WO2010059559A1 - Procédé de réduction du rapport redox de verre fondu et verre ultra transparent obtenu par ce procédé - Google Patents

Procédé de réduction du rapport redox de verre fondu et verre ultra transparent obtenu par ce procédé Download PDF

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Publication number
WO2010059559A1
WO2010059559A1 PCT/US2009/064557 US2009064557W WO2010059559A1 WO 2010059559 A1 WO2010059559 A1 WO 2010059559A1 US 2009064557 W US2009064557 W US 2009064557W WO 2010059559 A1 WO2010059559 A1 WO 2010059559A1
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Prior art keywords
glass
iron
weight percent
pool
oxygen
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PCT/US2009/064557
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English (en)
Inventor
Larry J. Shelestak
Ronald L. Schwenninger
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PPG Industries Ohio Inc
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PPG Industries Ohio Inc
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Priority to CN2009801540729A priority Critical patent/CN102272062A/zh
Priority to RU2011125304/03A priority patent/RU2536526C2/ru
Priority to KR1020117014146A priority patent/KR101304664B1/ko
Priority to BRPI0921419A priority patent/BRPI0921419A2/pt
Priority to MX2011005385A priority patent/MX343670B/es
Application filed by PPG Industries Ohio Inc filed Critical PPG Industries Ohio Inc
Priority to CA2744380A priority patent/CA2744380A1/fr
Priority to EP09756894.3A priority patent/EP2396284B1/fr
Priority to JP2011537534A priority patent/JP5785092B2/ja
Priority to ES09756894.3T priority patent/ES2577527T3/es
Publication of WO2010059559A1 publication Critical patent/WO2010059559A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B5/00—Melting in furnaces; Furnaces so far as specially adapted for glass manufacture
    • C03B5/16—Special features of the melting process; Auxiliary means specially adapted for glass-melting furnaces
    • C03B5/173—Apparatus for changing the composition of the molten glass in glass furnaces, e.g. for colouring the molten glass
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B5/00—Melting in furnaces; Furnaces so far as specially adapted for glass manufacture
    • C03B5/16—Special features of the melting process; Auxiliary means specially adapted for glass-melting furnaces
    • C03B5/18—Stirring devices; Homogenisation
    • C03B5/193—Stirring devices; Homogenisation using gas, e.g. bubblers
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
    • C03B5/00—Melting in furnaces; Furnaces so far as specially adapted for glass manufacture
    • C03B5/16—Special features of the melting process; Auxiliary means specially adapted for glass-melting furnaces
    • C03B5/235—Heating the glass
    • 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
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
    • C03C3/085—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal
    • C03C3/087—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal containing calcium oxide, e.g. common sheet or container glass
    • 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
    • C03C4/00—Compositions for glass with special properties
    • C03C4/0092—Compositions for glass with special properties for glass with improved high visible transmittance, e.g. extra-clear glass
    • 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
    • C03C4/00—Compositions for glass with special properties
    • C03C4/10—Compositions for glass with special properties for infrared transmitting glass

Definitions

  • This invention relates to a method of reducing the redox ratio
  • Solar collectors and solar mirrors use solar energy to heat a fluid, e.g. as disclosed in U.S. Patent Nos. 4,224,927 and 5,253,105, or to convert solar energy to electrical energy.
  • the solar collectors have a cover plate to pass the solar energy, to reduce heat loss due to convection, and to protect the photovoltaic cells of the electric power generating solar collectors
  • the solar mirrors have a glass substrate to pass the solar energy to a reflective coating and reflect the solar energy back through the glass substrate to direct the solar energy to a designated area.
  • the glass cover plates and the glass substrates are the glass cover plates and the glass substrates.
  • the glass cover plates used for photovoltaic cover plates, and the glass substrates used for solar mirrors preferably above 380 nanometers ("nm") of the electromagnetic spectrum have a high transmission, e.g. above 90% in the visible and the infrared ("IR") range, and a low absorption, e.g. below 2% in the visible and the IR ranges.
  • IR infrared
  • the particular visible and IR range of the electromagnetic spectrum, and the peak transmission varies depending on the semi-conductor material of the photovoltaic cell.
  • the preferred visible and IR wavelength range is 380-1200 nm, and the peak transmission is at about 900 nm.
  • the preferred visible and IR wavelength range is 380-1200 nm, and the peak transmission is at about 900 nm.
