WO2002060830A1 - A process for making rare earth doped optical fibre - Google Patents
A process for making rare earth doped optical fibre Download PDFInfo
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- WO2002060830A1 WO2002060830A1 PCT/IN2001/000014 IN0100014W WO02060830A1 WO 2002060830 A1 WO2002060830 A1 WO 2002060830A1 IN 0100014 W IN0100014 W IN 0100014W WO 02060830 A1 WO02060830 A1 WO 02060830A1
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B37/00—Manufacture or treatment of flakes, fibres, or filaments from softened glass, minerals, or slags
- C03B37/01—Manufacture of glass fibres or filaments
- C03B37/012—Manufacture of preforms for drawing fibres or filaments
- C03B37/014—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD]
- C03B37/018—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD] by glass deposition on a glass substrate, e.g. by inside-, modified-, plasma-, or plasma modified- chemical vapour deposition [ICVD, MCVD, PCVD, PMCVD], i.e. by thin layer coating on the inside or outside of a glass tube or on a glass rod
- C03B37/01807—Reactant delivery systems, e.g. reactant deposition burners
- C03B37/01838—Reactant delivery systems, e.g. reactant deposition burners for delivering and depositing additional reactants as liquids or solutions, e.g. for solution doping of the deposited glass
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B37/00—Manufacture or treatment of flakes, fibres, or filaments from softened glass, minerals, or slags
- C03B37/01—Manufacture of glass fibres or filaments
- C03B37/012—Manufacture of preforms for drawing fibres or filaments
- C03B37/014—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD]
- C03B37/018—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD] by glass deposition on a glass substrate, e.g. by inside-, modified-, plasma-, or plasma modified- chemical vapour deposition [ICVD, MCVD, PCVD, PMCVD], i.e. by thin layer coating on the inside or outside of a glass tube or on a glass rod
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B37/00—Manufacture or treatment of flakes, fibres, or filaments from softened glass, minerals, or slags
- C03B37/01—Manufacture of glass fibres or filaments
- C03B37/012—Manufacture of preforms for drawing fibres or filaments
- C03B37/014—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD]
- C03B37/018—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD] by glass deposition on a glass substrate, e.g. by inside-, modified-, plasma-, or plasma modified- chemical vapour deposition [ICVD, MCVD, PCVD, PMCVD], i.e. by thin layer coating on the inside or outside of a glass tube or on a glass rod
- C03B37/01807—Reactant delivery systems, e.g. reactant deposition burners
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B37/00—Manufacture or treatment of flakes, fibres, or filaments from softened glass, minerals, or slags
- C03B37/01—Manufacture of glass fibres or filaments
- C03B37/012—Manufacture of preforms for drawing fibres or filaments
- C03B37/014—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD]
- C03B37/018—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD] by glass deposition on a glass substrate, e.g. by inside-, modified-, plasma-, or plasma modified- chemical vapour deposition [ICVD, MCVD, PCVD, PMCVD], i.e. by thin layer coating on the inside or outside of a glass tube or on a glass rod
- C03B37/01853—Thermal after-treatment of preforms, e.g. dehydrating, consolidating, sintering
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- 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
- C03B2201/08—Doped silica-based glasses doped with boron or fluorine or other refractive index decreasing dopant
- C03B2201/12—Doped silica-based glasses doped with boron or fluorine or other refractive index decreasing dopant doped with fluorine
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- 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
- C03B2201/20—Doped silica-based glasses doped with non-metals other than boron or fluorine
- C03B2201/28—Doped silica-based glasses doped with non-metals other than boron or fluorine doped with phosphorus
-
- 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
- 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
- C03B2201/34—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with rare earth metals, i.e. with Sc, Y or lanthanides, e.g. for laser-amplifiers
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- 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
- C03B2201/34—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with rare earth metals, i.e. with Sc, Y or lanthanides, e.g. for laser-amplifiers
- C03B2201/36—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with rare earth metals, i.e. with Sc, Y or lanthanides, e.g. for laser-amplifiers doped with rare earth metals and aluminium, e.g. Er-Al co-doped
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P40/00—Technologies relating to the processing of minerals
- Y02P40/50—Glass production, e.g. reusing waste heat during processing or shaping
- Y02P40/57—Improving the yield, e-g- reduction of reject rates
Definitions
- the present invention relates to a Process for Making Rare Earth Doped Optical Fibre. Background Art
- Rare-earth (RE) doped optical fibres have shown great potential for a number of applications including amplifiers, fibre lasers and sensors. Oxides of rare earths are doped into the core of such fibres as the active substance. Lasing and amplification have been demonstrated at several wavelengths with the incorporation of various rare-earths but for telecommunication applications erbium doped fibre (EDF) remains the most important since the operating wavelength matches with the third low loss optical window. Erbium doped fibre amplifier (EDF A) operating around 1.53 ⁇ m low loss window is playing the key role in the present day high capacity commumcation systems. It is able to amplify the optical signal directly independent of modulation format.
