CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation application and claims the benefit of priority under 35 U.S.C. § 120 of U.S. Non-Provisional patent application Ser. No. 16/970,187, filed on Aug. 14, 2020, which claims the benefit of priority under 35 U.S.C. § 371 to International Application Serial No. PCT/US2019/016687, filed on Feb. 5, 2019, which claims the benefit of priority under 35 U.S.C. § 119 to U.S. Provisional Application Ser. No. 62/630,449, filed on Feb. 14, 2018, the contents of which are relied upon and incorporated herein by reference in their entirety as if fully set forth below.

The entire disclosure of each publication or patent document mentioned herein is incorporated by reference.

BACKGROUND

The disclosure relates to transparent tantalum oxide glass-ceramics and transparent aluminum tantalate glass-ceramics.

SUMMARY

In embodiments, the disclosure provides a transparent tantalum oxide containing glass-ceramic, or a transparent aluminum tantalate containing glass-ceramic.

In embodiments, the disclosure provides a transparent glass-ceramic containing tantalum oxide or aluminum tantalate, and additionally including a metal or metal oxide supplement or complement such as Nb, Ti, or W, and more specifically a metal oxide supplement such as Nb₂O₅, TiO₂or WO₃.

In embodiments, the disclosure provides a transparent glass-ceramic containing tantalum oxide or aluminum tantalate, and additionally including a metal or metalloid supplement or complement such as B or B₂O₃while maintaining or reducing the other glass constituents such as the Si content.

In embodiments, the disclosure provides a transparent glass-ceramic containing tantalum oxide or aluminum tantalate, and additionally including a metal or metalloid supplement or complement such as Ga or Ga₂O₃while maintaining or reducing the other glass constituents such as the Al content.

In embodiments, the disclosure provides a transparent glass-ceramic containing tantalum oxide or aluminum tantalate, and additionally including a performance enhancing dopant.

In embodiments, the disclosure provides a method of making a transparent glass-ceramic from certain Ta-containing aluminophosphosilicate glasses.

In embodiments, the disclosure provides a method of making a transparent glass-ceramic having a major crystalline phase of either Al-containing Ta₂O₅when cerammed at low temperatures, or AlTaO₄when cerammed at high temperature.

BRIEF DESCRIPTION OF THE DRAWINGS

In embodiments of the disclosure:

FIGS. 1A and 1B show different X-ray diffraction patterns of the same source composition 9Ta₂O₅:15 Al₂O₃:6P₂O₅:70SiO₂that was separately cerammed under different conditions of: 925° C. for 2 hrs (FIG. 1A); and 1075° C. for 2 hrs (FIG. 1B).

FIG. 2 shows a ²⁷Al MAS NMR spectrum of glass 1 (Example 4 in Table 1), cerammed at 950° C. for 2 hrs.

FIGS. 3A and 3B show TEM photomicrograph images of glass 1 (Example 4 in Table 1).

FIG. 4 shows dependence of Young's modulus (E) versus the ceram temperature for a composition of the formula: 9Ta₂O₅:15Al₂O₃:6P₂O₅:70SiO₂of Example 4 in Table 1.

FIG. 5 shows hardness (H) versus the ceram temperature for a composition of the formula: 9Ta₂O₅:15Al₂O₃:6P₂O₅:70SiO₂of Example 4 in Table 1.

FIG. 6 shows the refractive index (nD or nD) versus the ceram temperature for a composition of the formula: 9Ta₂O₅:15Al₂O₃:6P₂O₅:70SiO₂of Example 4. in Table 1

FIGS. 7A and 7B show the ³¹P MAS NMR spectra and the ²⁷Al MAS NMR spectra, respectively, for the precursor glass of Example 1 in Table 1.

FIGS. 8A and 8B show the ³¹P MAS NMR and ²⁷Al MAS NMR, respectively, for the cerammed glass of Example 1 in Table 1.

FIGS. 9A and 9B show the ³¹P MAS NMR and the ²⁷Al MAS NMR spectra, respectively, of Example 4 in Table 1 after a ceramming treatment defined as Schedule 1 (“925/2”).

FIGS. 10A and 10B show the ³¹P MAS NMR and the ²⁷Al MAS NMR spectra, respectively, of Example 4 in Table 1 after a ceramming treatment defined as Schedule 3 (“1075/2” only).

FIGS. 11A and 11B show the effect of increasing the ceramming temperature on phase assemblage in the disclosed method of making.

DETAILED DESCRIPTION

Various embodiments of the disclosure will be described in detail with reference to drawings, if any. Reference to various embodiments does not limit the scope of the invention, which is limited only by the scope of the claims attached hereto. Additionally, any examples set forth in this specification are not limiting and merely set forth some of the many possible embodiments of the claimed invention.

In embodiments, the disclosed compositions, and methods of making and using provide one or more advantageous features or aspects, including for example as discussed below. Features or aspects recited in any of the claims are generally applicable to all facets of the invention. Any recited single or multiple feature or aspect in any one claim can be combined or permuted with any other recited feature or aspect in any other claim or claims.

Definitions

“Ta₂O₅” has two different but related meanings in the present disclosure. In batch or source ingredient circumstances “Ta₂O₅” refers to a source of Ta₂O₅. In cerammed transparent glass-ceramic composition circumstances “Ta₂O₅” refers to Ta_2-xAl_xO_5-xwhere x is significantly less than 1, as defined herein.

“Include,” “includes,” or like terms means encompassing but not limited to, that is, inclusive and not exclusive.

“About” modifying, for example, the quantity of an ingredient in a composition, concentrations, volumes, process temperature, process time, yields, flow rates, pressures, viscosities, and like values, and ranges thereof, or a dimension of a component, and like values, and ranges thereof, employed in describing the embodiments of the disclosure, refers to variation in the numerical quantity that can occur, for example: through typical measuring and handling procedures used for preparing materials, compositions, composites, concentrates, component parts, articles of manufacture, or use formulations; through inadvertent error in these procedures; through differences in the manufacture, source, or purity of starting materials or ingredients used to carry out the methods; and like considerations. The term “about” also encompasses amounts that differ due to aging of a composition or formulation with a particular initial concentration or mixture, and amounts that differ due to mixing or processing a composition or formulation with a particular initial concentration or mixture.

“Optional” or “optionally” means that the subsequently described event or circumstance can or cannot occur, and that the description can include instances where the event or circumstance occurs and instances where it does not.

The indefinite article “a” or “an” and its corresponding definite article “the” as used herein means at least one, or one or more, unless specified otherwise.

Abbreviations, which are well known to one of ordinary skill in the art, may be used (e.g., “h” or “hrs” for hour or hours, “g” or “gm” for gram(s), “mL” for milliliters, and “rt” for room temperature, “nm” for nanometers, and like abbreviations).

Specific and preferred values disclosed for components, ingredients, additives, dimensions, conditions, times, and like aspects, and ranges thereof, are for illustration only; they do not exclude other defined values or other values within defined ranges. The composition and methods of the disclosure can include any value or any combination of the values, specific values, more specific values, and preferred values described herein, including explicit or implicit intermediate values and ranges.

