Flat panel liquid crystal display such as for a laptop computer, having alkali-free aluminoborosilicate glass

Abstract

Flat panel liquid-crystal displays, such as for laptop computers. The displays include twisted nematic displays, supertwisted nematic displays, active matrix liquid-crystal displays, thin film transistor displays, and plasma addressed liquid-crystal displays. The displays are furnished with glass substrates. The glass substrates exhibit high resistance to thermal shock, a high transparency over a broad spectral range in the visible and ultra violet ranges and the glass being configured to be free of bubbles, knots, inclusions, streaks, and surface undulations, which glass substrates are made from alkali-free aluminoborosilicate glasses. There are also provided analogous thin-film photovoltaics.

Description

BACKGROUND OF THE INVENTION

1. Field of the Invention

The invention relates to an alkali-free aluminoborosilicate glass. The invention also relates to uses of this glass.

2. Background of the Invention

High requirements are made of glasses for applications as substrates in flat-panel liquid-crystal (or expressed differently: liquid crystal) display technology, for example in TN (twisted nematic)/STN (supertwisted nematic, or expressed differently: super twisted) displays, active matrix liquid crystal displays (AMLCDs), thin film transistors (TFTs) or plasma addressed liquid crystals (PALCs). Besides high thermal shock resistance and good resistance to the aggressive chemicals employed in the process for the production of flat-panel screens, the glasses should have high transparency over a broad spectral range (VIS, UV) and, in order to save weight, a low density. Use as substrate material for integrated semiconductor circuits, for example in TFT displays (“chip on glass”) in addition requires thermal matching to the thin-film material silicon which is usually deposited on the glass substrate in the form of amorphous silicon (a-Si) at low temperatures of up to 300° C. The amorphous silicon is partially recrystallized by subsequent heat treatment at temperatures of about 600° C. Owing to the a-Si fractions, the resulting, partially crystalline poly-Si layer is characterized by a thermal expansion coefficient of α 20/300 ≅3.7×10 −6 /K. Depending on the a-Si/poly-Si ratio, the thermal expansion coefficient α 20/300 may vary between 2.9×10 −6 /K and 4.2×10 −6 /K. When substantially crystalline Si layers are generated by high temperature treatments above 700° C. or direct deposition by CVD processes, which is likewise desired in thin-film photovoltaics, a substrate is required which has a significantly reduced thermal expansion of 3.2×10 −6 /K or less. In addition, applications in display and photovoltaics technology require the absence of alkali metal ions. Sodium oxide levels of less than 1000 ppm (parts per million) as a result of production can be tolerated in view of the generally “poisoning” action due to diffusion of Na + into the semiconductor layer.

It should be possible to produce suitable glasses economically on a large industrial scale in adequate quality (no bubbles, knots, inclusions), for example in a float plant or by drawing methods. In particular, the production of thin (<1 mm) streak-free substrates with low surface undulation by drawing methods requires high devitrification stability of the glasses. In order to counter compaction of the substrate during production, in particular in the case of TFT displays, which has a disadvantageous effect on the semiconductor microstructure, the glass needs to have a suitable temperature-dependent viscosity characteristic line: with respect to thermal process and shape stability, it should have a sufficiently high glass transition temperature, i.e. T g >700° C., while on the other hand not having excessively high melting and processing (V A ) temperature, i.e. a V A of ≦1350° C.

The requirements of glass substrates for LCD display technology or thin-film photovoltaics technology are also described in “Glass substrates for AMLCD applications: properties and implications” by J. C. Lapp, SPIE Proceedings, Vol. 3014, invited paper (1997), and in “Photovoltaik—Strom aus der Sonne” by J. Schmid, Verlag C. F. Muller, Heidelberg 1994, respectively.

The abovementioned requirement profile is fulfilled best by alkaline earth metal aluminoborosilicate glasses. However, the known display or solar cell substrate glasses described in the following publications still have disadvantages and do not meet the full list of requirements.

Some documents describe glasses containing relatively little or no BaO, e.g. European Patent No. 714 862 B1, International Patent Application No. 98/27019, Japanese Patent No. 10-72237 A and European Patent No. 510 544 B1. Glasses of this type, in-particular those having low coefficients of thermal expansion, i.e. low RO content and high network former content, are very susceptible to crystallization. Furthermore, most of the glasses, in particular in EP 714862 B1 and JP 10-72237 A, have high temperatures at a viscosity of 10 2 dPas.

However, the preparation of display glasses having high levels of the heavy alkaline earth metal oxides BaO and/or SrO is likewise associated with great difficulties owing to the poor meltability of the glasses. In addition, glasses of this type, as described, for example, in DE 37 30 410 A1, U.S. Pat. Nos. 5,116,789, 5,116,787, EP 341 313 B1, EP 510 543 B1 and JP 9-100135 A, have an undesirably high density.

Even glasses having relatively low SrO contents in combination with moderate to high BaO levels have unfavorable viscosity characteristic lines with respect to their meltability, for example the glasses described in JP 9-169538 A, WO 97/11920 and JP 4-160030 A.

Glasses having relatively high levels of light alkaline earth metal oxides, in particular MgO, as described, for example, in JP 9-156953 A, JP 8-295530 A, JP 9-48632 A and DE 197 39 912 C1, exhibit good meltability and have a low density. However, they do not meet all requirements made of display and solar cell substrates with regard to chemical resistance, in particular to buffered hydrofluoric acid, to crystallization stability and to heat resistance. Glasses having low boric acid contents exhibit excessively high melting-temperatures or, as a result of this, excessively high viscosities at the melt and processing temperatures required for processes involving these glasses. This applies to the glasses of JP 10-45422 A and JP 9-263421 A.

Moreover, glasses of this type have a high devitrification tendency when combined with low BaO contents.

In contrast, glasses having high boric acid contents, as described, for example, in U.S. Pat. No. 4,824,808, have insufficient heat resistance and chemical resistance, in particular to hydrochloric acid solutions.

Glasses having a relatively low SiO 2 content do not have sufficiently high chemical resistance either, in particular when they contain relatively large amounts of B 2 O 3 and/or MgO and are low in alkaline earth metals. This applies to the glasses of WO 97/11919 and EP 672 629 A2. The relatively SiO 2 -rich variants of the latter document have only low Al 2 O 3 levels, which is disadvantageous for the crystallization behavior.

The glasses described in Japanese Patent No. 9-12333 A for hard disks are comparatively low in Al 2 O 3 or B 2 O 3 , the latter merely being optional. The glasses have high alkaline earth metal oxide contents and have high thermal expansion, which makes them unsuitable for use in LCD or PV technology.

Federal Republic of Germany Patent No. 196 17 344 C1 (U.S. Pat. No. 5,908,703) and Federal Republic of Germany Patent No. 196 03 698 C1 (U.S. Pat. No. 5,770,535) by the Applicant disclose alkali-free, tin oxide-containing glasses having a coefficient of thermal expansion α 20/500 of about 3.7×10 −6 /K and very good chemical resistance. They are suitable for use in display technology. However, since they must contain ZnO, they are not ideal, in particular for processing in a float plant.

In particular at higher ZnO contents (>1.5% by weight), there is a risk of formation of ZnO coatings on the glass surface by evaporation and subsequent condensation in the hot-shaping range.

Federal Republic of Germany Patent No. 196 01 022 A1 describes glasses which are selected from a very wide composition range and which must contain ZrO 2 and SnO. The glasses, which, according to the examples, contain SrO, tend to exhibit glass defects because of their ZrO 2 level.

Federal Republic of Germany Patent No. 42 13 579 A1 describes glasses for TFT applications having a coefficient of thermal expansion α 20/300 Of <5.5×10 −6 /K, according to the examples of ≧4.0×10 −6 /K. These glasses which have relatively high B 2 O 3 levels and relatively low SiO 2 contents do not have a high chemical resistance, in particular to diluted hydrochloric acid.

