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WO1997009279A1 - ACCROISSEMENT DE LA RETENTION DE GeO2 DURANT LA PRODUCTION D'ARTICLES EN VERRE - Google Patents

ACCROISSEMENT DE LA RETENTION DE GeO2 DURANT LA PRODUCTION D'ARTICLES EN VERRE Download PDF

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Publication number
WO1997009279A1
WO1997009279A1 PCT/US1996/014194 US9614194W WO9709279A1 WO 1997009279 A1 WO1997009279 A1 WO 1997009279A1 US 9614194 W US9614194 W US 9614194W WO 9709279 A1 WO9709279 A1 WO 9709279A1
Authority
WO
WIPO (PCT)
Prior art keywords
porous preform
glass
precursors
oxide
metal
Prior art date
Application number
PCT/US1996/014194
Other languages
English (en)
Other versions
WO1997009279A9 (fr
Inventor
Gerald E. Burke
Carlton M. Truesdale
Original Assignee
Corning Incorporated
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from US08/566,354 external-priority patent/US5641333A/en
Application filed by Corning Incorporated filed Critical Corning Incorporated
Priority to AU69651/96A priority Critical patent/AU698054B2/en
Priority to CA002230976A priority patent/CA2230976A1/fr
Publication of WO1997009279A1 publication Critical patent/WO1997009279A1/fr
Publication of WO1997009279A9 publication Critical patent/WO1997009279A9/fr

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C1/00—Ingredients generally applicable to manufacture of glasses, glazes, or vitreous enamels
    • C03C1/02—Pretreated ingredients
    • C03C1/028—Ingredients allowing introduction of lead or other easily volatile or dusty compounds
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B19/00—Other methods of shaping glass
    • C03B19/14—Other methods of shaping glass by gas- or vapour- phase reaction processes
    • C03B19/1415—Reactant delivery systems
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/06—Glass compositions containing silica with more than 90% silica by weight, e.g. quartz
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B2201/00—Type of glass produced
    • C03B2201/06—Doped silica-based glasses
    • C03B2201/30—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi
    • C03B2201/31—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with germanium
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B2207/00—Glass deposition burners
    • C03B2207/80—Feeding the burner or the burner-heated deposition site
    • C03B2207/85—Feeding the burner or the burner-heated deposition site with vapour generated from liquid glass precursors, e.g. directly by heating the liquid
    • C03B2207/87—Controlling the temperature
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C2201/00—Glass compositions
    • C03C2201/06—Doped silica-based glasses
    • C03C2201/30—Doped silica-based glasses containing metals
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C2201/00—Glass compositions
    • C03C2201/06—Doped silica-based glasses
    • C03C2201/30—Doped silica-based glasses containing metals
    • C03C2201/31—Doped silica-based glasses containing metals containing germanium
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C2203/00—Production processes
    • C03C2203/40—Gas-phase processes

