# Patent

## Title
Antimony-free glass, antimony-free frit and a glass package that is hermetically sealed with the frit

## Abstract

An antimony-free glass suitable for use in a frit for producing a hermetically sealed glass package is described. The hermetically sealed glass package, such as an OLED display device, is manufactured by providing a first glass substrate plate and a second glass substrate plate and depositing the antimony-free frit onto the first substrate plate. OLEDs may be deposited on the second glass substrate plate. An irradiation source (e.g., laser, infrared light) is then used to heat the frit which melts and forms a hermetic seal that connects the first glass substrate plate to the second glass substrate plate and also protects the OLEDs. The antimony-free glass has excellent aqueous durability, good flow, low glass transition temperature and low coefficient of thermal expansion.

## Background
PRIORITY
This application is a continuation of U.S. patent application Ser. No. 14/458,738, which issued as U.S. Pat. No. 9,573,840, filed on Aug. 13, 2014, which claims the benefit of priority under 35 U.S.C. § 119 of U.S. Provisional Application Ser. No. 61/870,419 filed on Aug. 27, 2013, the contents of which are relied upon and incorporated herein by reference in their entireties.


TECHNICAL FIELD
The present disclosure relates to an antimony-free glass containing boron in an amount to effectively lower the glass transition temperature of the glass, a frit made therefrom, and a hermetically sealed glass packages sealed with the frit that is suitable to protect electronic devices that are sensitive to the ambient environment. Some examples of such devices are organic emitting light diode (OLED) displays, sensors, photovoltaic and other optical devices. Embodiments disclosed herein are demonstrated using OLED displays as an example.
BACKGROUND
OLEDs have been the subject of a considerable amount of research in recent years because of their use and potential use in a wide variety of electroluminescent devices, and are now reaching commercialization. For instance, a single OLED can be used in a discrete light emitting device or an array of OLEDs can be used in lighting applications or flat-panel display applications (e.g., OLED displays). OLED displays are known as being very bright and having a good color contrast and wide viewing angle. However, OLED displays, and in particular the electrodes and organic layers located therein, are susceptible to degradation resulting from interaction with oxygen and moisture leaking into the OLED display from the ambient environment. It is well known that the life of the OLED display can be significantly increased if the electrodes and organic layers within the OLED display are hermetically sealed from the ambient environment. Unfortunately, in the past it was very difficult to develop a sealing process to hermetically seal the OLED display. Some of the factors that made it difficult to properly seal the OLED display are briefly mentioned below:

    The hermetic seal should provide a barrier for oxygen (10−3 cc/m2/day) and water (10−6 g/m2/day).
    The size of the hermetic seal should be minimal (e.g., <2 mm) so it does not have an adverse effect on size of the OLED display.
    The temperature generated during the sealing process should not damage the materials (e.g., electrodes and organic layers) within the OLED display. For instance, the first pixels of OLEDs which are located about 1-2 mm from the seal in the OLED display should not be heated to more than 100° C. during the sealing process.
    The gases released during the sealing process should not contaminate the materials within the OLED display.
    The hermetic seal should enable electrical connections (e.g., thin-film chromium) to enter the OLED display.


One method for sealing the OLED display is to use different types of epoxies, inorganic materials and/or organic materials that form the seal after they are cured, such as by irradiation. For example, some seals use a composite-based approach where alternate layers of inorganic materials and organic materials can be used to seal the OLED display. Although these types of seals usually provide good mechanical strength, they can be very expensive and there are many instances in which they have failed to prevent the diffusion of oxygen and moisture into the OLED display. Another common way for sealing the OLED display is to utilize metal welding or soldering. However, the resulting seal is not durable in a wide range of temperatures because of the substantial differences between the coefficients of thermal expansions (CTEs) of the glass plates and metal in the OLED display.
More recently, glass-based frits have been used to seal glass substrate plates in a glass package that provides excellent hermeticity to the enclosed device. But many of these frits contain toxic elements, such as antimony, which pose environmental hazards. Accordingly, there is a need for a glass-based frit suitable for hermetically sealing glass packages, such as electronic devices (e.g. for display-type applications), having a low coefficient of thermal expansion (CTE) that does not contain antimony.
SUMMARY
The present disclosure describes an antimony-free glass, a frit comprising the antimony-free glass and an hermetically sealed OLED display and method for manufacturing the hermetically sealed OLED display. Basically, an hermetically sealed OLED display is manufactured by providing a first glass substrate plate and a second glass substrate plate and depositing the frit onto the second glass substrate plate. An organic material, such as those used in the manufacture of an OLED may be deposited on the first substrate plate. An irradiation source (e.g., laser, infrared light) is then used to heat the frit which melts and forms a hermetic seal that connects the first glass substrate plate to the second glass substrate plate and also protects the OLEDs. The frit is an antimony-free glass that includes vanadium, and possibly a CTE lowering filler, such that when the irradiation source irradiates the frit, the frit is heated, softens and forms a bond between the substrate plates while avoiding thermal damage to the OLEDs. Vanadium phosphate frits, for example, have proven especially suitable for sealing glass packages of the type just described, and in particular antimony-containing vanadium phosphate frits. Such frits are stable, exhibit high optical absorbance and have excellent mechanical and aqueous durability. Unfortunately, antimony is a toxic element, and efforts have been directed toward finding a replacement for antimony that does not detrimentally affect the other beneficial attributes of the frit.
To that end, the excellent aqueous durability performance of Sb-vanadium phosphate frits was maintained without Sb2O3 by replacement of the antimony oxide by a combination of Fe2O3+TiO2, along with a small addition of ZnO to maintain flow performance and B2O3 to reduce the glass transition temperature of the glass. The presence of Fe2O3 was found to have the greatest effect in improving durability. However, it raised Tg, thus degrading frit flow during sealing. In addition, frits with high Fe2O3 levels (equal to or greater than about 25 mole %) tended to be oxidatively unstable, with repeat samples fired to the same schedule (425° in N2) exhibiting different colors (brown or black), with marked differences in the degree of flow. Although TiO2 alone actually degraded aqueous durability to some extent, the combination of Fe2O3+TiO2+B2O3 proved to be an ideal combination from the standpoint of obtaining laser-sealable frits with both high aqueous durability and low Tg (≦365° C.).
Both lab bench tests exposing the glass to 90° C. deionized water as well as 85° C./85% relative humidity (RH) environmental chamber testing of laser-sealed samples indicate that frits based on the V2O5—P2O5—Fe2O3—TiO2—ZnO—B2O3 system are capable of forming a low Tg frit that provides excellent sealing properties.
The antimony-free glass may contain V2O5 in any amount in the range from ≧40 mole % to ≦52.5 mole % where the upper and lower limits of suitable ranges fall therein, for example from ≧40 mole % to ≦50 mole %, from ≧40 mole % to ≦48 mole %, from ≧42 mole % to ≦50 mole %, from ≧42 mole % to ≦52.5 mole %, or from ≧42 mole % to ≦48 mole %.
The antimony-free glass may contain P2O5 in an amount from ≧20 mole % to <25 mole %, from ≧20 mole % to <24 mole %, from ≧20 mole % to <23 mole %, or from ≧20 mole % to <22.5 mole %.
The antimony-free glass may contain Fe2O3 in an amount from >0 mole % to <25 mole %, from ≧10 mole % to ≦20 mole %, from ≧10 mole % to ≦18 mole %, from ≧10 mole % to ≦16 mole %, from ≧10 mole % to ≦15 mole %, or from ≧10 mole % to ≦14 mole %.
The antimony-free glass may contain TiO2 in an amount from >0 mole % to <25 mole %, from ≧5 mole % to ≦20 mole %, from ≧5 mole % to ≦18 mole %, from ≧5 mole % to ≦15 mole %, or from ≧10 mole % to ≦18 mole %.
The antimony-free glass may contain ZnO in an amount from ≧0 mole % to ≦10 mole %, from ≧2 mole % to ≦5 mole %, from ≧0 mole % to ≦4 mole %, or from ≧2.5 mole % to ≦5 mole %.
The antimony-free glass may contain B2O3 in an amount from >0 mole % to ≦20 mole %, from >0 mole % to ≦15 mole %, from >0 mole % to ≦10 mole %, from >0 mole % to ≦7.5 mole %, from ≧1 mole % to ≦20 mole %, from ≧3 mole % to ≦20 mole %, or from ≧5 mole % to ≦15 mole %.
TiO2+Fe2O3 may be in a range from 15 mole % to 30 mole %, while TiO2+Fe2O3+B2O3 may be in a range from 25 mole % to 35 mole %, and in some embodiments TiO2+Fe2O3+B2O3 may be in a range from 27.5 mole % to 35 mole %.
Accordingly, as disclosed herein, an antimony-free glass is described comprising:

