AU704313B2 - Gallium sulfide glasses - Google Patents

Description

AUSTRALIA

Patents Act COMPLETE SPECIFICATION

(ORIGINAL)

Class Int. Class Application Number: Lodged: Complete Specification Lodged: Accepted: Published: Priority Related Art: Name of Applicant: Corning Incorporated Actual Inventor(s): Bruce Gardiner Aitken Mark Andrew Newhouse Address for Service: PHILLIPS ORMONDE FITZPATRICK Patent and Trade Mark Attorneys 367 Collins Street Melbourne 3000 AUSTRALIA Invention Title: GALLIUM SULFIDE GLASSES Our Ref 537263 POF Code: 1602/1602 The following statement is a full description of this invention, including the best method of performing it known to applicant(s):

WM

1A GALLIUM SULFIDE GLASSES This application is a divisional application of AU 16233/95, the entire disclosure of which is incorporated herein by reference.

Background of the Invention U. S. Patent No. 5,240,885 (Aitken et al.) describes the preparation of rare earth metal-doped cadmium halide glasses, which glasses transmit radiation well into the infrared portion of the electromagnetic radiation spectrum due to their low phonon energy. That capability commended their utility for the fabrication of efficient lasers, amplifiers, and upconverters when doped with the appropriate rare earth metals. Because metal-sulfur bonds are generally weaker than metal-oxygen bonds, sulfide glasses exhibit much lower phonon energies than oxide glasses and, therefore, transmit radiation much further into the infrared regiron of the electromagnetic radiati.on spectrum. Accordi gly, sulfide glasses were seen to have the potential of I eing excellent host materials of rare earth metals for 20 applications such as those listed above requiring efficient radiative emission.

Unfortunately, however, many sulfide glasses are black and, consequently, are unsuitable for some of the above applications inasmuch as such a host glass would tend to absorb the pump radiation instead of the rare earth metal dopant. One of the best known sulfide glasses, viz., .arsenic sulfide, is transparent to radiation in the long wavelength range of the visible portion of the radiation spectrum as well as far into the infrared region and, hence, would appear to be a suitable host glass for rare earth metals. Neveruh less, rare earth metals have been found to ~L be relatively insoluble in arsenic sulfide glasses, and it has proven to be difficult to dope those glasses with enough rare earth metal for sufficient pump power absorption.

Rare earth metals are known to be very soluble in most oxide glasses and their apparent insolubility in arsenic sulfide glasses has been conjectured to be due to the gross eaructural dissimilarity existing between the latter and oxide glasses. Arsenic sulfide glasses are believed to consist of long chains and layers of covalently bonded pyramidal AsS 3 groups, whereas oxide glasses typically comprise a three-dimensional network of relatively ionically bonded MO 4 tetrahedra, where M is a so-called network-forming metal such as silicon, phosphorus, aluminum, boron, etc.

Rare earth metals are readily accommodated in these ionic network structures where they can compensate charge imbalances that arise from the presence of two or more network-forming metals, aluminum and silicon in aluminosilicate glasses energetically similar sites may not exist in the two-dimensional covalent structures typical 20 of arsenic sulfide and related glasses.

One system of sulfide glasses which exhibit good transparency in both the visible and infrared portions of the radiation spectrum, and which possess a relatively ionic three-dimensional structure that would be expected to be more accommodating of rare earth metals, comprises gallium S'..*sulfide glasses. In contrast to arsenic sulfide glasses, the structure of these glasses is based upon a threedimensional linkage of corner sharing GaS 4 tetrahedra. Rare earth metals are readily soluble in these glasses. In fact, some of the most stable gallium sulfide glasses contain a rare earth metal as a major constituent. Of general interest are U.S. Patents 4,612,294, 4,704,371 and 4,942,144, and the following Literature Articles: ["Verres Formes Par Les Sulfures LS 3 Des Terres Rares Avec Le Sulfure De Gallium Ga 2 S3", Loireau-Lozac'h et al., Mat. Res. Bull., 11, 1489-1496 (1976)]. Other academic n studies of gallium sulfide-containing glasses have included the following publications: ["Systeme GeS--GaS Diagramme De Phases Obtention Et Proprietes Dss Verres", Loireau- Lozac'h et al., Ann. Chim.. 10, 101-104 (1975)]; ["Etude Du Systeme Ga 2

S

3 -Na 2 Palazzi, C. R. Acad. Sc. Paris, 229, Serie II, No. 9, 529-532 (1984)]; ["Study on Ge-Ga-x(X=S,Se) Glass Systems", Xilai et al., Collected Papers XIV Intl.

