# Patent

## Title
Intermediate thermal expansion coefficient glass

## Abstract

Aluminoborosilicate glasses which may be useful in photovoltaic, photochromic, electrochromic, or Organic Light Emitting Diode (OLED) lighting applications are described.

## Background
This application claims the benefit of priority to U.S. Provisional Application No. 61/103,126 filed on Oct. 6, 2008 and to U.S. Provisional Application No. 61/177,827 filed on May 13, 2009.


BACKGROUND
1. Field
Embodiments relate generally to aluminoborosilicate glasses and more particularly to low alkali aluminoborosilicate glasses which may be useful in photovoltaic, photochromic, electrochromic, or Organic Light Emitting Diode (OLED) lighting applications.
2. Technical Background
The fusion forming process typically produces flat glass with optimal surface and geometric characteristics useful for many electronics applications, for instance, substrates used in electronics applications, for example, display glass for LCD televisions.
Over the last 10 years, Corning fusion glass products include 1737FTM, 1737GTM, Eagle2000FTM, EagleXGTM, JadeTM, and Codes 1317 and 2317 (Gorilla GlassTM). Efficient melting is generally believed to occur at a temperature corresponding to a melt viscosity of about 200 poise (p). These glasses share in common 200p temperatures in excess of 1600° C., which can translate to accelerated tank and electrode corrosion, greater challenges for fining due to still more elevated finer temperatures, and/or reduced platinum system life time, particularly around the finer. Many have temperatures at 3000 poise in excess of about 1300° C., and since this is a typical viscosity for an optical stirrer, the high temperatures at this viscosity can translate to excessive stirrer wear and elevated levels of platinum defects in the body of the glass.
Many of the above described glasses have delivery temperatures in excess of 1200° C., and this can contribute to creep of isopipe refractory materials, particularly for large sheet sizes.
These attributes combine so as to limit flow (because of slow melt rates), to accelerate asset deterioration, to force rebuilds on timescales much shorter than product lifetimes, to force unacceptable (arsenic), expensive (capsule) or unwieldy (vacuum fining) solutions to defect elimination, and thus contribute in significant ways to the cost of manufacturing glass.
In applications in which rather thick, comparatively low-cost glass with less extreme properties is required, these glasses are not only overkill, but prohibitively expensive to manufacture. This is particularly true when the competitive materials are made by the float process, a very good process for producing low cost glass with rather conventional properties. In applications that are cost sensitive, such as large-area photovoltaic panels and OLED lighting, this cost differential is so large as to make the price point of LCD-type glasses unacceptable.
To reduce such costs, it is advantageous to drive down the largest overall contributors (outside of finishing), and many of these track directly with the temperatures used in the melting and forming process. Therefore, there is a need for a glass that melts at a lower temperature than those aforementioned glasses.
Further, it would be advantageous to have a glass useful for low temperature applications, for instance, photovoltaic and OLED light applications. Further, it would be advantageous to have a glass whose processing temperatures were low enough that the manufacturing of the glass would not excessively consume the energy that these applications are aiming to save.
SUMMARY
One embodiment is a glass comprising, in mole percent:

    
    
        60 to 65 percent SiO2;
        8 to 12 percent Al2O2;
        7 to 15 percent B2O3;
        greater than 0 to 8 percent M2O; and
        9 to 15 percent RO;
    
    


wherein, M is an alkali metal and wherein, R is an alkaline earth metal.
Such glasses address one or more of the above-mentioned disadvantages of conventional glasses and provide one or more of the following advantages: the alkalis added to the glass can greatly accelerate melting, permitting higher pull rates and lower melting temperatures. They can also raise the coefficient of thermal expansion so as to be a better match for, for example, CdTe photovoltaics.
Additional features and advantages will be set forth in the detailed description which follows, and in part will be readily apparent to those skilled in the art from the description or recognized by practicing the invention as described in the written description and claims hereof, as well as the appended drawings.
It is to be understood that both the foregoing general description and the following detailed description are merely exemplary of the invention, and are intended to provide an overview or framework for understanding the nature and character of the invention as it is claimed.
The accompanying drawings are included to provide a further understanding of the invention, and are incorporated in and constitute a part of this specification. The drawings illustrate one or more embodiment(s) of the invention and together with the description serve to explain the principles and operation of the invention.



BRIEF DESCRIPTION OF THE DRAWINGS
The invention can be understood from the following detailed description either alone or together with the accompanying drawing figures.
FIG. 1 is a graph of estimated liquidus viscosity.
FIG. 2 is an illustration of features of a photovoltaic device according to one embodiment.



DETAILED DESCRIPTION
Reference will now be made in detail to various embodiments of the invention. Wherever possible, the same reference numbers will be used throughout the drawings to refer to the same or like features.
As used herein, the term “substrate” can be used to describe either a substrate or a superstrate depending on the configuration of the photovoltaic cell. For example, the substrate is a superstrate, if when assembled into a photovoltaic cell, it is on the light incident side of a photovoltaic cell. The superstrate can provide protection for the photovoltaic materials from impact and environmental degradation while allowing transmission of the appropriate wavelengths of the solar spectrum. Further, multiple photovoltaic cells can be arranged into a photovoltaic module.
As used herein, the term “adjacent” can be defined as being in close proximity. Adjacent structures may or may not be in physical contact with each other. Adjacent structures can have other layers and/or structures disposed between them.
As used herein, the term “planar” can be defined as having a substantially topographically flat surface.
Although exemplary numerical ranges are described in the embodiments, each of the ranges can include any numerical value including decimal places within the range including each of the ranges endpoints.
As used herein, multivalent components of the exemplary compositions are represented, for example, as Fe2O3, SnO2, As2O5, Sb2O5. These materials are batched as said oxides but mixed valences or alternative valences could be used.
One embodiment is a glass comprising, in mole percent:

    
    
        60 to 65 percent SiO2;
        8 to 12 percent Al2O3;
        7 to 15 percent B2O3;
        greater than 0 to 8 percent M2O; and
        9 to 15 percent RO;
    
    


wherein, M is an alkali metal and wherein, R is an alkaline earth metal.
Another embodiment is a glass comprising, in mole percent:

    
    
        61 to 64 percent SiO2;
        8 to 12 percent Al2O3;
        9 to 15 percent B2O3;
        greater than 0 to 4 percent M2O; and
        12 to 15 percent RO;
    
    


wherein, M is an alkali metal and wherein, R is an alkaline earth metal.
Another embodiment is a glass comprising, in mole percent:

    
    
        60 to 65 percent SiO2;
        8 to less than 10 percent Al2O3;
        greater than 11 to 15 percent B2O3;
        greater than 0 to less than 1 percent M2O; and
        9 to 15 percent RO;
    