  • 5,030,593; 5,030,594, and 6,962,887 disclose the making of low iron glasses that are almost colorless by processing raw glass batch materials that have a very low content of total iron expressed as Fe 2 O 3 , e.g. less than 0.020 % by weight (hereinafter also referred to as “wt%” or “wt. %”).
  • wt% 0.020 % by weight
  • ppm parts per million
  • iron in the ferric state is a less powerful colorant than iron in the ferrous state and shifts the transmittance spectrum of the glass toward yellow and away from the usual green-blue effect of the ferrous iron in glass. Stated another way, increasing iron in the ferric state while decreasing iron in the ferrous state, increases the transmission, and decreases the absorption of the glass in the visible and the IR range.
  • cerium oxide is not a colorant in glass, but is a powerful oxidizing agent in glass, and its function in decolorized glass is to oxidize the iron in the ferrous state (Fe ++ ) to iron in the ferric (Fe +++ ) state.
  • cerium oxide is useful to decolorize the remaining traces of ferrous iron, the use of cerium oxide has limitations, e.g. but not limiting to the discussion, when the glass is to be used as cover plates for electric power generating solar collectors and as glass substrates for solar mirrors.
  • exposing low iron glass cover plate having cerium oxide to the sun has a solarizing effect on the glass, which results from the photo-oxidation of Ce +++ to Ce ++++ and the photo-reduction of Fe +++ to Fe ++ .
  • the solarization effect of cerium and the photo-reduction of Fe +++ to Fe ++ reduces the transmission, and increases the absorption, of the glass in the visible and the IR range of the electromagnetic spectrum, which reduces the power generation of the solar cells.
  • This invention relates to a soda-lime-silica glass, having, among other things:
  • the spectral properties of the glass measured at a thickness 5.5 millimeters include, among other things, a visible transmission of greater than 85% measured using C. I. E.
  • the invention relates to a method of reducing redox ratio of soda-lime-silica glass by, among other things, heating a pool of molten soda- lime-silica glass having iron in a ferrous state (Fe ++ ) and in a ferric state (Fe +++ ), wherein the pool of molten glass is heated with an ignited mixture of combustion gas and fuel gas emanating from one or more burners, wherein flow of the combustion gas exceeds the amount of combustion gas required to ignite the fuel gas such that excess oxygen of the combustion gas oxidizes the iron in the ferrous state to iron in the ferric state to reduce the redox ratio.
  • oxygen gas can simultaneously be moved through the pool of molten glass wherein flow of the oxygen gas is in a direction from bottom of the pool of molten glass to top of the pool.
  • the invention relates to a method of reducing redox ratio of soda-lime-silica glass by, among other things, heating a pool of molten soda-lime-silica glass in a heating chamber, the pool of molten glass having iron in a ferrous state (Fe ++ ) and in a ferric state (Fe +++ ); moving glass batch materials onto the pool of molten glass contained in the heating chamber, the batch materials having iron in the ferrous state (Fe ++ ) and in the ferric state (Fe +++ ); melting the glass batch materials as they float on surface of the molten pool of glass; moving oxygen through the pool of molten glass to oxidize the ferrous iron to the ferric iron to reduce the redox ratio, and forming a glass ribbon from the pool of molten glass.
  • Fig. 1 is a horizontal section of a glass melting furnace that can be used in the practice of the invention; Fig. 1 A is the melting section of the furnace, and Fig. 1 B is the refining and homogenizing section of the furnace..
  • Fig. 2 is a vertical section of the melting section shown in Fig. 1 A.
  • Fig. 3 is an elevated side view partially in cross section of a glass melting and refining apparatus that can be used in the practice of the invention.
  • each numerical parameter should at least be construed in light of the number of reported significant digits and by applying ordinary rounding techniques.
  • all ranges disclosed herein are to be understood to encompass any and all subranges subsumed therein.
  • a stated range of "1 to 10" should be considered to include any and all subranges between and inclusive of the minimum value of 1 and the maximum value of 10; that is, all subranges beginning with a minimum value of 1 or more and ending with a maximum value of 10 or less, e.g., 1 to 6.7, or 3.2 to 8.1 , or 5.5 to 10.
  • composition amounts such as “by weight percent”, “wt%” or “wt. %”, “parts per million” and “ppm” are based on the total weight of the final glass composition, or the total weight of the mixed ingredients, e.g. but not limited to the glass batch materials, which ever the case may be.
  • the “total iron” content of the glass compositions disclosed herein is expressed in terms of Fe 2 O 3 in accordance with standard analytical practice, regardless of the form actually present. Likewise, the amount of iron in the ferrous state (Fe ++ ) is reported as FeO, even though it may not actually be present in the glass as FeO.