Congr. on Glass, 118-127 (1986)]; ["Le Systeme GaS 3 -Ag 2

S",

Guittard et al., Ann. Chim.. 8, 215-225 (1983)]; ["An EXAFS Structural Approach of the Lanthanum-Gallium-Sulfur Glasses", Benazeth et al., J. Non-Crst. S__lids. 110, 89-100 (1989)]; ["Glass Formation and Structural Studies of Chalcogenide Glasses in the CdS-Ga 2

S

3 -GeS 2 System", Barnier et al., Materials Science and Engineering,__.B, 209-214 (1990)], NMR Study of [(Ga 2

S

3 0 25 (GeS 2 7 5 0 7 5 (NaF) 0 2 Glass", Baidakov et al., Soviet Journal of Glass Physics and Chemistry. 18, No. 4, 322-324 (1992)); ["Chalcogenide Glasses in Ga 2

S

3 -GeS:-MeFn Systems", Orkina et al., Glass Physics and Chemistry 19, No. 3 (1993)]; "Active Fiber 20 Research Highlights", Snitzer et al., Fiber Optics Materials Research Program. Rutgers University, page 32 (April 13, 1993)]; and ["Pr 3 :La-Ga-S Glass: A Promising Material for 1.3 jm Fiber Amplification", Becker et al., Optical Amp. and heiAppn.., PD5, 19-23 (1992).

Summary of the Invention The above listing of literature references is indicative of the extensive research which has been conducted in recent years in the general field of gallium sulfide-containing glasses. That research disclosed properties exhibited by such glasses that suggested studies .i be undertaken to modify glasses having base compositions within the gallium sulfide system such that, when doped with rare earth metals, particularly neodymium, erbium, and praseodymium, they could be fabricated into very efficient lasers, amplifiers, and upconverters. Therefore, our invention was directed to developing glass compositions which .:re not only eminently suitable for those applications, but also which can be melted and formed into desired configurations utilizing standard glass melting and forming techniques.

According to the present invention, there is provided a transparent glass exhibiting excellent transmission far into the infrared region of the electromagnetic radiation spectrum consisting substantially expressed in the terms of mole percent, of 5-30% Ga 2

S

3 0-10% R 2

S

3 wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, and indium, 94.5% GeS 2 0.5-25% MS, wherein M is at least one modifying metal cation selected from the group consisting of barium, calcium, mercury, strontium, tin, yttrium, and a rare earth metal of the lanthanide series selected from the group consisting of lanthanum, cerium, praseodymium, neodymium, promethium, samarium, gadolinium, terbium, dysprosium, holmium, erbium, thulium, ytterbium, and lutetium, 0-10% total selenide, 0-25% total chloride and/or fluoride, and wherein the sulfur and/or selenium content can vary between 85-125% of the stoichiometric value.

The present invention also provides a waveguide structure exhibiting a 20 desired numerical aperture, including a core glass demonstrating a high refractive index surrounded by a cladding glass demonstrating a lower refractive index, wherein said core glass and said cladding glass, both consist of a lanthanum gallium sulfide glass according to the invention, but wherein in the cladding glass calcium has replaced a sufficient proportion of the lanthanum to lower the 25 refractive irndex thereof to a value appropriate to achieve the desired numnerical aperture in said waveguide structure.

The present invention further provides a waveguide structure exhibiting a desired numerical aperture, including a core glass demonstrating a high refractive index surrounded by a cladding glass demonstrating a lower refractive index, wherein said core glass and said cladding glass, both consist of a lanthanum gallium sulfide glass according to the invention, but wherein in the core glass gadolinium has replaced a sufficient proportion of the lanthanum to raise the IC C rW, NORD JLONAJ.MHWMMHSPECIflTVl233 DOC 9~a~r -4arefractive index thereof to a value appropriate to achieve the desired numerical aperture in said waveguide structure.

The present invention further provides a waveguide structure exhibiting a desired numerical aperture, including a core glass demonstrating a high refractive index surrounded by a cladding glass demonstrating a lower refractive index, wherein said core glass and said cladding glass, both consist of a bariummodified, germanium gallium sulfide glass according to the invention, but wherein the barium content of said core glass is sufficiently higher than the barium content o' said cladding glass to impart a sufficient difference between the refractive index of said core glass and said cladding glass to achieve the desired numerical aperture in said waveguide structure.