    


wherein, M is an alkali metal and wherein, R is an alkaline earth metal.
Another embodiment is a glass comprising, in mole percent:

    
    
        60 to 65 percent SiO2;
        10 to 12 percent Al2O3;
        7 to 11 percent B2O3;
        1 to 8 percent M2O; and
        9 to 15 percent RO;
    
    


wherein, M is an alkali metal and wherein, R is an alkaline earth metal.
In one embodiment, M is an alkali metal selected from Li, Na, K, Rb, Cs, and a combination thereof. In some embodiments, M is selected from Li, K, Cs, and a combination thereof.
In one embodiment, R is selected from Mg, Ca, Sr, Ba, and a combination thereof. In some embodiments, R is selected from Mg, Ca, Sr, and a combination thereof.
According to another embodiment, the glass is substantially free of BaO. For example, the content of BaO can be 0.05 mole percent or less, for example, zero mole percent.
In some embodiments, the glass is substantially free of Sb2O3, As2O3, or combinations thereof, for example, the glass comprises 0.05 mole percent or less of Sb2O3 or As2O3 or a combination thereof. For example, the glass can comprise zero mole percent of Sb2O3 or As2O3 or a combination thereof.
In some embodiments, the glass comprises 60 to 65 mole percent SiO2. In some embodiments, the glass comprises 61 to 64 mole percent SiO2. In some embodiments, the glass comprises 62 to 64 mole percent SiO2.
In another embodiment, the glass comprises 0.01 to 0.4 mole percent SnO2.
The glass according to one embodiment, comprises in mole percent:

    
    
        62 to 65 percent SiO2;
        10 to 12 percent Al2O3;
        7 to 11 percent B2O3;
        3 to 8 percent MgO;
        3 to 10 percent CaO;
        3 to 8 percent SrO; and
        1 to 8 percent M2O;
    
    


wherein, M is an alkali metal selected from K, Na, and combinations thereof and wherein, CaO/(CaO+SrO) is from 0.4 to 1.
The glass, in one embodiment, is rollable. The glass, in one embodiment, is down-drawable. The glass can be slot drawn or fusion drawn, for example. According to another embodiment, the glass can be float formed.
The glass can further comprise 2 mole percent or less of TiO2, MnO, ZnO, Nb2O5, MoO3, Ta2O5, WO3, ZrO2, Y2O3, La2O3, HfO2, CdO, SnO2, Fe2O3, CeO2, As2O3, Sb2O3, Cl, Br, P2O5, or combinations thereof.
As mentioned above, the glasses, according some embodiments, comprise 7 to 15 mole percent, for example, 7 to 11 mole percent B2O3. B2O3 is added to the glass to reduce melting temperature, to decrease liquidus temperature, to increase liquidus viscosity, and to improve mechanical durability relative to a glass containing no B2O3.
Also as mentioned above, the glasses, according to some embodiments, 9 to 15 mole percent RO wherein, R is an alkaline earth metal. The glass can comprise, for example, 1 to 8 mole percent MgO. MgO can be added to the glass to reduce melting temperature and to increase strain point. It can disadvantageously lower CTE relative to other alkaline earths (e.g., CaO, SrO, BaO), and so other adjustments may be made to keep the CTE within the desired range. Examples of suitable adjustments include increase SrO at the expense of CaO, increasing alkali oxide concentration, and replacing a smaller alkali oxide (e.g., Na2O) in whole or in part with a larger alkali oxide (e.g., K2O).
The glasses, in some embodiments, comprise 1 to 9 mole percent CaO. Relative to alkali oxides or SrO, CaO contributes to higher strain point, lower density, and lower melting temperature. It is a primary component of certain possible denitrification phases, particularly anorthite (CaAl2Si2O8), and this phase has complete solid solution with an analogous sodium phase, albite (NaAlSi3O8). High Na and Ca contents taken alone can cause liquidus temperatures to be unacceptably high. However, the chemical sources for CaO include limestone, a very inexpensive material, so to the extent that high volume and low cost are factors, it is typically useful to make the CaO content as high as can be reasonably achieved relative to other alkaline earth oxides.
The glasses can comprise, in some embodiments, 0 to 5 mole percent SrO. In certain embodiments, the glass contains no deliberately batched SrO, though it may of course be present as a contaminant in other batch materials. SrO contributes to higher coefficient of thermal expansion, and the relative proportion of SrO and CaO can be manipulated to improve liquidus temperature, and thus liquidus viscosity. SrO is not as effective as CaO or MgO for improving strain point, and replacing either of these with SrO tends to cause the melting temperature to increase.
In certain embodiments, the glass satisfies one or more of the following expressions:

1.0≦(M2O+RO)/Al2O3≦2; and

0.4≦CaO/(CaO+SrO)≦1.

The ratio (M2O+RO)/Al2O3 is advantageously greater than 1.0 to assist in removing bubbles from the glass during the initial melt step. This occurs because the alkali and alkaline earth metal oxides that are not involved in stabilizing Al2O3 are available to digest the silica source, typically a commercial sand. Surface area that might be sites for bubble nucleation and growth are therefore eliminated early in melting, and a comparatively bubble-free glass is obtained.

The ratio CaO/(CaO+SrO) is advantageously kept between 0.4 and 1 to obtain a good balance between liquidus temperature (and hence liquidus viscosity) and melting temperature. For example, compositions with low alkali concentrations and high SrO concentrations have comparatively high melting temperatures, and if SrO is too high then liquidus temperatures may be elevated as well relative to glasses with more alkali oxide and lower SrO. However, for fixed concentrations of all other components, a local minimum in liquidus temperature is often obtained for CaO/(CaO+SrO) ratios between 0.4 and 1.
Also as mentioned above, the glasses, according to some embodiments, include greater than zero to 8 mole percent M2O, for example, 0.05 to 8 mole percent M2O, 0.1 to 8 mole percent M2O, 0.5 to 8 mole percent M2O, 1 to 8 mole percent M2O, where M is one or more of the alkali cations Li, Na, K, Rb and Cs. In certain embodiments, it is desirable that the alkalis in question be Li, K and Cs or combinations thereof. The alkali cations raise the CTE steeply, but also lower the strain point and, depending upon how they are added, increase melting temperatures. The least effective alkali oxide for CTE is Li2O, and the most effective alkali oxide is Cs2O. As noted above, sodium can participate in one of the possible denitrification phases of the inventive glasses, and while adjustments in other components can be used to counteract this, e.g., changing the CaO/(CaO+SrO) ratio, this tendency may make it advantageous to replace sodium with other alkalis, or to use a mix of alkalis instead of sodium alone. If high volume and low cost are important, then it is desirable to as much as possible confine the alkali oxides to Na2O and K2O or combinations thereof.
The glasses, according to some embodiments, can further comprise a variety of other components. For example, the glasses can comprise SnO2, Fe2O3, MnO, CeO2, As2O3, Sb2O3, Cl, Br, or combinations thereof. These materials can be added as fining agents (e.g., to facilitate removal of gaseous inclusions from melted batch materials used to produce the glass) and/or for other purposes. In certain embodiments, the glasses comprise SnO2 (e.g., as calculated in mole percent on an oxide basis, 0.02 to 0.3 SnO2, etc.) and Fe2O3 (e.g., as calculated in mole percent on an oxide basis, 0.005 to 0.08 Fe2O3, 0.01 to 0.08 Fe2O3, etc.). By way of illustration, in certain embodiments, the glasses comprise SnO2 and Fe2O3f wherein, in mole percent on an oxide basis:

0.02≦SnO2≦0.3; and

0.005≦Fe2O3≦0.08.