Definitions

  • This invention relates to an improved method for making Ge0 2 -doped glass articles.
  • a specific application of the invention is the production of optical waveguide fibers and, in particular, preforms from which such fibers can be produced.
  • Optical waveguide fibers consist of a core surrounded by cladding material having a refractive index lower than that of the core.
  • the radial distribution of the refractive index across the face of the fiber can be simple or complex.
  • single-mode fibers typically have a refractive index profile which is a simple step, i.e., a substantially uniform refractive index within the core and a sharp decrease in refractive index at the core-cladding interface.
  • multimode fiber requires achieving a nearly parabolic radial refractive index profile in the fiber core so as to minimize intermodal dispersion.
  • Optical fibers can be prepared by various known techniques. The present invention is concerned with those techniques such as the outside vapor deposition (OVD) technique and the axial vapor deposition (AVD) technique wherein a porous glass preform is formed and then consolidated.
  • ODD outside vapor deposition
  • ALD axial vapor deposition
  • Preforms produced by vapor deposition techniques typically are composed of silicon dioxide (Si0 2 ) selectively doped with at least one metal or metalloid oxide to provide the desired refractive index profile.
  • germanium dioxide germanium dioxide
  • precursors for the deposition of metal oxide dopants are relatively expensive raw ingredients. It is therefore important that the dopant be effectively incorporated in the preform with a minimum of dopant loss during processing.
  • glass particles can be formed by oxidizing and/or hydrolyzing the halide materials SiCl 4 and GeCl 4 in a burner.
  • the preform is formed from the glass particles by moving the burner back and forth along the length of a rotating mandrel. See U.S. Patent No. 4,486,212, for example.
  • the distance between the mandrel and the burner is selected so that the glass particles collect on the mandrel in thin layers with each pass of the burner.
  • the amount of halide materials supplied to the burner is adjusted during the glass laydown process so as to produce a dopant concentration in the preform which varies with radius.
  • This dopant concentration profile is selected so that the finished fiber will have the desired refractive index profile.
  • the mandrel is removed from the porous preform, thereby forming an aperture.
  • the porous preform is then placed in a consolidation furnace where it is dried and sintered.
  • a first drying gas mixture which usually contains helium and a drying agent such as chlorine or fluorine, flows into the aperture.
  • a drying agent can also be flowed through the furnace (see, for example, U.S. Patent No. 4,165,223).
  • the drying step reduces the residual OH content of the preform, thereby reducing in the resultant optical fiber the absorption loss caused by OH groups in the vicinity of the 1300 nm operating wavelength.
  • the step of sintering a porous preform produces a dense, substantially clear glass article which itself can be drawn into the optical fiber or which can be provided with additional cladding and then drawn into an optical fiber.
  • the entire porous preform can be dried before the sinter step begins; alternatively, the preform can be subjected to a gradient consolidation process whereby the temperature of each individual element of the preform increases and decreases with the approach and passing of the hot zone, respectively.
  • the preform element becomes sufficiently hot that the drying gas mixture can react with the OH ions in the glass, but the preform temperature is not so high that preform porosity is decreased to the point that drying gas flow is impeded.
  • the pore size decreases and the preform element then completely sinters and clarifies.
  • dopant from the core portion of a porous preform can migrate through the pores to the cladding portion, thereby creating a dopant depleted region at the edge of the core and a corresponding dopant rich region in the adjacent cladding; this combination is known as a "diffusion tail".
  • dopant can migrate from the region of higher concentration to the region of lesser concentration to alter the core refractive index profile.
  • Two features of the refractive index profile, the central dip and the diffusion tail have been recognized as limiting the optical performance of optical fibers. The central dip has been shown to be correlated with decreasing the optical bandwidth of the fiber.
  • Modelling has revealed that the diffusion tail has the effect of increasing the optical attenuation of the fiber.
  • the migration of germanium out of the preform is very costly, especially in a process for fabricating multimode optical fibers.
  • a multimode fiber fabrication process requires a large amount of germanium source material in order to produce cores having greater radii and greater refractive indices as compared to single-mode fibers. Therefore, processes which could retain more germania in the sample could result in the production of more product (increased select) , a better performance distribution, and a capital avoidance of buying germanium- containing source materials.
  • the objects of the invention include: 1) reducing the amount of germanium containing precursors used in the formation of consolidated draw blanks from which optical fibers are drawn and 2) improving the refractive index profiles of germanium containing optical fiber draw blanks.
  • the present invention relates to a process for forming a Ge0 2 -doped SiO -based glass article.
  • a reactant stream which includes precursors of Si0 2 and GeO : is flowed to a reaction zone.