The present invention still further provides a transparent glass exhibiting excellent transmission far into the infrared region of the electromagnetic radiation spectrum consisting substantially expressed in terms of mole percent, of 5-30% Ga 2

S

3 0-10% R 2

S

3 wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, and indium, 55-94.5% GeS 2 0.5-25% trivalent europium sulfide, 0-10% total se!enide, 0-25% total chloride and/or fluoride, and wherein the sulfur and/or selenium content can vary between 85-125% of the stoichiometric value.

General Description of the Invention In view of the description in the last two citations in the above Literature Articles, we began our research by investigating the utility of gallium sulfide-based 25 glasses as hosts of Pr 3 ions, principally for the purpose of fabricating a fiber amplifier capable of exhibiting gain at a wavelength of 1.3 The measured lifetime of the 1.3|Lim fluorescence from Pr 3 is large in these glasses and, due to their large refractive index, the radiative emission process is about for times more efficient than in a Pr-doped halide glass with the same T. In order to produce a fiber amplifier, one must be able to control the refractive index of the material in such a manner as to form a waveguide structure typically consisting of IC C .W MIRDILONAJMi'.MHSPECI'DIV16233 DOC n--a.

-4ba core glass demonstrating a high refractive index surrounded by a cladding glass of lower refractive index.

The refractive index of lanthanum gallium sulfide glass is about 2.5 and our experiments indicated that the index appears to be rather insensitive to variations in the La:Ga ratio, as will be seen in Table I infra. We have discovered, however, that the refractive index thereof can be lowered substantially by partially replacing lanthanum with at least one modifier selected from the group calcium, sodium, and potassium. On the other hand, we have found that the partial replacement of lanthanum with other rare earth metals, in particular gadolinium, can lead to a significant increase in the refractive index, as will also be seen in Table I infra.

Such replacements can, in principle, allow one to achieve a core/clad structure with a numerical aperture well in excess of 0.4. From a .:a IC C NWOCRDILONA MKAMNMHSPEC'IIVl6233 DOC

I

practical point of view, calcium-substituted glasses are preferred for the cladding where the core glass is a Prdoped lanthanum gallium su3fide glass, inasmuch as the other relevant physical properties of the calcium-substituted glasses, thermal expansion and viscosity, more closely match those of the core glass. Thus, as is reported in Table I infra, a calcium-substituted glass exhibits a linear coefficient of thermal expansion over the temperature range of 25°-300°C of about 95 X 10- 7 /OC which closely matches the linear coefficient of thermal expansion of about 90-100 X exhibited by lanthanum gallium sulfide glasses.

We have found that the compositional region over which gallium sulfide glasses can be formed is quite extensive.

To illustrate, not only is there a broad glass forming region in the La 2

S

3 -Ga 2

S

3 system from about 50-80 mole percent Ga 2 S3, but also lanthanum can be replaced, in some instances completely, by other modifying cations including Ag, Sr, Li, Cd, Na, Hg, K, Pb, Ca, Tl, Ba, Sn, Y, and the other rare earth metals of the lanthanide series. The use of substantial amounts of La and/or Gd as modifiers in Pr-doped glasses has been theorized to suppress the tendency of Pr to cluster, thereby permitting higher dopant levels of Pr without compromising T. In addition, the network forming component Ga can be replaced in part by other tetrahedrally coordinated metals such aF Al, Ge, and In, or by pyramidally "'coordinated metals such as As and Sb. Examples of Pr 3 '-doped and Eu '-doped glasses illustrating that compositional flexibility are recorded in Table I infra. F i n a 1ly sulfide can be replaced in part by chloride without 30 degrading the infrared radiation transmission of these glasses. Fluoridation of the glasses may lead to blue- "shifting the spectral lines of rare earth metal dopants and, in particular, centering the 'G 4 3 H emission of Pr 3 at about 1.3 um, in like manner to the effect which the replacement of oxide by fluoride has in rare earth metal-doped oxide glasses.

In summary, a transparent gallium sulfide-based glass exhibiting excellent transmission far into the infrared region of the electromagnetic spectrum can be prepared from compositions consisting essentially, expressed in terms of mole percent on the sulfide basis, of 40-80?6 Ga-S,, 0-35% RS,, wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, arsenic, germanium, and indium, 1-50% LnS 3 wherein Ln is at least one cation selected from the group consisting of a rare earth metal and yttrium, and 1-45%; MS,, wherein M is at least one modifying cation selected from the group consisting of bariun, cadmium, calcium, lead, lithium, mercury, potassium, silver, sodium, strontium, thallium, and tin, and 0-10% total chloride and/or fluoride.