In certain embodiments, the glasses comprise less than 0.05% mole percent of Sb2O3, As2O3, or combinations thereof. In certain embodiments, the glasses comprise SnO2, Fe2O3, CeO2, Cl, Br, or combinations thereof and include less than 0.05% (e.g., less than 0.04%, less than 0.03%, less than 0.02%, less than 0.01%, etc.) mole percent of Sb2O3, As2O3, or combinations thereof. In certain embodiments, the glasses comprise SnO2 and Fe2O3 and include less than 0.05 mole percent (e.g., less than 0.04 mole percent, less than 0.03 mole percent, less than 0.02 mole percent, less than 0.01 mole percent, etc.) of Sb2O3f As2O3, or combinations thereof. In certain embodiments, the glasses comprise SnO2 and Fe2O3, wherein, in mole percent on an oxide basis:

0.02≦SnO2≦0.3; and

0.005≦Fe2O3≦0.08,

and include less than 0.05% mole percent of Sb2O3, As2O3, or combinations thereof.

The glasses, according to some embodiments, (e.g., any of the glasses discussed above) can include F, Cl, or Br, for example, as in the case where the glasses comprise Cl and/or Br as fining agents. For example, the glass can comprise fluorine, chlorine, and/or bromine, wherein, as calculated in mole percent: F+Cl+Br≦0.4, such as where F+Cl+Br≦0.3, F+Cl+Br≦0.2, F+Cl+Br≦0.1, 0.001≦F+Cl+Br≦0.4, and/or 0.005≦F+Cl+Br≦0.4. By way of illustration, in certain embodiments, the glass comprises SnO2 and Fe2O3 and, optionally, fluorine, chlorine, and/or bromine, such that, as calculated in mole percent on an oxide basis: 0.02≦SnO2≦0.3, 0.005≦Fe2O3≦0.08, and F+Cl+Br≦0.4; and, in certain embodiments, the glass comprises SnO2 and Fe2O3 and, optionally, Sb2O3, As2O3, fluorine, chlorine, and/or bromine, such that, as calculated in mole percent on an oxide basis, 0.02≦SnO2≦0.3, 0.005≦Fe2O3≦0.08, and F+Cl+Br≦0.4, and such that the glass includes less than 0.05 mole percent (e.g., less than 0.04, less than 0.03, less than 0.02, less than 0.01, etc.) mole percent of Sb2O3, As2O3, or combinations thereof.
The glasses, according to some embodiments, comprise BaO. In certain embodiments, the glasses comprise less than 0.1 mole percent of BaO.
The glasses, according to some embodiments, can further include contaminants as typically found in commercially prepared glass. In addition or alternatively, a variety of other oxides (e.g., TiO2, MnO, ZnO, Nb2O5, MoO3, Ta2O5, WO3, ZrO2, Y2O3, La2O3, P2O5, and the like) can be added, albeit with adjustments to other glass components, without compromising their melting or forming characteristics. In those cases where the glasses, according to some embodiments, further include such other oxide(s), each of such other oxides are typically present in an amount not exceeding 2 mole percent, and their total combined concentration is typically less than or equal to 5 mole percent, although higher amounts can be used so long as the amounts used do not place the composition outside of the ranges described above. The glasses, according to some embodiments, can also include various contaminants associated with batch materials and/or introduced into the glass by the melting, fining, and/or forming equipment used to produce the glass (e.g., ZrO2).
The glass, according to some embodiments, is down-drawable; that is, the glass is capable of being formed into sheets using down-draw methods such as, but not limited to, fusion draw and slot draw methods that are known to those skilled in the glass fabrication arts. Such down-draw processes are used in the large-scale manufacture of flat glass, for example, display glass or ion-exchangeable glass.
The fusion draw process uses an isopipe that has a channel for accepting molten glass raw material. The channel has weirs that are open at the top along the length of the channel on both sides of the channel. When the channel fills with molten material, the molten glass overflows the weirs. Due to gravity, the molten glass flows down the outside surfaces of the isopipe. These outside surfaces extend down and inwardly so that they join at an edge below the drawing tank. The two flowing glass surfaces join at this edge to fuse and form a single flowing sheet. The fusion draw method offers the advantage that, since the two glass films flowing over the channel fuse together, neither outside surface of the resulting glass sheet comes in contact with any part of the apparatus. Thus, the surface properties are not affected by such contact.
The slot draw method is distinct from the fusion draw method. Here the molten raw material glass is provided to a conduit. The bottom of the conduit has an open slot that is wider in one dimension than the other dimension with a nozzle that extends the length of the slot. The molten glass flows through the slot/nozzle and is drawn downward as a continuous sheet therethrough and into an annealing region. Compared to the fusion draw process, the slot draw process provides a thinner sheet, as only a single sheet is drawn through the slot, rather than two sheets being fused together, as in the fusion down-draw process.
In order to be compatible with down-draw processes, the aluminoborosilicate glass described herein has a high liquidus viscosity. In one embodiment, the glass has a liquidus viscosity of 50,000 poise or greater, for example, 150,000 poise or greater, for example, greater than or equal to 500,000 poise. The liquidus viscosities of the glasses are very closely correlated with the difference between the liquidus temperature and the softening point. This correlation is indicated by line 10 in FIG. 1. For downdraw processes, the glasses preferably have liquidus—softening point less than about 230° C., more preferably less than 200° C.
Accordingly, in one embodiment, the glass has a strain point of 600° C. or greater, for example, 620° C. or greater. In some embodiments, the glass has a coefficient of thermal expansion of 38×10−7 or greater, for example, 40×10−7 or greater, for example, 45×10−7 or greater.
The glass according to one embodiment can have a strain point of 620° C. or greater and/or a coefficient of thermal expansion of 45×10−7 or greater.
According to one embodiment, the glass is ion exchanged in a salt bath comprising one or more salts of alkali ions. The glass can be ion exchanged to change its mechanical properties. For example, smaller alkali ions, such as lithium or sodium, can be ion-exchanged in a molten salt containing one or more larger alkali ions, such as sodium, potassium, rubidium or cesium. If performed at a temperature well below the strain point for sufficient time, a diffusion profile will form in which the larger alkali moves into the glass surface from the salt bath, and the smaller ion is moved from the interior of the glass into the salt bath. When the sample is removed, the surface will go under compression, producing enhanced toughness against damage. Such toughness may be desirable in instances where the glass will be exposed to adverse environmental conditions, such as photovoltaic grids exposed to hail. A large alkali already in the glass can also be exchanged for a smaller alkali in a salt bath. If this is performed at temperatures close to the strain point, and if the glass is removed and its surface rapidly reheated to high temperature and rapidly cooled, the surface of the glass will show considerable compressive stress introduced by thermal tempering. This will also provide protection against adverse environmental conditions. It will be clear to one skilled in the art that any monovalent cation can be exchanged for alkalis already in the glass, including copper, silver, thallium, etc., and these also provide attributes of potential value to end uses, such as introducing color for lighting or a layer of elevated refractive index for light trapping.
According to another embodiment, the glass can be float formed as known in the art of float forming glass.
In one embodiment, the glass is in the form of a sheet. The glass in the form of a sheet can be thermally tempered.
In one embodiment, an Organic Light Emitting Diode device comprises the glass in the form of a sheet.
In one embodiment, a photovoltaic device comprises the glass in the form of a sheet. The photovoltaic device can comprise more than one of the glass sheets, for example, as a substrate and/or as a superstrate. In one embodiment, the glass sheet is substantially planar. According to one embodiment, the glass sheet is transparent.
According to some embodiments, the glass sheet has a thickness of 4.0 mm or less, for example, 3.5 mm or less, for example, 3.2 mm or less, for example, 3.0 mm or less, for example, 2.5 mm or less, for example, 2.0 mm or less, for example, 1.9 mm or less, for example, 1.8 mm or less, for example, 1.5 mm or less, for example, 1.1 mm or less, for example, 0.5 mm to 2.0 mm, for example, 0.5 mm to 1.1 mm, for example, 0.7 mm to 1.1 mm. Although these are exemplary thicknesses, the glass sheet can have a thickness of any numerical value including decimal places in the range of from 0.1 mm up to and including 4.0 mm.
In another embodiment, the photovoltaic device comprising a glass sheet and an active photovoltaic medium adjacent to the glass sheet.
The active photovoltaic medium can comprise multiple layers, for example, an amorphous silicon layer and a microcrystalline silicon layer.
In one embodiment, the active photovoltaic medium comprises cadmium telluride, copper indium gallium diselenide, amorphous silicon, crystalline silicon, microcrystalline silicon, or combinations thereof.
Another embodiment, as shown in FIG. 2 features 200 of a photovoltaic device comprising a glass sheet 12 comprising any of the glass compositions previously described and an active photovoltaic medium 16 adjacent to the glass sheet, wherein the active photovoltaic medium comprises cadmium telluride. According to one embodiment, the glass sheet has a thickness as previously described. The photovoltaic device can further comprise a conductive layer 14, such as a transparent conductive oxide adjacent to or disposed on the glass sheet.
In one embodiment, an electrochromic device comprises the glass in the form of a sheet. The electrochromic device can be, for example, an electrochromic window.
EXAMPLES
The following is an example of how to fabricate a sample of an exemplary glass, according to one embodiment of the invention, as shown in Table 1. This composition corresponds to composition number 46 shown in Table 7.