Glass-ceramics are well known as materials that provide the excellent properties of polycrystalline ceramics and the possibility of zero porosity and the ability to make complex shapes via traditional glass forming techniques. However, most glass-ceramics are opaque due to the difficulty of: maintaining the size of the crystallite population below visible light wavelengths; minimizing the refractive index contrast between the dominant crystal phase and residual glass; or both. Some transparent glass-ceramic “families” are known, notably the β-quartz and petalite glass-ceramics from the Li aluminosilicate system and the mullite glass-ceramics from the aluminosilicate system, but they are relatively rare. Even rarer are transparent glass-ceramics where the major crystalline phase is a non-silicate, with the only major example being the spinel glass-ceramics from the Zn/Mg aluminosilicate system. Such materials are of particular interest for scratch-resistant cover glass applications, fluorescence applications when doped with optically-active transition metal or rare earth ions, and like applications. Other unknown transparent glass-ceramic systems having a non-silicate major phase are of interest.

U.S. Pat. No. 7,323,426, entitled HIGH STRAIN POINT GLASSES, mentions a family of glasses from the SiO₂—Al₂O₃—P₂O₅ternary system exhibiting high strain point, transparency, and low coefficients of thermal expansion. The glasses have the following composition, expressed in mol percent and calculated from the glass batch on an oxide basis: 55 to 80% SiO₂, 12 to 30% Al₂O₃, and 2 to 15% P₂O₅.

In embodiments, the disclosure provides a transparent glass-ceramic composition (i.e., the Si—Al—Ta—P transparent glass-ceramic compositions) comprising:

- 65 to 75% SiO₂;
- 10 to 25% Al₂O₃;
- 5 to 15% Ta₂O₅; and
- 3 to 10% P₂O₅, based on 100 mol % total.

In embodiments, the disclosure provides a transparent glass-ceramic composition comprising, for example, 70% SiO₂, 14.5% Al₂O₃, 7.5% P₂O₅, and 8% Ta₂O₅based on 100 mol % total.

In embodiments, the glass-ceramic composition can further comprise, for example, SnO₂in from 0.01 to 2 mol %, by inclusion in the total 100 mol % (i.e., not super addition).

In embodiments, the Ta₂O₅content in the transparent glass-ceramic composition can be, for example, of from 5 to 14 mol %, or of from 8 to 12 mol %, including intermediate values and ranges.

In embodiments, the transparency (i.e. allowing passage of light, e.g., some or most wavelengths in visible spectrum, about 390 to 700 nm) of the composition can be demonstrated when, for example, the composition is cast as a one half inch thick specimen and is generally visibly clear to, for example, a human viewer or other trained observer.

In embodiments, the disclosed transparent composition has a refractive index that can be, for example, of from 1.55 to 1.61; the elastic modulus can be, for example, of from 50 to 95 GPa; and the hardness can be, for example, of from 6 to 9 GPa.

In embodiments, the disclosed transparent composition can have a crystallite size, for example, of from 5 to 25 nm, including intermediate values and ranges.

In embodiments, the disclosure provides transparent glass-ceramic compositions having a portion such as from 0.1 to 50 mol % of the Ta content of the above mentioned Si—Al—Ta—P transparent glass-ceramic compositions supplemented (i.e., partially substituted or replaced) or complemented (i.e., an ingredient that completes the composition) with, for example, Nb, Ti, or W, to produce Si—Al—Ta—P—Nb transparent glass-ceramic compositions, Si—Al—Ta—P—Ti transparent glass-ceramic compositions, or Si—Al—Ta—P—W transparent glass-ceramic compositions.

In embodiments, the disclosure provides a metal supplemented transparent glass-ceramic composition comprising, for example:

- 65 to 75% SiO₂;
- 10 to 25% Al₂O₃;
- 4 to 7.5% Ta₂O₅;
- 0.01 to 7.5% M_xO_yor M_xM′_xO_y; and
- 3 to 10% P₂O₅, based on 100 mol % total,
  
  wherein in the formulas M_xO_yor M_xM′_xO_y, M or M′ is selected from the group of a source of Nb, Ti, W, Al, B, Ga, or a mixture thereof, x and x′ are independently an integer from 1 to 2, and y is an integer from 1 to 5. M_xO_ycan be, for example, Nb₂O₅, TiO₂, WO₃, and like oxides. M_xM′_xO_ycan be, for example, Al₂TiO₅, B₂O₃, Ga₂O₃, and like oxides, which metal oxide or metalloid oxide can provide a primary or supplemental source of TiO₂, Al₂O₃, or like oxides. In embodiments, the M_xO_ycan have, for example, a formal valence of 4⁺, 5⁺, or 6⁺.

In embodiments, a transparent glass-ceramic composition can have a metal (M) supplement of a Nb source and the Nb can be present in an amount of from 0.1 to 50 mol % of the Ta content, and 4 to 7.5% Ta₂O₅and 0.01 to 7.5% Nb in the composition. The supplementation with Nb produces a Si—Al—Ta—P—Nb transparent glass-ceramic composition.

In embodiments, a transparent glass-ceramic composition can have a metal (M) supplement of a Ti source and the Ti can be present in an amount of from 0.1 to 25 mol % of the Ta content, and 4 to 11.25 mol % Ta₂O₅and 0.01 to 3.75 mol % Ti in the composition. The supplementation with Ti produces a Si—Al—Ta—P—Ti transparent glass-ceramic composition.

In embodiments, a transparent glass-ceramic composition can have a metal (M) supplement of a W source and the W can be present in an amount of from 0.1 to 25 mol % of the Ta content, and 4 to 11.25 mol % Ta₂O₅and 0.01 to 3.75 mol % Win the composition. The supplementation with Ti produces a Si—Al—Ta—P—W transparent glass-ceramic composition.

In embodiments, the disclosed transparent glass-ceramic composition can further comprise, for example, a dopant in an amount of 1 mol % or less, for example, of from 0.01 to 1 mol %, of from 0.1 to 0.9 mol %, of from 0.1 to 0.85 mol %, of from 0.5 to 0.8 mol %, of from 0.5 to 0.75 mol %, including intermediate values and ranges, based on the 100 mol %. The dopant can be selected from the group of, for example, a Cr oxide, a Ni oxide, a Co oxide, a rare earth oxide, or mixtures thereof. Other dopants of interest can include, for example, Ti, V, Mn, Cu, Er, and like oxide dopants, or mixtures thereof.

In embodiments, the oxide dopant can be, for example, selected from Cr₂O₃, NiO, CoO, Er₂O₃, or a mixture thereof.

In embodiments, the resulting transparent glass-ceramic composition preferably contains at least 5 mol % or more of Ta₂O₅, which permits the glass-ceramic composition to be a transparent glass-ceramic product.

In preferred embodiments, the resulting transparent glass-ceramic composition preferably contains at least about 10 mol % Ta₂O₅.

In other more preferred embodiments, the resulting transparent glass-ceramic composition preferably contains at least about 8 mol % Ta₂O₅.

In embodiments, the precursor glass preferably contains at least 3 mol % or more of P₂O₅, which P₂O₅content permits the precursor glass to melt at or below 1650° C., and avoids phase separation and opacity in the resulting transparent glass-ceramic composition.