    
    
        V2O5≧40 mole % and ≦52.5 mole %;
        P2O5≧20 mole % and <25 mole %;
        ZnO≧0 mole % and ≦10 mole %;
        Fe2O3>0 mole % and <25 mole %;
        TiO2>0 mole % and <25 mole %;
        B2O3>0 mole % and 20 mole %; and

wherein TiO2+Fe2O3 is in a range from 15 mole % to 30 mole %.

    
    


The antimony-free glass may, for example, comprise:

    
    
        V2O5≧40 mole % and ≦52.5 mole %;
        P2O5≧20 mole % and <25 mole %;
        ZnO≧0 mole % and ≦5 mole %;
        Fe2O3≧10 mole % and <20 mole %;
        TiO2>2 mole % and <20 mole %;
        B2O3≦1 mole % and ≧20 mole %; and

wherein TiO2+Fe2O3 is in a range from 15 mole % to 30 mole %.

    
    


In some examples, the antimony-free glass may comprise:

    
    
        V2O5≧40 mole % and ≦50 mole %;
        P2O5≧20 mole % and <25 mole %;
        ZnO≧2 mole % and <5 mole %;
        Fe2O3>0 mole % and <20 mole %;
        TiO2>0 mole % and <20 mole %;
        B2O3≧3 mole % and ≦20 mole %; and

wherein TiO2+Fe2O3 is in a range from 15 mole % to 30 mole %.

    
    


In other examples, the antimony-free glass can comprise:

    
    
        V2O5≧40 mole % and ≦50 mole %;
        P2O5≧20 mole % and <25 mole %;
        ZnO≧2 mole % and <5 mole %;
        Fe2O3>0 mole % and <25 mole %;
        TiO2>0 mole % and <25 mole %;
        B2O3>5 mole % and ≦20 mole %; and

wherein TiO2+Fe2O3 is in a range from 15 mole % to 30 mole %.

    
    


The antimony-free glass may, for example, comprise the following composition:

    
    
        V2O5 40 mole %;
        P2O5 20 mole %;
        ZnO 5 mole %;
        Fe2O3>7.5 mole % and <15 mole %;
        TiO2>7.5 mole % and <15 mole %;
        B2O3>5 mole % and ≦20 mole %; and

wherein TiO2+Fe2O3 is ≧15 and ≦30 mole %.

    
    


In other examples, the antimony-free glass may comprise the following composition:

    
    
        V2O5 47.5 mole %;
        P2O5≧20 mole % and <22.5 mole %;
        ZnO 2.5 mole %;
        Fe2O3>12.5 mole % and <17 mole %;
        TiO2>2.5 mole % and <9.5 mole %;
        B2O3>1 mole % and ≦15 mole %; and

wherein TiO2+Fe2O3 is ≧15 and ≦26.5 mole %.

