Germanium gallium sulfide glasses

Abstract: This invention is directed broadly to transparent glasses exhibiting excellent transmission far into the infrared region of the electromagnetic radiation spectrum, those glasses consisting essentially, expressed in terms of mole percent, of 40-80% Ga 2 S 3 , 0-35% RS x , wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, arsenic, germanium, and indium, 1-50% Ln 2 S 3 , wherein Ln is at least one cation selected from the group consisting of a rare earth metal cation and yttrium, 1-45% MS x , 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, and tin, and 0-10% total chloride and/or fluoride. Glass compositions consisting essentially, 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, arsenic, 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, cadmium, calcium, lead, lithium, potassium, silver, sodium, strontium, tin, yttrium, and a rare earth metal of the lanthanide series, 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 when doped with Pr demonstrate exceptionally high values of τ.

Description: This invention relates to germanium gallium sulfide glasses. US 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 region of the electromagnetic radiation spectrum. Accordingly, sulfide glasses were seen to have the potential of being excellent host materials of rare earth metals for 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. Nevertheless, rare earth metals have been found to 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 structural 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, e.g., aluminum and silicon in aluminosilicate glasses -- energetically similar sites may not exist in the two-dimensional covalent structures typical 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 sulfide glasses. In contrast to arsenic sulfide glasses, the structure of these glasses is based upon a three-dimensional 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 L 2 S 3 Des Terres Rares Avec Le Sulfure De Gallium Ga 2 S 3 ", Loireau-Lozac'h et al., Mat. Res. Bull., 11 , 1489-1496 (1976)]. Other academic studies of gallium sulfide-containing glasses have included the following publications: ["Systeme GeS 2 -Ga 2 S 3 Diagramme De Phases Obtention Et Proprietes Des Verres", Loireau-Lozac'h et al, Ann. Chim,, 10 , 101-104 (1975)]; ["Etude Du Systeme Ga 2 S 3 -Na 2 S", 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. Cong. on glass , 118-127 (1986)]; ["Le Systeme Ga 2 S 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-Cryst. Solids, 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, B7 , 209-214 (1990)], {"F NMR Study of [(Ga 2 S 3 ) 0.25 (GeS 2 ) 0.75 ] 0.75 (NaF) 0.25 Glass", Baidakov e t al, Soviet Journal of Glass Physics and Chemistry, 18 , No 4, 322-324 (1992)}; ["Chalcogenide Glasses in Ga 2 S 3 -GeS 2 -MeF n Systems", Orkina et al, Glass Physics and Chemistry, 19 , No 3, (1993)]; ["Active Fiber 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 1.3µm Fiber Amplification", Becker et al, Optical Amp. and Their Appl. , PD5, 19-23 (1992)]. The following references disclose sulfide glasses with the composition stated: Barnier et al, Mat. Res. Bull., 15 , 689-705(1980): 20-80 moles GeS 2 ; 10-50 moles Ga 2 S 3 ; 10-50 moles EuS; Barnier et al, Mat. Sci. Eng., B22 , 191-200 (1994): 30-80% Ge 2 S 4 ; 10-50% Ga 2 S 3 ; 10-60% Ag 2 S; Barnier & Guittard, Mat. Sci. Eng., B7 , 209-214 (1990); 16-84% GeS 2 ; 1.6-54% Ga 2 S 3 ; 7-62% CdS; US-A-4,942,144 (Martin); 5-70% MX; 5-70% M 1 2 x 3 ; 10-90% siX 2 , where M is Ca, Ba, Sr, Zn or Pb; M 1 is Al or Ga; X is S, Se or Te; US-A-3,214,241 (Forber et al ); 20-75% GeS; 0-25% GaS; 0-25% InS; 0-20% As 2 S 3 ; 0-15% SrS; SU-A-1 135 726 (Derwent Abstract AN 85-2020720; 55-75% gEs 2 ; 15-25% Ga 2 S 3 ; 10-20% NaCl; SU-A-1 402 913 (Derwent Abstract AN 88-367158) : 20-85% GeS 2 ; 5-35% Ga 2 S 3 ; 5-30% NaCl; Baidakov et al, Soviet Journal of Glass Physics and Chemistry, 18(1) , 91-92 (1992); GeS 2 -Ga 2 O 3 ; 0.25-30 mol% PbF 2 ; Baidakov et al, Soviet Journal of Glass Physics and Chemistry; 18(4) , 322-324 (1992); 75% [3GeS 2 1Ga 2 S 3 ]; 25% NaF; SU-A- 1715 725 (Derwent Abstract AN 93-034117); 10-50% Ge; 5-45% Ga; 30-50% S, 1-20% NaF; Orkina & Baidakov, Soviet Journal of Glass Physics and Chemistry, 19(3) , 228-234 (1993); GeS 2 -Ga 2 S 3 ; MeFn where Me is Bi, Mn, Pb, Tl or Na. 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. According to one aspect the present invention provides a transparent glass exhibiting excellent transmission far into the infrared region of the electromagnetic radiation spectrum consisting essentially, 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, arsenic, 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, lithium, mercury, potassium, strontium, tin, yttrium, and a rare earth metal of the lanthanide series other than europium, 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. Laboratory investigation of gallium sulfide-based glasses discovered a composition system, viz. , germanium gallium sulfide glasses, which can demonstrate exceptionally high values of τ 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 τ as high as 362 µm, 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 τ, but improved thermal stability. The region of glass formation is quite extensive when a third sulfide component is included. For example, modifying cations, including barium, calcium, lithium, potassium, 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 mercury 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 85% of the stoichiometric amount in order to avoid severely 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 volatilze sulfur when reheated to an appropriate forming temperature. Finally, sulfur can be partially replaced with a selenium up to a total of 10% selenide, although the ratio Se:Se+S is preferably held below 0.1 in order to avoid significant darkening of the glass. 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 exhibit a τ value greater than 300 µsec. 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. 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°C-170°C. It has been discovered that this stabilizing effect is maximized when barium is employed as a modifying cation. Thus, barium modified, germanium gallium sulfide glasses are unusually stable and can have an effective working range of about 200°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 µm. 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 from core/cladding glass pairs which are thermally and mechanically compatible with sufficient differences in refractive index. Finally, it is 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 1 G 4 → 3 H 5 emission from 1.34 µm to shorter wavelengths, so that the desired fluorescence is more closely centered in the transmission window of 1.3 µm 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 2 , 0.5-25% MS x , wherein M is a modifying cation which may be incorporated as a sulfide and/or chloride and/or fluoride, and 0-10% R 2 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. According to a further aspect, the present invention provides a waveguide structure exhibiting a desired numerical aperture comprising a core glass demonstrating a high refractive index surrounded by a cladding glass demonstrating a lower refractive index characterised in that both the core glass and the cladding glass are germanium gallium sulfide glasses as defined above containing barium as the modifying cation M and wherein the barium content of the core glass is sufficiently higher than the barium content of the cladding glass to impart a sufficient difference between the refractive index of said core glass and the cladding glass to achieve the desired numerical aperture in the waveguide structure. Table I records a group of glass compositions, expressed in terms of mole percent, illustrating glasses having compositions composed of GeS 2 , Ge 2 S 3 , and at least one modifying metal cation being included as a sulfide and/or a chloride and/or a fluoride. Table I recites the same glass compositions in terms of atomic percent. Most of the glasses were doped with Pr 3+ ions to determine the level of τ. 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 of VYCOR® ampoules which had been evacuated to about 10 -5 to 10 -6 Torr. The ampoules were placed into a furnace designed to impart a rocking motion to the batch during melting. After melting the batches for about 1-2 days at 900°C-950°C, the melts were quenched in a blast of compressed air to form homogeneous glass rods having diameters of about 7-10 mm and lengths of about 60-70 mm, which rods were annealed at about 400°-450°C. Table III also recites the differences in temperature between the crystallization temperature (T x ) and the transition temperature (T g ) expressed in terms of °C, and the τ expressed in terms of µsec. As can be seen from Table I, the Pr-doped glasses in the ternary field Ga 2 S 3 -GeS 2 -MS x , where M is a modifying cation, exhibit excellent optical properties, as evidenced by τ values typically in excess of 300 µsec, and working ranges in excess of 100°C, with some compositions approaching 200°C. 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 sufficiently high temperature for a sufficient length of time to obtain a homogeneous melt, and the 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% Ga 2 S 3 , 58-89% GeS 2 , 0.5-22% BaS and/or 0.5-15% MS x , wherein M is at least one modifying cation selected from the group consisting of Ca, Sn, Sr, Y and a rare earth metal of the lanthanide series other than europium, 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 chloride and/or fluoride, and wherein the sulfur and/or selenium content can vary between 90-120% of the stoichiometric value. Example 10 constitutes the most preferred embodiment of the invention.