In embodiments, the disclosure provides a more preferred transparent glass-ceramic composition comprising:

- 65 to 72% SiO₂;
- 10 to 20% Al₂O₃;
- 4 to 9% P₂O₅; and
- 8 to 13% Ta₂O₅, based on 100 mol %.

In embodiments, an example of the more preferred transparent glass-ceramic composition can be, for example:

- 70% SiO₂;
- 14.5% Al₂O₃;
- 7.5% P₂O₅; and
- 8 to 13% Ta₂O₅, based on 100 mol % total.

In embodiments, the composition of the crystalline phase of the more preferred transparent glass-ceramic composition can be, for example: of the formula Ta_2-xAl_xO_5-xwhere x is less than 1 such as x is of from 0.001 to 0.2, 0.01 to 0.15, 0.01 to 0.1, including intermediate values and ranges.

In embodiments, x in the formula Ta_2-3Al_xO_5-xcan be, for example, from about 0.001 to about 0.99 mol %, from about 0.01 to about 0.9 mol %, from about 0.1 to about 0.8 mol %, from about 0.1 to about 0.7 mol %, from about 0.1 to about 0.6 mol %, and from about 0.1 to about 0.5 mol %, including intermediate values and ranges.

In embodiments, the disclosed transparent glass-ceramic composition has a crystallite size of from 5 to 25 nm.

In embodiments, the disclosure provides a boron supplemented or complemented transparent glass-ceramic composition comprising:

- 60 to 70% SiO₂;
- 10 to 25% Al₂O₃;
- 4 to 7.5% Ta₂O₅;
- 0.01 to 5% B₂O₃; and
- 3 to 10% P₂O₅, based on 100 mol % total,

In embodiments, the SiO₂content can be partially supplemented or replaced by, for example, of from 0.01 to 5 mol % B₂O₃.

In embodiments, the disclosure provides a gallium supplemented or complemented transparent glass-ceramic composition comprising:

- 65 to 75% SiO₂;
- 2 to 17% Al₂O₃;
- 4 to 7.5% Ta₂O₅;
- 0.01 to 8% Ga₂O₃; and
- 3 to 10% P₂O₅, based on 100 mol % total,

In embodiments, Al₂O₃can be partially supplemented or replaced by, for example, of from 0.1 to 8 mol % Ga₂O₃. In supplemental amounts of greater than of from 8 mol % Ga₂O₃there may be some objectionable opalization of the precursor glasses and opacity in the resultant glass-ceramics.

In particularly preferred embodiments, the disclosure provides a method of making the aforementioned transparent glass-ceramic composition, comprising, for example:

- ceramming a suitable precursor glass composition at 900 to 950° C. for about 2 hrs, to produce a transparent glass-ceramic of the formula Ta_2-xAl_xO_5-xwhere x in this formula is less than 1.

In embodiments, the method of making the aforementioned transparent glass-ceramic composition, can further comprise, for example, including a dopant in an amount of 1 mol % or less based on the 100 mol % of the suitable precursor glass composition, and the dopant can be selected, for example, from the group of a Cr oxide, a Ni oxide, a Co oxide, a rare earth oxide, or a mixture thereof. Other dopants can include, for example, Ti, V, Mn, Cu, Er, and like dopants, such as their oxides and like sources, or mixtures thereof.

In preferred embodiments, a method of making the aforementioned transparent glass-ceramic composition, can comprise, for example:

- ceramming a suitable precursor glass composition at, for example, of from 1000 to 1100° C. for about 2 hrs, to produce a transparent glass-ceramic of the formula of a mixture of AlTaO₄and AlPO₄(i.e., AT+AP). A suitable precursor glass composition can be, for example, the aforementioned preferred or more preferred transparent glass-ceramic composition.

In embodiments, the method of making any of the preceding transparent glass-ceramic compositions, can further comprise, for example: including a dopant in an amount of 1 mol % or less based on the 100 mol % total of the suitable precursor glass composition, and the dopant can be selected, for example, from the group of a Cr oxide, a Ni oxide, a Co oxide, a rare earth oxide, or mixtures thereof. Other transition metal dopants can include, for example, Cr, Ni, Co, V, Mn, Cu, Er, and like oxide dopants or equivalent metal sources, or mixtures thereof.

When cerammed at low temperatures, the disclosed transparent glass-ceramics are believed to be the first known glass-ceramics, transparent or opaque, which include Al-containing Ta₂O₅as the dominant crystal phase. The transparency of these materials is particularly remarkable and unexpected in view of the large refractive index contrast or difference between the Ta-containing crystalline phases and the silica-rich residual glass.

In embodiments, the present disclosure is advantaged in several aspects, including for example: the presence of Ta in the crystalline phases causes these materials to have a higher refractive index than other transparent glass-ceramics (e.g., spinel: 1.586). Other transparent glass-ceramics can become translucent or opaque when heated above 1000° C. Unexpectedly, the presently disclosed glass-ceramic compositions retain their transparency to at least 1100° C. In addition, the presently disclosed glass-ceramic compositions provide a unique crystalline environment for transition metal dopants and allow one to tailor the luminescent properties of the transparent glass-ceramics. The crystalline environment can provide a host site, for example, for a transition metal dopant or rare earth dopant.

In embodiments, the present disclosure provides a transparent Ta₂O₅glass-ceramic, a transparent AlTaO₄glass-ceramic, a transparent glass-ceramic containing a mixture of Ta₂O₅and AlTaO₄, or a mixture thereof. These disclosed glass-ceramics can be made by, for example, heat treatment of a suitable precursor glass having a composition comprising or consisting of, for example: 5 to 15% Ta₂O₅, 10 to 25% Al₂O₃, 3 to 10% P₂O₅, and 65 to 75% SiO₂based on a 100 mol % total. The precursor glasses, but not glass-ceramics, having these compositions were disclosed in the above-mentioned U.S. Pat. No. 7,323,426.

In the present disclosure when exemplary precursor glasses were individually cerammed at temperatures of from 900 to 950° C., the crystalline phase has the Ta₂O₅structure (FIG. 1A). However, the ²⁷Al MAS NMR spectra of such materials show that this crystalline phase contains some aluminum (Al) in solid solution (FIG. 2) and its composition is better described by the formula Ta_2-xAl_xO_5-x, where x in this formula is less than 1. Maximum transparency of these Ta_2-xAl_xO_5-xglass-ceramics is observed when their glass precursors are cerammed at temperatures in the lower portion of the above-mentioned range, i.e., 900 to 950° C. When heat treated at temperatures above 900 to 950° C. but below 1,000° C., the resulting Ta_2-xAl_xO_5-xglass-ceramics can become slightly hazy. As indicated in the accompanying Table 1 and Table 2, these Ta_2-xAl_xO_5-xglass-ceramics are characterized by an elastic modulus of from 77 to 91 GPa.

When the precursor glasses are cerammed at top temperatures in the range of from about 975 to 1000° C., the crystalline assemblage of the resultant transparent glass-ceramics are a mixture of Ta_2-xAl_xO_5-xand AlTaO₄. While not bound by theory, it is believed that Ta_2-xAl_xO_5-xgradually reacts with residual glass to form AlTaO₄in response to heating in this temperature range. With increasing top temperature, the volume fraction of AlTaO₄increases relative to that of Ta_2-xAl_xO_5-xbased on XRD results.