TABLE 1







oxide
mol %



















SiO2
63.5



Al2O3
10.7



B2O3
10.3



K2O
2.3



MgO
4.4



CaO
5.2



SrO
3.5



SnO2
0.1










In some embodiments, the total does not add up to 100%, since certain tramp elements are present at non-negligible concentrations.

Batch materials, as shown in Table 2 were weighed and added to a 4 liter plastic container:










TABLE 2








batch



Batch Components
weight



















sand
1713.42



alumina
486.27



boric acid
570.42



Potassium carbonate
143.05



Magnesia
78.62



Limestone
240.73



Strontium carbonate
234.23



10% SnO2 and 90%
6.92



sand










It should be appreciated that in the batch, limestone, depending on the source can contain tramp elements and/or vary amounts of one or more oxides, for example, MgO and/or BaO. The sand is advantageously beneficiated so that at least 80% by mass passes 60 mesh, for example 80 mesh, for example 100 mesh. The SnO2 added, in this example, was pre-mixed with sand at a level of 10% by weight so as to ensure homogeneous mixing with the other components. The bottle containing the batch materials was mounted to a tumbler and the batch materials were mixed so as to make a homogeneous batch and to break up soft agglomerates. The mixed batch was transferred to a 1800 cc platinum crucible and placed into a high-temperature ceramic backer. The platinum in its backer was loaded into a glo-bar furnace idling at a temperature of 1550° C. After 6 hours, the crucible+backer was removed and the glass melt was poured onto a cold surface, such as a steel plate, to form a patty, and then transferred to an annealer held at a temperature of 670° C. The glass patty was held at the annealer temperature for 2 hours, then cooled at a rate of 1° C. per minute to room temperature.
Table 3, Table 4, Table 5, Table 6, Table 7, and Table 8 show exemplary glasses, according to embodiments of the invention, and made according to the above example. Properties data for some glasses are also shown in Table 3, Table 4, Table 5, Table 6, Table 7, and Table 8.
In view of its low liquidus temperature of 940° C. and, hence, its extremely high liquidus viscosity in excess of 5,000,000 poise, glass 49, shown in Table 8 is an advantageous glass for applications, such as glass for photovoltaics. The exemplary glasses shown in Table 8 comprise, in mole percent:

    
    
        62 to 64 percent SiO2;
        8 to 12 percent Al2O3;
        9 to 15 percent B2O3;
        greater than 0 to 4 percent M2O; and
        12 to 15 percent RO;
    
    


wherein, M is an alkali metal and wherein, R is an alkaline earth metal.
Further, the glasses shown in Table 8 have anneal points ≧640° C., thermal expansion coefficients (CTE) of 40-50×10−7/° C., 200 poise temperatures of ≦1550° C., and liquidus viscosities of ≧500,000 poise. Liquidus viscosity may be dependent on the K2O content, for example, exemplary glass 49 has a maximum value in excess of 5,000,000 poise for an intermediate K2O content when compared to exemplary glasses 48, 50, and 51.