  • the proportion of the total iron in the ferrous state is used as a measure of the redox state of the glass and is expressed as the ratio FeO/Fe 2 O 3 , which is the weight percent of iron in the ferrous state (expressed as FeO) divided by the weight percent of total iron (expressed as Fe 2 O 3 ).
  • the visible range of the electromagnetic spectrum is 380-780 nanometers (hereinafter also referred to as “nm"), and the infra red (hereinafter also referred to as "IR") range of the electromagnetic spectrum is greater than 780 nm and usually considered to be in the range of 780-10,000 nm.
  • IR infra red
  • visible transmittance or "luminous transmittance” or “LTA” is measured using C. I. E. standard illuminant "A” with a 2° observer over the wavelength range of 380 to 770 nanometers. Glass color, in terms of dominant wavelength and excitation purity, is measured using C. I. E.
  • total solar infrared transmittance or “TSIR” is measured over the wavelength range of 775 to 2125 nanometers
  • total solar energy transmittance” or “TSET” is measured over the wavelength range of 300 to 2500 nanometers.
  • the TSIR transmittance data is calculated using Parry Moon air mass 2.0 direct solar irradiance data and integrated using the Rectangular Rule, as is known in the art.
  • the TSET transmittance data is calculated using ASTM air mass 1.5 global solar irradiance data and integrated using the Trapezoidal Rule, as is known in the art.
  • spectral properties e.g. LTA, infrared transmission, TSIR and TSET are measured at the actual glass thickness and can be recalculated at any thickness.
  • spectral properties of the glass are given for glasses having a standard thickness of 5.5 millimeter, even though the actual thickness of a measured glass sample is different than the standard thickness.
  • the present invention provides a soda-lime-silica glass that is high in visible light and infrared energy transmittance as measured in a normal (i.e. perpendicular) direction to a major surface of the glass sheet, and the glass of the invention is particularly ideal for, but is not limited to, use as cover plates for electric generating solar collectors, and glass substrates for solar mirrors.
  • high visible light transmittance is meant measured visible light transmittance equal to or greater than 85%, such as equal to or greater than 87%, such as equal to or greater than 90%, at 5.5 mm glass thickness.
  • a glass having a 90% visible light transmittance at a thickness of 5.5 mm has a visible light transmission greater than 90% at a thickness less than 5.5 mm and has a visible light transmission less than 90% at a thickness greater than 5.5 mm.
  • high infrared energy transmittance is meant measured infrared energy transmittance equal to or greater than 85%, such as equal to or greater than 87%, such as equal to or greater than 90%, such as equal to or greater than 91 %, at 5.5 mm.
  • a glass having a 91 % infrared energy transmittance at a thickness of 5.5 mm has an infrared energy transmission greater than 91 % at a thickness less than 5.5 mm and has an infrared visible light transmission less than 91 % at a thickness greater than 5.5 mm for glasses having a thickness less than 5.5 mm.
  • the glass of the invention can be made using a conventional non- vacuum refiner float glass system, e.g. but limited to the type shown in Figs. 1 and 2, or using a vacuum refiner float glass system, e.g. but not limited to the type shown in Fig. 3.
  • a conventional non-vacuum system e.g. but limited to the type shown in Figs. 1 and 2
  • a vacuum refiner float glass system e.g. but not limited to the type shown in Fig. 3.
  • Other types of conventional non-vacuum systems are disclosed in U.S. Patent Nos. 4,354,866; 4,466,562 and 4,671 ,155, and other types of vacuum refiner float glass system are disclosed in U.S. Patent Nos. 4,792,536 and 5,030,594.
  • FIGs.1 and 2 there is shown a conventional continuously fed, cross-tank fired, glass melting and non-vacuum refining furnace 20 having an enclosure formed by a bottom 22, roof 24, and sidewalls 26 made of refractory materials.
  • the glass batch materials 28 are introduced through inlet opening 30 in an extension 32 of the furnace 20 known as the fill doghouse in any convenient or usual manner to form a blanket 34 floating on surface 36 of molten glass 38.
  • Overall progression of the glass as shown in Figs. 1 A and 1 B is from left to right in the figures, toward entrance end of a glass forming chamber 40 of the type used in the art to make float flat glass.
  • the glass batch materials 28 as they move downstream from the batch feeding end or doghouse end wall 46 are melted in the melting section 48 of the furnace 20, and the molten glass 38 moves through waist 54 to refining section 56 of the furnace 20.