When the precursor glasses are cerammed at top temperatures in of from about 1025 to 1050° C., the crystalline assemblage of the resultant transparent glass-ceramics are a mixture of Ta_2-xAl_xO_5-x, AlTaO₄, and AlPO₄. With increasing top temperature, the volume fraction of AlTaO₄continues to increase relative to that of Ta_2-xAl_xO_5-xas the reaction between the Ta_2-xAl_xO_5-xphase and residual glass progresses towards completion.

When the precursor glasses are cerammed at top temperatures of from about 1075 to 1100° C., the crystalline assemblage can be, for example, a mixture of AlTaO₄and AlPO₄(FIG. 1B). The transparency of these AlTaO₄glass-ceramics is comparable to the transparency of the Ta_2-xAl_xO_5-xglass-ceramics cerammed at 900 to 925° C., in part due to the AlTaO₄crystallites being on the order of 15 nm in diameter (FIG. 3). However, the elastic modulus of the AlTaO₄+AlPO₄glass-ceramics (e.g., 54 to 79 GPa) is typically lower than that of the Ta_2-xAl_xO_5-xglass-ceramics (e.g., 77 to 91 GPa).

Referring to the Figures, FIGS. 1A and 1B show different X-ray diffraction patterns of the same source composition 9Ta₂O₅:15 Al₂O₃:6P₂O₅:70SiO₂that was separately cerammed under different conditions of: 925° C. for 2 hrs (FIG. 1A); and 1075° C. for 2 hrs (FIG. 1B). FIG. 1A shows an X-ray diffraction pattern of glass 1, which is Example 4 in Table 1, cerammed at 925° C. for 2 hrs; the crystal phase is Ta_2-xAl_xO_5-x. FIG. 1B shows an X-ray diffraction pattern of glass 1, which is Example 4 in Table 1, cerammed at 1075° C. for 2 hrs; the crystal phases are AlTaO₄and AlPO₄.

FIG. 2 shows a ²⁷Al MAS NMR spectrum of glass 1, which is Example 4 in Table 1, cerammed at 950° C. for 2 hrs, has a sharp peak near 0 ppm that shows the presence of six-coordinated aluminum in a crystalline environment, and a broad main peak near 40 ppm that shows the presence of four-coordinated aluminum in a glassy environment. Fitting the data in FIG. 2 indicated that 15% of the Al₂O₃is 6-coordinated (for a ²⁷Al MAS NMR alumina film study see: A. Gleizes, et al., “Temperature Dependent 4-, 5- and 6-Fold Coordination of Aluminum in MOCVD-Grown Amorphous Alumina Films: From Local Coordination to Material Properties. Advances in Science and Technology, 2014, vol. 91, pp. 123-133).

FIGS. 3A and 3B show TEM photomicrograph images of glass 1, which is Example 4 in Table 1. The image in FIG. 3A was obtained from the composition (Example 4, Table 1, FIG. 1A) that was cerammed at schedule 1 (925° C. for 2 hrs) where the crystal phase is Ta_2-xAl_xO_5-xand the crystallite sizes are about 5 to 15 nm. The image in FIG. 3B was obtained from a composition (Example 4, Table 1) that was cerammed at schedule 2 (875° C. for 2 hrs followed by 1075° C. for 2 hrs) where the crystalline assemblage is AlTaO₄and AlPO₄, and the crystallite size is of from 15 to 25 nm.

FIGS. 7A and 7B show the ³¹P MAS NMR and the ²⁷Al MAS NMR, respectively, for the precursor glass of Example 1 in Table 1. Both the ³¹P and ²⁷Al magic-angle spinning nuclear magnetic resonance (MAS NMR) spectra of the precursor glass Example 1 in Table 1, have broad NMR signals, and confirm the absence of any crystalline Al- or P-containing phases in the annealed glass.

FIGS. 8A and 8B show the ³¹P MAS NMR and the ²⁷Al MAS NMR, respectively, for the cerammed glass of Example 1 in Table 1.

The ceramming of Example 1 in Table 1 was accomplished at 925/2 then 1125/4, which ceramming schedule is similar but not identical to Schedule 2. The ³¹P MAS NMR contains an intense, relatively sharp peak at −29 ppm. The position and shape of this peak is generally consistent with crystalline AlPO₄, in agreement with the XRD and ²⁷Al NMR data on similar samples. The P speciation, as measured by ³¹P MAS NMR, is approximately 90% in crystalline AlPO₄and 10% in residual glass, the residual glass is evident from the two weak signals around −35 to −37 ppm. The ²⁷Al MAS NMR data has two sharp peaks at 40 and 5 ppm, and the 40 ppm signal is consistent with four-coordinated Al in crystalline AlPO₄, and the 5 ppm signal is consistent with six-coordinated Al in crystalline AlTaO₄. These ²⁷Al NMR data indicate about 50% of Al₂O₃in AlPO₄, about 40% of Al₂O₃in AlTaO₄and up to about 10% of Al₂O₃in residual glass. The Al₂O₃in residual glass is a weak, broad signal that lies under the AlPO₄resonance at 40 ppm. Based on the peak areas in the ²⁷Al NMR data, 90 to 95% of the P₂O₅is crystallized as AlPO₄, and 70 to 75% of the Ta₂O₅is crystallized as AlTaO₄. The residual glass is silica rich, with a small amount of Al₂O₃and Ta₂O₅, and a negligible amount of P₂O₅.

FIGS. 9A and 9B show the ³¹P MAS NMR and the ²⁷Al MAS NMR spectra, respectively, of Example 4 in Table 1 after a ceramming treatment defined as Schedule 1 (“925/2”).

The ³¹P MAS NMR data (9A) contain an intense, single resonance from amorphous phosphate groups. The ²⁷Al MAS NMR spectrum (9B) is comprised of two peaks: the left peak is relatively broad and intense, consistent with four-coordinated Al in the glass, and the right peak at 3 ppm is significantly narrower and assigned to six-coordinated Al in crystalline Ta_2-xAl_xO_5-x. This sample after Schedule 1 ceramming has about 88% of Al₂O₃in residual glass and 12% of Al₂O₃in the Ta_2-xAl_xO_5-xcrystalline phase.

FIG. 2 and FIG. 9B are very similar but are not exactly the same. FIG. 2 and FIG. 9B both represent ²⁷Al NMR of Example 4 in Table 1, but with ceramming at two different temperatures: 950/2 (FIG. 2) and 925/2 (FIG. 9). The results are nearly the same and confirm that Al partially enters the crystalline Ta_2-xAl_xO_5-x, phase and exhibits some temperature dependence on the amount of Al in this phase. Additionally, the ³¹P NMR data in FIG. 9A indicate that P speciation is unaffected by “Schedule 1” and similar nucleation treatments.

