Dental porcelains

Abstract

Opaque porcelains for use with metal cores in the manufacture of PFM restorations. The porcelains exhibit a coefficient of thermal expansion (CTE) substantially equal to or slightly above the CTE of the metal to which it is applied. The porcelains exhibit a CTE equal to or up to about 1.5×10−6/° C. higher than the dental alloys to which they are applied as the opaque. The porcelains are fabricated from a mixture of two frit compositions. A high expansion, leucite containing frit is combined with a low melting glass frit to provide a porcelain having an expansion in the range of 16.9 to about 18.5×10−6/° C. in the temperature range of 25°-600° C.

Description

FIELD OF THE INVENTION

[0002] This invention relates to low fusing high-expansion dental porcelain especially useful for the fabrication of both all-ceramic and porcelain-fused-to-metal (PFM) restorations.

BACKGROUND OF THE INVENTION

[0003] Porcelains are typically designed to be used in the manufacture of either all-ceramic dental restorations or in PFM restorations, but are not normally functional with both types of restorations due to the differences in properties of ceramics and metals. One such porcelain, OPC® Low Wear™ porcelain, available from Jeneric/Pentron Inc., Wallingford, Conn. and covered in copending, commonly assigned patent application Ser. No. 09/133,582 filed Aug. 13, 1998, now U.S. Pat. No. 6,120,591, which is hereby incorporated by reference, was initially designed to be used as overlay for pressed all-ceramic restorations as well as for the fabrication of porcelain jacket crowns and veneers. However, OPC® Low Wear™ porcelain is not currently used for PFM restorations despite its wear resistance, forgiveness to natural dentition and strength being superior to those of conventional PFM porcelains as shown in the Table 1 below:

TABLE 1
	OPC ® Low	Conventional Porcelain
Property	Wear ™ Porcelain	for PFM
Leucite average grain	About 2-3	About 5-8
Size, μm
Leucite volume	35-40	20-25
fraction, %
Enamel wear, × 10−2	7.69 ± 3.20	18.23 ± 5.20
mm2
Wear of	0.16 ± 0.04	0.49 ± 0.11
ceramics, × 10−2mm3
CTE, 10−6/° C.,	About 17	About 13
25° C.-500° C.

[0004] The major obstacle preventing use of the OPC™ Low Wear™ porcelain in PFM restorations is the absence of an opaque/alloy combination compatible with this porcelain having relatively high expansion of about 17×10−6/° C. (25° C.-500° C.).

[0005] There exists a Golden Gate System™ for PFM restorations available through Degussa™ (Dental Division, South Plainfield, N.J.) which combines Duceragold™ porcelain and Degunorm™, type IV crown and bridge alloy (CTE=16.4×10−6/° C., 25° C.-500° C.). This system requires rather tedious multistep alloy preparation procedures including a necessary wash bake step prior to application of the opaque; and an excessively long (16-20 min) and complex first dentine bake to assure proper bonding and compatibility of the Duceragold™ porcelain to the Degunorm™ alloy. In particular, the cooling segment (3-4 min between 720° C. and 680° C.) in the first dentine bake is required by the manufacturer to grow additional leucite and may be an indication of instability of leucite in this porcelain. The following Table 2 below sets forth the various properties of the Duceragold™ porcelain.

TABLE 2
Duceragold ™
Firing Temperature, ° C.    770-790
Glass Transition            490
Temperature, ° C.
Softening Temperature, ° C. 595
CTE 25°-600° C., 10−6/° C.  15.8
Recommended alloy           Degunorm
Alloy CTE 25°-500° C.,      16.4
10−6/° C.

[0006] U.S. Pat. No. 5,453,290 to Van der Zel is directed to a dental porcelain for use with a dental alloy. The porcelain described therein must be fabricated from three frits, making it more difficult and costly to control the expansion and the glass transition temperature of the final product. Moreover, the CTE of the porcelain must be below the CTE of the alloy by 0.5-1.5 limiting the components to be used together. There is a need to provide a porcelain-fused-to-metal system for dental restorations having simple manufacturing procedures. It is desirable to provide a porcelain that is compatible with alloys of relatively high expansion. It is desireable to provide a two-frit porcelain for use in PFM restorations.