TABLE 3








Glass
1
2
3
4
5





Weight Percent
SiO2
58.11
59.14
59.01
58.88
58.35



Al2O3
17.76
18.07
18.03
17.99
17.82



B2O3
9.79
9.96
9.94
9.92
9.82



MgO
3.26
4.45
3.88
3.31
3.27



CaO
4.03
4.10
4.87
5.64
4.04



SrO
2.85
0
0
0
0



BaO
0
0
0
0
0



Na2O
3.98
4.05
4.04
4.03
3.99



K2O
0
0
0
0
2.60



SnO2
0.23
0.23
0.23
0.23
0.12



Fe2O3
0
0
0
0
0



total
100.01
100
100
100
100.01


Mole Percent
SiO2
63.3
63.3
63.3
63.3
63.35



Al2O3
11.4
11.4
11.4
11.4
11.4



B2O3
9.2
9.2
9.2
9.2
9.2



MgO
5.3
7.1
6.2
5.3
5.3



CaO
4.7
4.7
5.6
6.5
4.7



SrO
1.8
0
0
0
0



BaO
0
0
0
0
0



Na2O
4.2
4.2
4.2
4.2
4.2



K2O
0
0
0
0
1.8



SnO2
0.1
0.1
0.1
0.1
0.05



Fe2O3
0
0
0
0
0



total
100
100
100
100
100


Properties
strain
593
598
606
597
588



anneal
642
647
656
646
638



softening point
867
868
882
874
881



CTE
44.9
44
43.5
46.4
50.1



density
2.447
2.332
2.414
2.422
2.393


Viscosity
A



−2.2233
−2.5584



B



5556.58
6588.87



To



305.47
220.27



T @ 200 p



1533.625
1576.164



T @ 35 kP



1126.554
1147.957



T @ 250 kP



1034.561
1048.398



T(200 P) − T(35 kP)



407.071
428.206


Resistivity
A



3.0838
3.9616



B



1183.49
4266.54



To



2156.83
3061.95



R @ 200 p



15.30245
12.30353


Liquidus
air
1070
1090
1065
1060
995



internal
1060
1080
1060
1050
980



Pt
1040
1050
1030
1040
975



phase
Albite
Albite
Albite
Albite
Albite



Liquidus viscosity



173742.1
1300909



Int liq - soft
193
212
178
176
99



estimated
107951.5
64408.99
168454.9
179256.1
4244242



liquidus viscosity


















Glass
6
7
8
9






Weight Percent
SiO2
58.40
58.54
58.74
58.56




Al2O3
17.83
17.88
17.94
17.88




B2O3
9.83
9.85
9.88
9.85




MgO
3.28
3.91
4.54
3.62




CaO
4.90
4.05
4.07
4.46




SrO
0
0
0
0




BaO
0
0
0
0




Na2O
3.04
3.05
2.10
3.34




K2O
2.60
2.61
2.62
2.17




SnO2
0.12
0.12
0.12
0.12




Fe2O3
0
0
0
0




total
100
100.01
100.01
100



Mole Percent
SiO2
63.35
63.35
63.35
63.35




Al2O3
11.4
11.4
11.4
11.4




B2O3
9.2
9.2
9.2
9.2




MgO
5.3
6.3
7.3
5.83




CaO
5.7
4.7
4.7
5.17




SrO
0
0
0
0




BaO
0
0
0
0




Na2O
3.2
3.2
2.2
3.5




K2O
1.8
1.8
1.8
1.5




SnO2
0.05
0.05
0.05
0.05




Fe2O3
0
0
0
0




total
100
100
100
100



Properties
strain
592
601
613
594




anneal
643
652
663
646




softening point
885
890
901
883




CTE
47.8
47
43.7
47.2




density
2.402
2.401
2.399
2.401



Viscosity
A








B








To








T @ 200 p








T @ 35 kP








T @ 250 kP








T(200 P) − T(35 kP)







Resistivity
A








B








To








R @ 200 p







Liquidus
air
1050
1040
1115
1030




internal
1040
1030
1105
1020




Pt
1020
1015
1075
1000




phase
Albite
Albite
Albite
Albite




Liquidus viscosity








Int liq - soft
155
140
204
137




estimated
360553.2
631087.4
79584.37
710936.1




liquidus viscosity






















TABLE 4








Glass
10
11
12
13
14





Weight Percent
SiO2
58.78
57.16
57.49
57.83
58.17



Al2O3
17.95
17.46
17.56
17.66
17.76



B2O3
9.89
9.62
9.67
9.73
9.79



MgO
3.96
3.21
3.48
3.76
4.04



CaO
4.88
3.96
4.34
4.72
5.11



SrO
0
0
0
0
0



BaO
0
0
0
0
0



Na2O
2.68
0
0
0
0



K2O
1.75
8.49
7.34
6.18
5.01



SnO2
0.12
0.11
0.11
0.11
0.12



Fe2O3
0
0
0
0
0



total
100.01
100.01
99.99
99.99
100


Mole Percent
SiO2
63.35
63.35
63.35
63.35
63.35



Al2O3
11.40
11.40
11.40
11.40
11.40



B2O3
9.20
9.20
9.20
9.20
9.20



MgO
6.36
5.30
5.72
6.14
6.56



CaO
5.64
4.70
5.12
5.54
5.96



SrO
0
0
0
0
0



BaO
0
0
0
0
0



Na2O
2.80
0
0
0
0



K2O
1.20
6.00
5.16
4.32
3.48



SnO2
0.05
0.05
0.05
0.05
0.05



Fe2O3
0
0
0
0
0



total
100
100
100
100
100


Properties
strain
604
608
621
624
632



anneal
655
661
674
675
685



softening point
885
914
911
916
925



CTE
44.5
52.1
48.9
45.6
44.1



density
2.411
2.382
2.389
2.393
2.397


Viscosity
A



−2.7798
−2.7896



B



6788.52
6506.53



To



263.53
291.74



T @ 200 p



1599.635
1569.878



T @ 35 kP



1190.434
1178.954



T @ 250 kP



1093.652
1086.427



T(200 P) − T(35 kP)



