Colored transparent, translucent and opaque glass-ceramics

BACKGROUND OF THE INVENTION
U.S. application Ser. No. 451,283, filed concurrently to Ser. No. 451,284 by me under the title Transparent Colorless Glass-Ceramics Especially Suitable for Use as Stove Windows, discloses a relatively narrow range of precursor glass compositions which, although containing TiO.sub.2 and up to 0.1% by weight Fe.sub.2 O.sub.3, can surprisingly be crystallized in situ through heat treatment to yield essentially colorless glass-ceramic articles wherein .beta.-quartz solid solution constitutes the predominant crystal phase. Thus, as is discussed therein, in crystallizing the typical parent glass article containing TiO.sub.2 as a nucleating agent and Fe.sub.2 O.sub.3 as an impurity in amounts greater than 0.01%, a reaction is believed to take place between the titanium and iron ions during the heat treatment process, whereby the valence state of the titanium ions is reduced from +4 to +3. The result of that reaction is the formation of an unattractive gray-brown coloration in the glass-ceramic. The crux of that inventive subject matter lies in the discovery that the essential absence of MgO from the compositions permits the production of virtually colorless, transparent glass-ceramic bodies from precursor glasses containing up to 0.1% Fe.sub.2 O.sub.3, wherein TiO.sub.2 comprised at least a substantial portion of the nucleating agent. And, because .beta.-quartz or .beta.-eucryptite solid solution crystals, as such have been variously denominated, can exhibit coefficients of thermal expansion over the range of 0.degree.-300.degree. C. of 0 or less, those glass-ceramics can demonstrate coefficients of thermal expansion over the same temperature interval within the regime of about -10 to +10.times.10.sup.-7 /.degree.C. Those glass-ceramic articles are produced by heat treating the following glass compositions, expressed in terms of weight percent on the oxide basis, at temperatures between about 750.degree.-950.degree. C.:
______________________________________SiO.sub.2 65-75Li.sub.2 O 1-4Al.sub.2 O.sub.3 15-25ZnO 0.5-2Na.sub.2 O and/or K.sub.2 O 0-2TiO.sub.2 2-6ZrO.sub.2 0-2BaO 0-2F 0-1.2Fe.sub.2 O.sub.3 >0.01 but <0.1______________________________________
The most preferred composition was stated to have an analyzed composition of about:
______________________________________ SiO.sub.2 66.6% Al.sub.2 O.sub.3 20.5 Li.sub.2 O 3.7 Na.sub.2 O 0.4 K.sub.2 O 0.5 ZnO 1.0 BaO 2.0 TiO.sub.2 2.6 ZrO.sub.2 1.6 As.sub.2 O.sub.3 0.5 Fe.sub.2 O.sub.3 0.05______________________________________
Those glass-ceramics are described as being especially useful as windows for coal and wood burning stoves since their transparency and lack of color provided an uninterrupted and undistorted view of the fire inside the stove. However, because the precursor glass therefor possesses the thermal stability and viscosity characteristics necessary for forming sheet, coupled with their high refractoriness, excellent chemical durability, very low coefficient of thermal expansion (about .+-.7.times.10.sup.-7 /.degree.C. over the range of 25.degree.-700.degree. C.), and capability of being crystallized in situ very rapidly, other applications for those glass-ceramics in sheet form such as countertops and range tops have become apparent.
As can be appreciated, not all such applications require a colorless transparent product. Indeed, where a decorative effect is wanted, colors immediately come to mind. (Even in windows for coal and wood burning stoves, there has been some desire voiced for a product having a light brown tint to impart a warm, cheerful appearance to the fire inside.) Furthermore, many applications do not require transparent products. Accordingly, it would be highly desirable to be able to produce transparent and opaque glass-ceramic articles having compositions approximating the analyzed values above, but exhibiting a range of colors.
SUMMARY OF THE INVENTION
Transparent, translucent, and opaque glass-ceramic articles containing .beta.-quartz solid solution as the predominant crystal phase exhibiting colors ranging from black to brown to red, and opaque glass-ceramic articles containing .beta.-spodumene solid solution as the predominant crystal phase exhibiting colors ranging from gray to brown to almond to beige to yellow to blue can be prepared from precursor glasses having base compositions essentially free from MgO consisting essentially, in weight percent, of:
______________________________________ SiO.sub.2 63.5-69 Al.sub.2 O.sub.3 15-25 Li.sub.2 O 2.5-4 Na.sub.2 O 0.1-0.6 K.sub.2 O 0.1-0.6 Zno 0-2 BaO 0-5 TiO.sub.2 2-3 ZrO.sub.2 0.5-2.5 As.sub.2 O.sub.3 0.4-0.8 Fe.sub.2 O.sub.3 0.05-0.1______________________________________
The desired colors are obtained through the use of a "color package" containing about 0.5-3% TiO.sub.2 and up to 0.15% Fe.sub.2 O.sub.3 with 0.3-3% total of at least two oxides in the indicated proportion selected from the group of up to 0.3% V.sub.2 O.sub.5, up to 3% CeO.sub.2, up to 2% CaO, up to 1% NiO, up to 1% WO.sub.3, and up to 1.5% SnO.sub.2. The total TiO.sub.2 content will range >2.5-6% and the Fe.sub.2 O.sub.3 content will range 0.05-0.2%.