SUMMARY OF THE INVENTION

[0007] These and other objects and advantages are accomplished by opaque porcelains for use with metal cores in the manufacture of PFM restorations. The porcelains exhibit a coefficient of thermal expansion (CTE) substantially equal to or slightly above the CTE of the metal to which it is applied. In a preferred embodiment, the porcelains exhibit a CTE equal to or up to about 1.0×10−6/° C. higher than the dental alloys to which they are applied as the opaque. The porcelains are fabricated from a mixture of two frit compositions. A high expansion, leucite containing frit is combined with a low fusing glass frit to provide a porcelain having an expansion in the range of 16.9 to about 18.5×10−6/° C. in the temperature range of 25°-600° C. By combining two frits, the expansion and fusing temperature can be controlled to the values stated above.

BRIEF DESCRIPTION OF THE DRAWINGS

[0008] Features of the present invention are disclosed in the accompanying drawing, wherein:

[0009] FIG. 1 is dilatometer reading for two opaque compositions and one metal composition.

DESCRIPTION OF THE INVENTION

[0010] The invention relates to a porcelain material for use in all-ceramic restorations and PFM restorations. The porcelains exhibit a coefficient of thermal expansion (CTE) substantially equal to or slightly above the CTE of the metal to which it is applied. Preferably, the porcelains exhibit a CTE equal to or up to about 1.5×10−6/° C. higher than the dental alloys to which they are applied as the opaque, and more preferably equal to or up to about 1.0×10−6/° C. FIG. 1 shows a dilatometer reading of two opaque porcelains herein having different pigment amounts. The two porcelains correspond to Example 6 in Table 7, except that they have different amounts of pigment. Both opaques exhibit higher thermal expansions than the metal after 540° C. Opaque 1 shows a higher thermal expansion than the metal, starting at 480° C. Table 3 below lists the coefficients of thermal expansion for the opaques and metal.

	TABLE 3
	CTE (25-500° C.)	CTE (25-600° C.)
	Metal	16.4	16.9
	Opaque 1	16.6	18.4
	Opaque 2	15.0	17.8

[0011] The porcelains herein are compatible with metals having coefficients of thermal expansion (CTE) in the range of from about 15.5 to about 18×10−6/° C. in the temperature range from 200 to 600° C. The porcelains exhibit CTEs in the range of about 16.9 to about 18.5 in the temperature range from 20° to 600° C., and preferably in the range of about 17 to about 18×10−6/° C. in the temperature range from 20° to 600° C. The porcelains are fabricated from a mixture of two frit compositions. A high expansion, leucite containing frit is combined with a low fusing glass frit to provide a porcelain having an expansion in the range of 16.9 to about 18.5×10−6/° C. in the temperature range of 25°-600° C. It is essential to this invention that both the high expansion and the low fusing components of the two-frit mixture exhibit a low glass transition temperature (GTT). It is extremely important that the low fusing component used in the opaque formulation exhibits a GTT lower than about 415° C. By combining two frits, the expansion and firing temperature can be controlled to the values stated above. Opaque porcelains herein having pigments exhibit a coefficient of thermal expansion of average value of about 18×10−6/° C. in the temperature range of 25°-600° C. Opaque porcelains without pigments, i.e., white opaques, exhibit coefficients of thermal expansion in the higher end of the range, such as about 17.5 to about 18.5×10−6/° C. in the temperature range of 25°-600° C.

[0012] Table 4 below shows the compositional ranges of the porcelains for use in the invention.