When glasses having compositions encompassed within the above ranges are doped with Pr ions in an amount equivalent to at least 0.005 mole percent Pr 2

S

3 they exhibit a -i value greater than 200 asec. Pr'ions in much larger amounts are operable, but a level equivalent to about 0.5% Pr,S 3 has been deemed to constitute a practical maximum. It is also of interest to note that, in view of the large optical nonlinearity of these Ga 2

S

3 glasses (X3 -45 X 1l' esu at 1.O6am) they possess the necessary properties f or making high X3 waveguides.

Further laboratory investigation of gallium sulfidebased glasses discovered a composition system, viz., germanium gallium sulf ide glasses, which can demonstrate exceptionally high values of T along with a substantial improvement in thermal stability and increased transmission in the visible portion of the electromagnetic radiation spectrum. We have found that Pr-doped analogues of germanium gallium sulfide glasses have a i as high as 362 *pm, that value being, to the best of our knowledge, the largest ever recorded for any glass.

In addition to Pr-doped binary germanium gallium sulfide glasses, we studied the optical and thermal properties of Pr-doped ternary glasses with the aim of synthesizing glasses with similarly high i, but improved thermal stability. As was shown to be the case for lanthanum gallium sulfide glasses, the region of glass formation is quite extensive when a third sulfide component is included. For example, modifying cations including barium, cadmium, calcium, lithium, potassium, silver, sodium, strontium, and tin can be added to broaden the field of stable glasses. Furthermore, either gallium or germanium can be partially replaced with other network forming cations such as aluminum, antimony, arsenic, and indium. Other components, such as lead, mercury, and thallium, can also be included to provide additional compositional flexibility, but their concentrations must be kept low so as not to degrade the visible transparency of the materials.

Furthermore, in these Ge-rich, gallium sulfide glass systems, we have found it to be possible to form stable glasses when the sulfur content of the glass is either more than or less than that dictated by normal stoichiometry. In practice, the sulfur content should not be less than about of the stoichiometric amount in order to avoid severely 20 curtailing the transmission of the glass in the visible portion of the radiation spectrum, and should not exceed about 125% of the stoichiometric amount in order to avoid materials with excessively high coefficients of thermal expansion or with a pronounced tendency to volatilize sulfur when reheated to an appropriate forming temperature.

Finally, sulfur can be partially replaced with selenium, although the ratio Se:Se+S must be held below 0.1 in order to avoid significant darkening of the glass.

In summary, a germanium gallium sulfide-based glass •*SCCC. 30 exhibiting excellent transmission far into the infrared region of the electromagnetic spectrum can be prepared from compositions consisting essentially, expressed in terms of mole percent on the sulfide basis, of 5-30% GaS 3 0-10% R 2

S

3 wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, arsenic, and indium, 55-94.5% GeS-, 0.5-25% MS,, wherein M is at least one modifying metal cation selected from the group consisting of barium, cadmium, calcium, lead, lithium, mercury, potassium, silver, sodium, strontium, thallium, tin, yttrium, and a rare earth metal of the lanthanide series, 0-10% total selenide, 0-25% total chloride and/or fluoride, and where the sulfur and/or selenium content can vary between about 85-125% of the stoichiometric value.

When glasses having compositions included within the above ranges are doped with Pr*3 ions in an amount equivalent to at least 0.005% Pr 2

S

3 they ex'iibit a T value greater than 300 gsec. Whereas much larger levels of Pr 3 ions are operable, an amount equivalent to about 0.5% Pr 2

S

3 has been considered to comprise a practical maximum.

As was observed above, the presence of a third sulfide component tends to broaden the working range of the binary germanium gallium sulfide glasses. Our laboratory work has demonstrated that these ternary sulfide glasses typically demonstrate working ranges between about 120 0 -170°C. It has been discovered that this stabilizing effect is maximized when barium is employed as a modifying cation. Thus, barium 20 modified, germanium gallium sulfide glasses are unusually stable and can have an effective working range of about 200 0 C. There is a broad area of enhanced glass stability in the BaS-Ga 2

S

3 -GeS 2 system which provides a wide range of compositions suitable for drawing Pr-doped glass fiber exhibiting gain at 1.3 gm. Moreover, because the thermal expansion and viscosity of these barium-containing sulfide glasses are believed to be relatively stable, whereas the refractive index exhibits an increase with increased levels of barium, single mode waveguide fibers can be fabricated 30 from core/cladding glass pairs which are thermally and mechanically compatible with sufficient differences in refractive index.