    
    


The antimony-free glass can have a Tg≦365° C., such as a Tg≦350° C.
In some embodiments, the antimony-free glass may be a component in a frit for sealing together glass articles, such as glass plates in order to form, for example, a glass package. The frit may further comprise a CTE lowering filler, such as β-eucryptite or β-quartz.
In some embodiments of the antimony-free glass, TiO2+Fe2O3+B2O3 may be in a range from 25 mole % to 35 mole %.
In some embodiments of the antimony-free glass, TiO2+Fe2O3+B2O3 may be in a range from 27.5 mole % to 35 mole %.
In another embodiment discloses herein a glass frit is disclosed comprising:

    
    
        V2O5≧40 mole % and ≦50 mole %;
        P2O5≧20 mole % and <25 mole %;
        ZnO≧0 mole % and ≦10 mole %;
        Fe2O3>0 mole % and <25 mole %;
        TiO2>0 mole % and <25 mole %;
        B2O3>0 mole % and 20 mole %; and

wherein TiO2+Fe2O3 is in a range from 15 mole % to 30 mole %.

    
    


In certain examples, TiO2+Fe2O3+B2O3 may be in a range from 25 mole % to 35 mole %.
In some examples, the glass frit further comprises a CTE-lowering filler such as β-eucryptite or β-quartz.
In another aspect, a glass package is described comprising a first glass plate, a second glass plate and a frit that connects the first glass plate to the second glass plate and forms an hermetic seal therebetween, the frit including an antimony-free glass comprising:

    
    
        V2O5≧40 mole % and ≦50 mole %;
        P2O5≧20 mole % and <25 mole %;
        ZnO≧0 mole % and ≦10 mole %;
        Fe2O3>0 mole % and <25 mole %;
        TiO2>0 mole % and <25 mole %;
        B2O3>0 mole % and 20 mole %; and

wherein TiO2+Fe2O3 is in a range from 15 mole % to 30 mole %.

    
    


In some embodiments of the glass package TiO2+Fe2O3+B2O3 may be in a range from 25 mole % to 35 mole %.
In some embodiment of the glass package TiO2+Fe2O3+B2O3 may be in a range from 27.5 mole % to 35 mole %.
The glass package may further comprise an organic material disposed between the first and second glass plates. For example, the glass package may include an organic light emitting device such as an organic light emitting diode.
The invention will be understood more easily and other objects, characteristics, details and advantages thereof will become more clearly apparent in the course of the following explanatory description, which is given, without in any way implying a limitation, with reference to the attached Figures. It is intended that all such additional systems, methods, features and advantages be included within this description, be within the scope of the present invention, and be protected by the accompanying claims.



BRIEF DESCRIPTION OF THE DRAWINGS
FIG. 1 is a cross sectional illustration of the sealing of an exemplary OLED device using a frit according to embodiments of the present invention;
FIG. 2 is a plot of coefficient of thermal expansion (CTE) as a function of the substitution of Fe2O3 for TiO2 in an Sb-free frit according to embodiments of the present invention in mole % where Fe2O3+TiO2 is between 20 mole % and 35 mole %;
FIG. 3 is a plot comparing CTE as a function of temperature for an Sb-free frit according to embodiments of the present invention and an Sb-containing frit under both heating and cooling conditions;
FIG. 4 is a photograph of the supernatant after temperature and humidity exposure of boron-containing antimony-free glasses compared to an antimony-containing glass;
FIG. 5 is a graph of glass transition temperature of both antimony-containing and antimony-free glasses as a function of B2O3 concentration;
FIGS. 6 and 7 are photographs of the supernatant after temperature and humidity exposure of various compositions of boron-containing antimony-free glasses as disclosed herein;
FIG. 8 is a top-down view of a portion of a glass package showing a seal made with a frit comprising a boron-containing antimony-free glass as disclosed herein.