FIGS. 10A and 10B show the ³¹P MAS NMR and ²⁷Al MAS NMR spectra, respectively, of Example 4 in Table 1 after a ceramming treatment defined as Schedule 3 (“1075/2” only). The ³¹P NMR data (FIG. 10A) contain an intense, relatively sharp peak at −29 ppm. The position and shape of this peak are generally consistent with crystalline AlPO₄, in agreement with the XRD and ²⁷Al NMR data on similar samples. The P speciation, as measured by ³¹P MAS NMR, is approximately 85% in crystalline AlPO₄and 15% in residual glass. The 15% in residual glass is evident from the two weak signals around −35 to −40 ppm. The ²⁷Al MAS NMR data (FIG. 10B) are comprised of two sharp peaks at 40 and 5 ppm. The 40 ppm peak is consistent with four-coordinated Al in crystalline AlPO₄, and the 5 ppm peak is consistent with six-coordinated Al in crystalline AlTaO₄. These ²⁷Al NMR data indicate 35% of Al₂O₃in AlPO₄, 45% of Al₂O₃in AlTaO₄, and up to 20% of Al₂O₃in residual glass. The up to 20% of Al₂O₃in residual glass is reflected in a weak, broad signal that lies under the AlPO₄resonance at 40 ppm. Based on the peak areas in the ²⁷Al NMR data, 85 to 90% of the P₂O₅is crystallized as AlPO₄, and 75% of the Ta₂O₅is crystallized as AlTaO₄. The residual glass is silica rich, with a small amount of Al₂O₃and Ta₂O₅, and a negligible amount of P₂O₅.

EXAMPLES

The following Examples demonstrate making, use, and analysis of the disclosed glass-ceramics and methods in accordance with the above general procedures. The following are representative of preparative and comparative preparative examples followed by a characterization example. The Tables 1, 2, and 3 list representative composition examples identified in the table headers. The Table 4 lists crystalline assemblage(s) present at selected ceram temperatures. The Table 5 lists boron-containing Ta₂O₅or AlTaO₄transparent glass-ceramics; and Ga-containing Ta₂O₅or AlTaO₄transparent glass-ceramics.

Preparative Example 1

Preparation of Precursor Glass The precursor glasses were made by melting 800 g ball milled batches of the respective oxides and aluminum metaphosphate, with or without a dopant, in 650 cc Pt crucibles at 1650° C. for 16 to 20 hrs. The molten batches were quenched to glass by pouring onto steel. The glasses were then annealed at 800° C.

Preparative Example 2

Preparation of Glass-ceramics Glass-ceramics were prepared by cutting the annealed precursor glass of Example 1 into pieces and subjecting the pieces to a one-step or a two-step ceram schedule in the range of 875 to 1100° C. For the purposes of property evaluation, one of three ceramming schedules (1, 2, or 3) defined herein was used.

A number of ceramming schedules were investigated, including a two hr hold at every 25° from 900 and 1100° C. (see also Preparative Example 3 and Table 4). All 2 hr hold ceram schedules yielded transparent glass-ceramics. In embodiments, it can be sufficient to ceram by heating at a high temperature, e.g., 1,000 to 1,100° C. or more for less than 1 hr.

Ceram Schedule 1 was: heating the suitable precursor glass pieces at 8° C./min to 925° C., hold at 925° C. for 2 hrs, followed by cooling at furnace rate to ambient temperature of about 25° C. (abbreviated in the Tables as “925/2” =Schedule 1).

Ceram Schedule 2 was: heating at 8° C./min to 875° C., hold at 875° C. for 2 hrs (i.e., a nucleation step), heating at 8° C./min to 1075° C., hold at 1075° C. for 2 hrs (i.e., a crystal growth step) (abbreviated in the Tables as the hold temperature (° C.) and the hold time (hr) ratios such as “875/2” and then “1075/2” defines Schedule 2; or alternatively “1075/2” only is Schedule 3), followed by cooling at furnace rate to ambient temperature of about 25° C. The heating at 8° C./min to 875° C., hold at 875° C. for 2 hrs (i.e., a nucleation step) can be optional, that is unnecessary, since the glass may already have been pre-nucleated, i.e., chemically segregated as indicated by transmission electron microscopy, and either Schedule 2 or Schedule 3 is believed to produce the same product as measured by XRD. However, comparative property measurements for glass-ceramics with and without the 875° C. hold are presently unavailable and could indicate significant differences in the compositions.

Preparative Example 3

Influence of Ceram Condition on Crystalline Phase Assemblage of the Glass-Ceramics Preparative Example 3 is a study that demonstrates the effect on the crystalline phase assemblage of tabulated Example 4 of Table 1 by raising the 2 hr ceram temperature from 900 to 1100° C. in increments of 25°. Example 4 of Table 1 had an initial composition of 9Ta₂O₅:15Al₂O₃:6P₂O₅:70SiO₂. FIGS. 11A and 11B show the effect of increasing the ceram temperature on phase assemblage in the disclosed method of making. The influence of ceram temperature on phase assemblage is shown in XRD patterns of the FIGS. 11A and 11B. FIG. 11A is a composite plot (i.e., an overlay for comparison) of the XRD patterns for ascending ceram temperatures 900, 925, 950, 975, or 1,000° C. FIG. 11B is also a composite plot (i.e., an overlay for comparison) of the XRD patterns for ascending ceram temperatures 1,000, 1,025, 1,050, 1,075, or 1,100° C. The XRD data shows that ceramming at 900, 925, or 950° C. for 2 hr yields “Ta₂O₅” (i.e., Ta_2-xAl_xO_5-x) as the sole crystalline phase. However, the increasing intensity of the major peak at 23° on raising the temperature from 900 to 925 to 950° C. indicates that the glass-ceramic contains a higher weight fraction or higher volume fraction of “Ta₂O₅” (i.e., Ta_2-xAl_xO_5-x) and a lower weight fraction or lower volume fraction of residual glass when cerammed at the higher temperatures in the range of 900 to 950° C. After ceramming at 975° C., the resulting glass-ceramic consists mainly of “Ta₂O₅” (i.e., Ta_2-xAl_xO_5-x) plus residual glass. However, there is a pronounced shoulder at about 24.5° indicating that AlTaO₄has begun to crystallize and indicates the onset of the reaction of “Ta₂O₅” (i.e., Ta_2-xAl_xO_5-x) and residual glass to produce AlTaO₄. By 1000° C./2, the 24.5° shoulder is now a resolved peak. With a further increase in ceram temperature above 1000° C., the relative intensity of the main “Ta₂O₅” (i.e., Ta_2-xAl_xO_5-x) peak at 23° decreases, and the peak at 24.5° representing the main AlTaO₄peak increases further. These XRD changes indicate the gradual conversion of “Ta₂O₅” (i.e., Ta_2-x,Al_xO_5-x) and glass into AlTaO₄with increasing temperature. This crystalline phase conversion appears to be complete by 1050° C. In addition, the appearance of an XRD diffraction peak at 21° in the 1025° C./2 sample signals the first appearance of AlPO₄as an additional crystalline phase. AlPO₄is present at all higher ceram temperatures. Table 4 summarizes the crystalline assemblage present at the selected ceram temperatures. The left to right listing of phases in Table 4 indicates their approximate relative abundance, e.g., for the 1025/2 sample, AlTaO₄is the most abundant phase, followed by “Ta₂O₅” (i.e., Ta_2-xAl_xO_5-x), and AlPO₄is the least abundant (i.e., AlTaO₄>Ta₂O₅>AlPO₄).