U.S. Pat. No. 5,374,595 describes glasses having coefficients of thermal expansion of between 3.2×10 −6 /K and 4.6×10 −6 /K. The glasses which, as the examples illustrate, have high BaO contents, are relatively heavy and exhibit poor meltability and a thermal expansion which is not ideally matched to substantially crystalline Si.

In the unexamined Japanese publication nos. 10-25132 A, 10-114538 A, 10-130034 A, 10-59741 A, 10-324526 A, 11-43350 A, 11-49520 A, 10-231139 A and 10-139467 A, mention is made of very wide composition ranges for display glasses, which can be varied by means of many optional components and which are admixed with one or more specific refining agents in each case. However, these documents do not indicate how glasses having the complete requirement profile described above can be obtained in a specific manner.

OBJECT OF THE INVENTION

It is an object of the present invention to provide glasses which meet said complex requirement profile with respect to the physical and chemical properties which is imposed on glass substrates for liquid-crystal displays, and for thin-film solar cells, in particular on the basis of μc-Si, glasses which have high heat resistance, a favorable processing range and sufficient devitrification stability.

SUMMARY OF THE INVENTION

The invention teaches that this object can be accomplished by an aluminoborosilicate glass having a coefficient of thermal expansion α 20/300 of between 2.8×10 −6 /K and 3.8×10 −6 /K, which has the following composition (in % by weight, based on oxide): silicon dioxide (SiO 2 )—from somewhat greater than 58% to 65% (>58%-65%); boric oxide (B 2 O 3 )—from somewhat greater than 6% to 10.5% (>6%-10.5%); aluminum oxide (Al 2 O 3 )−from somewhat greater than 14% to 25 (>14%-25%); magnesium oxide (MgO)−from 0% to somewhat less than 3% (0%-<3%); calcium oxide (CaO)−from 0% to 9% (0%-9%); barium oxide (BaO)−from somewhat less than 3% to 8% (>3%-8%); with magnesium oxide (MgO)+calcium oxide (Cao)+barium oxide (BaO)−from 8% to 18% (8%-18%); and zinc oxide (ZnO)−from 0%−to somewhat less than 2% (0%-<2%).

The glass contains between >58 and 65% by weight of SiO 2 . At lower contents, the chemical resistance is impaired, while at higher levels, the thermal expansion is too low and the crystallization tendency of the glass increases.

The glass contains relatively high levels of Al 2 O 3 , i.e. >14-25% by weight, preferably 18-25% by weight. Such Al 2 O 3 levels are favorable for the crystallization stability of the glass and have a positive effect on its heat resistance without excessively increasing the processing temperature. Preference is given to a content of more than 18% by weight, particularly preferably of at least 20.5% by weight, most preferably of at least 21.5% by weight, of Al 2 O 3 .

The B 2 O 3 content is >6-10.5% by weight, preferably >8-10.5% by weight. The B 2 O 3 content is restricted to the maximum content specified in order to achieve a high glass transition temperature T g . Higher contents would also impair the chemical resistance to hydrochloric acid solutions. The minimum B 2 O 3 content specified serves to ensure that the glass has good meltability and good crystallization stability. The network-forming components Al 2 O 3 and B 2 O 3 are preferably present at mutually dependent minimum levels, ensuring a preferred content of the network formers SiO 2 , Al 2 O 3 and B 2 O 3 . For example, in the case of a B 2 O 3 content of >6-10.5% by weight, the minimum Al 2 O 3 content is preferably >18% by weight, and in the case of an Al 2 O 3 content of >14-25% by weight, the minimum B 2 O 3 content is preferably >8% by weight. Preferably, in particular to achieve very low thermal expansion coefficients of up to 3.6×10 −6 /K, the sum of SiO 2 , B 2 O 3 and Al 2 O 3 is more than 84% by weight.

An essential glass component are the network-modifying alkaline earth metal oxides. In particular by varying their levels, a coefficient of thermal expansion α 20/300 of between 2.8×10 −6 /K and 3.8×10 −6 /K is achieved within a sum content of 8-18% by weight in total. The maximum sum of alkaline earth metal oxides is preferably 15% by weight, particularly preferably 12% by weight. The latter upper limit is in particular advantageous for obtaining glasses having very low α 20/300 <3.2×10 −6 /K) coefficients of thermal expansion. BaO is always present, while MgO and CaO are optional components. Preferably at least two alkaline earth metals are present, particularly preferably all three alkaline earth metals mentioned are present.

The BaO content is between >3 and 8% by weight. These relatively high BaO levels were found to ensure a sufficient crystallization stability for the various flat glass production processes such as float methods and the various drawing methods, in particular in the case of low-expansion glass variants having quite high levels of network-forming components and thus a crystallization tendency which is in principle rather high. The maximum BaO content is preferably limited to 5% by weight, particularly preferably 4% by weight, most preferably <4% by weight, which has a positive effect on the desired low density of the glasses.

SrO is omitted, thus maintaining low melting and hot shaping temperatures and a low density of the glass. However, minor amounts, i.e. less than 0.1% by weight, introduced into the glass melt as impurities of the batch raw materials, can be tolerated.

The glasses may furthermore contain up to 9% by weight of CaO. Higher levels would lead to an excessive increase in thermal expansion and an increase in crystallization tendency. The glass preferably contains at least 2% by weight of CaO.

The glass may also contain up to <3% by weight of MgO. Relatively high levels are beneficial for a low density and a low processing temperature, whereas relatively low levels are favorable with regard to the chemical resistance of the glass, in particular to buffered hydrofluoric acid, and its devitrification stability.

The glasses may furthermore contain up to <2% by weight of ZnO. ZnO has an effect on the viscosity characteristic line which is similar to that of boric acid, has a structure-loosening function and has less effect on the thermal expansion than the alkaline earth metal oxides. The maximum ZnO level is preferably limited to 1.5% by weight, particularly preferably 1.0% by weight, most preferably less than 1% by weight, in particular when the glass is processed by the float method. Higher levels would increase the risk of unwanted ZnO coatings on the glass surface which may form by evaporation and subsequent condensation in the hot-shaping range. The presence of at least 0.1% by weight is preferred, as the addition of ZnO, even in small amounts, leads to an increase in devitrification stability.

The glass is alkali-free. The term “alkali-free” as used herein means that it is essentially free from alkali metal oxides, although it can contain impurities of less than 1000 ppm (parts per million).

The glass may contain up to 2% by weight of ZrO 2 +TiO 2 , where both the TiO 2 content and the ZrO 2 content can each be up to 2% by weight. ZrO 2 advantageously increases the heat resistance of the glass. Owing to its low solubility, ZrO 2 does, however, increase the risk of ZrO 2 -containing melt relicts, so-called zirconium nests, in the glass. ZrO 2 is therefore preferably omitted. Low ZrO 2 contents originating from corrosion of zirconium-containing trough material are unproblematic. TiO 2 advantageously reduces the solarization tendency, i.e. the reduction in transmission in the visible wavelength region because of UV-VIS radiation. At contents of greater than 2% by weight, color casts can occur due to complex formation with Fe 3 + ions which are present in the glass at low levels as a result of impurities of the raw materials employed.

The glass may contain conventional refining agents in the usual amounts: it may thus contain up to 1.5% by weight of As 2 O 3 , Sb 2 O 3 , SnO 2 , CeO 2 , C1 − (for example in the form of BaCl 2 ), F − (for example in the form of CaF 2 ) and/or SO 4 2− (for example in the form of BaSO 4 ). The sum of the refining agents should, however, not exceed 1.5% by weight. If the refining agents As 2 O 3 and Sb 2 O 3 are omitted, this glass can be processed not only using a variety of drawing methods, but also by the float method.