	TABLE 4
	Body and	Opaque	Opaque	Opaque	Opaque
	Incisal	Porcelain	Porcelain	Porcelain	Porcelain
	Porcelain	(1)	(2)	(3)	(4)
	(by weight	(by weight	(by weight	(by weight	(by weight
	percent)	percent)	percent)	percent)	percent)
SiO2	about 59-	about 59-	about 59-	about 48-	about 48-
	about 65	about 65	about 65	about 65	about 65
B2O3	X	X	X	0-about 0.7	0-about 0.7
Al2O3	about 10-	about 10-	about 10-	about 10-	about 10-
	about 15	about 15	about 15	about 15	about 15
ZnO	X	X	X	0-about 5	0-about 5
CaO	about 0.5-	about 0.5-	about 0.5-	about 0.5-	about 0.5-
	about 2	about 2	about 2	about 2	about 2
MgO	X	X	X	0-about 2	0-about 2
BaO	X	X	X	0-about 1	0-about 1
Li2O	about 1.5-	about 1.5-	about 1.5-	about 1.5-	about 1.5-
	about 3	about 3	about 3	about 3	about 3
K2O	about 15-	about 15-	about 12-	about 14-	about 15-
	about 17	about 17	about 17	about 17	about 17
Na2O	about 4-	about 4-	about 4-	about 4-	about 4-
	about 6	about 6	about 6	about 6	about 6
TiO2	X	X	X	0-about 2	0-about 2
ZrO2	X	X	X	0-about 17	0-about 17
CeO2	X	X	X	0-about 1	0-about 1
F	about 0.4-	about 0.4-	about 0.4-	about 0.4-	about 0.4-
	about 1	about 1	about 1	about 1	about 1
Ta2O5	—	X	X	0-about 2	0-about 2
SnO2	—	—	—	0-about 18	0-about 18
ZrSiO4	—	—	—	0-about 7	—
*Opaci-	0-about 1	about 13-	about 10-	—	—
fiers		about 20	about 20
**Pig-	0-about 5	about 2-	about 2-	—	—
ments		about 13	about 13
*Opacifiers, Al2O3, SnO2, TiO2, ZrO2, ZrSiO4, ZnO, CeO2, or Ta2O5, are admixed as fine powder to a mixture of two frits. The resulting composition is referred to below as White Porcelain (opaque, body or incisal).
**Pigments are admixed as fine powder to a White Porcelain powder. The resulting powder composition is referred to below as Shaded Porcelain (opaque, body or incisal).
X signifies non-essential components.

[0013] As set forth in Table 3 above, Li2O, present in an amount of from about 1.5% to about 3%, and F, present in an amount of 0.4%-1%, are instrumental in providing a low glass transition temperature. The presence of Li2O and F also assist as well in increasing the coefficient of thermal expansion and decreasing the maturing (firing) temperature. The high expansion, leucite containing component of the two-frit mixture has a reasonably low glass transition temperature as well. This is achieved by maintaining a reasonably low molar ratio of Al2O3 to the sum of alkali and alkaline earth oxides (R2O+RO). Normally, these compositions are extremely unstable and reactive as well as prone to sanidine precipitation in the temperature range of 650° C.-950° C. It was surprisingly found that certain compositions with specific combinations of K2O, Na2O and Li2O are very stable. In addition, it was found that the molar ratio of Al2O3/K2O should be within the range of 0.73-0.95 to assure both the required thermal stability and low glass transition temperature of the high expansion component of the porcelain. The low glass transition temperature provides a porcelain having good complatability with alloys having CTEs in the range of about 15.5 to about 18×10−6/° C. in the temperature range of 25°-600 ° C. Table 5 below sets forth the properties of the porcelain compositions.

TABLE 5
PORCELAIN	Body & Incisal	Opaque (1)	Opaque (3)
Firing	780-870	830-860	750-890
Temperature/Maturin
g Temperature, ° C.
Glass Transition	420-430	450-490	—
Temperature, ° C.
Softening	520	—	—
Temperature, ° C.
CTE 25°-420° C., 10−6/	15.2	—	—
° C.
CTE 25°-500° C., 10−6/	17.2	16.0 ± 0.1	17-17.5
° C.
CTE 25°-600° C., 10−6/	—	18.0 ± 0.5	—
° C.