The means for making the inventive products comprises three general steps:
(a) a batch for a glass having a composition within the above ranges is melted;
(b) the melt is simultaneously cooled to a temperature at least below the transformation range thereof and a glass article of a desired configuration shaped therefrom; and
(c) the glass article is heat treated in a manner to cause the crystallization in situ thereof.
Where a glass-ceramic article containing .beta.-quartz solid solution as the predominant crystal phase is desired, the precursor glass article will be heat treated at temperatures between about 750.degree.-950.degree. C. for a time sufficient to effect crystallization in situ. Where an article containing .beta.-spodumene solid solution as the predominant crystal phase is desired, the precursor glass article will be heat treated at temperature between about 950.degree.-1150.degree. C. for a time sufficient to cause crystallization in situ.
Each of the above-delineated members of the "color package" displays a tendency to raise the coefficient of thermal expansion of the base composition, especially when heat treated to effect crystallization of beta-spodumene solid solution. To illustrate, the coefficients of thermal expansion of such glass-ceramic bodies can be readily raised from the customary 6-8.times.10.sup.-7 /.degree.C. to >10.times.10.sup.-7 /.degree.C. (25.degree.-700.degree.) when the coloring oxides are incorporated. Consequently, it is essential that the concentrations of the "color package" ingredients be kept to a minimum, while still obtaining the desired tints, in order to secure the most thermally stable, crystallized articles.
It is possible to offset at least a portion of that increase in thermal expansion by varying the amounts of the components of the base composition. For example, utilizing levels of BaO, CaO, Na.sub.2 O, K.sub.2 O, Al.sub.2 O.sub.3, TiO.sub.2, and As.sub.2 O.sub.3 at the lower end of the operable ranges thereof, when possible, will reduce the coefficient of thermal expansion of a beta-spodumene solid solution-containing glass-ceramic. Further, the substitution of SnO.sub.2 for the combination of CeO.sub.2 +CaO substantially decreases the thermal expansion of those articles.
Finally, it is possible to make small additions, viz., no more than a total of about 3%, of such oxides as Cu.sub.2 O, La.sub.2 O.sub.3, B.sub.2 O.sub.3, and Cs.sub.2 O and the transition metal oxides CoO, MnO, Cr.sub.2 O.sub.3, and Nb.sub.2 O.sub.5 without seriously altering the colors and physical properties desired. In general, individual values of each addition will be held below 1%. MgO exerts a deleterious effect upon the colors produced (haze develops in transparent articles and the colors are not as intense in the opaque bodies), so no more than 0.5% can be tolerated and, preferably, the compositions will be essentially free from MgO.
The exact mechanism operating to produce the inventive coloration is not known with certainty but it is believed that the TiO.sub.2 and Fe.sub.2 O.sub.3 react with the other members of the "color package" and/or the above-cited transition metal oxides. Hence, as was disclosed in Ser. No. 451,283, the reaction deemed to take place between titanium and iron ions during the crystallization heat treatment, whereby the valence state of the titanium ions is reduced from +4 to +3, results in the development of an unattractive gray-brown coloration in the transparent glass-ceramic. Because of the relatively wide palette of colors which can be generated in the inventive glass-ceramics, it is believed apparent that a further and/or different reaction must be taking place during the crystallization heat treatment involving the other "color package" components and the transition metal oxides when present.
The presence of As.sub.2 O.sub.3 in the composition leads to the development of more intense colors. The mechanism underlying this phenomenon is also not understood, but the inclusion of about 0.4-0.6% As.sub.2 O.sub.3 is preferred to intensify the coloration generated.
U.S. application Ser. No. 451,282, filed concurrently to Ser. No. 451,284 by me under the title Transparent Glass-Ceramics Especially Suitable for Use as Stove Windows, discloses means by which glass-ceramic articles containing .beta.-quartz solid solution as the predominant crystal phase and having compositions within two regimes of components can be made exceptionally resistant to attack by the atmosphere generated in a coal or wood burning stove.