For example with regard to easy batch preparation, it is advantageous to be able to omit both ZrO 2 and SnO 2 and still obtain glasses having the property profile mentioned above, in particular having high heat and chemical resistance and low crystallization tendency.

The above-discussed embodiments of the present invention will be described further hereinbelow. When the word “invention” is used in this specification, the word “invention” includes “inventions”, that is the plural of “invention”. By stating “invention”, the Applicants do not in any way admit that the present application does not include more than one patentably and non-obviously distinct invention, and maintains that this application may include more than one patentably and non-obviously distinct invention. The Applicants hereby assert that the disclosure of this application may include more than one invention, and, in the event that there is more than one invention, that these inventions may be patentable and non-obvious one with respect to the other.

DESCRIPTION OF THE PREFERRED EMBODIMENT

The invention is further described with reference to examples, i.e. working examples, as follows.

WORKING EXAMPLES

Glasses were produced in Pt/Ir crucibles at 1620° C. from conventional raw materials which were essentially alkali-free apart from unavoidable impurities. The melt was refined at this temperature for one and a half hours, then transferred into inductively heated platinum crucibles and stirred at 1550° C. for 30 minutes for homogenization.

The Table shows fifteen examples of glasses according to the invention with their compositions (in % by weight, based on oxide) and their most important properties. The refining agent SnO 2 (Examples 1-8, 11, 12, 14, 15) or As 2 O 3 (Examples 9, 10, 13) at a level of 0.3% by weight is not listed. The following properties are given:

the coefficient of thermal expansion α 20/300 [10 −6 /K]

the density ρ [g/cm 3 ]

the dilatometric glass transition temperature T g [°C.] in accordance with DIN 52324

the temperature at a viscosity of 10 4 dPas (referred to as T 4 [°C.])

the temperature at a viscosity of 10 2 dPas (referred to as T 2 [°C.]), calculated from the Vogel-Fulcher-Tammann equation

the “HCl” acid resistance as weight loss (material removal value) from glass plates measuring 50 mm×50 mm×2 mm polished on all sides after treatment with 5% strength hydrochloric acid for 24 hours at 95° C. [mg/cm 2 ]

a “BHF” resistance to buffered hydrofluoric acid as weight loss (material removal value) from glass plates measuring 50 mm×50 mm×2 mm and polished on all sides after treatment with 10% strength NH 4 F.HF solution for 20 minutes at 23° C. [mg/cm 2 ]

the refractive index n d .

TABLE
Examples: Compositions (in % by weight, based on oxide) and
essential properties of glasses according to the
invention.
	1	2	3	4	5	6
SiO 2	60.0	60.0	59.9	58.9	59.9	61.0
B 2 O 3	7.5	7.5	7.5	8.5	7.5	9.5
Al 2 O 3	21.5	21.5	21.5	21.5	21.5	18.4
MgO	2.9	2.9	2.0	2.0	2.9	2.2
CaO	3.8	2.8	3.8	3.8	4.8	4.1
BaO	4.0	5.0	5.0	5.0	3.1	4.5
ZnO	—	—	—	—	—	—
α 20/300 [10 −6 /K]	3.07	3.00	3.01	3.08	3.13	3.11
ρ [g/cm 3 ]	2.48	2.48	2.48	2.48	2.47	2.45
T g [° C.]	747	748	752	741	743	729
T4 [° C.]	1312	1318	1315	1308	1292	1313
T2 [° C.]	1672	1678	1691	1668	1662	1700
n d	1.520	1.518	1.519	1.519	1.521	1.515
HCl [mg/cm 2 ]	1.05	n.m.	0.58	n.m.	1.1	n.m.
BHF [mg/cm 2 ]	0.57	0.58	0.55	0.55	0.56	0.49
	7	8	9	10	11	12
SiO 2	58.5	62.8	63.5	63.5	59.7	59.0
B 2 O 3	7.7	8.2	10.0	10.0	10.0	9.0
Al 2 O 3	22.7	16.5	15.4	15.4	18.5	17.2
MgO	2.8	0.5	2.0	1.0	—	2.0
CaO	2.0	4.2	5.6	6.6	8.3	9.0
BaO	5.0	7.5	3.2	3.2	3.2	3.5
ZnO	1.0	—	—	—	—	—
α 20/300 [10 −6 /K]	2.89	3.19	3.24	3.34	3.44	3.76
ρ [g/cm 3 ]	2.50	2.49	2.42	2.43	2.46	2.50
T g [° C.]	748	725	711	719	714	711
T4 [° C.]	1314	1325	1320	1327	1281	1257
T2 [° C.]	1674	1699	n.m.	n.m.	1650	1615
n d	1.520	1.513	1.511	1.512	1.520	1.526
HCl [mg/cm 2 ]	n.m.	0.30	0.89	n.m.	n.m.	0.72
BHF [mg/cm 2 ]	0.62	0.45	0.43	0.40	0.44	0.49
	13	14	15
SiO 2	61.4	59.5	63.9
B 2 O 3	8.2	10.0	10.4
Al 2 O 3	16.0	16.7	14.6
MgO	2.8	0.7	2.9
CaO	7.9	8.5	4.8
BaO	3.4	3.8	3.1
ZnO	—	0.5	—
α 20/300 [10 −6 /K]	3.75	3.60	3.21
ρ [g/cm 3 ]	2.48	2.48	2.41
T g [° C.]	709	702	701
T4 [° C.]	1273	1260	1311
T2 [° C.]	1629	1629	n.m.
n d	1.523	1.522	n.m.
HCl [mg/cm 2 ]	0.41	0.97	n.m.
BHF [mg/cm 2 ]	0.74	0.47	n.m.
n.m. = not measured

As the working examples illustrate, the glasses according to the invention have the following advantageous properties:

a thermal expansion α 20/300 of between 2.8×10 −6 /K and 3.8×10 −6 /K, in preferred embodiments <3.6×10 −6 /K, in particularly preferred embodiments <3.2×10 −6 /K, thus matched to the expansion behavior of both amorphous silicon and increasingly polycrystalline silicon.

T g >700° C., a very high glass transition temperature, i.e. a high heat resistance. This is essential for the lowest possible compaction as a result of production and for use of the glasses as substrates for coatings with amorphous Si layers and their subsequent annealing.

ρ<2.600 g/cm 3 , a low density

a temperature at a viscosity of 10 4 dPas (processing temperature V A ) of at most 1350° C., and a temperature at a viscosity of 10 2 dPas of at most 1720° C., which means a suitable viscosity characteristic line with regard to hot-shaping and meltability.

n d ≦1.526, a low refractive index. This property is the physical prerequisite for a high transmission of the glasses.

a high chemical resistance, as is evident inter alia from good resistance to buffered hydrofluoric acid solution, which makes them sufficiently inert to the chemicals used in the production of flat-panel screens.

The glasses have high thermal shock resistance and good devitrification stability. The glasses can be produced as flat glasses by the various drawing methods, for example microsheet down-draw, up-draw or overflow fusion methods, and, in a preferred embodiment, if they are free from As 2 O 3 and Sb 2 O 3 , also by the float process.

With these properties, the glasses are highly suitable for use as substrate glass in display technology, in particular for TFT displays, and in thin-film photovoltaics, in particular on the basis of amorphous and μc-Si.

Alkali-free aluminoborosilicate glass in accordance with the present invention may, for example, have any value of coefficient of thermal expansion α 20/300 in the range of between about 2.8×10 −6 /K and about 3.8×10 −6 /K, for example, 2.9 10 −6 /K and 3.7 10 −6 /K. Thus, the value of the coefficient of thermal expansion α 20/300 is not limited to the first and final values of the range, but can comprise any value of coefficient of thermal expansion α 20/300 between them.