  • the precursors are reacted to form a stream of glass particles, and the particles are collected to form a porous preform.
  • the porous preform is dried and sintered to form a clear glass article.
  • the reactant stream includes a precursor of an oxide of a metal M which in its oxide state is not a glass former with Si0 2 and which decomposes to provide oxygen to reduce the reaction of GeO : with chlorine to thereby enhance the retention of GeO_ in the article during the step of drying.
  • Fig. 1 is a graph showing Ge0 2 concentration in unconsolidated soot preforms as a function of the concentration of Sn0 2 in the soot particles.
  • Fig. 2 is a graph showing microprobe analyses of consolidated core canes made by processes employing the same amounts of GeCl in the reactant gas mixture, one of the processes also employing SnCllibrary in the glass particle deposition process.
  • Fig. 3 is a spectral attenuation curve of an optical fiber drawn from a preform formed by a process in which SnCl 4 was added to the reactant stream mixture.
  • the invention provides a stabilized optical fiber preform fabrication process in which 1) the efficiency of Ge0 2 incorporation into the porous preform produced by the laydown step is slightly increased and 2) the tendency of the Ge0 2 to move within the preform and either redeposit in an undesirable location or leave the preform is reduced. Since this technique is especially applicable to a method for forming draw blanks from which optical fibers are drawn, that method will be specifically described herein.
  • the improvement in efficiency of retention of Ge0 2 in a silica-based glass article is accomplished by initially co-doping the deposited Ge0 2 -Si0 2 porous glass with an oxide of a metal M selected from the group consisting of tin, antimony and bismuth.
  • tin in the form of SnClj can be mixed with chlorides of germania and silica in the reactant gas mixture that is fed to the burner to produce Sn0 2 -doped germania silicate porous preforms.
  • Sn0 2 to Ge0 2 -containing Si0 2 glass particles in an OVD soot deposition technique has resulted in the retention of up to 37% more Ge0 2 in the consolidated core preform or core cane as compared to a similar process wherein no Sn0 2 is deposited.
  • core cane is meant a preliminary glass article that includes the core portion of the resultant optical fiber and optionally includes some of the cladding portion.
  • the core cane is then overclad with cladding glass particles and consolidated to form a draw blank from which the optical fiber is drawn. It is noted that other source materials such as organometallics can also be used to deposit these oxides.
  • the improvement in the retention of Ge0 2 in a silica-based glass article is accomplished without adversely affecting the refractive index profile of the resultant preform.
  • germania silicate glass articles is specifically discussed herein, the present invention is also applicable to the formation of germania silicate glasses that also contain one or more dopants such as P 2 0 5 , B 2 0 3 and the like.
  • germania-silicate soot glass particles
  • Unconsolidated germania silicate porous preforms were prepared with and without tin to compare the germania concentration.
  • the deposition system employed a burner of the type shown in Fig. 3 of U.S. Patent No. 4,165,223, which is incorporated herein by reference. The burner included a face having a centrally located fume orifice surrounded by concentric rings of orifices.
  • the rings of orifices which are referred to in Tables 1 and 2, are the inner shield orifices IS, the premix orifices, and the outer shield orifices OS, named in order of increasing radius.
  • the reactant compounds emanate from the fume orifice where they are subjected to heat from a flame produced by the fuel gas and oxygen emanating from the premix orifices. Streams of oxygen flow from orifices IS and OS.
  • These soot samples were made using a bubbler delivery system of the type disclosed in U.S. Patent No. 3,826,560.
  • the heated bubblers contained SiCl 4 , GeCl 4 , and SnCl 4 maintained at the temperatures indicated in Tables 1 and 2.
  • Curve 10 of Fig. 1 is a graph showing Ge0 2 concentration in unconsolidated soot preforms as a function of the concentration of Sn0 2 in the soot particles.
  • the diamond- shaped data points on curve 10 show the effect of the addition of SnCl 4 at the different concentrations indicated in Table 1 to fixed flow rates of germania and silica. The flow rates of oxygen through the SnCl 4 -containing bubbler are given for most of the data points on curve 10.
  • the second set of data shows four samples made under the same flow conditions described above except that SnCl 4 is not added to the reactant gas mixture.
  • the oxygen which would have normally flowed through the tin tetrachloride bubbler is added to the fume stream to be certain that that oxygen which had delivered the tin was not responsible for the increase in Ge0 2 retention. Even though the extra oxygen in the fume stream slightly increases the Ge0 2 content of the unconsolidated soot preform, it is not responsible for the large Ge0 2 increase that has been observed in the consolidated glass article.
  • Chlorine will react at a fast rate with species that are not bound to the glass matrix. If the additional oxygen was not available to cause Ge0 2 to be retained, GeCl 4 would either leave the glass as a gas species, or react with oxygen to re-deposit Ge0 2 in another portion of the porous preform such as the cladding.
  • Bismuth and antimony are expected to have an effect similar to that of tin.