  • the refining section 56 bubbles in the molten glass 38 are removed, and the molten glass 38 is mixed or homogenized as the molten glass passes through the refining section 56.
  • the molten glass 38 is delivered in any convenient or usual manner from the refining section 56 onto a pool of molten metal (not shown) contained in the glass-forming chamber 40. As the delivered molten glass 38 moves through the glass-forming chamber 40 on the pool of molten metal (not shown), the molten glass is sized and cooled.
  • a dimensionally stable sized glass ribbon moves out of the glass- forming chamber 40 into an annealing lehr (not shown).
  • Glass making apparatus of the type shown in Figs. 1 and 2, and of the type discussed above are well known in the art and no further discussion is deemed necessary.
  • Fig. 3 Shown in Fig. 3 is continuously fed glass melting and vacuum refining equipment 78 for melting glass batch materials and refining the molten glass.
  • Batch materials 80 preferably in a pulverulent state, are fed into cavity 82 of a liquefying vessel, e.g. a rotating drum 84.
  • a layer 86 of the batch material 80 is retained on the interior walls of the vessel 84 aided by the rotation of the drum and serves as an insulating lining.
  • the batch material 80 on the surface of the lining 84 As the batch material 80 on the surface of the lining 84 is exposed to the heat within the cavity 82, it forms a liquefied layer 88 that flows out of a central drain opening 90 at the bottom 92 of the vessel 84 to a dissolving vessel 94 to complete the dissolution of unmelted particles in the liquefied material coming from the vessel 84.
  • a valve 96 controls the flow of material from the dissolving vessel
  • the invention is not limited to the process of and/or equipment for making glass, and any of the glass making processes and/or equipment known in the art can be used in the practice of the invention.
  • the glass batch used in the glass making apparatus shown in Figs. 1 and 2 includes sodium sulfate (salt cake) as a melting and refining aid in the amounts of about 5 to 15 parts by weight per 1000 parts by weight of the silica source material (sand), with about 10 parts by weight considered desirable to assure adequate refining, i.e. removal of bubbles from the molten glass.
  • the sulfur-containing materials can be added such that the retained sulfur content e.g., the average amount of SO 3 left in the resultant bulk glass is less than or equal to 0.2 wt. %, such as less than or equal to 0.15 wt. %, such as less than or equal to 0.1 wt.
  • the residual sulfur can be in the range of 0.005 wt. % to 0.13 wt. %.
  • the glass batch materials melted in the glass making apparatus 78 shown in Fig. 3 are essentially free of sulfur. By "essentially free of sulfur” is meant that no intentional addition of sulfur-containing compounds is made to the glass batch materials.
  • trace amounts of sulfur can be present in the glass due to impurities in the batch materials or other sources, e.g. but not limited to cullet.
  • trace amounts of sulfur is meant sulfur in the range of greater than 0 wt. % to 0.03 wt. %.
  • the "sulfur" content of the glass compositions disclosed herein is expressed in terms of SO 3 in accordance with standard analytical practice, regardless of the form actually present.
  • Glass batch materials used for making low iron glass cover plates for electric power generating solar collectors, and for making glass substrates for solar mirrors preferably provide a glass that has a high measured transmission, e.g. greater than 90%, and a high measured IR transmission, e.g. greater than 91 %.
  • iron is not intentionally added to the batch materials, and iron present in the molten glass as ferrous iron (Fe ++ ) is oxidized to ferric iron (Fe +++ ).
  • CeO 2 is added to the glass batch materials to oxidize the ferrous ion (Fe ++ ) to the ferric ion (Fe +++ ) to increase the visible and IR transmission of the glass. It is believed, however, that exposing glass having CeO 2 to the sun's radiation results in solarization reactions which photo-oxidizes Ce +++ to Ce ++++ and photo-reduces Fe +++ to Fe ++! , which results in the reduction of visible and IR transmission of the glass. CeO 2 in amounts less than 0.0025 wt. % (25 ppm) or less in the glass does not result in objectionable levels of solarization, e.g.
  • CeO 2 in amounts equal to, or greater than 0.0800 wt. % (800 ppm) results in unacceptable levels of solarization, e.g. a 1.0% reduction in the measured visible and IR transmission of the glass after exposure to sunlight for 28 days.
  • ingredients that oxidize the ferrous iron Fe ++ to the ferric Fe +++ , and can be solarized, e.g. CeO 2 are not added to the batch materials, and if present, are present as tramp materials, such that the glass preferably has equal to or less than 0.0025 wt. % (25 ppm) CeO 2 .