The alkali-free aluminoborosilicate glass in accordance with the present invention may, for example, have any value (in % by weight, based on oxide) of silica, silicon dioxide (SiO 2 ) in the range of from about 58 to about 65, for example, 59 and 64. Thus, the value for SiO 2 , in % by weight, based on oxide, is not limited to the first and final values of the range, but can comprise any value of SiO 2 between them.

The alkali-free aluminoborosilicate glass in accordance with the present invention may, for example, have any value (in % by weight, based on oxide) of boric oxide (B 2 O 3 ) in the range of from about 6 to about 10.5, for example, 6.5 and 10. Thus, the value for B 2 O 3 , in % by weight, based on oxide, is not limited to the first and final values of the range, but can comprise any value of B 2 O 3 between them.

Similarly, the alkali-free aluminoborosilicate glass in accordance with the present invention may, for example, have any value (in % by weight, based on oxide) of alumina, aluminum oxide (Al 2 O 3 ) in the range of from about 14 to about 25, for example, 15 and 24. Thus, the value for Al 2 O 3 , in % by weight, based on oxide, is not limited to the first and final values of the range, but can comprise any value of Al 2 O 3 between them.

Thus, components of the composition of the alkali-free aluminoborosilicate glass in accordance with our invention are likewise not limited to the first and final values of the indicated range, but can comprise any value between them.

The expression “coefficient of thermal expansion α 20/300 ” may indicate the fractional change in the length or volume of a body per degree of temperature change for the range of from 20 to 300 degrees Celsius.

The expression μc-Si is to mean in at least one embodiment of the invention: micro-crystalline silicon.

The expression thermal expansion coefficient or coefficient of thermal expansion (α 20/300 ) in at least one embodiment of the invention is to mean: a nominal thermal coefficient (α) as possibly applicable in the temperature range of from 20 to 300 in the Celsius scale, as possibly applicable in the context of the indicated data.

The expression glass transition temperature (T g ) in at least one embodiment of the invention is to mean: (1) the temperature below which a substance becomes superconducting; or (2) the temperature at which one polymorph changes into the next thermodynamically stable state; as the shown technical data suggest.

The density (ρ) is to mean in at least one embodiment of the invention: (1) the mass of a substance per unit of volume, expressed as kilograms per cubic meter, or expressed in smaller units, grams per cubic centimeter; or (2) the degree of opacity of a translucent material; as the technical data suggest.

The term DIN refers to the German Standard Organization “Deutsches Institute für Normung e.V., in Berlin, Germany, from which the numbered standards may be obtained.

The Vogel-Fulcher-Tammann equation is possibly related to the Fulcher equation meaning empirical in derivation; it relates glass viscosity to temperature: logη=−A+B/T−T 0 where the temperature T is in degrees Celsius, A, B, and T 0 are material-specific constants.

One feature of the invention resides broadly in an alkali-free aluminoborosilicate glass having a coefficient of thermal expansion α 20/300 of between 2.8×10 −6 /K and 3.8×10 −6 /K, which has the following composition (in % by weight, based on oxide): SiO 2 >58-65; B 2 O 3 >6-10.5; Al 2 O 3 >14-25; MgO 0-<3; CaO 0-9; BaO>3-8 with MgO+CaO+BaO 8-18; ZnO 0-<2.

Another feature of the invention resides broadly in an Aluminoborosilicate glass, characterized in that it comprises more than 8% by weight of B 2 O 3 .

Yet another feature of the invention resides broadly in an Aluminoborosilicate glass, characterized in that it comprises more than 18% by weight of Al 2 O 3 , preferably at least 20.5% by weight of Al 2 O 3 .

Still another feature of the invention resides broadly in an Aluminoborosilicate glass, characterized in that it comprises at most 4% by weight of BaO.

A further feature of the invention resides broadly in an Aluminoborosilicate glass, characterized in that it comprises at least 0.1% by weight of ZnO.

Another feature of the invention resides broadly in an Aluminoborosilicate glass, characterized in that it additionally comprises ZrO 2 0-2; TiO 2 0-2; with ZrO 2 +TiO 2 0-2; As 2 O 3 0-1.5; Sb 2 O 3 0-1.5; SnO 2 0-1.5; CeO 2 0-1.5; C1 − 0-1.5; F − 0-1.5; SO 4 2− 0-1.5; or with As 2 O 3 +Sb 2 O 3 +SnO 2 +CeO 2 +Cl − +F − +SO 4 2− <1.5.

Yet another feature of the invention resides broadly in an Aluminoborosilicate glass, characterized in that the glass is free of arsenic oxide and antimony oxide, apart from unavoidable impurities, and that it can be produced in a float plant.

Still another feature of the invention resides broadly in an Aluminoborosilicate glass, which has a coefficient of thermal expansion α 20/300 of from 2.8×10 −6 /K to 3.6×10 −6 /K, preferably to 3.2×10 −6 /K, a glass transition temperature T g of >700° C. and a density ρ of <2.600 g/cm 3 .

A further feature of the invention resides broadly in the use of the aluminoborosilicate glass as substrate glass in display technology.

Yet another feature of the invention resides broadly in the use of the aluminoborosilicate glass as substrate glass in thin-film photovoltaics.

The features disclosed in the various publications, disclosed or incorporated by reference herein, may be used in the embodiments of the present invention, as well as, equivalents thereof.

All, or substantially all, of the components and methods of the various embodiments may be used with at least one embodiment or all of the embodiments, if more than one embodiment is described herein.

All of the patents, patent applications and publications recited herein, and in the Declaration attached hereto, are hereby incorporated by reference as if set forth in their entirety herein.

The corresponding foreign and international patent publication applications, namely, Federal Republic of Germany Patent Application No. 100 00 836.4-45, filed on Jan. 12, 2000, having inventors Dr. Ulrich PEUCHERT and Dr. Peter BRIX, as well as their published equivalents, and other equivalents or corresponding applications, if any, in corresponding cases in the Federal Republic of Germany and elsewhere, and the references cited in any of the documents cited herein, are hereby incorporated by reference as if set forth in their entirety herein, are hereby incorporated by reference as if set forth in their entirety herein.

The corresponding foreign and international patent publication applications, namely, Federal Republic of Germany Patent Application No. 100 00 838.0-45, filed on Jan. 12, 2000, [NHL-SCT-19] having inventors Dr. Ulrich PEUCHERT and Dr. Peter BRIX, as well as their published equivalents, and other equivalents or corresponding applications, if any, in corresponding cases in the Federal Republic of Germany and elsewhere, and the references cited in any of the documents cited herein, are hereby incorporated by reference as if set forth in their entirety herein, are hereby incorporated by reference as if set forth in their entirety herein.

The corresponding foreign and international patent publication applications, namely, Federal Republic of Germany Patent Application No. 100 00 839.9-45, filed on Jan. 12, 2000, [NHL-SCT-20] having inventors Dr. Ulrich PEUCHERT and Dr. Peter BRIX, as well as their published equivalents, and other equivalents or corresponding applications, if any, in corresponding cases in the Federal Republic of Germany and elsewhere, and the references cited in any of the documents cited herein, are hereby incorporated by reference as if set forth in their entirety herein, are hereby incorporated by reference as if set forth in their entirety herein.

The corresponding foreign and international patent publication applications, namely, Federal Republic of Germany Patent Application No. 100 00 837.2-45, filed on Jan. 12, 2000, [NHL-SCT-21] having inventors Dr. Ulrich PEUCHERT and Dr. Peter BRIX, as well as their published equivalents, and other equivalents or corresponding applications, if any, in corresponding cases in the Federal Republic of Germany and elsewhere, and the references cited in any of the documents cited herein, are hereby incorporated by reference as if set forth in their entirety herein, are hereby incorporated by reference as if set forth in their entirety herein.

The U.S. Pat. No. 5,374,595 issued on Dec. 20, 1994 to William H. Dumbaugh, Jr., et al. and entitled “High liquidus viscosity glasses for flat panel displays”, and its other equivalents or corresponding applications, if any, and the references cited in any of the documents cited therein, are hereby incorporated by reference as if set forth in their entirety herein.