  • the oxides of these elements are not expected to form an amorphous network with silica or germania. These oxides easily give up oxygen as they are heated to 900 C. As can be observed in Table 3, it would be expected that the oxygen provided from the decomposition of oxides of bismuth and antimony would also help to retain germania.
  • the bismuth and antimony should be easily removed by the chlorine drying step.
  • Microprobe analyses of optical fiber "core canes" demonstrate that consolidated glass that is formed by a process that employs SnClweb in the soot laydown step has a much larger concentration of germania than consolidated glass that is formed by a process that does not employ SnCl 4 in that step.
  • Single-mode fibers are often made by forming a soot core preform that includes the layers of glass soot that are required to form the fiber core and a few layers of cladding soot (see U.S. Patent No. 4,486,212).
  • the soot core preform is consolidated to form a core cane that is thereafter overclad with cladding soot to form a preform that is consolidated and drawn into an optical fiber.
  • the germania retention enhancement feature of the present invention can be shown by analyzing the consolidated core cane.
  • Core canes were made by a process similar to the process described above in connection with Tables l and 2 for forming soot preforms.
  • the rates of oxygen flow through the bubblers containing SiCl.;, GeCl 4 and SnCl- and the inner shield oxygen, outer shield oxygen and fume oxygen are given in Table 4.
  • Premix CH 4 was linearly ramped from 8.5 1pm to 15 1pm and the premix 0 2 was linearly ramped from 8.24 1pm to 14.55 lpm during the formation of both preforms.
  • concentration of SnCl 4 in the reactant gas mixture used to produce porous preform #8055-19 was 13 vol.%, whereas no SnCl 4 was used to make porous preform #8055-18.
  • the porous preforms were consolidated to form core canes, the identifying numbers of which are the same as those of the corresponding preforms.
  • the porous preforms were consolidated under identical conditions. The mandrel was removed from the preform to form a tubular porous preform having a longitudinal aperture.
  • the preform was lowered into a 1510°C hot zone of a consolidation furnace at a rate of 6 mm/minute.
  • Helium flowed upwardly through the furnace muffle at a rate of 40 lpm.
  • a drying gas mixture of 0.66 lpm helium and 0.042 lpm chlorine flowed into the longitudinal aperture.
  • Fig. 2 shows microprobe analyses for the resultant consolidated core canes.
  • Curve 14 represents the microprobe analysis for core cane 8055-19
  • curve 16 represents the microprobe analysis for core cane 8055-18.
  • the total amount of germania in core cane 8055-19 is about 37% greater than that in core cane 8055-18.
  • the total amount of germania in each of core canes 8055-19 and 8055- 18 was determined by fitting curves 14 and 16 between points A and B to high order polynomials (12-14th order) and integrating over the radial coordinate. It is noted that the shapes of curves 14 and 16 are substantially independent of whether tin is present during the soot laydown process.
  • Bubblers containing SiCl 4 and GeCl 4 were held at 43°C, and a bubbler containing SnCl 4 was held at 55°C.
  • Initial flow rates to the burner were: 2.0 lpm oxygen through the bubbler containing SiCl 4 , 0.5 lpm oxygen through the bubbler containing GeCl 4 , 0.4 lpm oxygen through the bubbler containing SnCl 4 , 6 lpm Premix CH 4 ,
  • the burner deposited a porous core preform by traversing back and forth over a 50.8 cm length of an alumina mandrel having a diameter that tapered from 5.88 mm to 4.95 mm.
  • the mandrel was pulled from the porous preform to form an aperture therein.
  • the tubular porous preform was inserted into a consolidation furnace where it was consolidated as described in U.S. Patents Nos. 4,165,223 and 4,486,212.
  • the maximum furnace temperature was set at 1472°C.
  • the downfeed rate of the porous preform through the hot zone was 3.5 mm/minute.
  • a gas mixture of 20 lpm helium and 0.2 lpm chlorine flowed upwardly through the furnace muffle, while a gas mixture of 0.5 lpm helium and 0.1 lpm chlorine flowed into the preform aperture.
  • the consolidated core cane was mounted in a draw furnace where its tip was heated. A vacuum source was affixed to the opposite end. While an intermediate fiber having a diameter of 7 mm was drawn, the aperture closed. The intermediate fiber was severed into rods, one of which was employed as a mandrel upon which cladding soot was deposited to a diameter of approximately 80 mm.
  • the resultant composite preform was consolidated to form a draw blank that was drawn into an optical fiber having an outside diameter of 125 ⁇ m and a core diameter of about 9 ⁇ m.
  • the spectral attenuation curve for the resultant fiber is shown in Fig. 3. The attenuation at 1570 nm is 0.280 dB/km. The strength of the resultant fiber was as good as that of a standard telecommunication fiber.
  • the entire core portion of the above-described draw blank contained Ge0 2 , and the cladding portion consisted of pure silica.
  • the method of this invention could also be employed to make optical fibers having cores containing other dopants in addition to Ge0 2 .
  • the core could be made of more than one annular region, at least one of which contained Ge0 2 and at least one of which contained no Ge0 2 .
  • the cladding could be formed of silica doped with fluorine or boron or even with a dopant that increases the refractive index of silica, provided that the refractive index of the cladding does not exceed that of the core.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • General Chemical & Material Sciences (AREA)
  • Geochemistry & Mineralogy (AREA)
  • Manufacturing & Machinery (AREA)
  • Manufacture, Treatment Of Glass Fibers (AREA)
  • Glass Compositions (AREA)