:Finally, in like manner to the glass compositions in the gallium sulfide system described above, it is likewise possible to partially replace sulfide in these germanium gallium sulfide glasses with chloride and/or fluoride.

Fluoridation is contemplated to shift the maximum of the -semission from 1.34 ym to shorter wavelengths, so that the desired fluorescence is more closely centered in the transmission window of 1.3 Aum optical fiber.

The general composition region of the inventive germanium gallium sulfide glasses consists essentially, expressed in terms of mole percent on the sulfide basis, of about 5-30% Ga 2

S

3 55-94.5% GeS,, 0.5-25% MSX, wherein M is a modifying cation which may be incorporated as a sulfide and/or chloride and/or fluoride, and 0-10% R,S 3 wherein R is a network forming cation selected from the group of Al, As, In, and Sb. The preferred glasses contain barium as the modifying cation.

An effective waveguide structure comprises a core glass demonstrating a high refractive index surrounded by a cladding glass exhibiting a lower refractive index, the difference in those refractive indices being selected to achieve a desired numerical aperture. We have discovered three composition areas particularly suitable for the fabrication of waveguide structures.

20 The first area comprises a core glass consisting of a lanthanum gallium sulfide glass and a cladding glass consisting of a lanthanum gallium sulfide glass where calcium has replaced a sufficient proportion of the lanthanum to lower the refractive index thereof to a value appropriate to achieve the desired numerical aperture.

The second area comprises a cladding glass consisting of a lanthanum gallium sulfide glass and a core glass consisting of a lanthanum gallium sulfide glass wherein gadolinium has replaced a sufficient proportion of the lanthanum to raise the refractive index to a value appropriate to achieve the desired numerical aperture.

The third area comprises a core glass consisting of a barium-modified, germanium gallium sulfide glass and a cladding glass also consisting of a barium-modified, germanium gallium sulfide glass, but wherein the barium content of said core glass is sufficiently higher than the barium content of said cladding glass to impart a sufficient difference between the refractive index of said core glass and said cladding glass to achieve the desired numerical aperture.

Descritin of Preferre Embodiments Table I records a group of glass 2ompositions, expressed in terms of mole percent, illustrating glasses in the basic gallium sulfide system. Most of the glasses were doped with Pr 3 ions to determine the level of T. Because the glasses were prepared in the laboratory, a sulfide was used for each component. Such is not necessary, however.

Thus, sulfur-containing batch materials other than sulfides can be utilized so long as the chosen materials, upon melting together with the other batch ingredients, are converted into the desired sulfide in the proper proportions.

The glasses were prepared by compounding the batch constituents, thoroughly mixing the constituents together to 20 aid in securing a homogeneous glass, and then dispensing the batch mixtures into vitreous carbon or alumina crucibles.

The crucibles were moved into a furnace operating at about 1000-1100 0 C, maintained at that temperature for about 15-60 minutes, the melts thereafter poured into steel molds to form discs having a diameter of 4 cm and a thickness of mm, and those discs transferred immediately to an annealer operating at about 500 0 -550 0

C.

Table I also recites the density expressed in .terms of g/cm 3 the transition temperature and the temperature of the onset of crystallization expressed in terms of the refractive index the linear coefficient of thermal expansion expressed in terms of X 10 7 /oC, and the t values, expressed in terms of psec, of each glass where measured.

TABLE I 11- EXAMPLE 1 -2 Ga 2

S

3 La 2

S

3 Li2S Na 2

S

K

2

S

CaS GeS Pr 2

S

3 Den.

nco 65.00 24.95 10 .00 0 .05 208 70.00 65.00 19.97 24.95 10.00 10.00 0.03 0.05 3.74 3.80 528 534 663 627 2.31 242 65.00 14.95 20.00 0 .05 3.51 520 634 240 70.00 19.97 inl. 00 0 .03 3 .68 540 691 2.29 70.00 9.97 20.00 0.03 3.30 524 632 2 22 70.00 19 .97 10.00 0 .03 3 .84 536 667 2 6 48.80 20.85 30.30 0 22 S