Although only a few exemplary embodiments of this invention have been described in detail above, those skilled in the art will readily appreciate that many modifications are possible in the exemplary embodiments without materially departing from the novel teachings and advantages of this invention. Accordingly, all such modifications are intended to be included within the scope of this invention as defined in the following claims. In the claims, means-plus-function clauses are intended to cover the structures described herein as performing the recited function and not only structural equivalents but also equivalent structures.

Features concerning aluminoborosilicate glass, and the use thereof, which may possibly be incorporated in embodiments of the present invention may be found in U.S. Pat. No. 6,096,670 issued on Aug. 1, 2000 to Lautenschläger, et al. and entitled “Alkali metal-free aluminoborosilicate glass and its use”; U.S. Pat. No. 6,074,969 issued on Jun. 13, 2000 to Naumann, et al. and entitled “Earth-alkaline aluminoborosilicate glass for lamp bulbs”; U.S. Pat. No. 6,065,309 issued on May 23, 2000 to Cooper, et al. and entitled “Float processing of high-temperature complex silicate glasses and float baths used for same”; U.S. Pat. No. 6,013,310 issued on Jan. 11, 2000 to Yaoi, et al. and entitled “Method for producing a thin film semiconductor device”; U.S. Pat. No. 6,000,241 issued on Dec. 14, 1999 to Ranade, et al. and entitled “Process for making barium containing silicate glass powders”; U.S. Pat. No. 5,985,700 issued on Nov. 16, 1999 to Moore and entitled “TFT fabrication on leached glass surface”; U.S. Pat. No. 5,952,253 issued on Sep. 14, 1999 to Dejneka, et al. and entitled “Transparent apatite glass ceramics”; U.S. Pat. No. 5,932,326 issued on Aug. 3, 1999 to Kashima, et al. and entitled “Ceramic wiring boards and method for their manufacture”; U.S. Pat. No. 5,908,703 issued on Jun. 1, 1999 to Gaschler, et al. and entitled “Alkali-free aluminoborosilicate glass and its use” also referred to above; U.S. Pat No. 5,871,654 issued on Feb. 16, 1999 to Mannami, et al. and entitled “Method for producing a glass substrate for a magnetic disc”; U.S. Pat. No. 5,824,127 issued on Oct. 20, 1998 to Bange, et al. and entitled “Arsenic-free glasses”; U.S. Pat. No. 5,785,726 issued on Jul. 28, 1998 to Dorfeld, et al. and entitled “Method of reducing bubbles at the vessel/glass interface in a glass manufacturing system”; U.S. Pat. No. 5,770,535 issued on Jun. 23, 1998 to Brix, et al. and entitled “Alkali-free aluminoborosilicate glass and its use” also referred to above; U.S. Pat. No. 5,707,746 issued on Jan. 13, 1998 to Yaoi, et al. and entitled “Thin film transistor device with advanced characteristics by improved matching between a glass substrate and a silicon nitride layer”; U.S. Pat. No. 5,374,595 issued on Dec. 20, 1994 to Dumbaugh, Jr., et al and entitled “High liquidus viscosity glasses for flat panel displays”, corresponding European Patent Application 0 607 865 A1 with date of publication of application: Jul. 27, 1994; U.S. Pat. No. 5,326,730 issued on Jul. 5, 1994 to Dumbaugh, Jr., et al. and entitled “Barium Aluminosilicate glasses”; U.S. Pat. No. 5,017,434 issued on May 21, 1991 to Enloe, et al. and entitled “Electronic package comprising aluminum nitride and aluminum nitride-borosilicate glass composite”; U.S. Pat. No. 4,940,674 issued on Jul. 10, 1990 to Beall, et al. and entitled “High strength haze-free transparent glass-ceramics”; U.S. Pat. No. 4,399,015 issued on Aug. 16, 1983 to Endo, et al. and entitled “Method for fabricating an indium tin oxide film for a transparent electrode”; U.S. Pat. No. 4,248,615 issued on Feb. 3, 1981 to Seng, et al. and entitled “Pollution abating, energy conserving glass manufacturing process”; U.S. Pat. No. 3,998,667 issued on Dec. 21, 1976 to Rapp and entitled “Barium aluminoborosilicate glass-ceramics for semiconductor doping”; U.S. Pat. No. 3,962,000 issued on Jun. 8, 1976 to Rapp and entitled “Barium aluminoborosilicate glass-ceramics for semiconductor doping”; U.S. Pat. No. 3,961,969 issued on Jun. 8, 1976 to Rapp and entitled “Glass-ceramics for semiconductor doping”; and U.S. Pat. No. 3,907,618 issued on Sep. 23, 1975 to Rapp and entitled “Process for doping semiconductor employing glass-ceramic dopant”.

Examples of twisted nematic and/or super twisted nematic displays in which may possibly be incorporated embodiments of the present invention may be found in U.S. Pat. No. 6,023,317 issued on Feb. 8, 2000 to Xu, et al. and entitled “Normally white twisted nematic LCD with positive and negative retarders”; U.S. Pat. No. 5,859,681 issued on Jan. 12, 1999 to VanderPloeg, et al. and entitled “Normally white twisted nematic LCD with positive uniaxial and negative biaxial retarders having N x >N y >N z ”; U.S. Pat. No. 5,818,615 issued on Oct. 6, 1998 to Abileah, et al. and entitled “Liquid crystal display with patterned retardation films”; U.S. Pat. No. 5,694,187 issued on Dec. 2, 1997 to Abileah, et al. and entitled “LCD including negative biaxial retarder on each side of the liquid crystal layer”; U.S. Pat. No. 5,657,140 issued on Aug. 12, 1997 to Xu, et al. and entitled “Normally white twisted nematic LCD with positive and negative retarders”; U.S. Pat. No. 5,576,855 issued on Nov. 19, 1996 to Swirbel, et al. and entitled “Liquid crystal display having embossed appearing characters”; and U.S. Pat. No. 3,975,286 issued on Aug. 17, 1976 to Oh and entitled “Low voltage actuated field effect liquid crystals compositions and method of synthesis”.

