014 | A1 |
| 20140200129 | Durschang et al. | Jul 2014 | A1 |
| 20140249016 | Durschang et al. | Sep 2014 | A1 |
| 20140252272 | Durschang et al. | Sep 2014 | A1 |
| 20140335473 | Ritzberger et al. | Nov 2014 | A1 |
| Number | Date | Country |
|---|---|---|
| 2011-325524 | Apr 2013 | AU |
| 2213390 | Mar 1998 | CA |
| 2252660 | May 1999 | CA |
| 1306946 | Aug 2001 | CN |
| 14 21 886 | Jun 1969 | DE |
| 24 51 121 | May 1975 | DE |
| 197 50 794 | Jun 1999 | DE |
| 10 2004 013455 | Sep 2005 | DE |
| 10 2005 028637 | Dec 2006 | DE |
| 10 2007 011337 | Sep 2008 | DE |
| 10 2009 060274 | Jun 2011 | DE |
| 10 2010 050275 | May 2012 | DE |
| 0 536 572 | Apr 1993 | EP |
| 0 536 479 | Sep 1995 | EP |
| 0 690 031 | Jan 1996 | EP |
| 0 827 941 | Mar 1998 | EP |
| 0 916 625 | May 1999 | EP |
| 1 505 041 | Feb 2005 | EP |
| 1 688 397 | Aug 2006 | EP |
| 2 305 614 | Apr 2011 | EP |
| 2 377 831 | Oct 2011 | EP |
| 2 655 264 | Jun 1991 | FR |
| S39-007912 | May 1964 | JP |
| S58-120539 | Jul 1983 | JP |
| H08-040744 | Feb 1996 | JP |
| H10-101409 | Apr 1998 | JP |
| H11-314938 | Nov 1999 | JP |
| 2001-019468 | Jan 2001 | JP |
| 2005-053776 | Mar 2005 | JP |
| 2005-062832 | Mar 2005 | JP |
| 2006-219367 | Aug 2006 | JP |
| 2011-225441 | Nov 2011 | JP |
| 2013-515659 | May 2013 | JP |
| 908 355 | Feb 1982 | SU |
| WO 9532678 | Dec 1995 | WO |
| WO 2009126317 | Oct 2009 | WO |
| WO 2011076422 | Jun 2011 | WO |
| WO 2012059143 | May 2012 | WO |
| WO 2012175450 | Dec 2012 | WO |
| WO 2012175615 | Dec 2012 | WO |
| Entry |
|---|
| Borom et al., “Strength and Microstructure in Lithium Disilicate Glass-Ceramics”, Journal of the American Ceramic Society, vol. 58, No. 9-10, pp. 385-391 (1975). |
| De Oliveira et al., “Sintering and Crystallization of a Glass Powder in the Li2O—ZrO2—SiO2 System,” Communications of The American Ceramic Society, vol. 81, No. 3, pp. 777-780 (1998). |
| Durschang, “Comparison US2007/0042889 Example 2—ZLS Glass Ceramic 637-ZO Results Report,” Fraunhofer-Institut für Silicatforschung ISC, Würzburg, Germany, Nov. 2, 2015 (6 pgs.). |
| Höland et al., “Control of nucleation in glass ceramics,” Phil. Trans. R. Soc. Lond. A, 361: 575-589 (2003). |
| Höland et al., Glass-Ceramic Technology, The American Ceramic Society, Westerville, OH, Chapter 2: “Composition Systems for Glass-Ceramics,” pp. 75-83; Chapter 3, sections 3.4.1 “Chemical System and Crystalline Phases,” and 3.4.2 “Determination of Crystal Phases,” pp. 222-223 (2002). |
| Livingston et al., “Examination of the laser-induced variations in the chemical etch rate of a photosensitive glass ceramic,” Appl. Phys. A 89: 97-107 (2007). |
| Montedo et al. “Low Thermal Expansion Sintered LZSA Glass-Ceramics,” American Ceramic Society Bulletin, vol. 87. No. 7, pp. 34-40 (2008). |
| Stookey, “Chemical Machining of Photosensitive Glass”, Industrial and Engineering Chemistry, 45, pp. 115-118 (1993). |
| Von Clausbruch et al., “Crystallization, Microstructure and Properties of Selected Glasses and Glass-Ceramics in the SiO2—Li2O—ZnO—K2O—P2O5 System,” DGG Journal, vol. 1, No. 1, pp. 41-49 (2002). |
| Zheng Xin, China Doctoral Dissertations Full-text Database, Engineering Science and Technology I, No. 12, Abstract only, publication date: Dec. 15, 2008. |
| Australian Patent Office, Patent Examination Report No. 1 in Australian Patent Application No. 2010335472 (dated Mar. 4, 2014). |
| Canada Intellectual Property Office, Examination Report in Canadian Patent Application No. 2,785,348 (dated Apr. 25, 2016). |
| European Patent Office, claims as amended under Art. 34 in International Application No. PCT/EP2010/007918 (Feb. 28, 2012). |
| European Patent Office, claims as originally filed in International Application No. PCT/EP2010/007918 (Dec. 23, 2010). |
| European Patent Office, Observations by Third Parties in European Patent Application No. 10796296.1 (May 3, 2014). |
| Japanese Patent Office, Notice of Rejection in Japanese Patent Application No. 2012-545163 (dated May 9, 2014). |
| Korean Intellectual Property Office, Notification of Reason for Refusal in Korean Patent Application No. 10-2012-7019057 (dated Oct. 24, 2016). |
| State Intellectual Property Office of the People's Republic of China, Second Office Action in Chinese Patent Application No. 201080063038.3 (dated Sep. 16, 2014). |
| State Intellectual Property Office of the People's Republic of China, Fourth Office Action in Chinese Patent Application No. 201080063038.3 (dated Nov. 19, 2015). |
| State Intellectual Property Office of the People's Republic of China, Third Office Action in Chinese Patent Application No. 201080063038.3 (dated Jun. 3, 2015). |
| State Intellectual Property Office of the People's Republic of China, First Office Action in Chinese Patent Application No. 201080063038.3 (dated Apr. 2, 2014). |
| European Patent Office, International Search Report in International Application No. PCT/EP2010/007918 (dated Mar. 29, 2011). |
| European Patent Office, International Preliminary Report on Patentability in International Application No. PCT/EP2010/007918 (dated Mar. 29, 2011). |
| National Institute of Industrial Property (INPI), Office Action in Brazilian Patent Application No. BR 112012015576-8 (dated Dec. 5, 2018). |
| Number | Date | Country | |
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| 20180155234 A1 | Jun 2018 | US |
| Number | Date | Country | |
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| Parent | 14586229 | Dec 2014 | US |
| Child | 15401380 | US | |
| Parent | 13518765 | US | |
| Child | 14586229 | US |