Comparative Preparative Example 3

A comparative glass having the formula: 4Ta₂O₅:18.5Al₂O₃:7.5P₂O₅:70SiO₂, was prepared. The glass had a Ta₂O₅content of below 5 mol %. This glass remains fully glassy, i.e., no crystalline phase was observed visually or by XRD when cerammed at temperatures as high as 1100° C.

Preparative Example 4

Gallium (Ga) was selected as a supplemental metal or metalloid for inclusion in a composition containing Al (and the Al₂O₃content in the batch was reduced accordingly) in either of the phases, if present, of “Ta₂O₅” (i.e., Ta_2-xAl_xO_5-x) or AlPO₄Table 5 lists three supplemental examples of Ga-containing Ta₂O₅or AlTaO₄transparent glass-ceramics.

Preparative Example 5

Similarly, boron (B) such as B₂O₃was selected as a supplemental metal or metalloid for inclusion in a composition containing SiO₂(and the SiO₂content was reduced accordingly) in a transparent glass-ceramic composition which includes Ta₂O₅, Al₂O₃, P₂O₅and SiO₂. Table 5 lists two supplemental examples of boron-containing Ta₂O₅or AlTaO₄transparent glass-ceramics.

Supplementing with Ga or B as indicated in Preparative Examples 4 and 5, respectively, had the advantage of lowering the viscosity at the melting and forming temperatures. However, the Ga or B supplemented compositions were disadvantaged by producing noticeable haze, particularly in glass-ceramics made at 925° C. (e.g., slight haze).

Characterization Example

Characterization of Young's elastic modulus (E), hardness (H), or refractive index (nD or nu) for a transparent glass-ceramic composition of the molecular formula 9Ta₂O₅:15Al₂O₃:6P₂O₅:70SiO₂.

FIG. 4 shows dependence of Young's modulus (E) versus the ceram temperature for a composition of the formula: 9Ta₂O₅:15Al₂O₃:6P₂O₅:70SiO₂of Example 4 in Table 1.

FIG. 5 shows hardness (H) versus the ceram temperature for a composition of the formula: 9Ta₂O₅:15Al₂O₃:6P₂O₅:70SiO₂of Example 4 in Table 1.

FIG. 6 shows the refractive index (nD or nD) versus the ceram temperature for a composition of the formula: 9Ta₂O₅:15Al₂O₃:6P₂O₅:70SiO₂of Example 4 in Table 1.

In each of FIGS. 4 to 6, the points at 800° C. correspond to the annealed, uncerammed glass. The points at 925° C. correspond to a Ta_2-xAl_xO_5-xglass-ceramic made using the 925/2 schedule. The points at 1075° C. corresponds to a combined or a mixed AlTaO₄and AlPO₄glass-ceramic made using the combined 875/2 and 1075/2 ceram schedule 2 above. The E, H, and nD values are higher for the Ta_2-xAl_xO_5-x(925° C.) glass-ceramic than for the mixed AlTaO₄and AlPO₄(1075° C.) glass-ceramic. This trend was also observed for all of the disclosed starting glass compositions when cerammed using Schedule 1 and was the basis for selecting the Ta_2-xAl_xO_5-xglass-ceramics as the preferred disclosed glass-ceramics. For all examples for which E, H, and nD data are listed in Table 1 or 2, the value of each of E, H, and nD is always the greatest for the sample cerammed according to Schedule 1, i.e., the Ta_2-xAl_xO_5-xglass-ceramic.

Table 1 contains the undoped (i.e., without the transition metal oxide dopants or rare earth oxide dopants) Examples 1 to 21. Table 1 includes: compositional data in both mol and wt %; property data on the annealed glasses; property data on the Ta_2-xAl_xO_5-xglass-ceramics cerammed at 925° C. for 2 hrs; the crystal phase for each of glass-ceramic as observed by XRD; the appearance description; and property data for the AlTaO₄and AlPO₄glass-ceramics cerammed at 875° C. for 2 hrs followed by 1075° C. for 2 hrs. The samples of the transparent glass-ceramic compositions listed in Table 1 typically had a slight yellow or pale amber color, which may alternatively be indicative of minor iron contamination during work up.

FIGS. 1 to 2 and FIGS. 4 to 6 are related to composition Example 4 in Table 1, while the photomicrograph images in FIG. 3A (lower temperature ceramming) and FIG. 3B (higher temperature ceramming) are also for composition Example 4 in Table 1.

Table 2 contains the doped (i.e., with a transition metal oxide dopant or rare earth oxide dopant) Examples 22 to 26.

Regarding dopants, in antiquity erbia oxide (Er₂O₃, i.e., a Er sesquioxide) was used as a pink coloring agent in glazes and glasses. Modernly, erbia has been used as a luminescent dopant to provide fluorescence at 1.55 microns and is useful, for example, in optical amplifiers for telecommunications. The 1.55 microns wavelength is especially important for optical communications since standard single mode optical fibers have minimal loss at this particular wavelength.

In embodiments, the disclosure provides an optical article, such as a lens, a fiber, an amplifier component, and like articles, comprising: a transparent glass-ceramic composition including, for example, 65 to 75% SiO₂; 10 to 25% Al₂O₃; 5 to 15% Ta₂O₅; and 3 to 10% P₂O₅, based on 100 mol % total.

In embodiments, the optical article can further comprise, for example, a dopant comprising an oxide selected from Cr, Ni, Co, V, Mn, Cu, Er, or a mixture thereof.

In embodiments, the optical article can further comprise, for example, a supplement selected from the formulas M_xO_yor M_xM′_xO_y, where M or M′ is selected from the group of a source of Nb, Ti, W, Al, or a mixture thereof, x and x′ are independently an integer from 1 to 2, and y is an integer from 1 to 5.

In embodiments, the disclosure provides an optical apparatus including the abovementioned optical article. In embodiments, the optical apparatus can be, for example, an optical fiber, such as a single mode fiber or a multimode fiber, a component of an optical amplifier for use in telecommunications, and like optical apparatus.

Tabulated Results

Exemplary examples of the disclosed transparent glass-ceramics are listed in Table 1 (i.e., Si—Al—Ta—P transparent glass-ceramic compositions and free of a dopant) and Table 2 (i.e., Si—Al—Ta—P transparent glass-ceramic compositions and containing a dopant). The disclosed sample compositions were characterized and their properties are also listed in Tables 1 and 2. Selected samples listed in Table 1, i.e., tabulated examples 1, 4, 6, 7, 8, 10, and 11, were cerammed according to Schedule 2 (i.e., 875/2, and then 1100/2) and they were all unexpectedly transparent after cooling to ambient temperature. Similarly, selected samples listed in Table 2, i.e., tabulated examples 25 and 26 were cerammed according to Schedule 2 (i.e., 875/2, and then 1100/2) and they were also unexpectedly transparent after cooling to ambient temperature.

Table 3 lists examples of the aforementioned Si—Al—Ta—P transparent glass-ceramic compositions free of dopant that have at least one supplemental metal, i.e., a portion (e.g., 0.1 to 50 mol %) of the Ta content is substituted or replaced with, for example, Nb, Ti, or W, to produce a Si—Al—Ta—P—Nb, a Si—Al—Ta—P—Ti, or a Si—Al—Ta—P—W transparent glass-ceramic composition.