[0014] Table 6 sets forth compatible alloys for use with the porcelains.

TABLE 6
Alloy	CTE (25° C.-600° C.)	Application
Bio-75G ™ alloy	15.8	Fast Cool for single units
		only
GoldCore ™ 75	16.9	For single units and bridges
alloy
GoldCore ™ 55	17.35	For single units and bridges
alloy
JewelCast ™	17.32	For single units and bridges
alloy
GoldCore ™ 2	17.2	For single units and bridges
alloy

[0015] Table 7 below shows compositional examples of body (incisal) and opaque porcelains.

	TABLE 7
			Example		Example 4	Example 5	Example 6
			2 White	Example 3	White	White	White
			Opaque	White	Opaque	Opaque	Opaque
	Example 1		Porcelain	Opaque	Porcelain	Porcelain	Porcelain
	Body/	Compara-	for	Porcelain	for	for	for Light
	Incisal	tive	Light*	for Light*	Dark**	Dark**	and Dark
	Porcelain	Example 1	Shades	Shades	Shades	Shades	Shades
Two-Frit
Mixture
Composition
SiO2	61.9	61.5	60.0	58.5	60.1	58.6	60.1
B2O3	0.5	0.5	0.6	0.6	0.6	0.6	0.6
Al2O3	11.6	15.4	13.6	13.6	13.7	13.6	13.1
ZnO	0.0	0.0	0.0	2.0	0.0	2.0	0.0
CaO	1.7	0.6	1.2	1.2	1.2	1.2	1.2
MgO	0.8	0.2	0.2	0.1	0.2	0.1	0.7
BaO	0.0	0.0	0.4	0.4	0.4	0.4	0.4
Li2O	2.5	2.3	2.3	2.3	2.3	2.3	2.3
K2O	15.7	12.9	15.1	15.0	15.1	15.0	15.2
Ta2O5	0.0	0.0	0.0	0.0	0.0	0.0	0.0
Na2O	4.8	6.0	5.5	5.4	5.4	5.3	5.5
TiO2	0.0	0.0	0.0	0.0	0.0	0.0	0.0
ZrO2	0.0	0.0	0.0	0.0	0.0	0.0	0.0
CeO2	0.0	0.6	0.3	0.3	0.3	0.3	0.3
F	0.6	0.0	0.7	0.6	0.7	0.6	0.7
Mixed-In
Opacifiers
ZrO2			17	17	15	15	17
ZrSiO4
TiO2
SnO2
ZnO
CeO2
Ta2O5
Firing	857		871	871	871	871	830-860
temperture
CTE	17.2 ± 0.3		17.8	17.8	17.8	17.8	16.0 ± 1.0
(25° C.-
500° C.)
CTE (25-			18 ± 0.5	18 ± 0.5	18 ± 0.5	18 ± 0.5	18 ± 0.5
600° C.° C.)
*Light Opaque Shades - Pigment content < 6 wt %
**Dark Opaque Shades - Pigment content > 6 wt %

[0016] The low glass transition temperature of the opaque porcelain is paramount to assure its compatibility with alloys having CTE's in the range of about 15.5 to about 18 (25-600° C.), such as commercially available Gold Core 75™ alloy from Jeneric/Pentron Inc., Wallingford, Conn. This is a gold alloy that does not contain copper and other elements that form dark oxide layers and, therefore, requires much less intricate preparation procedures compared to the Degunorm alloy. Specifically, the Gold Core 75™ alloy forms an adequate oxide layer without compromising the appearance of the coping when degassed at 870° C.-885° C. for about 5-7 min in air or vacuum.