DETAILED DESCRIPTION
In the following detailed description, for purposes of explanation and not limitation, example embodiments disclosing specific details are set forth to provide a thorough understanding of the present invention. However, it will be apparent to one having ordinary skill in the art, having had the benefit of the present disclosure, that the present invention may be practiced in other embodiments that depart from the specific details disclosed herein. Moreover, descriptions of well-known devices, methods and materials may be omitted so as not to obscure the description of the present invention. Finally, wherever applicable, like reference numerals refer to like elements.
FIG. 1 depicts a cross-sectional side view illustrating the sealing of the basic components of a hermetically sealed OLED display 10. OLED display 10 includes a multilayer sandwich of a first glass substrate plate 12, one or more OLEDs 14, frit 16 and a second glass substrate plate 18. OLED display 10 comprises hermetic seal 18 formed from frit 16 that protects OLEDs 14 located between the first glass substrate plate 12 and the second glass substrate plate 18. Hermetic seal 20 is typically located around the perimeter of OLED display 10. OLEDs 14 are located within a perimeter of hermetic seal 20. The composition of frit 16, and more particularly the composition of the glass of frit 16, as well as how the hermetic seal 20 is formed from frit 16 is described in greater detail below.
In one embodiment, first and second substrate plates 12 and 18 are transparent glass plates. Frit 16 is deposited along the edges of second glass substrate plate 18. For instance, frit 16 can be placed approximately 1 mm away from the free edges of the second glass substrate plate 18. In the preferred embodiment, frit 16 is a low temperature antimony-free glass frit containing vanadium to enhance the optical absorbance of the frit. Frit 16 may also include a filler material, such as beta eucryptite or beta quartz, that lowers the coefficient of thermal expansion (CTE) of the frit so that it matches or substantially matches the CTEs of the two glass substrate plates 12 and 18.
OLEDs 14 and other circuitry are deposited onto second glass substrate plate 18. The typical OLED 14 includes an anode electrode, one or more organic layers and a cathode electrode. However, it should be readily appreciated that other environmentally sensitive components can be deposited onto second glass substrate plate 18.
Optionally, frit 16 can be pre-sintered to first glass substrate plate 12 prior to sealing glass substrates 12 and 18 together. To accomplish this, first substrate plate 12 comprising frit 16 deposited thereon is heated in a furnace or oven so that it becomes attached to the first glass substrate plate 12.
Next, first and second glass substrate plates 12 and 18 are brought together with frit 16 with one or more OLEDs positioned between them, and frit 16 is irradiated by irradiation source 22 (e.g. a laser or an infrared lamp) so that the frit 16 forms hermetic seal 20 that connects and bonds first substrate plate 12 to second substrate plate 18. Hermetic seal 18 also protects OLEDs 14 by preventing oxygen and moisture in the ambient environment from entering into the OLED display 10.
It should be readily appreciated that the irradiating wavelength should be within the band of high absorption in the particular frit 16. For instance, Ytterbium (900 nm<λ<1200 nm), Nd:YAG (λ=1064 nm), Nd:YALO (λ=1.08 μm), and erbium (λ≈1.5 μm) CW lasers can be used depending on the optical properties of the particular frit 16 and glass substrate plates 12 and 18.
It should also be noted that most traditional low temperature sealing frits are PbO-based, because PbO frits have good flow, and adhesion properties. However, the antimony-free frits disclosed herein not only have a lower CTE than PbO-based frits, but also possess better aqueous durability, as well as being comparable to the traditional Pb-based frits with respect to adhesion.
In addition, although the role played by P2O5 in a successful sealing frit is important, since it permits stable glasses to be formed, from a laser-sealing and post-seal performance standpoint the effect of Sb2O3 and V2O5 should not be ignored. In previous testing, seals made with Sb-free, Zn-based vanadium-phosphate frits could only survive the relatively benign environment of 60° C./40% relative humidity (RH), while seals made from mixed Sb—Zn vanadium phosphate frits survived 60° C./85% RH before failing. Conversely, only seals made with Sb-vanadium-phosphate frits survived 85° C./85% RH exposure. However, despite the role that Sb2O3 plays in improving aqueous durability, feedback from potential customers consistently raise concerns about its presence. Moreover, Sb2O3 is thought to impede achieving desirably low glass transition temperatures (Tg). Thus, recent emphasis has been placed on development of a glass suitable for a sealing frit that is more environmentally friendly, noting that antimony is a toxic element.
Work on Sb2O3-free compositions began by first expressing a basic OLED device sealing frit composition as a three component system (20 mole % Sb2O3-50 mole % V2O5-30 mole % P2O5), simplifying the composition to a two component Sb2O3-free system (either 50 mole % V2O5-30 P2O5, 45 mole % V2O5-30 mole % P2O5, or 40 mole % V2O5-20 mole % P2O5), and then identifying the remaining components from the standpoint of their effect on aqueous durability, flow, glass transition temperature (Tg), and laser-sealability. Both aqueous durability, laser-sealability, and flow of any candidate frit compositions needed to be comparable to the Sb2O3-containing control sample, while the Tg requirements were relaxed with the criterion that Tg had to be equal to or less than 400° C. (Frits with Tg>400° C. are unlikely to flow sufficiently during the presintering step for OLED frits to be handleable in subsequent processing.) The following oxides were investigated as potential substitutes for antimony (Sb2O3): WO3, MoO3, TeO2, Bi2O3, Fe2O3, and TiO2. ZnO was also investigated, although in view of the poor durability results obtained for a ZnO—V2O5—P2O5 frit, it was considered only as a minor component (5-10 mole %) to lower Tg and maintain flow. The various oxides selected were chosen on the basis that they formed stable binary glasses with V2O5.
All of the compositions investigated were melted, poured as glass patties, then ball-milled to form fine-particle frits (typically with a d50=3-5 μm). A key bench test to screen the different compositions was to prepare and fire flow buttons of the various frits, and then to assess their aqueous durability. The flow buttons were fired in N2 to 400° C.-450° C. (depending upon Tg and crystallization tendency). After firing, the flow buttons were immersed in 90° C. deionized water for 48 hours to assess their aqueous durability. Control samples of the OLED frit (either as the D1 base glass, or as a 70:30 by weight blend of the base glass with a β-eucryptite filler material) were also included in each evaluation. Of the potential replacements for Sb2O3 that were investigated (see above), only TiO2 and Fe2O3 appeared promising.
Listed in Tables 1 and 2 are results for a 50 mole % V2O5-30 mole % P2O5 composition series with WO3, MoO3, WO3+ZnO, Bi2O3, and TeO2 as the third component. Also shown are data on the standard OLED base glass, D1, as a comparison standard. All compositions (given in mole %) were evaluated for quality of glass formed from the pour, glass transition temperature (Tg) by DSC, flow and sinterability as a 3 μm powder hand-pressed into a pellet (“flow button”) and fired at 400° C. for 1 hour in N2, and aqueous durability (as gauged by the color of the supernatant for a fired flow button sample—the darker the color, the less durable the sample) in the bench aqueous durability test described above. Note that none of the potential Sb2O3 replacements listed in Tables 1 and 2 produced the acceptable level of glass quality, Tg, flow, and aqueous durability exhibited by the Sb2O3-containing control (as judged by the appearance of the supernatant after 48 hrs, 90° C. deionized H2O).










TABLE 1






D1 (control)
D2
D3







Composition
Sb2O3, 22.9
V2O5, 50
V2O5, 50


(molar basis)
V2O5, 46.4
P2O5, 30
P2O5, 30



P2O5, 26.3
WO3, 20
MoO3, 20



Fe2O3, 2.4





Al2O3, 1.0





TiO2, 1.0




Glass quality at
Excellent
Fluid, good 
Very fluid, good


pour

quality
quality


Tg
355° C.
349° C.
315° C.


Flow (400°-1 hr, 
Very good flow 
Semi-glossy, well-
Glossy and black


N2)
and sinterability
sintered, no flow
with some slump


Aqueous
V. slightly 
Black
Black


durability, 
tinted




appearance of





supernatant





(48 hrs, 90° C. 





D.I. H2O)



















TABLE 2






D4
D5
D6







Composition
V2O5, 50
V2O5, 50
V2O5, 50


(molar basis)
P2O5, 30
P2O5, 30
P2O5, 30



WO3, 10
Bi2O3, 20
TeO2, 20



ZnO, 10




Glass quality 
Good glass, fluid, 
Crystallized 
More viscous pour, 


at pour
poured well
after pouring
glass looked good


Tg
323° C.
Not eval.
329° C.