- EDF Erbium doped fibre amplifier
- EDF A has the capability to amplify simultaneous optical channels in a single fibre, which has enabled the implementation of WDM (wavelength division multiplexing) technology with the potential of increasing the bandwidth of long distance transmission systems from Gb/s to Tb/s ranges. It thus exhibits high gain, large bandwidth, low noise, polarisation insensitive gain, substantially reduced cross talk problems and low insertion losses at the operating wavelengths.
- WDM wavelength division multiplexing
- GeO 2 are deposited at a lower temperature to form unsintered porous soot, iii.
- the tube with the deposit is immersed into an aqueous solution of the dopant precursor (typical concentration 0.1 M) up to 1 hour. Any soluble form of the dopant ion is suitable for preparation of the solution although rare earth halides have been mostly used.
- the tube is rinsed with acetone and remounted on lathe.
- the core layer containing the RE is dehydrated and sintered to produce a clear glassy layer. Dehydration is carried out a temperature of 600°C by using chlorine. The level of OH " is reduced below lppm using Cl 2 / O 2 ratio of 5:2 provided the drying time exceeds 30 min.
- Fibre drawing is conventional.
- Al is said to be a key component in producing high RE concentrations in the core centre without clustering effect. It is further disclosed that Al and RE profile lock together in some way which retards the volatility of RE ion. The dip at the core centre is observed both for P and GeO 2 .
- each atom of erbium in the core cross section is exposed to substantially equal levels of the high intensity portion of the pump mode.
- the fibre with such design is reported to 3 » wt i i ? » »# ' - ⁇ ** — -
- the desiccation is carried out for a period of .24 -240 hours at a temperature of 60° - 70°C in an atmosphere of nitrogen gas or inert gas.
- This desiccated soot preform is heated and dehydrated for a period of 2.5 - 3.5 hours at a temperature of 950° - 1050°C in an atmosphere of helium gas containing 0.25 to 0.35% chlorine gas and further heated for a period of 3-5 hours at a temperature of 1400 ° - 1600°C to render it transparent, thereby forming an erbium doped glass preform.
- Step like RE distribution profile is obtained in the core resulting to poor overlap between the pump signal and the RE ions which lowers the pump efficiency.
- Step like RE distribution requires high numerical aperture (NA) of the core or confinement of the RE in the central region (say 50% of the total core area) for increase in pump efficiency which in turn leads to the following disadvantages: i) Doping of RE only in selected portion of the core is extremely difficult and affects the repeatability of the process due to the sensitivity of the method to process parameters during various stages of processing such as deposition, solution doping, drying and sintering.
- NA numerical aperture
- Residual stress produces undesirable increase in background loss of the fibre, vi) Residual stress is believed to introduce polarisation mode dispersion (PMD) which results in serious capacity impairments including pulse broadening. Since the magnitude of PMD at a given wavelength is not stable passive compensation becomes impossible.
- PMD polarisation mode dispersion
- the main object of the present invention is to provide a process for making Rare Earth doped optical fibre, which obviates the drawbacks as detailed above.
- Another object of the present invention is to provide fibres possessing controlled distribution of RE, more particularly Erbium in the doped region similar to the pump beam intensity distribution in the fibre with maximum concentration at the centre so that the overlapping between the two is considerably improved.
- Still another object of the present invention is to provide fibres in which the pump beam has a radius of distribution equal to or greater than the radius of distribution of RE ions in the core to increase the chances of all the active ions getting exposed to the pump light, consequently increasing the pump conversion efficiency in the fibre.