[0017] The high potassium content in the porcelain is essential to assure high stability of leucite. High potassium oxide content combined synergetically with other alkali elements (Li and Na) assures as well relatively low glass transition temperature (GTT) and, hence, increased resistance to thermal expansion mismatch cracking and increased adaptability to alloys of slightly lower expansion. It was surprisingly found that increased potassium content increases stability in compositions with low GTT, e.g., Example 1 was found to be much more stable than Comparative Example 1 (compare K2O content). Specifically, dental porcelain of Example 1 has excellent thermal expansion stability and maintains the same thermal expansion after 5 successive bakes at its firing temperature. Dental porcelain of Comparative Example 1 was found to change thermal expansion and opacity upon multiple bakes.

[0018] Essential to this invention is that opaque compositions possess a relatively low transition temperature and contain the same elements such as ZnO and Ta2O5 as the oxide layer forming on the alloy that assure good bonding to alloys. Specifically, the oxide layer on the Gold Core 75™ alloy was found to be enriched with ZnO and Ta2O5 and the same components were included in the opaque formulation to improve bonding.

[0019] Body and incisal porcelain are typically applied to opaque porcelain, respectively. Preferably, the body and incisal porcelains used with the opaque herein exhibit an average coefficient of thermal expansion of about 17.2.

[0020] In a preferred embodiment of the invention, alloys having a CTE in the range of about 15.5 to about 18×106/° C. in the temperature range of 25°-600° C. are used to manufacture metal core for a restoration. Opaque porcelains are applied thereto, wherein the CTE is in the range of about 16.9 to about 18.5×10−6/° C. in the temperature range of 25°-600° C. and body/incisal porcelains are applied thereto having CTEs in the range of about 16.9 to about 17.7 (from 25°-470 or 500° C.). It is preferred that the opaque porcelain has a CTE about equal to or up to about 1.5×10−6/° C. higher than the metal core. It is preferred that the body porcelain has a CTE about equal to or up to about 1.5×10−6/° C. higher than the metal core. It is preferable that the CTE of the opaque is between the CTE of the alloy and the CTE of the body porcelain.

[0021] The following examples illustrate the invention.

EXAMPLES

[0022] Copings and bridge frameworks cast from Bio-75G, GoldCore75, GoldCore55 and JewelCast alloys available from Jeneric/Pentron, Wallingford, Conn., were prepared with a carbide tool, sand-blasted with alumina sand at pressure of 2 bar and ultrasonically cleaned in water for about 5 min. The same degassing cycle given in the firing charts below was used for Bio-75G, JewelCast, GoldCore55 and GoldCore75 castings. Following degassing, the oxide layer was removed by sand-blasting and castings were ultrasonically cleaned in water for about 5 min. The opaque of the composition of Example 3 (Table 6) was applied in two thin coats and fired according to the firing cycle given in a table below. Body/Incisal porcelain of composition of Example 1 was used to build full contour crowns and bridges and fired up to 5 times as per firing charts below (Tables 8 and 9).

[0023] No cracking was observed on single unit restorations made from the alloys above. However, cracks in pontic areas were found when porcelain was fired onto bridge frameworks made from Bio-75G™ alloy. Both single and multiunit restorations made from GoldCore™ 75, GoldCore™ 55 and JewelCast2™ alloys exhibited no cracking upon multiple firings.

TABLE 8
Firing chart in ° F.
		Opaque	1st	2nd	3rd-5th
	Degassing	bake	OPC Low	OPC Low	OPC Low
	cycle	(2 coats)	Wear bake	Wear bake	Wear bake
Predry, min	0	6	6	6	6
Low T, ° F.	1200	600	1000	1000	1000
High T, ° F.	1625	1600	1575	1550	1550
Rate,	100	75	75	75	75
° C./min
Vacuum	100%	100%	100%	100%	100%
VacOn, ° F.	1200	750	1000	1000	1000
VacOff, ° F.	1625	1500	1525	1500	1500
Hold, min	5 in	0	0	0	0
	vacuum
Cool, min	0	0	0	0	0