Examples of active matrix liquid crystal displays (AMLCDs) in which may possibly be incorporated embodiments of the present invention may be found in U.S. Pat. No. 6,146,930 issued on Nov. 14, 2000 to Kobayashi, et al. and entitled “Method of fabricating and active-matrix liquid crystal display”; U.S. Pat. No. 6,140,990 issued on Oct. 31, 2000 to Schlig and entitled “Active matrix liquid crystal display incorporating pixel inversion with reduced drive pulse amplitudes”; U.S. Pat. No. 6,137,558 issued on Oct. 24, 2000 to Koma, et al. and entitled “Active-matrix liquid crystal display”; U.S. Pat. No. 6,091,473 issued on Jul. 18, 2000 to Hebiguchi and entitled “Active matrix liquid crystal display”; U.S. Pat. No. 6,075,580 issued on Jun. 13, 2000 to Kouchi and entitled “Active matrix type liquid crystal display apparatus with conductive light shield element”; U.S. Pat. No. 6,052,168 issued on Apr. 18, 2000 to Nishida, et al. and entitled “Active matrix liquid-crystal display with verticle alignment, positive anisotropy and opposing electrodes below pixel electrode”; U.S. Pat. No. 6,040,813 issued on Mar. 21, 2000 to Takubo and entitled “Active matrix liquid crystal display device and a method for driving the same”; U.S. Pat. No. 6,028,578 issued on Feb. 22, 2000 to Ota, et al. and entitled “Active matrix type liquid crystal display system and driving method therefor”; U.S. Pat. No. 5,990,998 issued on Nov. 23, 1999 to Park, et al. and entitled “Active matrix liquid crystal display and related method”; U.S. Pat. No. 5,880,794 issued on Mar. 9, 1999 to Hwang and entitled “Active matrix liquid crystal display and method with two anodizations”; U.S. Pat. No. 5,861,326 issued on Jan. 19, 1999 to Yamazaki, et al. and entitled “Method for manufacturing semiconductor integrated circuit”; U.S. Pat. No. 5,808,410 issued on Sep. 15, 1998 to Pinker, et al. and entitled “Flat panel light source for liquid crystal displays”; U.S. Pat. No. 5,767,930 issued to Kobayashi, et al. and entitled “Active-matrix liquid-crystal display and fabrication method thereof”; U.S. Pat. No. 5,739,180 issued on Apr. 14, 1998 to Taylor-Smith and entitled “Flat-panel displays and methods and substrates therefor”; U.S. Pat. No. 5,650,865 issued on Jul. 22, 1997 to Smith and entitled “Holographic backlight for flat panel displays”; U.S. Pat. No. Re 35,416 reissued on Dec. 31, 1996 to Suzuki, et al. and entitled “Active matrix liquid crystal display device and method for production thereof”; U.S. Pat. No. 5,546,204 issued on Aug. 13, 1996 to Ellis and entitled “TFT matrix liquid crystal device having data source lines and drain means of etched and doped single crystal silicon”; U.S. Pat. No. 5,493,986 issued on Feb. 27, 1996 to Augusto and entitled “Method of providing VLSI-quality crystalline semiconductor substrates; U.S. Pat. No. 5,465,052 issued on Nov. 7, 1995 to Henley and entitled “Method of testing liquid crystal display substrates”; U.S. Pat. No. 5,184,236 issued on Feb. 2, 1993 to Miyashita, et al. and entitled “Twisted nematic liquid crystal display device with retardation plates having phase axis direction with 15° of alignment direction”; U.S. Pat. No. 5,182,661 issued on Jan. 26, 1993 to Ikeda, et al. and entitled “Thin film field effect transistor array for use in active matrix liquid crystal display”; and U.S. Pat. No. 5,084,905 issued on Jan. 28, 1992 to Sasaki, et al. and entitled “Thin film transistor panel and manufacturing method thereof”.

Examples of thin-film transistors (TFT) displays in which may possibly be incorporated embodiments of the present invention may be found in U.S. Pat. No. 6,087,678 issued on Jul. 11, 2000 to Kim and entitled “Thin-film transistor display devices having composite electrodes”; U.S. Pat. No. 6,005,646 issued on Dec. 21, 1999 to Nakamura, et al. and entitled “Voltage application driving method”; U.S. Pat. No. 5,920,362 issued on Jul. 6, 1999 to Lee and entitled “Method of forming thin-film transistor liquid crystal display having a silicon active layer contacting a sidewall of a data line and a storage capacitor electrode”; U.S. Pat. No. 5,920,083 issued on Jul. 6, 1999 to Bae and entitled “Thin-film transistor display devices having coplanar gate and drain lines”; U.S. Pat. No. 5,917,564 issued on Jun. 29, 1999 and entitled “Methods of forming active matrix display devices with reduced susceptibility to image-sticking and devices formed thereby”; U.S. Pat. No. 5,619,357 issued on Apr. 8, 1997 to Angelopoulos, et al. and entitled “Flat panel display containing black matrix polymer”; U.S. Pat. No. 5,317,433 issued on May 31, 1994 to Miyawaki, et al. and entitled “Image display device with a transistor on one side of insulating layer and liquid crystal on the other side”; U.S. Pat. No. 5,250,937 issued on Oct. 5, 1993 to Kikuo, et al. and entitled “Half tone liquid crystal display circuit with an A.C. voltage divider for drivers”; U.S. Pat. No. 5,233,448 issued on Aug. 3, 1993 to Wu and entitled “Method of manufacturing a liquid crystal display panel including photoconductive electrostatic protection”; U.S. Pat. No. 4,723,838 issued on Feb. 9, 1988 to Aoki, et al. and entitled “Liquid crystal display device”; and U.S. Pat. No. 4,404,578 issued on Sep. 13, 1983 to Takafuji, et al. and entitled “Structure of thin film transistors”.

Examples of plasma addressed liquid crystals (PALCs) displays in which may possibly be incorporated embodiments of the present invention may be found in U.S. Pat. No. 6,094,183 issued on Jul. 25, 2000 to Tanamachi, et al. and entitled “Plasma addressed liquid crystal display device”; U.S. Pat. No. 6,081,245 issued on Jun. 27, 2000 to Abe and entitled “Plasma-addressed liquid-crystal display device”; U.S. Pat. No. 5,997,379 issued on Dec. 7, 1999 to Kimura and entitled “Method of manufacturing plasma addressed liquid crystal display”; U.S. Pat No. 5,984,747 issued on Nov. 16, 1999 to Bhagavatula, et al. and entitled “Glass structures for information displays”; U.S. Pat. No. 5,886,467 issued on Mar 23, 1999 to Kimura and entitled “Plasma addressed liquid crystal display device”; U.S. Pat. No. 5,844,639 issued on Dec. 1, 1998 to Togawa and entitled “Plasma addressed liquid crystal display device”; U.S. Pat. No. 5,810,634 issued on Sep. 22, 1998 to Miyazaki, et al. and entitled “Method of manufacturing a plasma addressed liquid crystal display device”; U.S. Pat. No. 5,757,342 issued on May 26, 1998 to Hayashi and entitled “Plasma addressed liquid crystal display device”; U.S. Pat. No. 5,725,406 issued on Mar. 10, 1998 to Togawa and entitled “Plasma addressed display device”; U.S. Pat. No. 5,698,944 issued on Dec. 16, 1997 to Togawa and entitled “Plasma addressed liquid crystal display device”; U.S. Pat. No. 5,526,151 issued on Jun. 11, 1996 to Miyazaki, et al. and entitled “Method of manufacturing a plasma addressed liquid crystal display device having planarized barrier ribs”; U.S. Pat. No. 5,499,122 issued on Mar. 12, 1996 to Yano and entitled “Plasma-addressed liquid crystal display device having a transparent dielectric sheet with a porous layer containing an impregnated liquid crystal”; U.S. Pat. No. 5,383,040 issued on Jan. 17, 1995 to Kim and entitled “Plasma addressed liquid crystal display with center substrate divided into separate sections”; U.S. Pat. No. 5,377,029 issued on Dec. 27, 1994 to Lee, et al. and entitled “Plasma addressed liquid crystal display”; and U.S. Pat. No. 5,221,979 issued on Jun. 22, 1993 to Kim and entitled “Plasma addressed liquid crystal display and manufacturing method”.

The details in the patents, patent applications and publications may be considered to be incorporable, at Applicants' option, into the claims during prosecution as further limitations in the claims to patentably distinguish any amended claims from any applied prior art.