  • the invention is directed to low iron soda-lime-silica glasses, e.g. soda-lime-silica glasses having equal to or less than 0.01 wt.
  • the invention is not limited thereto, and the invention can be practiced to lower the percent by weight of the ferrous iron in high iron glasses, e.g. soda-lime-silica glasses having greater than 0.01 wt. % (100 ppm) total iron expressed as Fe 2 O 3 .
  • the invention is not limited to glass cover plates for solar collectors, and to glass substrates for solar mirrors, and can be used (1 ) as a glass cover plate, or glass substrate for any type of solar cell or solar collector; (2) as residential and commercial windows; (3) as windows for any type of vehicle, e.g. land, air, space, above water, and below water, vehicle; (4) as furniture table tops, and (5) combinations thereof.
  • Table 1 lists the major constituents and their respective ranges in weight percent of a non-limiting embodiment of a commercial clear float glass of the invention that can be used to make cover plates for solar collectors, glass substrates for solar mirrors, and/or commercial, residential and appliance windows.
  • cerium is added to the batch materials as hydrated cerium carbonate (Ce 2 CO 3 3H 2 O) and can be present in the glass as Ce +++ (Ce 2 O 3 ) or Ce ++++ (CeO 2 ).
  • CeO 2 is present in the glass in amounts equal to or less than 0.0025 wt. %.
  • CeO 2 can be present in the glass as a tramp material, e.g. as an impurity in the batch materials and/or in the glass cullet added to the batch materials to aid in the melting of the batch materials.
  • CeO 2 can be present in the glass of the invention within the range of 0 to 0.0100 wt. %, preferably in the range of 0 to 0.0075 wt. %, more preferably in the range of 0 to 0.0050 wt. %, and most preferably in the range of 0 to 0.0025 wt. %.
  • Clear soda-lime-silica glasses having low amounts of iron have a substantial absence of color in visible transmittance.
  • the total iron expressed as Fe 2 O 3 is less than about 0.025 wt. % (250 parts per million), more preferably less than 0.015 wt.
  • the glasses have a redox value (FeO/Fe 2 O 3 ) of less than 0.35, preferably less than 0.25, more preferably less than 0.20, and most preferably less than 0.150.
  • the glasses of Table 2 can be made using the equipment shown in
  • the SO 3 is preferably less than 0.02 wt%.
  • oxygen is introduced into the molten glass to oxidize the ferrous iron (Fe ++ ) to the ferric iron (Fe +++ ).
  • oxygen is bubbled into the pool of molten glass; in another non-limiting embodiment of the invention, the ratio of oxygen to fuel or firing gas is increased to oxidize the iron in the ferrous state (Fe ++ ) to iron in the ferric state (Fe +++ ), and in still another non-limiting embodiment of the invention, oxygen is bubbled into the pool of molten glass and the ratio of oxygen to fuel or firing gas is increased to oxidize the iron in the ferrous state (Fe ++ ) to iron in the ferric state (Fe +++ ).
  • Starphire Commercial melts included 1000 grams of Starphire glass cullet.
  • the glass composition of the cullet was not analyzed; however, the Starphire glass has a glass composition within the ranges of the ingredients shown in column (B) of Table 2.
  • the cullet was contained in 4-inch silica crucibles and melted at a temperature of 2600 degrees F (1427 degrees C).
  • Oxygen gas was introduced into the molten glass using a porous ceramic tube made by etching the bottom 1 inch (2.54 centimeters) of the closed end of a mullite tube in hydrofluoric acid. Although the sizes of the holes were not measured, it is believed the holes had a diameter of about less than 1 millimeter.
  • Sample A was the control sample and no oxygen was introduced into the molten glass of Sample A.
  • the flow rate of oxygen introduced into the molten glass of Sample B was 10 cubic centimeters ("CC") per minute for 30 minutes; into the molten glass of Sample C was 20 CC per minute for 30 minutes; into the molten glass of each of Samples D and E was 20 CC per minute for 60 minutes, and into the molten glass of Sample F was 20 CC per minute for 120 minutes.
  • CC cubic centimeters
  • the Samples B-F each had a lower redox value than the redox value of Sample A indicating that more of the ferrous iron in Samples B-F was oxidized than in the Sample A. Based on the amount of oxygen added to the molten glass for sample F and sample C, the efficiency for below Reaction 1 ranged from 0.16 to 0.35%. The efficiency was determined by calculating the amount of oxygen that reacted with the ferrous iron divided by the total amount of oxygen introduced into the molten glass during the lab experiment through the porous ceramic tube.