Abstract

Le procédé faisant l'objet de cette invention sert à former un article en verre au SiO2 dopé par GeO2 en déposant des particules de verre, afin de former une préforme poreuse, puis en séchant et en frittant cette préforme poreuse. Un précurseur de SnO2 est également présent dans le flux de réactifs utilisés pour former les particules, pour que la réaction produise des particules de verre qui contiennent GeO2, SiO2 et SnO2. La présence de SnO2 dans les particules réduit la réaction de GeO2 avec le chlore pour former GeCl4 pendant l'étape de séchage. Le GeCl4 qui se serait formé soit ce serait échappé de la préforme poreuse soit aurait amené GeO2 à se redéposer dans une partie indésirable de la préforme. La rétention de GeO2 dans l'article en verre est par conséquent accrue.
PCT/US1996/014194 1995-09-08 1996-09-04 ACCROISSEMENT DE LA RETENTION DE GeO2 DURANT LA PRODUCTION D'ARTICLES EN VERRE WO1997009279A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
AU69651/96A AU698054B2 (en) 1995-09-08 1996-09-04 Increasing the retention of GeO2 during production of glass articles
CA002230976A CA2230976A1 (fr) 1995-09-08 1996-09-04 Accroissement de la retention de geo2 durant la production d'articles en verre

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
US348495P 1995-09-08 1995-09-08
US60/003,484 1995-09-08
US08/566,354 1995-12-01
US08/566,354 US5641333A (en) 1995-12-01 1995-12-01 Increasing the retention of Ge02 during production of glass articles

Publications (2)

Publication Number Publication Date
WO1997009279A1 true WO1997009279A1 (fr) 1997-03-13
WO1997009279A9 WO1997009279A9 (fr) 1997-05-01

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PCT/US1996/014194 WO1997009279A1 (fr) 1995-09-08 1996-09-04 ACCROISSEMENT DE LA RETENTION DE GeO2 DURANT LA PRODUCTION D'ARTICLES EN VERRE

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AU (1) AU698054B2 (fr)
CA (1) CA2230976A1 (fr)
WO (1) WO1997009279A1 (fr)

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4165223A (en) * 1978-03-06 1979-08-21 Corning Glass Works Method of making dry optical waveguides

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4165223A (en) * 1978-03-06 1979-08-21 Corning Glass Works Method of making dry optical waveguides

Also Published As

Publication number Publication date
AU698054B2 (en) 1998-10-22
AU6965196A (en) 1997-03-27
CA2230976A1 (fr) 1997-03-13

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