In the first embodiment of that inventive method the precursor glass article is initially exposed to a H.sup.+ ion and Li.sup.+ ion exchange reaction utilizing the practice generally disclosed in U.S. Pat. No. 3,834,981, i.e., by immersion into a bath of strong mineral acid at temperatures of about 25.degree.-320.degree. C. to remove Li.sup.+ ions from the glass surface to a depth of at least 10 microns and preferably 25 microns. Thereafter, the glass article is heat treated to be crystallized in situ to a glass-ceramic containing .beta.-quartz solid solution as the predominant crystal phase. The ion exchange reaction must be carried out on the parent glass article because crazing occurs when the glass-ceramic article is subjected to the H.sup.+ ion for Li.sup.+ ion exchange reaction.
In the second and preferred embodiment of that inventive method, the precursor glass article is first heat treated to be crystallized in situ to a glass-ceramic containing .beta.-quartz solid solution as the predominant crystal phase. Thereafter, the glass-ceramic article is subjected to a K.sup.+ ion for Li.sup.+ ion exchange reaction by contact with a source of K.sup.+ ions (customarily a bath of a molten potassium salt) at temperatures between about 400.degree.-800.degree. C. for a period of time sufficient to cause the replacement of Li.sup.+ ions in the .beta.-quartz solid solution crystals with K.sup.+ ions to a depth of at least 10 microns and preferably 25 microns into the surface of the article. A bath of molten KNO.sub.3 is the suggested source of K.sup.+ ions at temperatures of 400.degree.-600.degree. C. and the eutectic 52% KCl-48% K.sub.2 SO.sub.4 (by weight) as the source at 700.degree.-800.degree. C. The ion exchange must be carried out on the glass-ceramic because, when employed on the precursor glass and the glass then heat treated to be crystallized in situ, crazing always occurs.
Accordingly, where a colored window or other transparent element of a coal or wood burning stove is the desired product, either of the two method embodiments of Ser. No. 451,282 may be applied. For example:
(a) the glass article of the present inventive compositions may be subjected to a H.sup.+ for Li.sup.+ ion exchange via immersion into a bath of a strong mineral acid operating at about 25.degree.-320.degree. C. and thereafter crystallized in situ at about 750.degree.-950.degree. C., or
(b) the glass-ceramic article of the present inventive compositions may be subjected to a K.sup.+ for Li.sup.+ ion exchange via contact with a source of K.sup.+ ions about 400.degree.-800.degree. C., the source customarily consisting of a bath of a molten potassium salt.
Glass-ceramic articles containing .beta.-spodumene solid solution as the predominant crystal phase can also be made resistant to the fumes encountered in coal and wood burning stoves utilizing either of the two embodiments of the method disclosed in Ser. No. 451,282. Should such a product be desired, the precursor glass will be crystallized in situ at temperatures between 950.degree.-1150.degree. C., instead of the 750.degree.-950.degree. C. required in the crystallization of .beta.-quartz solid solution.
RELATED APPLICATIONS
Ser. No. 451,282 filed concurrently to Ser. No. 451,284 by me under the title Transparent Glass-Ceramic Especially Suitable for Use as Stove Windows.
Ser. No. 451,283 filed concurrently to Ser. No. 451,284 by me under the title Transparent Colorless Glass-Ceramics Especially Suitable for Use as Stove Windows.
PRIOR ART
U.S. Pat. No. 3,788,865 described colored, transparent glass-ceramic articles containing .beta.-eucryptite or .beta.-spodumene as the predominant crystal phase prepared from precursor glasses having compositions consisting essentially, in weight percent, of:
______________________________________SiO.sub.2 50-75 ZrO.sub.2 + TiO.sub.2 + SnO.sub.2 Not over 10Al.sub.2 O.sub.3 16-35 Alkaline Earth Oxides 0-4.5Li.sub.2 O 3-5.5 SiO.sub.2 + Al.sub.2 O.sub.3 75-92B.sub.2 O.sub.3 0-9 ZnO 0-4ZrO.sub.2 0-5 Na.sub.2 O 0-2TiO.sub.2 0-10 F.sub.2 0-0.2SnO.sub.2 0-5 Colorants 0.005-2P.sub.2 O.sub.5 0-3______________________________________
The colorants included V.sub.2 O.sub.5, MnO, Cr.sub.2 O.sub.3, Fe.sub.2 O.sub.3, CuO, NiO, CuO, and ZnS.
As can be observed, TiO.sub.2 and Fe.sub.2 O.sub.3 are merely optional components and no mention is made of a reaction taking place between those two components and with at least two members of the group CaO, CeO.sub.2, NiO, SnO.sub.2, V.sub.2 O.sub.5, and WO.sub.3. Yet, that reaction comprises the nub of the instant invention. Furthermore, the patent has no description of the facility of As.sub.2 O.sub.3 for enhancing the intensity of the colors developed.