Table 3 lists four compositions that demonstrate replacement of a portion of the Ta with, for example, Nb, Ti, or W, using, for example, a suitable source or oxide such as Nb₂O₅, TiO₂, or WO₂. The replacement or supplemental metal compositions results in compositions having transparent glass-ceramic properties and having the same phase assemblages, i.e., Ta₂O₅(Ta_2-xAl_xO_5-x) at low ceram temperature (e.g., 925/2 schedule 1), and AlTaO₄and AlPO₄at high ceram temperature (e.g., 875/2, 1075/2 schedule 2). Unexpectedly, the replacement or supplemental metal compositions example compositions A, B, and C, retain transparency up to a temperature of as high as 1100° C. Although not limited by theory, the presently disclosed transparent glass-ceramics are the only glass-ceramics that are transparent when heated above 1000° C. (1832° F.), i.e., the transparency of the composition remains at of from 1,000 to 1,100° C. Although not limited by theory, the Ta content in the disclosed compositions when combined with selected ceramming conditions appears to provide or insures glass-ceramic transparency by, for example, limiting the size of the crystallites or microcrystals. The Ta content in the compositions of about 5 mol % or more appears to assure glass-ceramic transparency, i.e., a glass-ceramic transparency agent.

The tabulated properties of the disclosed transparent glass-ceramics have abbreviated labels:

- T_stris the strain point;
- T_annis the anneal point;
- T_sis the softening point;
- a300 (i.e., alpha three hundred) is the average thermal expansion coefficient (also known as linear coefficient of thermal expansion or CTE) from ambient such as room temperature 25° C. to 300° C. in 10⁻⁷/° C.;
- T_gis the glass transition temperature;
- T_xis the onset of crystallization temperature;
- r is the density in g/cc;
- n is the Poisson's ratio;
- nD or nD is the refractive index at the Na D line;
- E is the Young's elastic modulus in GPa;
- G is the shear modulus in GPa; and
- H is the hardness in GPa.

The tabulated compositions also have abbreviated labels where:

- “Ta₂O₅” is an abbreviation for the formula Ta_2-xAl_xO_5-xcrystal phase identified by x-ray diffraction, where x in this formula is less than 1 such as 0.5, 0.4, 0.3, 0.2, 0.1, 0.005, 0.001, and like values, including intermediate values and ranges.
- “AP” is an abbreviation for the AlPO₄crystal phase identified by x-ray diffraction.
- “AT” is an abbreviation for the AlTaO₄crystal phase identified by x-ray diffraction.
- “AT+AP” is an abbreviation for a mixture of AlTaO₄and AlPO₄crystal phases.

TABLE 1

Transparent glass-ceramic compositions free of dopant.

Com-

position

Example
1
2
3
4
5
6
7
8
9
10

mol %

Ta₂O₅
8
7
8
9
8
7
10
10
8
9

Al₂O₃
14.5
14.5
17.5
15
16
15.5
15.5
14
13
15

P₂O₅
7.5
7.5
4.5
6
6
7.5
4.5
6
9
8

SiO₂
70
70
70
70
70
70
70
70
70
68

SnO₂
—
1
—
—
—
—
—
—
—
—

wt %

Ta₂O₅
34.4
30.9
34.8
37.6
34.6
31.1
40.7
40.5
34.2
37.1

Al₂O₃
14.4
14.8
17.5
14.5
16
15.9
14.6
13.1
12.8
14.3

P₂O₅
10.4
10.7
6.28
8.06
8.33
10.7
5.89
7.81
12.3
10.6

SiO₂
40.9
42.1
41.4
39.8
41.1
42.3
38.8
38.6
40.6
38.1

SnO₂
—
1.51
—
—
—
—
—
—
—
—

nD
—
—
—
1.569
—
—
—
—
—
—

Tstr (° C.)
823
817
—
—
—
—
—
—
—
—

Tann (° C.)
871
869
—
—
—
—
—
—
—
—

a300
12.4
12.5
—
—
—
—
—
—
—
—

Tg (° C.)
836
—
836
823
829
838
819
818
840
835

Tx (° C.)
959
—
1057
958
987
1036
947
917
—
—

r (gm/cc)
—
—
—
3.117
—
—
—
—
—
—

E (GPa)
79.4
—
—
82.9
83.4
79.4
89.3
84.3
76.5
79.7

G (GPa)
32.8
—
—
34.4
34.3
33
36.6
35
31.9
33.1

n
0.208
—
—
0.205
0.213
0.203
0.219
0.206
0.198
0.204

H (GPa)
—
—
—
7.23
—
—
—
—
—
—

Schedule 1
Ta₂O₅

Ta₂O₅

Ta₂O₅
Ta₂O₅
Ta₂O₅

925/2

ceram

appearance
transp.
—
—
transp.
—
—
—
transp.
transp.
transp.

nD
1.558
—
—
1.581
—
—
—
1.589
—
1.572

a300
—
—
—
—
—
—
22.0
17.6
—
15.1

r (gm/cc)
—
—
—
3.153
—
—
—
—
—
—

E (GPa)
82.2
—
—
87.1
—
—
—
87.6
77.6
82.8

G (GPa)
34.1
—
—
36.3
—
—
—
36.6
32.7
34.5

n
0.204
—
—
0.201
—
—
—
0.204
0.187
0.198

H (GPa)
—
—
—
7.89
—
—
—
—
—
—

Schedule 2
AT + AP
AT + AP
AT + AP
AT + AP
AT + AP
AT + AP
AT + AP
AT + AP
AT + AP
AT + AP

875/2, then

1075/2

ceram

appearance
transp.
hazy
—
transp.
transp.
transp.
transp.
transp.
transp.
transp.