[0024]

TABLE 9
Firing chart in ° C.
		Opaque	1st	2nd	3rd-5th
	Degassing	bake	OPC Low	OPC Low	OPC Low
	cycle	(2 coats)	Wear bake	Wear bake	Wear bake
Predry, min	0	6	6	6	6
Low T, ° C.	650	316	538	538	538
High T, ° C.	885	871	857	843	843
Rate,	55	42	42	42	42
° C./min
Vacuum	100%	100%	100%	100%	100%
VacOn, ° C.	650	399	538	538	538
VacOff, ° C.	885	816	829	816	816
Hold, min	5 in	0	0	0	0
	vacuum
Cool, min	0	0	0	0	0

[0025] In addition to dental restorations, bond flags were cast from the alloys listed above. Two thin coats of opaque (composition of Example 3) were applied and fired onto the bond flags. Bond flags were bent using pliers and metal surface exposed along the bend where opaque is fractured was inspected using optical stereomicroscope under magnification of 10×. Fracture along opaque-metal interface was found mostly adhesive, i.e. substantial fraction of the metal surface was covered by opaque indicating good bonding between alloys and opaque. The observed coverage was comparable to other metal-porcelain systems and therefore deemed sufficient. Bond strength was quantified according to ISO-9693 Metal-Ceramic Bond Test (Schwickerath crack initiation test). The following Table indicates the bond strengths calculated from the formula

τb=k·Ffail

[0026] wherein

[0027] τb is the debonding/crack initiation strength

[0028] k is a coefficient which is a function of the thickness of the metal substrate, and the value of Young's modulus of the used metallic material; and

[0029] Ffail is the fracture force

TABLE 10
		Elastic
	Thick-	Modu-
Spec-	ness	lus	Load	F(fail)		τb
imen	(mm)	(GPa)	(Lbs)	Newtons	k	(MPa)
gold	0.55	12.5	2.81	12.49950291	3.6	44.99821048
core
75
gold	0.54	12.5	2.262	10.06187743	3.75	37.73204037
core
75
gold	0.55	12.5	1.81	8.051281235	3.65	29.38717651
core
75
gold	0.55	12.5	3.02	13.43362946	3.65	49.03274754
core
75
gold	0.55	12.5	2.78	12.36605626	3.65	45.13610535
core
75
mean				0		41.25725605
Std				0		7.791412161
Dev
gold	0.5	15.12	1.42	6.316474781	4.1	25.8975466
core
55
gold	0.5	15.12	1.07	4.759597194	4.1	19.5143485
core
55
gold	0.52	15.12	2.88	12.81087843	3.8	48.68133803
core
55
gold	0.5	15.12	1.68	7.473012417	4.1	30.63935091
core
55
gold	0.47	15.12	1.51	6.716814732	4.7	31.56902924
core
55
gold	0.47	15.12	0.98	4.359257243	4.7	20.48850904
core
55
mean				0		29.46502039
Std						9.724481694
dev

[0030] As will be appreciated, the present invention provides porcelain compositions compatible with alloys for use in the manufacture of PFM restorations. The porcelains exhibit a coefficient of thermal expansion (CTE) substantially equal to or slightly above the CTE of the metal to which it is applied. The porcelains are fabricated from a mixture of two frit compositions. A high expansion, leucite containing frit is combined with a low melting glass frit to provide a porcelain having an expansion in the range of 16.9 to about 18.5×10−6/° C. in the temperature range of 25°-600° C. By combining two frits, the expansion and firing temperature can be easily controlled.

[0031] While various descriptions of the present invention are described above, it should be understood that the various features can be used singly or in any combination thereof. Therefore, this invention is not to be limited to only the specifically preferred embodiments depicted herein.