409.2009
390.9249


Resistivity
A



−2.6974
−3.1433



B



7362.61
7835.22



To



−175.21
−98.68



R @ 200 p



28.24312
35.68633


Liquidus
air
1040
990
980
1030
1070



internal
1030
980
970
1015
1065



Pt
1005
965
960
1000
1050



phase
Albite
Orthoclase
Orthoclase
Cordierite
Cordierite



Liquidus viscosity



1794130.5
421516.23



Int liq - soft
145
66
59
99
140



estimated
520319.01
39473174.9
73132031.9
4244242
631087.4



liquidus viscosity



















Glass
15
16
17
18
19






Weight Percent
SiO2
58.52
58.87
58.17
58.33
58.51




Al2O3
17.87
17.98
17.76
17.81
17.87




B2O3
9.85
9.91
9.79
9.82
9.84




MgO
4.33
4.61
4.04
4.05
4.06




CaO
5.50
5.90
5.11
5.54
5.99




SrO
0
0
0
0
0




BaO
0
0
0
0
0




Na2O
0
0
0
0
0




K2O
3.82
2.62
5.01
4.33
3.62




SnO2
0.12
0.12
0.12
0.12
0.12




Fe2O3
0
0
0
0
0




total
100.01
100.01
100
100
100.01



Mole Percent
SiO2
63.35
63.35
63.35
63.35
63.35




Al2O3
11.40
11.40
11.40
11.40
11.40




B2O3
9.20
9.20
9.20
9.20
9.20




MgO
6.98
7.40
6.56
6.55
6.55




CaO
6.38
6.80
5.96
6.45
6.95




SrO
0
0
0
0
0




BaO
0
0
0
0
0




Na2O
0
0
0
0
0




K2O
2.64
1.80
3.48
3.00
2.50




SnO2
0.05
0.05
0.05
0.05
0.05




Fe2O3
0
0
0
0
0




total
100
100
100
100
100



Properties
strain
631
639
630
630
635




anneal
683
689
683
682
687




softening point
914
913
921
918
922




CTE
41.5
39.6
43.3
41.6
40.4




density
2.412
2.43
2.4
2.404
2.408



Viscosity
A









B









To









T @ 200 p









T @ 35 kP









T @ 250 kP









T(200 P) − T(35 kP)








Resistivity
A









B









To









R @ 200 p








Liquidus
air
1110
1135
1085
1070
1075




internal
1100
1125
1070
1065
1060




Pt
1080
1105
1060
1050
1045




phase
Cordierite
Cordierite
Cordierite
Cordierite
Cordierite




Liquidus viscosity









Int liq - soft
186
212
149
147
138




estimated
132273.398
64408.987
447990.94
482556.71
683059.804




liquidus viscosity






















TABLE 5








Glass
20
21
22
23
24





Weight Percent
SiO2
57.49
57.65
57.82
58.47
57.78



Al2O3
17.55
17.6
17.65
17.86
17.64



B2O3
10.85
10.88
10.91
9.84
10.9



MgO
4
4
4.02
4.06
4.02



CaO
5.04
5.48
5.92
5.99
5.92



SrO
0
0
0
0
0



BaO
0
0
0
0
0



Na2O
0
0
0
0
0



K2O
4.95
4.28
3.57
3.62
3.57



SnO2
0.12
0.12
0.12
0.16
0.16



Fe2O3
0
0
0
0
0



total
100
100.01
100.01
100
99.99


Mole Percent
SiO2
62.65
62.65
62.65
63.33
62.63



Al2O3
11.27
11.27
11.27
11.40
11.27



B2O3
10.20
10.20
10.20
9.20
10.20



MgO
6.50
6.48
6.49
6.55
6.49



CaO
5.89
6.38
6.87
6.95
6.87



SrO
0
0
0
0
0



BaO
0
0
0
0
0



Na2O
0
0
0
0
0



K2O
3.44
2.97
2.47
2.50
2.47



SnO2
0.05
0.05
0.05
0.07
0.07



Fe2O3
100
100
100
100
100



total







Properties
strain
623
630
632
637
630



anneal
673
680
682
688
680



softening point
916
913
914
922
918



CTE
43.7
42.2
40.3
41.1
41



density
2.394
2.395
2.401
2.411
2.405


Viscosity
A



−2.826
−2.7517



B



6611.93
6318.79



To



284.22
304.73



T @ 200 p



1573.842
1555.299



T @ 35 kP



1181.353
1170.820



T @ 250 kP



1088.206
1080.076



T(200 P) − T(35 kP)