nD
1.548
—
—
1.565
—
—
—
1.572
—
1.558

r (gm/cc)
—
—
—
3.157
—
—
—
—
—
—

E (GPa)
70.4
—
—
79.1
61.4
58.3
77.2
71.4
53.6
59.6

G (GPa)
30.6
—
—
33.8
27.1
25.7
33.6
30.7
24.5
26.3

n
0.149
—
—
0.17
0.134
0.134
0.149
0.164
0.097
0.132

H (GPa)
—
—
—
7.67
—
—
—
—
—
—

Example
11
12
13
14
15
16
17
18
19
20
21

mol %

Ta₂O₅
9.5
8
11
9.5
11
8
9.5
11
12.5
9.5
8

Al₂O₃
16
13
18.5
18.5
17
18.5
17
15.5
17
15.5
17

P₂O₅
8.5
7
5.5
7
7
8.5
8.5
8.5
5.5
10
10

SiO₂
66
72
65
65
65
65
65
65
65
65
65

wt %

Ta₂O₅
38.1
34.7
42.5
38.2
42.3
33.5
38
42.1
46.2
38
33.4

Al₂O₃
14.8
13
16.5
17.2
15.1
17.9
15.7
13.7
14.5
14.2
16.4

P₂O₅
11
9.76
6.83
9.04
8.64
11.5
10.9
10.4
6.53
12.8
13.4

SiO₂
36
42.5
34.1
35.5
34
37.1
35.4
33.8
32.7
35.2
36.9

Tg (° C.)
829
832
822
830
825
835
834
821
831
851
849

Tx (° C.)
—
—
967
997
933

961

933
916
1017

r (gm/cc)
3.11
—
3.388
—
—
—
—
3.234
—
—
—

E (GPa)
81.4
77.2
90.5
85.7
86.8
81.5
82.1
81.8
—
—
—

G (GPa)
33.6
32.9
37.1
35.2
35.6
33.6
33.9
33.9
—
—
—

n
0.212
0.174
0.22
0.217
0.218
0.211
0.213
0.205
—
—
—

H (GPa)
6.44
—
7.5
—
—
—
—
6.98
—
—
—

Schedule 1
Ta₂O₅
—
—
—
Ta₂O₅
—
—
—
—
—
—

925/2

ceram

appearance
transp.
—
—
—
transp.
—
—
—
—
—
—

nD
1.577
—
—
—
1.604
—
—
—
—
—
—

r (gm/cc)
3.137
—
—
—
—
—
—
3.258
—
—
—

E (GPa)
83.7
81.7
—
—
90.5
—
85.4
85.5
—
—
—

G (GPa)
34.8
34.1
—
—
37.3
—
35.3
35.4
—
—
—

n
0.198
0.197
—
—
0.213
—
0.21
0.207
—
—
—

H (GPa)
7.45
—
—
—
—
—
—
7.41
—
—
—

Schedule 2
AT + AP
—
AT + AP
AT + AP
AT + AP
—
—
—
—
—
—

875/2,

then

1075/2

ceram

appearance
transp.
—
transp.
transp.
transp.
—
—
—
—
—
—

nD
1.565
—
1.596
—
1.588
—
—
—
—
—
—

r (gm/cc)
3.16
—
3.478
—
—
—
—
3.288
—
—
—

E (GPa)
61.6
66.2
77.7
66.7
66.3
60.9
67.2
65.6
—
—
—

G (GPa)
27.2
28.9
33.4
29.1
29
26.8
29.4
28.7
—
—
—

n
0.135
0.145
0.165
0.147
0.146
0.139
0.144
0.144
—
—
—

H (GPa)
6
—
8.43
—
—
—
—
7.56
—
—
—

TABLE 2

Transparent glass-ceramic compositions including a dopant.

Example
22
23
24
25
26

mol %

Ta₂O₅
9
9
9
9
9

Al₂O₃
15
15
15
15
15

P₂O₅
6
6
6
6
6

SiO₂
70
70
70
70
70

Cr₂O₃
0.017
—
—
—
—

NiO
—
0.035
—
—
—

CoO
—
—
0.033
—
—

Er₂O₃
—
—
—
0.015
0.075

wt %

Ta₂O₅
37.6
37.6
37.6
37.6
37.5

Al₂O₃
14.5
14.5
14.5
14.5
14.4

P₂O₅
8.06
8.06
8.06
8.05
8.04

SiO₂
39.8
39.8
39.8
39.8
39.7

Cr₂O₃
0.024
—
—
—
—

NiO
—
0.025
—
—
—

CoO
—
—
0.023
—
—

Er₂O₃
—
—
—
0.05
0.27

Schedule 1

925/2 ceram
Ta₂O₅
Ta₂O₅
Ta₂O₅
Ta₂O₅
Ta₂O₅

Appearance,
transparent,
tmnsp.,
tmnsp.,
tmnsp.,
tmnsp.,

color
green
amber
blue
amber
amber

Schedule 2

875/2, then

1075/2
AT + AP
AT + AP
AT + AP
AT + AP
AT + AP

Appearance,
transparent,
transp.,
transp.,
tmnsp.,
transp.,

color
green
amber
blue
amber
amber

TABLE 3

Metal supplemented transparent Ta containing

glass-ceramic compositions.

Example
A
B
C
D

mol %

Ta₂O₅
6.75
4.5
6.75
6.75

Nb₂O₅
2.25
4.5

TiO₂
2.25
—

WO₃
2.25

Al₂O₃
15
15
15
15

P₂O₅
6
6
6
6

SiO₂
70
70
70
70

wt %

Ta₂O₅
29.3
20.3
30.6
29.5

Nb₂O₅
5.88
12.2

TiO₂
1.84
—

WO₃
5.17

Al₂O₃
15.0
15.6
15.7
15.2

P₂O₅
8.37
8.71
8.73
8.44

SiO₂
41.4
43
43.1
41.7

Tg (° C.)
800
773
816
813

Tx (° C.)
927
927
927
927

Schedule 1

925/2

Ta₂O₅+
Ta₂O₅+

ceram
Ta₂O₅
AT
AP
Ta₂O₅

Appearance
transp.
transp.
translucent
transp.

Schedule 2

875/2 and

1075/2

ceram
AT + AP
AT + AP
AT + AP
AT + AP

Appearance
transp.
transp.
transp.
transp.

TABLE 4

Crystalline assemblage(s) at

selected ceram temperatures.

Temperature
Crystalline Assemblage(s)

(° C.)
Present

900
Ta₂O₅

925
Ta₂O₅

950
Ta₂O₅

975
Ta₂O₅+ AlTaO₄

1000
Ta₂O₅+ AlTaO₄

1025
AlTaO₄+ Ta₂O₅+ AlPO₄

1050
AlTaO₄+ AlPO₄

1075
AlTaO₄+ AlPO₄

1100
AlTaO₄+ AlPO₄

TABLE 5

Boron-containing Ta₂O₅or AlTaO₄transparent glass-ceramics;

and Ga-containing Ta₂O₅or AlTaO₄transparent glass-ceramics.

Example
I
II
III
IV
V

mol %

Ta₂O₅
9
9
9
9
11

Al₂O₃
15
15
11.25
7.5
12.75

Ga₂O₃
—
—
3.75
7.5
4.25

P₂O₅
6
6
6
6
7

SiO₂
68
66
70
70
65

B₂O₃
2
4
—
—
—

wt %

Ta₂O₅
37.6
37.5
36.4
35.4
40.9

Al₂O₃
14.4
14.4
10.5
6.81
10.9

Ga₂O₃
—
—
6.44
12.5
6.7

P₂O₅
8.04
8.03
7.8
7.58
8.36

SiO₂
38.6
37.4
38.5
37.4
32.9

B₂O₃
1.32
2.63
—
—
—

Tg (° C.)
800
780
796
774
798

Tx (° C.)
929
911
899
867
883

Schedule 1

Ta₂O₅+
Ta₂O₅+
Ta₂O₅+
Ta₂O₅+

925/2
Ta₂O₅
AT
AT
AT
AT

Appearance
slight
slight
slight
slight
slight

haze
haze
haze
haze
haze

Schedule 2

875/2, then
AT +
AT +
AT +
AT +
AT +

1075/2
AP
AP
AP
AP
AP

Appearance
transp.
transp.
transp.
transp.
transp.

The disclosure has been described with reference to various specific embodiments and techniques. However, many variations and modifications are possible while remaining within the scope of the disclosure.