U.S. Pat. No. 3,907,577 disclosed optionally-colored, translucent or opaque glass bodies having a surface compression layer produced via the in situ growth of .beta.-spodumene and/or h-quartz crystals during a heat treatment of the glass bodies. Compositions for the glasses consisted essentially, in weight percent, of:
______________________________________SiO.sub.2 52-70 MgO 0-5Al.sub.2 O.sub.3 10-25 ZnO 0-7B.sub.2 O.sub.3 0-8 CaO 0-10P.sub.2 O.sub.5 0-10 BaO 0-12Li.sub.2 O 1-4 TiO.sub.2 0-1.2Na.sub.2 O 0-8 ZrO.sub.2 0-2.5K.sub.2 O 0-10 Fe.sub.2 O.sub.3 and/or NiO 0-10 and/or CoO and/or Cr.sub.2 O.sub.3______________________________________
The patent has no discussion of the necessary reaction between TiO.sub.2 and Fe.sub.2 O.sub.3 with at least two members of the group CaO, CeO.sub.2, NiO, SnO.sub.2, V.sub.2 O.sub.5, and WO.sub.3. As a matter of fact, the TiO.sub.2 content of the patented glasses is less than one-half of the minimum TiO.sub.2 level demanded in the instant invention. The patent does not even suggest the capability of As.sub.2 O.sub.3 for augmenting the intensity of the colors produced.
U.S. Pat. No. 3,962,514 was concerned with the formation of glass-ceramic bodies containing .beta.-quartz and/or .beta.-spodumene solid solutions as the predominant crystal phase and having an integral, colored surface layer of transition metal spinel crystals. The precursor glass bodies consisted essentially, in weight percent, of:
______________________________________SiO.sub.2 55-80 Transition Metal Oxides 0.1-10Al.sub.2 O.sub.3 14-35 TiO.sub.2 + ZrO.sub.2 3-13Li.sub.2 O 0-5 ZrO.sub.2 0-10TiO.sub.2 0-7 F 0-3______________________________________
The transition metal oxides included 0-5% MnO.sub.2, 0-5% Fe.sub.2 O.sub.3, 0-3%, CoO, 0-2% CuO, 0-2% Cr.sub.2 O.sub.3, 0-3% V.sub.2 O.sub.5, and 0-10% NiO.
There is no indication of any reaction taking place between TiO.sub.2 and Fe.sub.2 O.sub.3 with at least two members of the group CaO, CeO.sub.2, NiO, SnO.sub.2, V.sub.2 O.sub.5, and WO.sub.3 ; and there is no reference made to the operability of As.sub.2 O.sub.3 for intensifying the colors produced.
U.S. Pat. No. 4,007,048 was directed to preparing dark red, transparent glass-ceramic bodies containing h-quartz and/or h-spodumene solid solution as the predominant crystal phase and consisting essentially, in weight percent of:
______________________________________SiO.sub.2 64.00 .+-. 0.30 ZnO 1.50 .+-. 0.50Al.sub.2 O.sub.3 21.30 .+-. 0.20 TiO.sub.2 2.30 .+-. 0.10Li.sub.2 O 3.50 .+-. 0.15 ZrO.sub.2 1.60 .+-. 0.10Na.sub.2 O 0.60 .+-. 0.15 MnO.sub.2 0.65 .+-. 0.15K.sub.2 O 0.50 .+-. 0.10 Fe.sub.2 O.sub.3 0.23 .+-. 0.03BaO 2.50 .+-. 0.50 CoO 0.37 .+-. 0.05CaO 0.20 .+-. 0.20 NiO 0.06 .+-. 0.02MgO 0.10 .+-. 0.10 Sb.sub.2 O.sub.3 0.85 .+-. 0.15______________________________________
Not only is the TiO.sub.2 content below the minimum required in the instant invention, but also there is no statement of a reaction occurring between TiO.sub.2 and Fe.sub.2 O.sub.3 with at least two members of the group CaO, CeO.sub.2, NiO, SnO.sub.2, V.sub.2 O.sub.5, and WO.sub.3. Nor is there even an allusion to the efficacy of As.sub.2 O.sub.3 for improving the colors generated.
U.S. Pat. No. 4,042,362 was directed to a two-step process for very rapidly converting molten glass into a glass-ceramic body. Whereas the process is not limited to specified compositions, several of the working examples produced glass-ceramic bodies containing .beta.-quartz and/or .beta.-spodumene solid solution as the predominant crystal phase. Colored articles are nowhere referred to and in those examples Fe.sub.2 O.sub.3 is merely an optional ingredient. There is no discussion of any reaction taking place between TiO.sub.2 and Fe.sub.2 O.sub.3 with at least two members of the group CaO, CeO.sub.2, NiO, SnO.sub.2, V.sub.2 O.sub.5, and WO.sub.3, nor any account of the effectiveness of As.sub.2 O.sub.3 in increasing the intensity of the colors developed.