- Yet another object of the present invention is to provide a method of controlling the
- Gaussian RE distribution profile along the radial direction in the core is Gaussian RE distribution profile along the radial direction in the core.
- Still another object of the present invention is to achieve high optical gain in the fibres for NA value close to 0.20 only thus avoiding wide variation in composition between the core and cladding glass to eliminate problems like residual stress and PMD.
- Yet another object of the present invention is to reduce the quantity of germanium halide required to achieve the desired NA in the fibre.
- One more object of the present invention is to provide a process where the numerical aperture of the fibre is varied from 0.10 to 0.30 maintaining RE concentration in the core between 50 to 6000 ppm along with variation in RE distribution profile in the doped region to produce fibres suitable for application as amplifiers, fibre lasers and sensors for different purposes. Summary of the invention
- the novelty of the present invention lies in controlling the concentration profile of RE ion in the collapsed preform by mimmising evaporation of the RE salt and also preventing diffusion of the rare earth ion due to subsequent heat treatment.
- the optimum soot density to achieve this objective is estimated to lie between 0.3 to 0.5 after deposition.
- the inventive step lies in transformation of the RE salts to oxides by gradually heating the tube to a higher temperature maintaining an oxidising atmosphere inside, thereby minimising the possibility of evaporation of RE during subsequent processing as the oxide has a very high melting temperature compared to halide/nitrate salts. This step also helps to remove the solvent trapped within the porous layer.
- the inventive step also includes increasing the temperature of the RE containing porous layer gradually in steps of 50 to 200°C up to the sintering temperature and above for sintering and further fixing of the RE ions in their desired sites.
- the steps will depend on the host glass composition and Er/Al concentration of the core layer.
- the incorporation efficiency of the RE from the solution to the core layer thus increases appreciably making the process more efficient and economic.
- the RE distribution along the transverse direction in the core will depend on the density of the porous soot layer, dipping period and the processing conditions during oxidation, sintering and collapsing.
- the sintering of the porous core layer in GeO 2 rich atmosphere along with the addition of oxygen and helium is another inventive step of the process which reduces the quantity of GeCLt required to achieve the desired NA and adds to the economy of the process.
- pure GeCl 4 is supplied with the input oxygen, the quantity of which depends on the NA desired in the fibre.
- the sintering is continued by gradually raising the temperature till a clear glassy layer is formed.
- the present invention provides an improved process for making rare earth doped optical fibre which comprises (a) providing deposition of P O 5 and F doped synthetic cladding within a silica glass substrate tube to obtain matched or depressed clad type structure, (b) forming a core by depositing unsintered particulate layer at a tube surface temperature in the range of 1200-1400°C, (c) maintaining P O 5 and GeO 2 concentrations from 0.5 to 5.0 mol% and 3.0 to 25.0 mol% in the said particulate layer respectively to obtain a tube containing F-doped cladding and porous soot layer, (d) immersing the tube containing the porous soot layer into a solution containing RE salt in the concentration range of 0.002M to 0.25 M with or without aluminium salt of the concentration range 0.05 M to 1.25 M for a period of 1 to 2 hours, (e) draining the solution out at a rate in the range of 10-50 cc/min, (f) drying the porous layer by flowing
- the present invention further provides an process for making erbium doped optical fibre which comprises (a) providing deposition of P O 5 and F doped synthetic cladding within a silica glass substrate tube to obtain matched or depressed clad type structure, (b) forming a core by depositing unsintered particulate layer at a tube surface temperature in the range of 1200-1350°C, (c) maintaining P 2 O 5 and GeO 2 concentrations from 0.5 to 3.5 mol% and 3.0 to 20.0 moP/o in the said particulate layer respectively to obtain a tube containing F-doped cladding and porous soot layer, (d) immersing the tube containing the porous soot layer into a solution containing Er salt in the concentration range of 0.004M to 0.20 M with or without aluminium salt at the concentration range of 0.05 M to 1.0 M for a period of 1 to 2 hours, (e) draining the solution out at a rate in the range of 10-30 cc/min, (f) drying the por
- the present invention also provides an process for making rare earth doped optical fibre wherein the RE distribution along the transverse direction in the core is varied by controlling the density of the porous soot layer, dipping period and the processing conditions during oxidation, sintering and collapsing depending on the host glass composition and RE/A1 concentration of the core layer.