  • the glass batch ingredients selected for making low iron glasses have no additions of iron, and any iron present in the batch materials is present as tramp materials.
  • Iron content generally referred to as tramp amounts of iron are amounts of iron less than 0.025 wt. %.
  • batch materials are selected to have an iron content to provide the glass with a total iron expressed as Fe 2 O 3 of less than 0.025 wt. % (250 ppm).
  • batch materials are selected for minimal iron contamination, but it would be difficult to reduce the total iron content (Fe 2 O 3 ) in the glass batch materials to provide a glass having less than about 0.005 wt.
  • batch selection includes a low iron sand, which can have an iron content of about 0.008 wt. % iron (80 ppm) analyzed as Fe 2 O 3 .
  • Limestone and dolomite conventional glass batch materials, are avoided because of their typical iron contamination. Instead, it is preferred to use a purer source of calcium such as aragonite, which is a mineral form of calcium carbonate with only about 0.020 wt. % (200 ppm) Fe 2 O 3 .
  • low iron dolomite having an iron (Fe 2 O 3 ) content of less than about 0.020 wt.
  • a preferred alumina source is aluminum hydrate, with about 0.008 wt. % (80 ppm) Fe 2 O 3 .
  • An example of a glass batch mixture that can be used to make glasses within the ranges of the glass of Table 1 is shown in Table 4.
  • cerium is not added to the batch materials, and preferably, but not limiting to the invention, cerium is only present as a tramp material, e.g. less than 0.010 wt. % (100 ppm).
  • Figs. 1 -3 preferably include the ingredients in the range shown on Table 4, except that the glass making apparatus shown in Fig. 3 is preferably operated using two parts by weight of sodium sulfate per 1000 parts by weight of the sand (the silica source material); whereas, it is preferred to operate the glass making apparatus of Figs. 1 and 2 using 7 parts by weight of sodium sulfate per 1000 parts by weight of the silica source material.
  • the glass batch materials of Table 4 provide glasses having compositions shown in Table 5 below.
  • the glass compositions of Table 5 were computer calculated from the batch formula of Table 4. It should be noted, however, that the glass composition of the fifth experiment discussed below was selected to be similar to computer calculated glass composition of Column (A) of Table 5. The computer program does not provide a redox ratio; however, the redox ratios of the invention discussed above are applicable for the glass compositions shown in Table 5.
  • the glasses listed in Table 5 made using the glass making apparatus of Fig. 3 would have an SO 3 content less than 0.02 wt. %. As can be appreciated, the invention is not limited to the glass compositions listed in Table 5.
  • tramp materials which are impurities found in the batch materials and can include MnO 2 , ZrO 2 , CoO, Se, NiO, Cl, P 2 O 5 , V 2 O 5 , CeO 2 , Cr 2 O 3 , Li 2 O, K 2 O and TiO 2 .
  • Each of the spargers was spaced 42 inches (1.1 meters) above the bottom surface of the furnace. Twenty five (25) cubic feet per hour (“CFH") of oxygen were moved through each of the spargers. It was observed that the spargers generated gas bubbles that were about 1/8 inch (0.32 centimeter) in diameter as they burst on the surface of the molten glass.
  • the batch composition had ingredients to make glass similar to the glass listed in column B of Table 5.
  • the batch ingredients initially added to the melter did not have any additions of CeO 2 , the only CeO 2 present in the batch materials were tramp amounts, and the CeO 2 present in the glass cullet. Twice during the glass production run hydrated cerium carbonate was added to the batch materials. A first sample of the glass was taken before the first addition of the hydrated cerium carbonate and was analyzed; the first sample had a redox ratio of 0.48. Three (3) pounds of hydrated cerium carbonate per 1000 pounds of sand was added to the batch materials for 12 hours.
  • a second sample of the glass was taken and analyzed; the second sample had a redox ratio of 0.43.
  • the CeO 2 in the glass increased from 0.04 wt. % to 0.06 wt. %.
  • a second addition of hydrated cerium carbonate was made. The second addition was 3 pounds of hydrated cerium carbonate per 1000 pounds of sand for 26 hours.
  • Four (4) days after the second addition a third sample of the glass was taken and analyzed.
  • the third sample of glass had a redox ratio of 0.471 ; contained 0.0102 wt % (102 ppm) Fe 2 O 3 , and 0.04 wt% (400 ppm) CeO 2 .
  • the usual level of CeO 2 is about 0.07% (700 ppm) and the usual level of the redox ratio is in the range of about 0.48-0.50.