C

-12- TABLE I (cont.) 2a .12 I- I

EXAMPLE

Ga 2

S

3 La 2

S

3 CaS BaS In 2

S

3 EuS Gd 2 S3 Pr 2

S

3 Den.

Tg

T

no 6 2 1 5.00 65.00 65.00 4.95 14.95 29.95 0.00 20.00 5 .00 52.50 29.95 17.50 65.00 34.90 65.00 34.00 65.00 24.95 65.00 17.4 .jft 0.05 3.85 536 638 224 94.5 0.05 0.05 0.05 JLU .L UU 10.00 0.05 4.06 4.15 -549 658 218 17.50 0.05 4.22 541 657 2.60 212 Table II records a expressed in ter of further group of glass compositions, mole percent, illustrating glasses A A AS..o

*.SA

having compositions composed of GeS 2 Ga 2

S

3 and at- )east c modifying metal cation being included as a sulfide and/or a chloride and/or a fluoride. Table IIa recites the same glass compositions in terms of atomic percent. Similarly to the glass compositions recited in Tables I and II, most of the glasses were doped with Pr3 ions to determine the level of r. The glasses were typically prepared by melting mixtures of the respective elements, although in some cases a given metal was batched as a sulfide.

The batch materials were compounded, mixed together, and sealed into silica or VYCOR® cmpoules which had been evacuated to about 10 5 to 10 6 Torr. The ampoules were placed into a furnace desiqned to impart a rocking motion to the .'-atch diring melting. After melting the batches for about 1-2 days at 900°-950 0 C, the melts were quenched in a blast of compressed air to form homogeneous glass rods a A OS A S 3 having diameters of about 7-10 mm and lengths of about 60-70 mm, which rods were annealed at about 400"-450':r Table III also recites the differences in temperature between the crystallization temperature and the transition temperature expressed in terms of Cand the T expressed in terms of Azsec.

EXAMPLE

Ga 2

S

3 GeS 2 La 2

S

3 Na 2

S

K

2

S

Ag 2

S

CaS Pr 2

S

3 T, -T9 9.98 85.0 11.48 86.0 8.98 86.0 13.98 83.5 11.48 86.0 11.48 86.0 13.98 81.0 2.5 0.02 278 0.02 139 316 0 2 169 234 0 .02 157 0 .02 142 2.5 0 .02 160 304 0 .02 152 0*

EXARPLE

Ga 2

S

3 GeS, CdS SnS 30 In 2 3- BaS Pr 2

S

3 T~ T 13.98 83.5 11.18 86.0 8.98 86.0 5.0 13.98 78.5 9.31 86.0 11.48 86.0 2.5 13.98 81.0 0.02 190 288 4.67 0.02 119 0.02 130 340 0.02 105 304 0.02 136 2.5 0.02 0.02 151 182 306 298 -124 maRTE IT (cont- EXAMPLE a2 31 3_4 8.98 86.0 Ga 2

S

3 GeS 2 BaS BaC1 2 AZs 2S3 Sb 2

S

3 GeSe 2 Pr 2

S

3 TX Tq

EXAMPLE

Ga 2

S

3 GeS 2 BaS B a C1 2 BaF 2 Excess S Pr 2

S

3 T, Tq

I

17.98 75 .0 7.5 0 .02 196 285 19.48 70.0 10. 0 0.02 17 1 267 13.98 81.0 2.5 0 .02 140 8.98 86.0 11.48 81.0 5.0 3-7 13.98 75.78 5.0 0 .02 139 312 0 .02 140 336 0 .02 189 5 .22 0 .02 150 297 38a 6.48 86.0 7.5 19 .98 65.0 15 .0 21.38 64 .3 14 0 76.0 10.0 14.0 17.48 76.0 75.0 10.0 5.0 2.5 19.98 70.0 14 .3 0 .02 142 20.0 -10.0 0 .02 126 242 0. 02 169 232 0.02 172 318 0 .02 115 357 TABlETIIa EXAMPLE 11 1 1 20 2. 22 1 Ga 6.05 7.11 5.64 8.52 7.11 7.16 8.65 Ge 25.76 26.63 27.04 25.46 26.63 26.83 25.08 La 3.03 Na 1.55 3.14 K 1.52 Ag 1.55 Ca 0.78 1.55 Pr 0.02 0.02 0.02 0.02 0.02 0.02 0.02 S 65.15 64.71 64.15 64.48 64.71 65.21 64.71 EXAMPLE 4 25 Zi 97l 2az Ga 8.59 7.16 5.73 8.72 5.67 7.16 8.65 Ge 25.65 26.83 27.48 24.49 26.22 26.83 25.08 Cd 0.77 Sn 0.7a 1.60 2.34 In 2.85 Ba 0.78 1.55 Pr 0.02 0.02 0.02 0.02 0.02 0.02 0.02 S 64.98 65.21 65.18 64.43 65.24 65.21 64.71 EXAMPLE 14 Ga 10.67 12.11 8.59 5.47 5.47 7.11 8.65 Ge 22.90 21.21 24.88 26.22 26.22 25.08 2E.08 Ba 2.29 3.03 1.54 1.55 1.55 As 3.05 Sb 3.05 1.55 Pr 0.02 0.02 0.02 0.02 0.02 0.02 0.02 S 64.12 63.64 63.44 65.24 65.24 64.71 61.47 S 35 Cl 1.54 Se 3.24 e I- -16- TABLE Ia (ConcJ.) EXAMPLE 31a 41 4l Ga Ge Ba Pr