- the numerical aperture of the fibre is varied from 0.10 to 0.30 maintaining RE concentration in the core between 50 to 6000 ppm along with variation in RE distribution profile along the radial direction in the doped region to produce fibres suitable for application as amplifiers, fibre lasers and sensors for different purposes.
- theoretically estimated relative density of the porous soot ranges between 0.30 to 0.50 to avoid core-clad interface defect.
- GeCl 4 supplied during soot deposition is
- the pump beam has a radius of distribution equal to or greater than the radius of distribution of Er ions in the core, which enhances the chance of all the active ions getting exposed to the pump light.
- RE salt used is selected from chloride, nitrate or any other salt soluble in solvent used in the process.
- aluminium salt used is selected from chloride, nitrate or any other salt soluble in solvent used in the process.
- solution for aluminium and RE salts is prepared using solvent selected from alcohol and water.
- the temperature of the core layer is increased in steps of 50 to 200°C during oxidation and sintering depending on the composition and Al/RE concentration of the core layer.
- the mixture of O and He is in the range of 3:1 to 9:1.
- source of chlorine is selected from CC1 4 where Helium is used as carrier gas.
- the porous core is sintered in presence of germania by supplying GeCl with the input oxygen at a temperature of 1200°C to 1400°C during sintering to facilitate germania incorporation and obtain appropriate numerical aperture.
- the process provides variation in the numerical aperture of the fibre from 0.10 to 0.30 maintaining RE concentration in the core between 50 to 6000 ppm along with variation in RE distribution profile along the transverse direction in the doped region to produce fibres suitable for application in any devices.
- the devices are amplifiers, fibre lasers and sensors for different purposes where optical fibre is used.
- Another embodiment of the invention is a method of controlling the Gaussian RE distribution profile along the radial direction in a core used in the process of making rare earth doped optical fibre wherein, said process comprising the steps of: a) Depositing P 2 O 5 and F within a high silica glass substrate tube to make matched clad or depressed clad type structure. b) Depositing predefined composition of unsintered particulate layer at a temperature of 1200 to 1400°C for the forming a core, wherein P 2 O 5 and GeO 2 levels in the core vary from 0.5 to 5.0 mol% and 3.0 to 25.0 mol% respectively, and GeCl 4 concentration in the gas phase is kept 10 to 30% lower than that required for achieving the desired NA of 0.20.
- the deposition temperature is dependent on the composition and desired porosity of the soot.
- a theoretically estimated porosity of 0.3 to 0.5 is found suitable to avoid core-clad interface defect and clustering after dipping and to control the RE distribution in the core with maximum concentration at the centre.
- d) Immersing the tube containing the porous soot layer into an alcoholic/aqueous solution of REC1 3 / RE(NO 3 ) 3 of strength varying between 0.002 M and 0.25 M with or without the addition of A1C1 3 / Al(NO 3 ) 3 in the concentration range 0.05
- the particulate core layer containing RE is dehydrated at a temperature between 800° to 1200°C in presence of excess chlorine.
- CC1 4 is used as the source material for Cl 2 and supplied by using Helium as a carrier gas which being a lighter gas diffuses through the small pores and assists in the drying process.
- the proportion of Cl : O 2 varies from 1.5: 1 to 3.5: 1 while the dehydration period lies between 1 to 2 hours.
- the porous core layer is then sintered in presence of O 2 and He by heating the tube to a temperature as high as 1900°C.
- the temperature is gradually increased in steps of 50 to 200°C depending on the composition and RE/Al concentration of j) the core layer from the drying temperature between 800 to 1200°C mentioned above, k) At temperatures between 1200° to 1400°C during sintering pure GeCl 4 is supplied with the input oxygen to carry out the sintering of the porous layer in germania rich atmosphere which facilitates germania incorporation.
- the flow rate of GeCl 4 and the no. of pass depend on the NA desired in the fibre.
- the supply of GeCl 4 is then stopped and the sintering is continued by gradually raising the temperature till a clear glassy layer is formed.
- EXAMPLE 1 • Deposition of F-doped cladding within a silica tube by MCND process at a temperature of l855°C.
- the temperature was increased in 4 steps up tol400°C.