  • the results from the first experiment suggested that the introduction of oxygen gas into the molten glass through the two porous refractory spargers can serve as a substitute for adding CeO 2 to oxidize the ferrous iron to the ferric iron, and to lower the glass redox ratio by about 0.01 -0.03, in a large commercial glass furnace.
  • a second experiment was conducted on a glass production run to make clear glass having 0.10 wt% Fe 2 O 3 , i.e. high iron glass.
  • the sparger positions in relationship to the furnace walls was the same, however the spargers were spaced 8 inches (20 cm) from the bottom surface of the furnace.
  • each of the the spargers in the second experiment was a thicker porous refractory cylindrical block (3 inch (7.6 cm) diameter compared to only 2 inch (5.08 cm) diameter used in the first experiment) to increase the useable life of the spargers.
  • the oxygen flow rate was 20 CFH at 40 PSI through each of the spargers.
  • the average redox ratio of the glass two weeks before oxygen was flowed through the spargers was 0.338 and the range of the redox ratio was 0.005.
  • the average redox ratio with oxygen moving through the spargers was 0.336 and the range of the redox ratio was 0.01. There was no significant change in the mean value of redox ratio, only an increase in the variability of the redox value.
  • the conclusion of the second experiment was that while the glass redox ratio was lowered at least part of the time while using the oxygen spargers, the glass redox ratio was not lowered on a continuous basis due to non-homogeneous mixing of the molten glass in the furnace.
  • a glass composition included 0.05 wt% CeO 2 .
  • oxygen was moved through selected bubblers of one row of 19 individual gas bubblers (water cooled metal tubes) 150 (see Fig. 1 A) mounted in the base 26 of the furnace 20.
  • the bubblers extended upward into the molten glass about 24 inches (0.61 meters) from the bottom surface of the furnace and 33 inches (0.84 meters) below the surface 36 of the molten glass 38.
  • the bubblers 150 were positioned about 50 feet from the wall 46 of the furnace 20 in the area of the 4 th port 42 (see Fig. 2).
  • the bubblers 150 were spaced about 18 inches (0.46 meters) apart and span the furnace 20 in a perpendicular fashion to the direction of the molten glass flow. Initially oxygen was moved through 6 bubblers, and then over the next three days through 12 of the remaining 13 bubblers; one bubbler did not function because it was clogged. Although the position of the first six bubblers was not recorded, it is believed the six bubblers were the three outer bubbles on each end of the row of bubblers. The oxygen flow was initially 5 CFH through each of the 18 bubblers and was increased after 3 days by 5 CFH, and increased by 5 CFH once again 4 days after the first increase.
  • the last step of 5 CFH was reversed because the high rate of oxygen bubbling was entraining and leaving residual bubbles in the molten glass. It was observed that the bubblers generated gas bubbles that were about 6 inches (15.2 cm) in diameter as they burst on the surface of the molten glass.
  • the glass redox ratio prior to introducing oxygen gas through the bubblers was 0.45.
  • the glass made with oxygen moving through the 18 bubblers and after the last step of 5 CFH was reversed had a redox ratio of 0.41 and an Fe 2 O 3 of 0.0096 wt. %.
  • the use of the oxygen gas in the bubblers lowered the glass redox by 0.04.
  • a fourth experiment was conducted on the glass composition of the third experiment except that the only CeO 2 present in the batch materials was tramp CeO 2 in the glass cullet in an amount of 0.04 wt. %.
  • the bubblers were raised to a position 27 inches (0.69 meters) from the level of the molten glass and the oxygen was moved through each of the 18 bubblers 150 at a flow rate of 12.5 CFH.
  • the oxygen gas flow rate was increased from 12.5 CFH to 17.5 CFH per bubbler, and from 17.5 CFH to 20 CFH per bubbler over the next five days.
  • the rate of oxygen was dropped back to 17.5 CFH because the high rate of oxygen gas bubbling was entraining and leaving residual bubbles in the molten glass.
  • the glass redox ratio can be lowered by introducing oxygen gas into the molten glass as a substitute for the need to add CeO 2 to oxidize the iron in the ferrous state (Fe ++ ) to iron in the ferric state (Fe +++ ).
  • the oxygen gas can be introduced through either a sparger consisting of a porous refractory block or a water cooled metal bubblers. It was observed that the size of the bubbles generated by the oxygen gas was much smaller using the sparger than with the water cooled bubbler More particularly, the size of the bubbles from the spargers were similar to the bubbles moved through the molten glass in the lab experiment. In the instance when the glass is made in the glass making apparatus shown in Fig. 3, the oxygen would be bubbled into the molten glass in the dissolution chamber 94 through bubblers 1 10 (only one shown in Fig. 3) mounted through the base 1 12 of the dissolution chamber 94.