Flow (400° C.- 
Poor flow
Not eval.
Semi-glossy black, 


1 hr, N2)


no slump


Aqueous
Black
Not eval.
Black


durability









More positive results for Sb2O3-free vanadium phosphate frits were obtained by Fe2O3 and/or TiO2 replacement of Sb2O3 (see Tables 3 and 4). All compositions are expressed in mole %. Several combinations of Fe2O3+TiO2 produced good glasses at pouring. High TiO2 glasses (i.e., ≧25 mole %) such as D8 had acceptable Tg and flow properties, but also exhibited poor aqueous durabilities. Higher Fe2O3 glasses (i.e., ≧25 or ≧30 mole %) such as D7 and D11 tended to produce poor glasses at pour, as evidenced by substantial surface devitrification. The relatively poor stability of these glasses (as indicated by the high amount of surface devitrification formed in the patty at pouring) resulted in poor flow as frits. They also tended to be unstable with respect to oxidation state, with a fired flow button from the same lot of powder alternately appearing either black (reduced) or red (oxidized) after the same firing conditions. Also included in Table 4 is D14, a glass with relatively high Fe2O3 and TiO2 levels, but with 10 mole % ZnO to lower the expected increase in Tg from the Fe2O3. Note that a second approach to accommodating high Fe2O3 levels is increasing the V2O5 content. But as may be seen for D9 and D10, aqueous durability was compromised at higher V2O5 content.











TABLE 3






D7
D8
D9
D10







Composition
V2O5, 45
V2O5, 45
V2O5, 50
V2O5, 50


(molar basis)
P2O5, 30
P2O5, 30
P2O5, 30
P2O5, 30



Fe2O3, 25
TiO2, 25
TiO2, 15
TiO2, 10





Fe2O3, 5
Fe2O3, 10


Glass quality
Substantial
Poured 
Poured 
Poured 


at pour
surface devit
nicely
nicely
nicely


Tg
353°
345°
323°
322°


Flow (400° C., 
Poorly 
Semi-glossy
Sintered, 
Sintered, 


1 hr, N2)
sintered
black, 
some
slight




no slump
flow
flow


Aqueous
Not tested
Black
Med. green
Med.


durability, 



green


appearance of






supernatant






(48 hrs, 90° C.






D.I. H2O)




















TABLE 4






D11
D12
D13
D14







Composition
V2O5, 42
V2O5, 40
V2O5, 45
V2O5, 40


(molar basis)
P2O5, 28
P2O5, 25
P2O5, 25
P2O5, 20



TiO2, 0
TiO2, 17.5
TiO2, 0
TiO2, 15



Fe2O3, 30
Fe2O3, 17.5
Fe2O3, 30
Fe2O3, 15






ZnO, 10


Glass quality
Viscous, 
Good 
Viscous, 
Good 


at pour
surface 
glass,
surface
glass, no



devit
no devit
devit
devit


Tg
371°
364°
376°
360°


Flow 
Poor-
Poor-
Poor
Semi-glossy


(400° C.,
powdery and
powdery

black, 


1 hr, N2)
unconsolidated


sintered,






no slump


Aqueous
Not eval.
Not eval.
Not eval.
Lt. brown


durability









It should also be noted that although the test samples of Tables 3 and 4 having P2O5 levels equal to or greater than 25 mole % performed poorly, it is anticipated that P2O5 levels less than 25 mole % can be successfully employed. Table 5 summarizes the results of a second set of Fe2O3 and TiO2 melts at 10 mole % ZnO. All compositions are expressed in mole %. As for the initial series, some combination of Fe2O3 and TiO2 is preferred, since Fe2O3 contributes excellent aqueous durability (but at the cost of high Tg and reduced frit sintering at 400°), and TiO2 results in lower Tg and improved flow (but at the cost of aqueous durability).












TABLE 5






D15
D16
D17
D18
D19







Composition
V2O5, 50
V2O5, 50
V2O5, 50
V2O5, 50
V2O5, 50


(molar 
P2O5, 20
P2O5, 20
P2O5, 20
P2O5, 20
P2O5, 20


basis)
ZnO, 10
ZnO, 10
ZnO, 10
ZnO, 10
ZnO, 10



Fe2O3, 0
Fe2O3, 5
Fe2O3, 10
Fe2O3, 15
Fe2O3, 20



TiO2, 20
TiO2, 15
TiO2, 10
TiO2, 5
TiO2, 0


Glass quality 
Poured 
Poured
Poured
Poured
Poured


at pour
nicely
nicely
nicely
nicely
nicely


Tg
297°
310°
322°
333°
348°


Flow (400°-
Well-
Well-
Sintered, 
Sintered, 
Sintered, 


1 hr, N2)
sintered,
sintered, 
slight 
some 
little 



good flow
good flow
flow
flow
flow


Aqueous 
Dark black
Dark 
Dark 
Clear
Clear


durability

black
black









An additional series of melts were made at higher levels of [Fe2O3+TiO2] with ZnO maintained at 5 mole % (see Tables 6 and 7 below). All compositions are expressed in mole %. Note that to accommodate the higher Tg of the high Fe2O3 glasses, flow was evaluated at 425° C., rather than the 400° C. previously used.











TABLE 6






D20
D21
D22
D23







Composition
V2O5, 40
V2O5, 40
V2O5, 40
V2O5, 40


(molar basis)
P2O5, 20
P2O5, 20
P2O5, 20
P2O5, 20



ZnO, 5
ZnO, 5
ZnO, 5
ZnO, 5



Fe2O3, 35
Fe2O3, 30
Fe2O3, 25
Fe2O3, 20



TiO2, 0
TiO2, 5
TiO2, 10
TiO2, 15


Glass quality
Substantial surface +
Surface devit
Surface devit
Good glass, no


at pour
bulk devit


devit


Tg
416°
407°
400°
389°


Flow (425°-
Not sinterable at
Not sinterable at
Not sinterable at
Sintered, no


1 hr, N2)
425°
425°
425°
flow


Aq. durability
Not tested
Not tested
Not tested
Clear





















TABLE 7






D24
D25
D26
D27
D28







Composition
V2O5, 40
V2O5, 40
V2O5, 40
V2O5, 40
V2O5, 40


(molar basis)
P2O5, 20
P2O5, 20
P2O5, 20
P2O5, 20
P2O5, 20



ZnO, 5
ZnO, 5
ZnO, 5
ZnO, 5
ZnO, 5



Fe2O3, 17.5
Fe2O3, 15
Fe2O3, 10
Fe2O3, 5
Fe2O3, 0



TiO2, 17.5
TiO2, 20
TiO2, 25
TiO2, 30
TiO2, 35


Glass quality
Good glass, 
Good glass, 
Good glass, 
Good glass, no
Good glass, no


at pour
no devit
no devit
no devit
devit
devit


Tg
3790
367°
351°
333°
324°


Flow (425°-
Sintered, 
Sintered
Sintered, 
Sintered, mod. 
Sintered, good


1 hr, N2)
slight flow
slight flow
mod, flow
flow
flow


Aq.
Clear with v.
Clear
Med. green
Med. green
Med. green


durability
slight tint


(residue)
(residue)