- GeCl 4 was added from this stage with input oxygen with 3 passes between 1200° 1400°C.
- the tube was further heated to increase the temperature stepwise to 1650°C for complete sintering of the Er & Al containing porous soot layer. During sintering O and He flow was in the ratio of 4.5:1.
- the Er 3+ ion concentration in the fibre was 950 ppm with maximum concentration at the core centre and distribution as shown in fig.l accompanying this specification.
- the Er distribution in the core was measured from the fibre section by fluorescence spectroscopy by Photonics Resource Facility, 60 St. George Street, Suite No. 331, Toronto, Ontario, Canada M5S 1 A7.
- EXAMPLE 2 • Deposition of F-doped cladding inside a silica glass tube by MCND process at a temperature of 1840°C.
- the temperature was increased in 3 steps up tol200°C.
- GeCl 4 was added from this stage with input oxygen with one pass each at 1200°, 1300° and 1400°C.
- the tube was further heated to increase the temperature stepwise to 1610°C for complete sintering of the Er & Al containing porous soot layer. During sintering O 2 and He flow was in the ratio of 5:1.
- the NA measured in the fibre was 0.201 ⁇ 0 .01. • The Er 3+ ion concentration in the fibre was 460 ppm with peak at the core centre and similar distribution as shown in accompanying drawings as figure 1.
- the temperature was increased in 4 steps up tol400°C.
- GeCl was added with the input oxygen with 2 passes at 1200°C and one pass each at 1300°C and 1400°C.
- the tube was further heated to increase the temperature stepwise to 1725°C for complete sintering of the Er & Al containing porous soot layer. During sintering O 2 and He flow was in the ratio of 4: 1.
- the Er 3+ ion concentration in the fibre was 3020 ppm with peak concentration at the core centre and Er distribution in the core as shown in accompanying drawing as figure -2 measured from the fibre section by fluorescence spectroscopy by Photonics Resource Facility, 60 St. George Street, Suite No. 331, Toronto, Ontario, Canada M5S-
- the developed fibres have a RE distribution in the doped region similar to the Gaussian pump beam intensity distribution in the fibre so that the overlapping between the two is considerably improved consequently increasing the pump conversion efficiency in the fibre.
- the pump beam has a radius of distribution equal to or greater than the radius of distribution of RE ions in the core, which enhances the chance of all the active ions getting exposed to the pump light.
- the RE distribution along the transverse direction in the core is varied by controlling the density of the porous soot layer, dipping period and the processing conditions during oxidation, sintering and collapsing depending on the host glass composition and RE/Al concentration of the core layer.
- the compositions of the core and cladding glass are varied to achieve NA close to 0.20 for Er 3+ ion concentration in the range of 100 to 1500 ppm in order to provide erbium doped fibre suitable for pumping for amplification of the input signal with gain in the range 10 to 37 dB for optical amplifier application.
- the developed fibres mentioned under 4 and 5 above have NA and mode field diameter not widely different from signal transmitting fibre for ease of splice. This minimises the optical loss of the signal travelling through the fibres.
- the oxidation step before drying and sintering of the particulate layer reduces the possibility of change in composition due to evaporation of RE salts during subsequent processing.
- the stepwise increase in temperature during oxidation and sintering stages prevents diffusion of RE and the codopants minimising the probability of a change in composition.
- the incorporation efficiency of RE in the doped region is increased due to the reason stated in 8 and 9 above, which adds to the economy of the process. 11.
- the improvement in process efficiency due to the reasons mentioned in 8 - 10 above enhances the yield and repeatability of the process.
- the concentration of RE in the core is varied between 50 to 6000 ppm along with variation in RE distribution profile in the doped region and NA between 0.10 to 0.30 to produce fibres suitable for application as amplifiers, microlasers and sensors for different purposes.