U.S. Pat. No. 4,084,974 was drawn to the preparation of light absorbing glass-ceramic bodies manifesting a blue-to-black coloration and containing .beta.-quartz and .beta.-spodumene solid solution as the predominant crystal phase from base compositions in the Li.sub.2 O-Al.sub.2 O.sub.3 -SiO.sub.2 system nucleated with TiO.sub.2. Fe.sub.2 O.sub.3 is nowhere mentioned so, self-evidently, there was no suggestion of a reaction occurring between TiO.sub.2 and Fe.sub.2 O.sub.3 with at least two members of the group CaO, CeO.sub.2, NiO, SnO.sub.2, V.sub.2 O.sub.5, and WO.sub.3. As.sub.2 O.sub.3 appears in the working examples but there is no statement of its utility in enhancing color intensity.
U.S. Pat. No. 4,211,820 disclosed transparent glass-ceramic articles exhibiting a warm brown coloration and containing .beta.-quartz solid solution as the predominant crystal phase with, optionally, a minor amount of .beta.-spodumene solid solution. The compositions therefor consisted essentially, in weight percent, of:
______________________________________Li.sub.2 O 2.5-4.5 SiO.sub.2 66.5-68MgO 1-2 TiO.sub.2 4-5ZnO 1-2 V.sub.2 O.sub.5 0.02-0.2Al.sub.2 O.sub.3 19.5-21______________________________________
V.sub.2 O.sub.5 was stated to impart the desired color.
Fe.sub.2 O.sub.3 was not intentionally included in the composition but is merely present as an impurity in several of the working examples. There is no discussion of any reaction taking place between TiO.sub.2 and Fe.sub.2 O.sub.3 with at least two members of the group CaO, CeO.sub.2, NiO, SnO.sub.2, V.sub.2 O.sub.5, and WO.sub.3 to yield a wide spectrum of colors. The patented products exhibited a brown coloration only. MgO is a required component of the patented compositions whereas, because of its adverse effect upon the coloration of the instant inventive products, its essential absence is greatly preferred. As.sub.2 O.sub.5 is referred to only as a fining agent; there is no indication of its faculty for enhancing the intensity of a color produced.

DESCRIPTION OF PREFERRED EMBODIMENTS
Table I records a group of exemplary compositions, expressed in terms of parts by weight on the oxide basis, illustrating the compositional parameters of the inventive products. Because the sum of the individual components totals or closely approximates 100, for all practical purposes the values reported may be deemed to represent weight percent. The actual ingredients employed in preparing the batch may comprise materials, either the oxides or other compounds which, when melted together, will be converted into the desired oxide in the proper proportions.
The batch ingredients were compounded, ballmilled together to aid in obtaining a homogeneous melt, the batches deposited into platinum crucibles, lids placed upon the crucibles, and the crucibles introduced into a furnace operating at about 1550.degree.-1600.degree. C. The batches were melted for about 16 hours with stirring, canes having a diameter of about 0.25" were hand-drawn from each melt and the remainder of each melt poured into a steel mold to form a glass slab having dimensions of about 6".times.6".times.0.5". The slabs were transferred immediately to an annealer operating at about 650.degree.-700.degree. C.
As.sub.2 O.sub.3 is present to perform its customary function of a fining agent as well as to promote the development of more intense colors.