As seen in previous results from Tables 1, 2 and 3, 4, Fe2O3 levels not much higher than 20 mole % (e.g. about 25 mole %) resulted in frits with high Tg, poor stability, and unacceptable flow during 400° C.-425° C. sintering. Similarly, TiO2 not much higher than 20 mole % (e.g. about 25 mole %), resulted in frits with acceptable Tg, flow, and stability, but with unacceptable aqueous durability. Frits with Fe2O3 levels ranging between from about 10 mole % to less than 25 mole %, and with TiO2 levels from about 15 mole % to less than 25 mole % (at 5-10 mole % ZnO) combine excellent aqueous durability with acceptable flow, Tg, and glass stability.
The aqueous durability of the (Fe2O3+TiO2+ZnO) Sb2O3-free V2O5—P2O5 frits were found to be comparable to or slightly superior to the Sb2O3-containing standard composition. An unexpected result of the Sb2O3-free work is that the coefficient of thermal expansion (CTE) becomes dramatically lower for the (Fe2O3+TiO2+ZnO) frits at higher Fe2O3 levels. Shown below in FIG. 2 are CTE data for sintered frits whose composition is listed in Tables 3, 4 and 5. Data are presented for all sinterable frits in the 20 mole % (Fe2O3+TiO2) series of Tables 3, 4, (curve 120) and for the 35 mole % (Fe2O3+TiO2) series of Table 5 as indicated by curve 122. CTE data for sintered frit bars are plotted as a function of Fe2O3 level in each series up to 20 mole % Fe2O3, the apparent upper limit to achieving frits with good sinterability and oxidative stability. Note that CTE values are highest at 0 mole % Fe2O3/maximum TiO2 (20 mole % and 35 mole %, respectively), become essentially constant with increasing Fe2O3 level at 60-65×10−7/° C., and then decrease substantially at Fe2O3>15 mole % (5 mole % and 20 mole % TiO2, respectively), reaching a value of approximately 40×10−7/° C. at 17.5-20 mole % Fe2O3. By comparison, the CTE of the Sb2O3-containing base frit is approximately 70-80×10′/° C.
A more direct comparison of CTE between the Sb2O3-containing and Sb2O3-free frits is shown in FIG. 3 where CTE curves are plotted for D1 under both heating and cooling conditions (curves 124 and 126, respectively) and D29 (remelt of D24, Table 7) also under both heating and cooling conditions (curves 128 and 130, respectively). With a CTE value of approximately 40×10−7/° C. for an unfilled frit, it is possible, with the addition of fillers such as β-eucryptite or beta quartz, to lower the CTE value of this frit close to that of fused silica.
The lab scale aqueous durability results for Sb-free frits were corroborated in a large scale sealing trial involving 85° C./85% RH exposure of laser-sealed samples. Shown in Table 8 are results of the trial and comparison between the standard OLED frit (D1, Table 1; used as a 70:30 blend by weight with low CTE filler (β-eucryptite), and an Sb-free frit (D29, remelt of D24, Table 7; used as an 80:20 wt. blend with low CTE filler (β-quartz). Each frit blend was made into a paste, dispensed on several sheets of EAGLEXG display glass, presintered (Sb-containing standard, heated at 325° C. for 2 hours in air+400° C. for 1 hr in N2; Sb-free, heated at 325° C. for 2 hours in air+425° C. for 1 hour in N2), sealed to sheets of EAGLEXG, placed in an 85° C./85% relative humidity (RH) environmental chamber, and then examined periodically for evidence of seal leakage and Ca metal breakdown. In total, there were 3 sheets of the Sb-containing control composition and 7 sheets of the antimony-free composition included in the study, with 9 sealed arrays of Ca metal tabs per sheet. As may be seen in Table 8, several arrays failed either immediately after sealing or within 100 hrs of placing them in a 85° C./85% RH chamber for both the Sb-control and the Sb-free frits; these failures were related, most likely, to gross defects such as contamination present at random for each frit. However, after 96 hrs, no additional failures were observed for either the Sb-control or the Sb-free frit seals.








TABLE 8








No. of good cells












Laser-
At start of 
After 96 hrs
After 1056 hrs of



sealed
85/85
of 85/85
85/85





Standard Sb-frit blend (70:30, 
27 (3
25
24
24


D1: β-eucryptite)
sheets)





Sb-free frit blend (80:20, 
63 (7
61
57
57


D29: β-quartz)
sheets)