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Abstract
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Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
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CA002436579A CA2436579C (en) | 2001-02-02 | 2001-02-02 | A process for making rare earth doped optical fibre |
KR1020037010252A KR100655480B1 (en) | 2001-02-02 | 2001-02-02 | A process for making rare earth doped optical fibre |
CNB018230083A CN1274618C (en) | 2001-02-02 | 2001-02-02 | Process for making rare earth doped optical fibre |
AU2001242728A AU2001242728B2 (en) | 2001-02-02 | 2001-02-02 | A process for making rare earth doped optical fibre |
PCT/IN2001/000014 WO2002060830A1 (en) | 2001-02-02 | 2001-02-02 | A process for making rare earth doped optical fibre |
GB0318455A GB2388367B (en) | 2001-02-02 | 2001-02-02 | A process for making rare earth doped optical fibre |
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PCT/IN2001/000014 WO2002060830A1 (en) | 2001-02-02 | 2001-02-02 | A process for making rare earth doped optical fibre |
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WO2002060830A8 WO2002060830A8 (en) | 2003-11-20 |
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KR (1) | KR100655480B1 (en) |
CN (1) | CN1274618C (en) |
AU (1) | AU2001242728B2 (en) |
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Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1440947A1 (en) * | 2003-01-16 | 2004-07-28 | Sumitomo Electric Industries, Ltd. | Optical fibre and its preform and method of their manufacture starting from a glass tube |
EP2108624A1 (en) * | 2008-01-15 | 2009-10-14 | Sumitomo Electric Industries, Ltd. | Rare-earth-doped optical fiber, optical fiber amplifier, and method of manufacturing a preform for such fiber |
US20100142033A1 (en) * | 2008-12-08 | 2010-06-10 | Draka Comteq, B.V. | Ionizing Radiation-Resistant Optical Fiber Amplifier |
CN104058587A (en) * | 2014-07-14 | 2014-09-24 | 富通集团有限公司 | Rare earth-doped optical fiber perform and preparation method thereof |
CN106966581A (en) * | 2017-05-18 | 2017-07-21 | 江苏亨通光导新材料有限公司 | A kind of preform and preparation method thereof |
CN110510864A (en) * | 2019-09-11 | 2019-11-29 | 烽火通信科技股份有限公司 | The preparation method and preform of highly doped rare-earth-doped fiber precast rod |
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- 2001-02-02 WO PCT/IN2001/000014 patent/WO2002060830A1/en active IP Right Grant
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- 2001-02-02 CA CA002436579A patent/CA2436579C/en not_active Expired - Lifetime
- 2001-02-02 AU AU2001242728A patent/AU2001242728B2/en not_active Expired
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EP1440947A1 (en) * | 2003-01-16 | 2004-07-28 | Sumitomo Electric Industries, Ltd. | Optical fibre and its preform and method of their manufacture starting from a glass tube |
EP2108624A1 (en) * | 2008-01-15 | 2009-10-14 | Sumitomo Electric Industries, Ltd. | Rare-earth-doped optical fiber, optical fiber amplifier, and method of manufacturing a preform for such fiber |
US20100142033A1 (en) * | 2008-12-08 | 2010-06-10 | Draka Comteq, B.V. | Ionizing Radiation-Resistant Optical Fiber Amplifier |
US8467123B2 (en) * | 2008-12-08 | 2013-06-18 | Draka Comteq B.V. | Ionizing radiation-resistant optical fiber amplifier |
CN104058587A (en) * | 2014-07-14 | 2014-09-24 | 富通集团有限公司 | Rare earth-doped optical fiber perform and preparation method thereof |
CN104058587B (en) * | 2014-07-14 | 2016-06-22 | 富通集团有限公司 | A kind of rare earth doped optical fibre prefabricated rods and preparation method thereof |
CN106966581A (en) * | 2017-05-18 | 2017-07-21 | 江苏亨通光导新材料有限公司 | A kind of preform and preparation method thereof |
CN110510864A (en) * | 2019-09-11 | 2019-11-29 | 烽火通信科技股份有限公司 | The preparation method and preform of highly doped rare-earth-doped fiber precast rod |
Also Published As
Publication number | Publication date |
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GB2388367A (en) | 2003-11-12 |
CA2436579C (en) | 2006-09-26 |
CN1500069A (en) | 2004-05-26 |
GB2388367B (en) | 2005-05-18 |
GB0318455D0 (en) | 2003-09-10 |
WO2002060830A8 (en) | 2003-11-20 |
KR20040034595A (en) | 2004-04-28 |
KR100655480B1 (en) | 2006-12-08 |
AU2001242728B2 (en) | 2007-05-10 |
CA2436579A1 (en) | 2002-08-08 |
CN1274618C (en) | 2006-09-13 |
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