TABLE I______________________________________ 1 2 3 4 5 6 7 8 9______________________________________SiO.sub.2 67.1 67.3 66.0 67.6 67.4 66.3 68.8 68.4 66.8Al.sub.2 O.sub.3 20.0 20.0 20.0 20.0 20.0 21.0 19.0 19.0 19.0Li.sub.2 O 3.8 3.8 3.5 3.8 4.0 3.6 3.8 4.0 3.8Na.sub.2 O 0.3 0.3 0.4 0.3 0.3 0.1 0.3 0.3 0.3K.sub.2 O 0.5 0.5 0.6 0.3 0.3 0.1 0.3 0.3 0.3ZnO 0.8 0.8 0.8 0.8 0.8 1.2 0.8 0.8 1.2BaO 0.8 0.8 0.8 1.0 0.8 2.5 1.0 0.8 2.5TiO.sub.2 3.2 3.4 4.6 3.4 3.4 3.0 3.4 3.4 3.3ZrO.sub.2 1.6 1.6 1.6 1.6 1.6 1.6 1.6 1.6 1.6As.sub.2 O.sub.3 0.6 0.6 0.6 0.6 0.6 0.4 0.6 0.6 0.6Fe.sub.2 O.sub.3 0.15 0.15 0.15 0.15 0.1 0.15 0.15 0.1 0.15V.sub.2 O.sub.5 0.2 0.2 0.2 0.2 0.2 0.2 0.2 0.2 0.2CeO.sub.2 1.0 0.3 0.8 0.2 0.3 0.1 -- 0.3 --CaO -- 0.3 -- 0.1 0.3 0.3 -- 0.3 --SnO.sub.2 -- -- -- -- -- -- 0.1 -- 0.1______________________________________ 10 11 12 13 14 15 16 17 18______________________________________SiO.sub.2 67.4 67.1 68.1 63.9 64.6 66.4 66.4 67.3 66.1Al.sub.2 O.sub.3 19.0 19.0 18.0 20.0 20.0 19.0 19.0 19.0 19.0Li.sub.2 O 3.0 3.5 3.5 3.5 3.5 3.8 3.8 3.8 3.5Na.sub.2 O 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3K.sub.2 O 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3ZnO 1.2 1.2 1.2 2.0 1.2 1.2 1.2 1.2 2.0BaO 2.5 2.5 2.5 2.5 4.0 2.5 2.5 2.5 2.5TiO.sub.2 3.3 3.3 3.3 3.3 3.3 3.3 3.3 3.3 3.3ZrO.sub.2 1.6 1.6 1.6 1.6 1.6 1.6 1.6 1.6 1.6As.sub.2 O.sub.3 0.8 0.8 0.8 0.8 0.8 0.8 0.8 0.8 0.8Fe.sub.2 O.sub.3 0.15 0.15 0.15 0.15 0.15 0.15 0.06 0.15 0.15V.sub.2 O.sub.5 0.2 0.2 0.2 0.2 0.2 0.2 0.2 0.2 0.2CeO.sub.2 0.2 -- -- 0.2 -- 0.2 -- -- 0.2CaO 0.1 -- -- 0.1 -- 0.1 -- -- 0.1SnO.sub.2 -- 0.1 0.1 -- 0.1 -- 0.1 0.1 --______________________________________ 19 20 21 22 23 24 25 26______________________________________SiO.sub.2 66.0 66.9 64.9 64.3 65.3 66.0 66.0 67.2Al.sub.2 O.sub.3 19.0 19.0 20.0 20.0 20.0 20.0 20.0 20.0Li.sub.2 O 3.5 3.5 3.5 3.5 3.5 3.5 3.5 3.5Na.sub.2 O 0.3 0.3 0.4 0.4 0.4 0.4 0.3 0.4K.sub.2 O 0.3 0.3 0.6 0.6 0.6 0.6 0.4 0.6ZnO 2.0 1.2 0.8 0.8 0.8 0.8 0.8 0.8BaO 2.5 2.5 0.8 0.8 0.8 0.8 0.8 0.8TiO.sub.2 3.3 3.3 4.6 4.6 4.6 4.6 5.0 2.8ZrO.sub.2 1.6 1.6 1.6 1.6 1.6 1.6 1.6 1.6As.sub.2 O.sub.3 0.8 0.8 0.6 0.6 0.6 0.6 0.6 0.6Fe.sub.2 O.sub.3 0.15 0.15 0.15 0.15 0.15 0.15 0.1 0.1V.sub.2 O.sub.5 0.2 0.2 0.1 0.1 0.1 0.2 0.1 --CeO.sub.2 -- 0.2 2.0 2.0 1.6 0.8 -- --CaO -- -- -- 0.6 -- -- -- --SnO.sub.2 0.1 -- -- -- -- -- 0.8 --NiO -- -- -- -- -- -- -- 0.8WO.sub.3 -- -- -- -- -- -- -- 0.8______________________________________
TABLE II recites the heat treatment schedules applied to the specimens of TABLE I in an electrically-heated furnace, a visual description of the crystallized glass-ceramic body, the predominant crystal phase present as identified through X-ray diffraction analysis, and the coefficient of thermal expansion (25.degree.-700.degree. C.) of the glass-ceramic body, where determined, utilizing measuring techniques conventional in the art. In each instance, the parent glass was heated to the first temperature level at about 100.degree. C./hour, held at the first level to induce nucleation, the temperature raised to the second level at about 100.degree. C./hour, held thereat to grow crystals on the nuclei, and then the crystallized body cooled to room temperature at furnace rate.