In summary, the excellent aqueous durability performance of Sb-vanadium phosphate frits was maintained without Sb2O3 by replacing the antimony oxide with a combination of Fe2O3+TiO2, along with a small addition of ZnO to maintain flow and glass transition temperature (Tg). The presence of Fe2O3 was found to have the greatest effect in improving durability. However, in large amounts it raised Tg, thus degrading frit flow during sealing. In addition, frits with high Fe2O3 levels (equal to or greater than about 25 mole %) tended to be oxidatively unstable, with repeat samples fired to the same schedule (425° C. in N2) exhibiting different colors (brown or black), with marked differences in the degree of flow. Although TiO2 actually degraded aqueous durability to some extent when added by itself, the combination of (Fe2O3+TiO2) appeared to be an ideal combination from the standpoint of obtaining laser-sealable frits with both high aqueous durability and low Tg 400° C.).
Both lab bench tests in 90° C. deionized water as well as 85° C./85% RH environmental chamber testing of laser-sealed samples indicate that frits based on the Fe2O3—TiO2—ZnO—V2O5—P2O5 system are capable of forming a hermetic seal after laser-sealing that will withstand high humidity conditions for extended times (≧1000 hrs). An unexpected result of the (Fe2O3+TiO2) replacement of Sb2O3 was that the CTE of the Sb-free frit without fillers decreased by approximately half (from 70-80×10−7/° C. to 35-45×10−7/° C.), with only a minor increase in Tg (from 355° C. to 370° C.). Frits with CTE values near 40×10−7/° C. have the potential, with the addition of fillers such as β-eucryptite or β-quartz, of being able to seal fused silica and other low CTE substrates such as KovarTM.
However, in spite of the success in developing the foregoing antimony-free frits, the high Tg (380° C.) resulted in a higher pre-sintering temperature ( ̃425° C.) than comparable antimony-containing frits like D1, and needed to be sustained for a longer period of time at the pre-sintering temperature. Thus, while environmentally friendly, such antimony-free frits tend to increase process times and therefore process costs. Moreover, the antimony-free frits described above were found to crystallize to at least some extent during the pre-sintering cycle, leading to somewhat reduced adhesion properties. Accordingly, additional work was conducted on a lower Tg, but still Sb-free, variant. The Tg of this newer frit, D30, was approximately 30° C. lower than D24, and was essentially identical to D1 in Tg and flow. This decreased Tg in D30 was achieved by incorporating about 7.5 mole % more V2O5 at the expense of ZnO and TiO2, indicating the role that small composition changes have on certain properties of the V2O5—P2O5 glasses. Shown in Table 9 is a comparison between D24 and the revised composition D30. All compositional values are in mole %.









TABLE 9






D24
D30

















V2O5
40
47.5


P2O5
20
22.5


ZnO
5
2.5


TiO2
17.5
10


Fe2O3
17.5
17.5


Al2O3
0
0


Tg
378° C.
351° C.









A key component in both D24 and D30 is Fe2O3, which may serve as a redox moderator of V2O5 (as did Sb2O3 in D1). Fe2O3, however, also acts to increase Tg. The other components of D24, namely ZnO and TiO2, serve to counteract to some extent the role of Fe2O3 in raising Tg, although they can also tend to lessen resistance to aqueous attack.
FIG. 4 shows photographs of sintered glass pellets of selected glass compositions suitable for the manufacture of glass frits in laboratory beakers for after being immersed in 90° C. deionized water for 48 hours. Prior to immersion the pellets were heat treated by exposing each flow button to 300° C. for one hour in air followed by 400° C. for one hour in nitrogen. FIG. 4 depicts, in order, from left to right, (a) D1, (b) D24, and (c) D30.
Although the lowering of Tg in Sb-free composition D30 to 350° C. was highly desirable, further composition efforts were undertaken to determine whether additional decreases in Tg were possible. Accordingly, B2O3, a low Tg glass former, was added. In making the B2O3 additions, the addition should be done in such as manner as to not degrade glass stability, aqueous durability, and flow. Indeed, the following guidelines were followed: (a) B2O3 should not be substituted for P2O5, since, as noted, P2O5 plays an important role in stabilizing the frit. When P2O5 is present at moderate levels (approximately 20 mole %), the vanadate glass frit tends to exhibit minimal crystallization, and as a result, the frit exhibits an extended region of viscous flow during the sealing process, leading to improved adhesion; (b) B2O3 should not be substituted for V2O5, since, as noted, this component is important for good flow and low CTE; (c) Fe2O3 should be maintained as close as possible to the level (17.5 mole %) present in the starting D24 and D30 compositions, or durability could be impaired. However, small decreases in Fe2O3 (down to about 12.5 mole %) can be tolerated with acceptable loss in aqueous durability; and (d) to maintain glass stability, the total amount of glass former (e.g., V2O5+P2O5+B2O3) should be at least 60 mole %, with 65-70 mole % more preferred for glass stability. With these prescriptions in mind, B2O3 was added as follows: B2O3 for (ZnO+TiO2+Fe2O3), with Fe2O3 maintained at ≧12.5 mole %). It should be noted that while the following discussion is centered around D1, D24 and D30, this samples are representative of families of compositions. For example, as shown below in Table 10, each of the samples D31-D35 is a glass composition essentially the same as the D24 composition, with the exception that B2O3 was substituted for Fe2O3 and TiO2 in varying amounts. The same is true for Table 11, except that the glass is the D30 glass and the variations are D36-D41 (and D40 had decreased P2O5).
Listed below in Table 10 is the B2O3 substitution series, including for reference D24. B2O3 was added in an amount up to 20 mole % following the substitution schema presented above. Tg decreased by approximately 70° C., from a temperature of 376° C. recorded for a remelt of D24 to a low of 305° C. for D34. The onset of crystallization is designated by Tx. All compositional values are in mole %.














TABLE 10







D24
D31
D32
D33
D34
D35






















V2O5
40
40
40
40
40
40


P2O5
20
20
20
20
20
20


B2O3
0
5
7.5
10
15
20


Fe2O3
17.5
15
13.7
12.5
10
7.5


TiO2
17.5
15
13.8
12.5
10
7.5


ZnO
5
5
5
5
5
5


Tg
376° C.
364° C.
356° C.
348° C.
325° C.
305° C.


Tx (onset)
497° C.
507° C.
506° C.
506° C.
511° C.
485° C.









Additionally, B2O3 substitutions were also made to D30, using the substitution schema presented earlier. B2O3 was added in an amount up to 15 mole %. The glass transition temperature Tg for this series decreased by approximately 50° C., from 351° C. to 299° C.