Claims: A transparent glass exhibiting excellent transmission far into the infrared region of the electromagnetic radiation spectrum consisting essentially, 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, arsenic, 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, lithium, mercury, potassium, strontium, tin, yttrium, and a rare earth metal of the lanthanide series other than europium, 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. A transparent glass according to claim 1 also containing up to an amount of selenium equivalent to 10% GeS 2 , but wherein the ratio Se:Se+S is less than 0.1. A transparent glass according to claim 1 which, when doped with praseodymium in an amount equivalent to at least 0.005% Pr 2 S 3 , exhibits a τ value greater than 300 µsec. A transparent glass according to claim 1 wherein the difference between the temperature of the onset of crystallization and the transition temperature is at least 120°C. A transparent glass according to claim 1 consisting essentially of 5-26% Ga 2 S 3 , 58-89% GeS 2 , 0.5-22% BaS and/or 0.5-15% MS x , 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 other than europium, 0-6% R 2 S 3 , wherein R is at least one network forming cation selected from the group consisting of aluminum, antimony, arsenic, and indium, 0-5% total selenide, and 0-10% total chloride and/or fluoride, and wherein the sulfur and/or selenium content can vary between 90-120% of the stoichiometric value. A waveguide structure exhibiting a desired numerical aperture comprising a core glass demonstrating a high refractive index surrounded by a cladding glass demonstrating a lower refractive index, characterised in that both the core glass and the cladding glass are germanium gallium sulfide glasses as claimed in any of claims 1 to 4 containing barium as the modifying metal cation M and wherein the barium content of the core glass is sufficiently higher than the barium content of the cladding glass to impart a sufficient difference between the refractive index of the core glass and the cladding glass to achieve the desired numerical aperture in the waveguide structure.

Inventors: AITKEN BRUCE GARDINER, NEWHOUSE MARK ANDREW, AITKEN, BRUCE GARDINER, NEWHOUSE, MARK ANDREW
Applicants: CORNING INC, CORNING INCORPORATED
Application year: 1995
Main classification: C03C3
IPC codes: C03C3, C03C13