392.489
384.480


Resistivity
A



−4.9927
−2.6521



B



13663.94
5980.3



To



−556.65
129.56



R @ 200 p



26.35204
34.86784


Liquidus
air
1040
1050
1065
1060
1040



internal
1035
1045
1050
1055
1030



Pt
1020
1025
1030
1040
1020



phase
Cordierite
Cordierite
Cordierite
Cordierite
Cordierite



Liquidus viscosity



565239.4
913330.2



Int liq - soft
119
132
136
133
112



estimated
1542714
872242.2
740167
836776.9
2153251



liquidus viscosity


















Glass
25
26
27
28






Weight Percent
SiO2
58.61
57.36
56.92
58.14




Al2O3
17.27
17.51
17.39
17.03




B2O3
9.86
10.82
10.74
10.45




MgO
4
3.98
3.96
3.85




CaO
6.3
6.61
7.31
5.67




SrO
0
0
0
0




BaO
0
0
0
0




Na2O
0
0
0
0




K2O
3.84
3.55
3.52
4.69




SnO2
0.12
0.16
0.16
0.16




Fe2O3
0
0
0
0




total
100
99.99
100
99.99



Mole Percent
SiO2
63.35
62.10
61.55
63.15




Al2O3
11.00
11.17
11.08
10.90




B2O3
9.20
10.11
10.02
9.8




MgO
6.45
6.43
6.38
6.23




CaO
7.30
7.67
8.47
6.60




SrO
0
0
0
0




BaO
0
0
0
0




Na2O
0
0
0
0




K2O
2.65
2.45
2.43
3.25




SnO2
0.05
0.07
0.07
0.07




Fe2O3
100
100
100
100




total







Properties
strain
633
628
630
624




anneal
683
677
677
674




softening point
918
907
901
911




CTE
41.9
42
43.2
44.1




density
2.412
2.414
2.424
2.404



Viscosity
A
−2.6477
−3.0308
−2.8977
−3.0702




B
6160.22
6642.81
6307
6906.16




To
314.38
271.68
291.74
253.21




T @ 200 p
1559.188
1517.558
1504.921
1538.979




T @ 35 kP
1170.945
1148.634
1139.254
1160.212




T @ 250 kP
1080.039
1059.794
1052.019
1068.756




T(200 P) − T(35 kP)
388.243
368.924
365.667
378.766



Resistivity
A
−2.6628
−2.9715
−2.7071
−3.4632




B
6172.99
6668.56
5845.08
8147.16




To
100.8
50.95
149.34
−101.76




R @ 200 p
37.14907
37.62072
40.24979
31.79388



Liquidus
air
1065
1060
1025
1010




internal
1050
1050
1015
1000




Pt
1040
1030
1000
990




phase
Anorthite
Anorthite
Anorthite
Anorthite




Liquidus viscosity
532706.2
319158
664567.2
1505199




Int liq - soft
132
143
114
89




estimated
872242.2
561623.8
1953516
7623399




liquidus viscosity



























TABLE 6






Glass
29
30
31
32
33
34
35
36
37
38


























Weight
SiO2
56.19
56.33
56.46
56.6
56.72
56.48
57.32
58.17
57.29
56.92


Percent
Al2O3
17.45
17.01
16.56
16.11
15.66
17.77
17.52
17.27
17.03
16.63



B2O3
11.27
10.63
9.98
9.33
8.68
11.17
9.70
8.21
9.26
9.38



MgO
2.78
2.61
2.43
2.26
2.08
2.76
2.39
2.01
2.27
2.29



CaO
4.62
4.36
4.10
3.84
3.58
4.57
3.94
3.31
3.77
3.84



SrO
5.83
5.52
5.20
4.89
4.57
5.76
5.00
4.23
4.79
4.88



BaO
0
0
0
0
0
0
0
0
0
0



Na2O
1.68
3.37
5.06
6.77
8.48
1.30
3.92
6.56
5.39
5.86



K2O
0
0
0
0
0
0
0
0
0
0



SnO2
0.18
0.18
0.21
0.21
0.23
0.18
0.20
0.23
0.21
0.21



Fe2O3
0
0
0
0
0
0
0
0
0
0



total
100
100.01
100
100.01
100
99.99
99.99
99.99
100.01
100.01


Mole
SiO2
62.18
62.16
62.14
62.12
62.10
62.56
63.28
64.00
63.08
62.60


Percent
Al2O3
11.38
11.06
10.74
10.42
10.10
11.60
11.40
11.20
11.05
10.78



B2O3
10.76
10.12
9.48
8.84
8.20
10.68
9.24
7.80
8.80
8.90



MgO
4.58
4.29
3.99
3.70
3.40
4.56
3.93
3.30
3.72
3.75



CaO
5.48
5.16
4.84
4.52
4.20
5.42
4.66
3.90
4.45
4.52



SrO
3.74
3.53
3.32
3.11
2.90
3.70
3.20
2.70
3.06
3.11



BaO
0
0
0
0
0
0
0
0
0
0



Na2O
1.80
3.60
5.40
7.20
9.00
1.40
4.20
7.00
5.75
6.25



K2O
0
0
0
0
0
0
0
0
0
0



SnO2
0.08
0.08
0.09
0.09
0.10
0.08
0.09
0.10
0.09
0.09



Fe2O3
0
0
0
0
0
0
0
0
0
0



total
100
100
100
100
100
100
100
100
100
100


Proper-
strain
611
590
578
565

620
589
577
577
576


ties
anneal
659
636
622
607

670
635
623
625
621



softening
887.1
856.5
831.1
807.2
780
899.5
866.3
850.5
843
836.1



point













CTE
41.6
47.7
53.9
59.6

40.4
48.1
56.6
52.8
55.4



density
2.478
2.48
2.492
2.494
2.501
2.472
2.467
2.463
2.472
2.478


Viscos-
A
−2.475
−2.209
−2.175
−2.086
−1.813

−2.817

−2.501
−1.845


ity
B
5764.2
5523.2
5563.1
5506.2
4988.5

6843.6

6402.1
5180.5



To
306
290.2
258.9
231
242.7

193.3

197.4
272



 200
1512.9
1514.85
1501.76
1486.11
1455.26

1530.46

1530.61
1521.51



 3000
1274.43
1261.55
1243.15
1220.77
1185.68

1280.6

1268.32
1245.39



30000
1135.13
1116.27
1095.19
1069.96
1035.77

1131.54

1114.85
1091.42



50000
1109.49
1089.74
1068.2
1042.53
1008.75

1103.84

1086.58
1063.64


Liquidus
internal
1010
1025
1040
1020
980
1030
1020
1070
1010
1040



Liquidus
516159.7
203050.1
88539.17
78110.11
89722.76



238527.3
79513.84



viscosity













Int liq -
122.9
168.5
208.9
212.8
200
130.5
153.7
219.5
167
203.9



soft


























TABLE 7






Glass
39
40
41
42
43
44
45
46
47

























Weight
SiO2
56.76
57.00
57.33
57.72
58.11
59.01
56.88
57.06
57.30


Percent
Al2O3
17.19
16.95
17.52
17.64
17.76
15.66
17.09
16.32
17.52



B2O3
10.19
9.6
9.66
9.72
9.79
9.84
10.20
10.72
9.70



MgO
2.50
2.35
2.37
2.81
3.26
2.45
2.56
2.65
2.39



CaO
4.17
3.92
3.97
4.00
4.03
4.01
4.15
4.36
3.94



SrO
5.24
4.98
5.00
3.93
2.85
5.04
5.16
5.42
5.00



BaO
0
0
0
0
0
0
0
0
0



Na2O
3.74
4.99
3.92
3.95
3.98
3.77
3.74
0
3.92



K2O
0
0
0
0
0
0
0
3.24
0



SnO2
0.20
0.20
0.23
0.23
0.23
0.23
0.23
0.23
0.23



Fe2O3
0
0
0
0
0
0
0
0
0



total
99.99
99.99
100
100
100.01
100.01
100.01
100
100


Mole
SiO2
62.63
62.78
63.3
63.3
63.30
64.6
62.7
63.50
63.28


Percent
Al2O3
11.18
11.00
11.40
11.40
11.40
10.10
11.10
10.70
11.40



B2O3
9.70
9.13
9.20
9.20
9.20
9.30
9.70
10.30
9.24



MgO
4.12
3.86
3.90
4.60
5.30
4.00
4.20
4.40
3.93



CaO
4.93
4.63
4.70
4.70
4.70
4.70
4.90
5.20
4.66



SrO
3.35
3.18
3.20
2.50
1.80
3.20
3.30
3.50
3.20



BaO
0
0
0
0
0
0
0
0
0



Na2O
4.00
5.33
4.20
4.20
4.20
4.00
4.00
0.00
4.20



K2O
0
0
0
0
0
0
0
2.3
0



SnO2
0.09
0.09
0.10
0.10
0.10
0.10
0.10
0.10
0.10



Fe2O3
0
0
0
0
0
0
0
0
0



total











Properties
strain
589
578
596
597
596
590
593
619
597



anneal
638
626
643
644
645
637
640
669
645



softening point
858.5
843.2
867.6
867
876.9
859.5
858.5
898
873



CTE
48.4
51.7
48.1
47.3
46.1
47.6
48
44.2
47.2



density
2.477
2.474
2.475
2.466
2.451
2.472
2.476
2.465
2.466


Viscosity
A
−2.549
−2.625



−2.625

−2.567




B
6218.5
6434.5



6434.5

6097.1




To
233.8
223.8



223.8

303.3