TABLE 11







D30
D36
D37
D38
D39
D40
D41























V2O5
47.5
47.5
47.5
47.5
47.5
47.5
47.5


P2O5
22.5
22.5
22.5
22.5
22.5
22.5
20


B2O3
0
1
3
5
7.5
10
15


Fe2O3
17.5
17
16
15
13.5
12.5
12.5


TiO2
10
9.5
8.5
7.5
6.5
5
2.5


ZnO
2.5
2.5
2.5
2.5
2.5
2.5
2.5


Tg
351°
350°
345°
331°
320°
311°
299°


Tx (onset)
493°
476°
442°
510°
512°
515°
511°









FIG. 5 is a graph illustrating the effect of including boron (B2O3) in certain frit glasses. For example, curve 200 depicts the effect on Tg for varying amounts of B2O3 in the general composition for D24, while curve 202 depicts the effect on Tg for varying amounts of B2O3 in the general composition for D30. Note that the addition of B2O3 into these glasses resulted in a monotonic, linear decrease in Tg, indicating that no abrupt structural changes are occurring in the base vanadium phosphate glass with boron addition over the composition range studied. Equally interesting is the data represented by curve 204, wherein B2O3 was added to the glass of D1, an antimony-containing glass. Curve 204 illustrates virtually no change in Tg, suggesting that the simple addition of boron per se may not result in a significant effect on Tg.
FIG. 6 shows photographs of sintered glass frit pellets in laboratory beakers for D24 glass, with varying amounts of B2O3 added, after being immersed in 90° C. deionized water for 48 hours. The pellets were produced by forming a glass melt, grinding the solidified glass to form a glass frit, compressing the frit into pellets and sintering the pellets by exposing each pellet to 300° C. for one hour in air followed by 400° C. for one hour in nitrogen. FIG. 4 depicts, in order, from left to right, (a) 0 mole % B2O3, (b) 5 mole % B2O3, (c) 7.5 mole % B2O3, (d) 10 mole % B2O3, (e) 15 mole % B2O3, and (f) 20 mole % B2O3. Aqueous durability can be judged based on the “darkness” (opacity) of the supernatant: The darker the supernatant, the less durable the glass. The results shown in FIG. 6 indicate acceptable aqueous durability for B2O3 in amounts up to about 10 mole %. It should be understood, however, that the acceptability of aqueous durability will depend on the end use of the glass.
FIG. 7 shows photographs of sintered glass pellets in laboratory beakers for D30 glass, with varying amounts of B2O3 added, after being immersed in 90° C. deionized water for 48 hours. The pellets were produced as above, by forming a glass melt, grinding the solidified glass to form a glass frit, compressing the frit into pellets and sintering the pellets by exposing each pellet to 300° C. for one hour in air followed by 400° C. for one hour in nitrogen. FIG. 7 depicts, in order, from left to right, (a) 0 mole % B2O3, (b) 1 mole % B2O3, (c) 3 mole % B2O3, (d) 5 mole % B2O3, (e) 7.5 mole % B2O3, (f) 10 mole % B2O3, and 15 mole % B2O3. As illustrated, aqueous durability in the samples of FIG. 7 are improved over a range from about 5 mole % to about 7.5 mole %, compared with other concentrations shown.
Shown in FIG. 8 is a bright field image of a section of a laser-sealed section of two LOTUSXT display glasses 12, 18 sealed with a frit 16 made with a blend of the 5 mole % B2O3-modified D30 frit and a CTE-lowering glass-ceramic filler using a method as previously described in the present disclosure. The view in looking downward through glass substrate 12 to glass substrate 18. The frit connecting the glass plates includes a sealed portion 206 and unsealed portions 208. Note that the width 210 of the sealed portion of the frit, i.e. that portion of the frit actually bonded to the glass substrates, is approximately 90% of the total frit width 212 (968 μm/1083 μm=89.38%), indicating excellent flow and sealing behavior for a boron-containing, antimony-free frit as disclosed herein.
Sb-free frits containing boron (B2O3) are described for sealing electronic devices, such as OLED displays, that offer comparable-to-lower Tg and comparable-to-improved aqueous durability than current Sb-containing frits, such as represented by D1. These same boron-containing Sb-free frits also possess lower Tg and comparable aqueous durability than non-boron-containing but Sb-free frits.
Although embodiments disclosed herein have been illustrated in the accompanying Drawings and described in the foregoing Detailed Description, it should be understood that these embodiments are not limited to those disclosed, but are capable of numerous rearrangements, modifications and substitutions without departing from the spirit of the disclosure as set forth and defined by the following claims.

## Claims

1. A glass article, comprising:
a glass substrate;
a frit sealing material attached to the glass substrate, the frit sealing material including an antimony-free glass comprising:
V2O5≧40 mole % and ≦52.5 mole %;
P2O5≧15 mole % and <25 mole %;
ZnO≧0 mole % and ≦10 mole %;
Fe2O3>0 mole % and <25 mole %;
TiO2>0 mole % and <25 mole %;
B2O3>0 mole % and ≦20 mole %; and

wherein TiO2+Fe2O3 is in a range from 15 mole % to 30 mole %, and a Tg of the antimony-free glass is ≦365° C.

2. The glass article according to claim 1, wherein the antimony-free glass comprises:
V2O5≧40 mole % and ≦50 mole %;
P2O5≧20 mole % and <23 mole %;
ZnO≧2 mole % and ≦5 mole %;
Fe2O3≧10 mole % and ≦20 mole %;
TiO2≧5 mole % and ≦20 mole %; and
B2O3≧1 mole % and ≦20 mole %.

3. The glass article according to claim 1, wherein the Tg of the antimony-free glass is ≦350° C.

4. The glass article according to claim 1, wherein a CTE of the sealing material substantially matches a CTE of the glass substrate.

5. The glass article according to claim 1, wherein the frit sealing material comprises a CTE-lowering filler.

6. The glass article according to claim 1, further comprising a second glass substrate, the second glass substrate sealed to the first glass substrate by the frit sealing material.

7. The glass article according to claim 6, wherein the glass article comprises an electronic device.

8. The glass article according to claim 7, wherein the glass article comprises one of a sensor, a photovoltaic device or a display device.

9. The glass article according to claim 8, wherein the glass article is an OLED display device.