S

F

4.24 28.15 2.45 0.02 65.14 12.29 20.00 4.62 0.02 63.08 12.47 18.76 4.17 0.01 56.24 8.34 7.80 21.18 2.79 68.23 9.41 10.59 25.54 22.73 3.36 2.27 0.02 61.69 62.88 3.

1 3 .1.93 20.90 2.99 0.01 1.19 2.99 1.52 9 9** 9.* .9 9 9 9* 9.

As can be seen from Table II, the Pr-doped glasses in the ternary field Ga 2

S

3 -GeS 2 -MSx, where M is a modifying cation, exhibit excellent optical properties, as evidenced by T values typically in excess of 300 psec, and working ranges in excess of 100°C, with some compositions approaching 2000C.

It will be appreciated that the above procedures reflect laboratory practice only. That is, the batches for the inventive glasses can be melted in large commercial melting units and the melts formed into desired glass shapes employing commercial glass forming techniques and equipment.

It is only necessary that the batches be heated to a 25 sufficiently high temperature for a sufficient length of time to obtain a homogeneous melt, and tne melt then cooled and simultaneously shaped at a sufficiently rapid rate to avoid the development of devitrification.

Based upon an overall balance of properties, the preferred inventive composition ranges consist essentially, expressed in terms of mole percent, of 5-26% GaS 3 58-89% GeS 2 0.5-22% BaS and/or 0.5-15% MSx, wherein M is at least one modifying cation selected from the group consisting of Ag, Ca, Cd, Sn, Sr, Y, and a rare earth metal of the 35 lanthanide series, 0-6% R 2

S

3 wherein R is at least one network forming cation selected from the group consisting of Al, As, In, and Sb, 0-5% total selenide, and 0-10% total I. *e 9* 9 -17chloride and/or fluoride, and wherein the sulfur and/or selenium content can vary between 90-120% of the stoichiometric value.

Example 31 constitutes the most preferred embodiment of the invention.

0 a 000 o ee 4

Claims (5)

1. A transparent glass exhibiting excellent transmission far into the infrared region of the electromagnetic radiation spectrum consisting substantially expressed in the terms of mole percent, of 5-30% Ga 2 S 3 0-10% R 2 S 3 wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, and indium, 55-94.5% GeS 2 0.5-25% MSx, wherein M is at least one modifying metal cation selected from the group consisting of barium, calcium, mercury, strontium, tin, yttrium, and a rare earth metal of the lanthanide series selected from the group consisting of lanthanum, cerium, praseodymium, neodymium, promethium, samarium, gadolinium, terbium, dysprosium, holmium, erbium, thulium, ytterbium, and lutetium, 0-10% total selenide, 0-25% total chloride and/or fluoride, and wherein the sulfur and/or selenium content can vary between 85-125% of the stoichiometric value.

2. A transparent glass according to claim 1 also containing up to an amount of selenium equivalent to 10% GeSe 2 but wherein the ratio Se:Se S is less than 0.1.

3. A transparent glass according to claim 1 or 2 which, when doped with praseodymium in an amount equivalent to at least 0.005% Pr 2 S 3 exhibits a T value greater than 300 .lsec.