[0032] Further, it should be understood that variations and modifications within the spirit and scope of the invention may occur to those skilled in the art to which the invention pertains. Accordingly, all expedient modifications readily attainable by one versed in the art from the disclosure set forth herein that are within the scope and spirit of the present invention are to be included as further embodiments of the present invention. The scope of the present invention is accordingly defined as set forth in the appended claims.

Claims

1. A porcelain composition for use as an opaque on dental alloys in the manufacture of a dental restoration comprising by weight percent: about 48 to about 65% SiO2, about 10 to about 15% Al2O3; about 0.5 to about 2% CaO; about 1.5 to about 3% Li2O; about 15 to about 17% K2O; about 4 to about 6% Na2O; and about 0.4 to about 1 F; wherein the porcelain possesses a coefficient of thermal expansion of about 16.9 to about 18.5 in the temperature range of 25° C. to 600° C.

2. The porcelain of claim 1 wherein the coefficient of thermal expansion is slightly higher than the dental alloys to which it is applied as the opaque.

3. The porcelain of claim 2 wherein the coefficient of thermal expansion is equal to or up to about 1.5×10−6/° C. higher than the dental alloys to which it is applied as the opaque in the temperature range of 25° C. to 600° C.

4. The porcelain composition of claim 1 possessing a coefficient of thermal expansion which is compatible with alloys possessing a coefficient of thermal expansion in the range of about 15.5 to about 18×10−6/° C. in the temperature range of 25°-600° C.

5. The composition of claim 1 further comprising by weight: about 0 to about 0.7% B2O3; about 0 to about 5% ZnO; about 0 to about 2% MgO; about 0 to about 1% BaO; about 0 to about 2% TiO2; about 0 to about 17% ZrO2; about 0 to about 7% ZrSiO4; about 0 to about 1% CeO2; about 0 to about 2% Ta2O5; and about 0 to about 18% SnO2.

6. A method of making a dental restoration comprising: forming a dental porcelain powder from a dental composition comprising about 48 to about 65% SiO2, about 10 to about 15% Al2O3, about 0.5 to about 2% CaO, about 1.5 to about 3% Li2O, about 14 to about 17% K2O, about 4 to about 6% Na2O, and about 0.4 to about 1 F, wherein the maturing temperature is in the range of about 750° C. to about 890° C.; shaping the dental porcelain powder onto a metal core; and heating the shaped dental porcelain powder to between about 750° C. to about 880° C. to fuse the dental porcelain powder to the metal core; wherein the metal core exhibits a coefficient of thermal expansion in the range from about 15.5 to about 18×10−6/° C. (measured from 25° C. to 600° C.).

7. The method of claim 6 wherein the metal framework comprises a gold alloy.

8. The method of claim 6 wherein the porcelain powder is an opaque porcelain.

9. The method of claim 8 further comprising applying a body porcelain over the opaque porcelain.

10. The method of claim 9 further comprising applying an incisal porcelain over the body porcelain.

11. The method of claim 10 wherein the incisal porcelain comprises: about 59 to about 65% SiO2; about 10 to about 15% Al2O3; about 0.5 to about 2% CaO; about 1.5 to about 3% Li2O; about 15 to about 17% K2O; about 4 to about 6% Na2O; and about 0.4 to about 1 F.

12. The method of claim 11 wherein the incisal porcelain comprises a mixture of a high expansion leucite-containing frit and a low fusing glass frit.

13. The method of claim 12 wherein the incisal porcelain comprises a mixture of frits.

14. The method of claim 9 wherein the body porcelain comprises: about 59 to about 65% SiO2, about 10 to about 15% Al2O3; about 0.5 to about 2% CaO; about 1.5 to about 3% Li2O; about 15 to about 17% K2O; about 4 to about 6% Na2O; and about 0.4 to about 1 F.