TABLE II______________________________________Ex- Heat Coef. Exp.am- Treatment Visual Crystal (.times. 10.sup.-7 /ple (.degree.C.) Appearance Phase .degree.C.)______________________________________1 780 for 1 hr. Glossy, .beta.-Quartz -3 900 for 1 hr. black, Solid transparent Solution1 780 for 1 hr. Glossy, .beta.-Spodumene -- 1100 for 1 hr. gray, Solid opaque Solution2 780 for 1 hr. Glossy, .beta.-Quartz -1.9 900 for 1 hr. black, Solid translucent Solution2 780 for 1 hr. Glossy, .beta.-Spodumene 10.5 1100 for 1 hr. brown-beige, Solid opaque Solution3 780 for 1 hr. Brown- .beta.-Quartz -1.5 900 for 1 hr. black, Solid translucent Solution3 780 for 1 hr. Glossy, .beta.-Spodumene 13.3 1100 for 1 hr. gray-beige, Solid opaque Solution4 780 for 1 hr. Black, .beta.-Quartz -4.9 900 for 1 hr. transparent Solid Solution4 780 for 1 hr. Glossy, .beta.-Spodumene 9.8 1100 for 1 hr. gray-beige, Solid opaque Solution5 780 for 1 hr. Black, .beta.-Quartz -6.8 900 for 1 hr. transparent Solid Solution5 780 for 1 hr. Glossy, .beta.-Spodumene 8.9 1100 for 1 hr. gray-beige, Solid opaque Solution6 780 for 1 hr. Black, .beta.-Quartz -5.1 900 for 1 hr. translucent Solid Solution6 780 for 1 hr. Glossy, .beta.-Spodumene 10.0 1100 for 1 hr. gray-beige, Solid opaque Solution7 780 for 1 hr. Black, .beta.-Quartz -4.0 900 for 1 hr. translucent Solid Solution7 780 for 1 hr. Glossy, .beta.-Spodumene 10.3 1100 for 1 hr. gray-beige, Solid opaque Solution8 780 for 1 hr. Black, .beta.-Quartz -5.3 900 for 1 hr. translucent Solid Solution8 780 for 1 hr. Glossy, .beta.-Spodumene 9.1 1100 for 1 hr. gray-beige, Solid opaque Solution9 780 for 1 hr. Black, .beta.-Quartz -3.0 900 for 1 hr. translucent Solid Solution9 780 for 1 hr. Glossy, .beta.-Spodumene 11.0 1100 for 1 hr. almond- Solid beige, Solution opaque10 780 for 1 hr. Black, .beta.-Quartz 3.3 900 for 1 hr. translucent Solid Solution10 780 for 1 hr. Glossy .beta.-Spodumene 15.2 1100 for 1 hr. gray, Solid opaque Solution11 780 for 1 hr. Black, .beta.-Quartz 0.7 900 for 1 hr. translucent Solid Solution11 780 for 1 hr. Glossy, .beta.-Spodumene 14.3 1100 for 1 hr. yellow- Solid almond, Solution opaque12 780 for 1 hr. Black, .beta.-Quartz -2.7 900 for 1 hr. translucent Solid Solution12 780 for 1 hr. Glossy, .beta.-Spodumene 9.7 1100 for 1 hr. almond, Solid opaque Solution13 780 for 1 hr. Black, .beta.-Quartz -1.9 900 for 1 hr. translucent Solid Solution13 780 for 1 hr. Glossy, .beta.-Spodumene -- 1100 for 1 hr. gray-beige, Solid opaque Solution14 780 for 1 hr. Black, .beta. -Quartz 1.4 900 for 1 hr. translucent Solid Solution14 780 for 1 hr. Glossy, .beta.-Spodumene 15.5 1100 for 1 hr. beige, Solid opaque Solution15 780 for 1 hr. Black, .beta.-Quartz -1.6 900 for 1 hr. translucent Solid Solution15 780 for 1 hr. Glossy, .beta.-Spodumene 12.8 1100 for 1 hr. almond, Solid opaque Solution16 780 for 1 hr. Black, .beta.-Quartz -1.2 900 for 1 hr. translucent Solid Solution16 780 for 1 hr. Glossy, .beta.-Spodumene 4.8 1100 for 1 hr. gray, Solid opaque Solution17 780 for 1 hr. Black, .beta.-Quartz -2.5 900 for 1 hr. translucent Solid Solution17 780 for 1 hr. Glossy, .beta.-Spodumene 11.9 1100 for 1 hr. gray-beige, Solid opaque Solution18 780 for 1 hr. Black, .beta.-Quartz -1.1 900 for 1 hr. translucent Solid Solution18 780 for 1 hr. Glossy, .beta.-Spodumene 13.5 1100 for 1 hr. almond, Solid opaque Solution19 780 for 1 hr. Black, .beta.-Quartz -2.8 900 for 1 hr. translucent Solid Solution19 780 for 1 hr. Glossy, .beta.-Spodumene 11.9 1100 for 1 hr. gray-beige, Solid opaque Solution20 780 for 1 hr. Black, .beta.-Quartz -2.4 900 for 1 hr. translucent Solid Solution20 780 for 1 hr. Glossy, .beta.-Spodumene 11.0 1100 for 1 hr. almond, Solid opaque Solution21 780 for 1 hr. Black- .beta.-Quartz 0.9 900 for 1 hr. brown, Solid translucent Solution21 780 for 1 hr. Glossy, .beta.-Spodumene 11.7 1100 for 1 hr. beige, Solid opaque Solution22 780 for 1 hr. Black- .beta.-Quartz -- 900 for 1 hr. brown, Solid translucent Solution22 780 for 1 hr. Glossy, .beta.