Examples of thin-film photovoltaic apparatus and methods of making them in which may possibly be incorporated embodiments of the present invention may be found in U.S. Pat. No. 6,137,048 issued on Oct. 24, 2000 to Wu, et al. and entitled “Process for fabricating polycrystalline semiconductor thin-film solar cells, and cells produced thereby”; U.S. Pat. No. 5,922,142 issued on Jul. 13, 1999 to Wu, et al. and entitled “Photovoltaic devices comprising cadmium stannate transparent conducting films and method for making”; U.S. Pat. No. 5,503,898 issued on Apr. 2, 1996 to Lauf and entitled “Method for producing textured substrates for thin-film photovoltaic cells”; U.S. Pat. No. 5,378,639 issued on Jan. 3, 1995 to Sasaki, et al. and entitled “Method for manufacturing a thin-film photovoltaic conversion device”; U.S. Pat. No. 5,306,646 issued on Apr. 26, 1994 to Lauf and entitled “Method for producing textured substrates for thin-film photovoltaic cells”; U.S. Pat. No. 5,057,163 issued on Oct. 15, 1991 to Barnett, et al. and entitled “Deposited-silicon film solar cell”; U.S. Pat. No. 4,772,564 issued on Sep. 20, 1988 to Barnett, et al. and entitled “Fault tolerant thin-film photovoltaic cell fabrication Process”; U.S. Pat. No. 4,677,250 issued on Jun. 30, 1987 to Barnett, et al. and entitled “Fault tolerant thin-film photovoltaic cell”; U.S. Pat. No. 4,647,711 issued on Mar. 3, 1987 to Basol, et al. and entitled “Stable front contact current collectors for photovoltaic devices and method of making same”; U.S. Pat. No. 4,604,791 issued on Aug. 12, 1986 to Todorof and entitled “Method for producing multi-layer, thin-film, flexible silicon alloy photovoltaic cells”; and U.S. Pat. No. 4,595,790 issued on Jun. 17, 1986 to Basol and entitled “Method of making current collector grid and materials therefor”.

Features of processing technology which may possibly be incorporated in embodiments of the present invention may be found in U.S. Pat. No. 5,766,296 issued on Jun. 16, 1998 to Moreau and entitled “Furnace for melting glass and method for using glass produced therein”; U.S. Pat. No. 5,764,415 issued on Jun. 9, 1998 to Nelson, et al. and entitled “Coatings on glass”; U.S. Pat. No. 5,057,140 issued on Oct. 15, 1991 to Nixon and entitled “Apparatus for melting glass batch material”; U.S. Pat. No. 5,054,355 issued on Oct. 8, 1991 to Tisse, et al. and entitled “Automatic glass cutting and positioning system”; U.S. Pat No. 4,781,742 issued on Nov. 1, 1988 to Hill, et al. and entitled “Method and apparatus for detecting unwanted materials among cullet”; U.S. Pat. No. 4,489,870 issued on Dec. 25, 1984 to Prange, et al. and entitled “Apparatus for severing edges of a glass sheet”; and U.S. Pat. No. Re 30,147 reissued on Nov. 13, 1979 to Jordan, et al. and entitled “Method of coating a glass ribbon on a liquid float bath”.

The invention as described hereinabove in the context of the preferred embodiments is not to be taken as limited to all of the provided details thereof, since modifications and variations thereof may be made without departing from the spirit and scope of the invention.

Claims

1. A flat panel liquid-crystal display, the flat panel liquid-crystal display comprising one of: a twisted nematic display, a supertwisted nematic display, an active matrix liquid-crystal display, a thin film transistor display, and a plasma addressed liquid-crystal display, said flat panel liquid-crystal display comprising:backlight apparatus; a first linear polarizer adjacent said backlight apparatus; a first positive uniaxial retardation film adjacent said first linear polarizer; a first negative retardation film adjacent said first positive uniaxial retardation film; a first orientation film adjacent said first negative retardation film; a liquid-crystal layer adjacent said first orientation film; a second orientation film adjacent said liquid-crystal layer; a second negative retardation film adjacent said second orientation film; a second positive uniaxial retardation film adjacent said second negative retardation film; a second linear polarizer adjacent said second positive uniaxial retardation film; a first glass substrate being disposed between said first orientation film and said first negative retardation film; a second glass substrate being disposed between said second orientation film and said second negative retardation film; a first electrode being disposed between said first glass substrate and said first orientation film; and a second electrode being disposed between said second glass substrate and said second orientation film; said first and said second glass substrates comprising: an alkali-free aluminoborosilicate glass; said glass having a coefficient of thermal expansion α20/300 of between 2.8×10−6/K and 3.8×10−6/K; said glass having the composition (in % by weight, based on oxide): SiO2greater than 58 to 65B2O3greater than 6 to 10.5Al2O3greater than 14 to 25MgO0 to less than 3CaOless than or equal to 9BaOgreater than 3 to 5with MgO + CaO + BaOgreater than or equal to 8 to lessthan 17ZnO0 to less than 2SrO0 to less than 0.1;said glass being resistant to thermal shock; said glass having a high transparency over a broad spectral range in the visible and ultra violet ranges; and said glass being free of bubbles, knots, inclusions, streaks, and surface undulations.

2. The flat panel liquid-crystal display according to claim 1, wherein:said glass comprises at least one of (a.), (b.), (c.), (d.), (e.), (g.), and (h.), where (a.), (b.), (c.), (d.), (e.), (g), and (h.) are: (a.) more than 8% by weight of B2O3; (b.) one of: more than 18% by weight of Al2O3, and at least 20.5% by weight of Al2O3; (c.) at most 4% by weight of BaO; (d.) at least 0.1% by weight of ZnO; (e.) additionally (in % by weight): ZrO20 to 2TiO20 to 2with ZrO2 + TiO20 to 2As2O30 to 1.5Sb2O30 to 1.5SnO20 to 1.5CeO20 to 1.5Cl−0 to 1.5F−0 to 1.5SO42−0 to 1.5with As2O3 + Sb2O3 + SnO2 +less than orCeO2 + Cl− + F− + SO42−equal to 1.5;(g.) a float glass; and (h.) one of (i.) and (ii.), where (i) and (ii) are: (i.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.6×10−6/K; a glass transition temperature Tg of greater than 700° C.; and a density ρ of less than 2.600 g/cm3; (ii.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 32×10−6/K; a glass transition temperature Tg of greater than 700° C.; and a density ρ of less than 2.600 g/cm3.

3. The flat panel liquid-crystal display according to claim 1, wherein:said glass comprises (a.), (b.), (c.), (d.), (e.), (g.), and (h.), where (a.), (b.), (c.), (d.), (e.), (g.), and (h.) are: (a.) more than 8% by weight of B2O3; (b.) one of: more than 18% by weight of Al2O3, and at least 20.5% by weight of Al2 O3; (c.) at most 4% by weight of BaO; (d.) at least 0.1% by weight of ZnO; (e.) additionally (in % by weight): ZrO20 to 2TiO20 to 2with ZrO2 + TiO20 to 2As2O30 to 1.5Sb2O30 to 1.5SnO20 to 1.5CeO20 to 1.5Cl−0 to 1.5F−0 to 1.5SO42−0 to 1.5with As2O3 + Sb2O3 + SnO2 +less than orCeO2 + Cl− + F− + SO42−equal to 1.5;(g.) a float glass; and (h.) one of (i.) and (ii.), where (i) and (ii) are: (i.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.6×10−6/K; a glass transition temperature Tg of greater than 700° C.; and a density ρ of less than 2.600 g/cm3; (ii.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.2×10−6/K; a glass transition temperature T8 of greater than 700° C.; and a density ρ of less than 2.600 g/cm3.

4. A glass substrate for a flat panel liquid-crystal display, the flat panel liquid-crystal display including a twisted nematic display, a supertwisted nematic display, an active matrix liquid-crystal display, a thin film transistor display, and a plasma addressed liquid-crystal display, said substrate comprising:an alkali-free aluminoborosilicate glass; said glass having a coefficient of thermal expansion α20/300 of between 2.8×10−6/K and 3.8×10−6/K; said glass having the composition (in % by weight, based on oxide): SiO2greater than 58 to 65B2O3greater than 6 to 10.5Al2O3greater than 14 to 25MgO0 to less than 3CaOless than or equal to 9BaOgreater than 3 to 5with MgO + CaO + BaOgreater than or equal to 8 to lessthan 17ZnO0 to less than 2SrO0 to less than 0.1;said glass being resistant to thermal shock; said glass having a high transparency over a broad spectral range in the visible an ultra violet ranges; and said glass being free of bubbles, knots, inclusions, streaks, and surface undulations.