15. A porcelain composition comprising by weight percent: about 59 to about 65% SiO2, about 10 to about 15% Al2O3; about 0.5 to about 2% CaO; about 1.5 to about 3% Li2O; about 12 to about 17% K2O; about 4 to about 6% Na2O; about 0.4 to about 1% F; and about 10 to about 20% of an opacifier; wherein the porcelain composition is used as an opaque in the manufacture of dental restorations and possesses a coefficient of thermal expansion of about 16.9 to about 18.5 in the temperature range of 25° C. to 600° C.

16. The porcelain composition of claim 15 wherein the opacifier is selected from Al2O3, ZnO, TiO2, ZrO2, ZrSiO4, CeO2, Ta2O5, SnO2 and mixtures thereof.

17. The porcelain composition of claim 15 wherein it is applied to dental alloys and wherein the coefficient of thermal expansion is equal to or up to about 1.5×10−6/° C. higher than the dental alloys to which it is applied as the opaque in the temperature range of 25° C. to 600° C.

18. A dental restoration comprising: a metal core, having a coefficient of thermal expansion below about 18×10−6/° C. (measured from 25° C. to 600° C.); and an opaque porcelain applied on the metal core, having a coefficient of thermal expansion (measured from 25° C. to 600° C.) about equal to or up to about 1.5×10−6/° C. higher than the metal core; wherein the opaque porcelain comprises about 48 to about 65% SiO2, about 10 to about 15% Al2O3; about 0.5 to about 2% CaO; about 1.5 to about 3% Li2O; about 15 to about 17% K2O; about 4 to about 6% Na2O; and about 0.4 to about 1 F.

19. The dental restoration of claim 18 wherein the opaque porcelain further comprises: about 0 to about 0.7% B2O3; about 0 to about 5% ZnO; about 0 to about 2% MgO; about 0 to about 1% BaO; about 0 to about 2% TiO2; about 0 to about 17% ZrO2; about 0 to about 7% ZrSiO4; about 0 to about 1% CeO2; about 0 to about 2% Ta2O5; and about 0 to about 18% SnO2.

20. A dental restoration comprising: a metal core, having a coefficient of thermal expansion below about 18×10−6/° C. (measured from 25° C. to 600° C.); an opaque porcelain applied on the metal core, having a coefficient of thermal expansion (measured from 25° C. to 600° C.) about equal to or up to about 1.5×10−6/° C. higher than the metal core; and a body porcelain applied to the opaque porcelain having a coefficient of thermal expansion (measured from 25° C. to 600° C.) about equal to or up to about 1.5×10−6/° C. higher than the metal core.

21. The dental restoration of claim 20 wherein the coefficient of thermal expansion of the opaque porcelain is between the coefficient of thermal expansion of the alloy and the coefficient of thermal expansion of the body porcelain.

22. A dental restoration comprising: a metal core, having a coefficient of thermal expansion below about 18×10−6/° C. (measured from 25° C. to 600° C.); and an opaque porcelain applied on the metal core, having a coefficient of thermal expansion (measured from 25° C. to 600° C.) about equal to or up to about 1.5×10−6/° C. higher than the metal core; wherein the opaque porcelain comprises about 59 to about 65% SiO2; about 10 to about 15% Al2O3; about 0.5 to about 2% CaO; about 1.5 to about 3% Li2O; about 12 to about 17% K2O; about 4 to about 6% Na2O; and about 0.4 to about 1 F.

23. A method of making a dental restoration comprising: forming a dental porcelain powder from a dental composition comprising about 59 to about 65% SiO2, about 10 to about 15% Al2O3; about 0.5 to about 2% CaO; about 1.5 to about 3% Li2O; about 12 to about 17% K2O; about 4 to about 6% Na2O; and about 0.4 to about 1 F, wherein the maturing temperature is in the range of about 750° C. to about 890° C.; shaping the dental porcelain powder onto a metal core; and heating the shaped dental porcelain powder to between about 750° C. to about 880° C. to fuse the dental porcelain powder to the metal core; wherein the metal core exhibits a coefficient of thermal expansion in the range from about 15.5 to about 18×10−6/° C. (measured from 25° C. to 600° C.).