 200
1515.96
1530.02



1530.02

1555.78




 3000
1265.72
1278.27



1278.27

1312.07




30000
1118.85
1129.8



1129.8

1168.86




50000
1091.76
1102.35



1102.35

1142.43



Liquidus
internal
1045
1040
1095
1080
1060
1015
1060
1050
1065



Liquidus
130859
181336.2



321798.1

396638.1




viscosity












Int liq - soft
186.5
196.8
227.4
213
183.1
155.5
201.5
152
192





















TABLE 8






Glass
48
49
50
51




















Mole Percent
SiO2
63
62.95
62.9
62.85



Al2O3
11
10.3
9.65
9



B2O3
10.2
11.6
13.05
14.5



MgO
5.5
4.13
2.75
1.38



CaO
6.1
4.6
3.05
1.53



SrO
1.8
1.43
1.05
1.68



BaO
0
3.1
6.15
9.22



K2O
2.4
1.8
1.2
0.6



SnO2
0.1
0.1
0.1
0.1


Weight Percent
SiO2
57.2
54.9
52.9
51



Al2O3
16.9
15.3
13.8
12.4



B2O3
10.7
11.7
12.7
13.6



MgO
3.34
2.42
1.55
0.75



CaO
5.17
3.74
2.4
1.16



SrO
2.81
2.16
1.53
0.95



BaO
0
6.91
13.2
19.1



K2O
3.41
2.47
1.58
0.76



SnO2
0.23
0.22
0.21
0.2


Properties
strain
628
609
603
598



anneal
678
659
651
644



softening
909
890
876
858



CTE
42.8
43.9
45.4
46



Density
2.44
2.516
2.606
2.677


Viscosity
200
1529
1525
1528




Internal Liquidus
1020
940
980
980



Liquidus Viscosity
822,000
5,233,000
1,100,000









The alkalis in the glass according to the present invention and low melting temperature combine to accelerate melting thus enabling high volume, low-cost melting and forming relative to alkali-free alternatives while retaining competitive properties, including in particular mechanical and dimensional stability when reheated to high temperature. These glasses are well suited for large-volume sheet glass applications, particularly OLED lighting and cadmium telluride (CdTe) photovoltaics, for which thermal stability, large volumes, and low cost are desirable substrate attributes.
It will be apparent to those skilled in the art that various modifications and variations can be made to the present invention without departing from the spirit or scope of the invention. Thus, it is intended that the present invention cover the modifications and variations of this invention provided they come within the scope of the appended claims and their equivalents.

## Claims

1. A glass comprising, in mole percent:
60 to 65 percent SiO2;
8 to 12 percent Al2O3;
7 to 15 percent B2O3;
0.1 to 8 percent M2O;
9 to 15 percent RO; and
0.01 to 0.4 percent SnO2,
wherein, M is an alkali metal and wherein, R is an alkaline earth metal.

2. The glass according to claim 1, comprising, in mole percent:
61 to 64 percent SiO2;
8 to 12 percent Al2O3;
9 to 15 percent B2O3;
0.1 to 4 percent M2O; and
12 to 15 percent RO;
wherein, M is an alkali metal and wherein, R is an alkaline earth metal.

3. The glass according to claim 1, comprising, in mole percent:
60 to 65 percent SiO2;
8 to less than 10 percent Al2O3;
greater than 11 to 15 percent B2O3;
0.1 to less than 1 percent M2O; and
9 to 15 percent RO;
wherein, M is an alkali metal and wherein, R is an alkaline earth metal.

4. The glass according to claim 1, comprising, in mole percent:
60 to 65 percent SiO2;
10 to 12 percent Al2O3;
7 to 11 percent B2O3;
1 to 8 percent M2O; and
9 to 15 percent RO;
wherein, M is an alkali metal and wherein, R is an alkaline earth metal.

5. The glass according to claim 1, wherein M is selected from Li, Na, K, Rb, Cs, and a combination thereof.

6. The glass according to claim 5, wherein M is selected from Li, K, Cs and a combination thereof.

7. The glass according to claim 1, wherein R is selected from Mg, Ca, Sr, Ba, and a combination thereof.

8. The glass according to claim 7, wherein R is selected from Mg, Ca, Sr, and a combination thereof.

9. The glass according to claim 1, comprising 62 to 65 percent SiO2.

10. The glass according to claim 1, comprising:
62 to 65 percent SiO2;
10 to 12 percent Al2O3;
7 to 11 percent B2O3;
3 to 8 percent MgO;
3 to 9 percent CaO;
3 to 8 percent SrO; and
1 to 8 percent M2O;
wherein, M is an alkali metal selected from K, Na, and combinations thereof.

11. The glass according to claim 1, wherein the glass is down-drawable.

12. The glass according to claim 1, wherein the glass is slot drawn or fusion drawn.

13. The glass according to claim 1, wherein the glass is float formed.

14. The glass according to claim 1, wherein the glass is substantially free of BaO.

15. The glass according to claim 1, wherein the glass is substantially free of Sb2O3, As2O3, or combinations thereof.

16. The glass according to claim 1, wherein the glass is ion exchanged in a salt bath comprising one or more salts of alkali metal ions.

17. The glass according to claim 1, further comprising 2 mole percent or less of TiO2, MnO, ZnO, Nb2O5, MoO3, Ta2O5, WO3, ZrO2, Y2O3, La2O3, P2O5, or combinations thereof.

18. The glass according to claim 1, having a strain point of 600° C. or greater.

19. The glass according to claim 1, having a coefficient of thermal expansion of 38×10−7 /° C. or greater.

20. The glass according to claim 1, having a coefficient of thermal expansion of 45×10−7 /° C. or greater.

21. The glass according to claim 1, having a strain point of 620° C. or greater and a coefficient of thermal expansion of 45×10−7 /° C. or greater.

22. The glass according to claim 1, having a liquidus viscosity of 50,000 poise or greater.

23. The glass according to claim 22, having a liquidus viscosity of 150,000 poise or greater.

24. The glass according to claim 1, wherein CaO/(CaO +SrO) is from 0.4 to 1.

25. The glass according to claim 1, wherein the glass is in the form of a sheet.

26. The glass according to claim 25, wherein the glass is thermally tempered.

27. An Organic Light Emitting Diode device comprising the glass according to claim 25.

28. A photovoltaic device comprising the glass according to claim 25.

29. The photovoltaic device according to claim 28, further comprising an active photovoltaic medium adjacent to the glass.

30. The photovoltaic device according to claim 29, wherein the active photovoltaic medium comprises cadmium telluride, copper indium gallium diselenide, amorphous silicon, crystalline silicon, microcrystalline silicon, or combinations thereof.