-Spodumene -- 1100 for 1 hr. yellow, Solid opaque Solution23 780 for 1 hr. Black-brown, .beta.-Quartz -- 900 for 1 hr. translucent Solid Solution23 780 for 1 hr. Glossy, .beta. -Spodumene -- 1100 for 1 hr. beige, Solid opaque Solution24 780 for 1 hr. Black- .beta.-Quartz -1.5 900 for 1 hr. brown, Solid translucent Solution24 780 for 1 hr. Glossy, .beta.-Spodumene 13.3 1100 for 1 hr. gray-beige, Solid opaque Solution25 780 for 1 hr. Black, .beta.-Quartz -0.5 900 for 1 hr. opaque Solid Solution25 780 for 1 hr. Glossy, .beta.-Spodumene 12.8 1100 for 1 hr. blue, Solid opaque Solution26 780 for 1 hr. Ruby, .beta.-Quartz -- 900 for 1 hr. transparent Solid Solution26 780 for 1 hr. Glossy, .beta.-Spodumene 10.4 1100 for 1 hr. light blue, Solid opaque Solution______________________________________
TABLE III records a summary of the general trends in colors and optical transmissions produced in the inventive glass-ceramic bodies as a function of compositional variations. It must be emphasized that the descriptions provided represent trends only and assume precursor glasses having base compositions within the above-cited regimes. As reported, "higher" values reflect amounts of a component at the higher end of the operable range thereof and "lower" values the other extreme of the range. The "lower" values of the "color package" ingredients V.sub.2 O.sub.5, CeO.sub.2 CaO, and SnO.sub.2 signify the virtual absence thereof.
TABLE III______________________________________ Beta-Quartz Beta-SpodumeneComponent Solid Solution Solid Solution______________________________________High Al.sub.2 O.sub.3 Haze develops Greater gray color, thermal expansion risesLow Al.sub.2 O.sub.3 Translucency develops, Greater yellow- blacker color beige colorHigh Li.sub.2 O Blacker color, opacity Greater gray develops colorLow Li.sub.2 O Greater transparency, Greater yellow browner color colorHigh ZnO Blacker color, opacity Greater beige develops colorLow ZnO Browner color, greater Greater gray transparency colorHigh BaO Blacker color, opacity Greater beige develops colorLow BaO Greater transparency, Greater grayer browner color colorHigh TiO.sub.2 Blacker color, opacity Greater beige develops color, thermal expansion risesLow TiO.sub.2 Greater transparency, Greater gray browner color colorHigh ZrO.sub.2 Browner color Greater beige colorLow ZrO.sub.2 Greater gray color Greater gray color, satin surface developsHigh As.sub.2 O.sub.3 Blacker color, opacity Greater beige develops colorLow As.sub.2 O.sub.3 Greater transparency, Greater gray greater amber color colorHigh Na.sub.2 O Slightly greater brown Slightly greater color beige colorLow Na.sub.2 O Slightly greater black Slightly greater color gray colorHigh K.sub.2 O Slightly greater brown Slightly greater color beige colorLow K.sub.2 O Slightly greater black Slightly greater color gray colorHigh Fe.sub.2 O.sub.3 Blacker color, Greater beige translucency develops colorLow Fe.sub.2 O.sub.3 Greater transparency, Greater gray browner color color, thermal expansion fallsHigh V.sub.2 O.sub.5 Blacker color, Greater black- translucency develops gray colorLow V.sub.2 O.sub.5 Greater transparency, Greater beige browner color colorHigh CeO.sub.2 Blacker color, Greater beige translucency develops colorLow CeO.sub.2 Greater transparency, Greater gray browner color colorHigh CaO Blacker color, Greater beige- translucency develops yellow colorLow CaO Greater transparency, Greater gray browner color colorHigh SnO.sub.2 Blacker color, Greater gray translucency develops colorLow SnO.sub.2 Greater transparency, Greater beige brown color color______________________________________

Number	Name	Date
3788865	Babcock et al.	Jan 1974
3907577	Kiefer et al.	Sep 1975
3962514	Rittler	Jun 1976
4007048	Sack et al.	Feb 1977
4042362	MacDowell	Aug 1977
4084974	Beall et al.	Apr 1978
4211820	Cantaloupe et al.	Jul 1980

Colored transparent, translucent and opaque glass-ceramics

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Continuation in Parts (1)