4. A transparent glass according to any one of claims 1 to 3, wherein the difference between the temperature of the onset of crystallization and the i transition temperature is at least 120 0 C. "oo 5. A transparent glass according to claim 1 consisting substantially of 5-26% Ga 2 S 3

58-89% GeS 2 0.5-22% BaS and/or 0.5-15% MSx, wherein M is at least one modifying cation selected from the group consisting of calcium, strontium, tin, yttrium, and a rare earth metal of the lanthanide series selected from the group consisting of lanthanum, cerium, praseodymium, neodymium, promethium, samarium, gadolinium, terbium, dysprosium, holmium, erbium, thulium, ytterbium, and lutetium, 0-6% R 2 S3, wherein R is at least one network forming cation Sa.. selected from the group consisting of aluminium, antimony, and indium, total selenide, and 0-10% total chloride and/or fluoride, and wherein the sulfur IC C WlNVA'ORDLONAyMHMMHSPECIIV16233 DOC -19- and/or selenium content can vary between 90-120% of the stoichiometric value. 6. A waveguide structure exhibiting a desired numerical aperture, including a core glass demonstrating a high refractive index surrounded by a cladding glass demonstrating a lower refractive index, wherein said core glass and said cladding glass, both consist of a lanthanum gallium sulfide glass according to claim 1, but wherein in the cladding glass calcium has replaced a sufficient proportion of the lanthanum to lower the refractive index thereof to a value appropriate to achieve the desired numerical aperture in said waveguide structure. 7. A waveguide structure exhibiting a desired numerical aperture, including a core glass demonstrating a high refractive index surrounded by a cladding glass demonstrating a lower refractive index, wherein said core glass and said cladding glass, both consist of a lanthanum gallium sulfide glass according to claim 1, but wherein in the core glass gadolinium has replaced a sufficient proportion of the lanthanum to raise the refractive index thereof to a value appropriate to achieve the desired numerical aperture in said waveguide structure. 8. A waveguide structure exhibiting a desired numerical aperture, including a core glass demonstrating a high refractive index surrounded by a cladding glass demonstrating a lower refractive index, wherein said core glass and said cladding glass, both consist of a barium-modified, germanium gallium su;fide glass according to claim 1, but wherein the barium content of said core glass is sufficiently higher than the barium content of said cladding glass to impart a V',I,6 sufficient difference between the refractive index of said core glass and said cladding glass to achieve the desired numerical aperture in said waveguide structure. A transparent glass exhibiting excellent transmission far into the infrared region of the electromagnetic radiation spectrum consisting substantially *expressed in terms of mole percent, of 5-30% Ga 2 S 3 0-10% R 2 S 3 wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, and indium, 55-94.5% GeS 2 0.5-25% trivalent europium sulfide, 0-10% total selenide, 0-25% total chloride and/or fluoride, and wherein the sulfur and/or selenium content can vary between 85-125% of the stoichiometric value. IC C \NV VORDdLO,'r-, MHtMHSPECIIrVI6233 DOC A transparent glass according to claim 9 also containing up to an amount of selenium equivalent to 10% GeSe 2 but wherein the ratio Se:Se S is less than 0.1. 11. A transparent glass according to claim 9 or 10 which, when doped with praseodymium in an amount equivalent to at least 0.005% Pr 2 S 3 exhibits a T value greater than 300 pisec. 12. A transparent glass according to any one of claims 9 to 11, wherein the difference between the temperature of the onset of crystallization and the transition temperature is at least 120°C. 13. A transparent glass according to claim 1, wherein M is selected from the group consisting of barium, calcium, strontium, tin, yttrium, and a rare earth metal of the lanthanide series selected from the group consisting of lanthanum, cerium, praseodymium, neodymium, promethium, samarium, gadolinium, terbium, dysprosium, holmium, erbium, thulium, ytterbium, and lutetium. 14. A transparent glass according to claim 1, substantially as herein described with reference to any one of the Examples. DATED: 22 July, 1998 20 PHILLIPS ORMONDE FITZPATRICK Attorneys for: CORNING INCORPORATED *I *ii 1* I IC C WN ORO LONA\MHMIUiMHSPECI\flIV1B233 DOC ABSTRACT A transparent glass exhibiting excellent transmission far into the infrared region of the electromagnetic radiation spectrum consisting substantially expressed in the terms of mole percent, of 5-30% Ga 2 S 3 0-10% R 2 S 3 wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, and indium, 55-94.5% GeS 2 0.5-25% MS x wherein M is at least one modifying metal cation selected from the group consisting of barium, calcium, mercury, strontium, tin, yttrium, and a rare earth metal of the lanthanide series selected from the group consisting of lanthanum, cerium, praseodymium, neodymium, promethium, samarium, gadolinium, terbium, dysprosium, holmium, erbium, thulium, ytterbium, and lutetium, 0-10% total selenide, 0-25% total chloride and/or fluoride, and wherein the sulfur and/or selenium content can vary between 85-125% of the stoichiometric value. *0*t e* feoto9 IC C WtMNWORDULONA\MMHMMHSPECIVI68233 DCC