5. The glass substrate according to claim 4, wherein:said glass comprises at least one of (a.), (b.), (c.), (d.), (e.), (g.), and (h.), where (a.), (b.), (c.), (d.), (e.), (g.), and (h.) are: (a.) more than 8% by weight of B2O3; (b.) one of: more than 18% by weight of Al2O3, and at least 20.5% by weight of Al2O3; (c.) at most 4% by weight of BaO; (d.) at least 0.1% by weight of ZnO; (e.) additionally in % by weight): ZrO20 to 2TiO20 to 2with ZrO2 + TiO20 to 2As2O30 to 1.5Sb2O30 to 1.5SnO20 to 1.5CeO20 to 1.5Cl−0 to 1.5F−0 to 1.5SO42−0 to 1.5with As2O3 + Sb2O3 + SnO2 +less than orCeO2 + Cl− + F− + SO42−equal to 1.5;(g.) a float glass; and (h.) one of (i.) an (ii.), where (i) and (ii) are: a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.6×10−6/K; a glass transition temperature Tg of greater than 700° C.; and a density ρ of less than 2.600 g/cm3. (ii.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.2×10−6/K; a glass transition temperature Tg of greater than 700° C.; and a density ρ of less than 2.600 g/cm3.

6. The glass substrate according to claim 4, wherein:said glass comprises (a.), (b.), (c.), (d.). (e.), (g.), and (h.), where (a.) (b.), (c.), (d.), (e.), (g.), and (h.) are: (a.) more than 8% by weight of B2O3; (b.) one of: more than 18% by weight of Al2O3, and at least 20.5% by weight of Al2O3; (c.) at most 4% by weight of BaO; (d.) at least 0.1% by weight of ZnO; (e.) additionally (in % by weight): ZrO20 to 2TiO20 to 2with ZrO2 + TiO20 to 2As2O30 to 1.5Sb2O30 to 1.5SnO20 to 1.5CeO20 to 1.5Cl−0 to 1.5F−0 to 1.5SO42−0 to 1.5with As2O3 + Sb2O3 + SnO2 +less than orCeO2 + Cl− + F− + SO42−equal to 1.5;(g.) a float glass; and (h.) one of (i.) an (ii.), where (i) and (ii) are: (i.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.6×10−6/K; a glass transition temperature Tg of greater than 700° C.; and a density ρ of less than 2.600 g/cm3. (ii.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.2×10−6/K; a glass transition temperature Tg of greater than 700° C.; and a density ρ of less than 2.600 g/cm3.

7. A glass comprising:a substantially alkali-free aluminoborosilicate glass; said glass having a coefficient of thermal expansion α20/300 of between 2.8×10−6/K and 3.8×10−6/K; said glass having the composition (in % by weight, based on oxide): SiO2greater than 58 to 65B2O3greater than 6 to 10.5Al2O3greater than 14 to 25MgO0 to less than 3CaOless than or equal to 9BaOgreater than 3 to 5with MgO + CaO + BaOgreater than or equal to 8 to lessthan 17ZnO0 to less than 2; andSrO0 to less than 0.1.

8. The glass according to claim 7, wherein:said glass is resistant to thermal shock; said glass has a high transparency over a broad spectral range in the visible and ultra violet ranges; and said glass is free of bubbles, knots, inclusions, streaks, and surface undulations.

9. The glass according to claim 8, wherein:said glass comprises more than 8% by weight of B2O3.

10. The glass according to claim 9, wherein:said glass comprises one of (i.) and (ii.): (i.) more than 18% of by weight of Al2O3; and (ii.) at least 20.5% by weight of A2O3.

11. The glass according to claim 10, wherein:said glass comprises one of (i.) and (ii.): (i.) at most 4% by weight of BaO; (ii.) at least 0.1% by weight of ZnO.

12. The glass according to claim 11, wherein:said glass additionally comprises (in % by weight): ZrO20 to 2TiO20 to 2with ZrO2 + TiO20 to 2As2O30 to 1.5Sb2O30 to 1.5SnO20 to 1.5CeO20 to 1.5Cl−0 to 1.5F−0 to 1.5SO42−0 to 1.5with As2O3 + Sb2O3 + SnO2 +less than orCeO2 + Cl− + F− + SO42−equal to 1.5;

13. The glass according to claim 12, wherein:said glass comprises a float glass.

14. The glass according to claim 13, wherein:said glass has one of (i.), (ii.), (iii.), and (iv.): (i.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.6×10−6/K; (ii.) a coefficient thermal expansion α20/300 of between 2.8×10−6/K to 3.2×10−6/K; (iii.) a glass transition temperature Tg of greater than 700° C.; (iv.) a density ρ of less than 2.600 g/cm3.

15. The glass according to claim 8, wherein:said glass comprises at least one of (a.), (b.), (c.), (d.), (e.), (g.), and (h.), where (a.), (b.), (c.), (d.), (e.), (g.), and (h.) are: (a.) more than 8% by weight of B2O3; (b.) one of: more than 18% by weight of Al2O3, and at least 20.5% by weight of Al2O3; (c.) at most 4% by weight of BaO; (d.) at least 0.1% by weight of ZnO; (e.) additionally (in % by weight): ZrO20 to 2TiO20 to 2with ZrO2 + TiO20 to 2As2O30 to 1.5Sb2O30 to 1.5SnO20 to 1.5CeO20 to 1.5Cl−0 to 1.5F−0 to 1.5SO42−0 to 1.5with As2O3 + Sb2O3 + SnO2 +less than orCeO2 + Cl− + F− + SO42−equal to 1.5;(g.) a float glass; and (h.) one of (i.), (ii.), (iii.), and (iv.): (i.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.6×10−6/K; (ii.) a coefficient of thermal expansion α20/300 of between 2.8×10−6/K to 3.2×10−6/K; (iii.) a glass transition temperature Tg of greater than 700° C.; (iv.) a density ρ of less than 2.600 g/cm3.

16. The glass according to claim 7, wherein:said glass is configured as a glass substrate in combination in or with a flat panel liquid-crystal display, the flat panel liquid-crystal display including a twisted nematic display, a supertwisted nematic display, an active matrix liquid-crystal display, a thin film transistor display, and a plasma addressed liquid-crystal display.

17. The glass according to claim 16, wherein:said flat panel liquid-crystal display comprises: backlight apparatus; a first linear polarizer adjacent said backlight apparatus; a first positive uniaxial retardation film adjacent said first linear polarizer; a first negative retardation film adjacent said first positive uniaxial retardation film; a first orientation film adjacent said first negative retardation film; a liquid-crystal layer adjacent said first orientation film; a second orientation film adjacent said liquid-crystal layer; a second negative retardation film adjacent said second orientation film; a second positive uniaxial retardation film adjacent said second negative retardation film; a second linear polarizer adjacent said second positive uniaxial retardation film; said glass substrate comprising a first glass substrate; said first glass substrate being disposed between said first orientation film and said first negative retardation film; said glass substrate comprising a second glass substrate; said second glass substrate being disposed between said second orientation film and said second negative retardation film; a first electrode being disposed between said first glass substrate and said first orientation film; and a second electrode being disposed between said second glass substrate and said second orientation film.

18. The glass according to claim 7, wherein:said glass is configured as a glass substrate in combination in or with a thin-film photovoltaic device, including a thin-film solar cell.

19. The glass according to claim 18, wherein:said thin-film photovoltaic device comprises: said glass substrate; a transparent conductive oxide film disposed on said glass substrate; an insulating buffer layer disposed atop said transparent conductive oxide film; said film being disposed between said glass substrate and said buffer layer and being configured to be a front contact current collector; a first semiconductor layer disposed upon said buffer layer; a second semiconductor layer disposed upon said first semiconductor layer to form a heterojunction; a first electrical contact disposed upon said second semiconductor layer and in ohmic contact therewith; and a second electrical contact disposed upon said transparent conductive oxide film.