  • oxygen to oxidize the ferrous iron (Fe ++ ) to ferric iron (Fe +++ ) is provided by increasing the ratio of combustion air, i.e. oxygen gas to the fuel or firing gas at the firing ports.
  • the normal firing ratio of combustion air to fuel gas is 10.9 as determined by the formula "total combustion air flow rate (the combustion air to all of the firing ports) divided by total fuel gas flow rate (fuel gas to all of the firing ports)."
  • the flow rate of combustion air and fuel gas is not evenly distributed to each of the firing ports; however, in the practice of the invention the total flow rate of the combustion air and the total flow rate of the fuel gas is of interest.
  • the combustion gas includes 21 % oxygen and the remaining percent mostly nitrogen. Therefore, the normal firing ratio of oxygen to fuel gas for combustion air/fuel gas fired furnaces is 2.29 (10.9 total combustion air/total fuel gas x 0.21 oxygen in combustion air).
  • the "air firing ratio” is determined by the formula "total combustion air flow rate (the combustion air to all of the firing ports) divided by total fuel gas flow rate (fuel gas to all of the firing ports)" and is normally 10.9.
  • the "oxygen firing ratio" for an oxygen/fuel gas fired furnace is determined by the formula "total oxygen gas flow rate (the oxygen to all of the firing ports) divided by total fuel gas flow rate (fuel gas to all of the firing ports)" and is normally 2.29
  • the “oxygen firing ratio” for a combustion air/fuel gas firing furnace is determined by the formula "total combustion air flow rate times percent of oxygen in the combustion air divided by total fuel gas flow rate (fuel gas to all of the firing ports)” and is normally 2.29.
  • Increasing the air firing ratio to greater than 1 1.0, or the oxygen firing ratio to 2.31 by increasing the total combustion air flow rate or the total combustion oxygen, respectively, provides excess oxygen to oxidize the ferrous iron (Fe ++ ) to ferric iron (Fe +++ ).
  • dolomite also helps to lower the glass redox, because the dolomite does not contain high levels of carbon impurities, which are present in the aragonite and can act as a reducing agent to reduce the ferric iron (Fe +++ ) to the ferrous iron (Fe ++ ).
  • Combustion air at each of the 7 ports 42 on each side of the furnace 20 was increased during their firing cycle by increasing the air firing ratio from 12.3 to 13.3 in steps of 0.1 -0.4 (increasing the oxygen firing ratio from 2.58 to 2.79 in steps of 0.02-0.084) each over a five day period. About 72 hours after the ratio was increased, a sample of glass was taken and analyzed. The redox ratio of the sample was 0.39.
  • the low iron float glass composition produced is similar to the computer generated glass composition of Column (A) in Table 5 and contained 0.0084 wt. % (84 ppm) Fe 2 O 3 and 0.0021 wt. % (21 ppm) CeO 2 .
  • the glass had a LTA (visible transmittance value) of 91.3%, a TSIR value of 90.4% and a TSET value of 90.7% at an actual thickness of about 3.2 mm (0.1254 inches).
  • An LTA value of 91.3% is a very high glass transmittance that is useful as a cover plate to protect the photovoltaic cells in electric power generating solar collectors and as a glass substrate for solar mirrors. It is concluded from this fifth experiment that the glass redox ratio can be lowered by about 0.06 by increasing the air firing ratio (the oxygen firing ratio).
  • the oxygen firing ratio provides oxygen to the molten glass to oxidize the ferrous iron (Fe ++) to ferric iron (Fe +++ ).
  • the invention is not limited to any particular ratio value; however, it is preferred to have an oxygen firing ratio of 2.31 (an air firing ratio of 1 1.0), more preferred an oxygen firing ratio of 2.63 (an air firing ratio of 12.5), and most preferred an oxygen firing ratio of 2.71 (an air firing ratio of 12.9).
  • bubbling oxygen through the molten glass provides oxygen to the molten glass to oxidize the ferrous iron (Fe ++) to ferric iron (Fe +++ ).
  • 2400 CF per 24 hours of oxygen per 7564 cubic feet of molten glass (0.32 CFper 24 hours per cubic foot of molten glass) is equal to about 0.01 % CeO 2 in terms of causing an equivalent decrease in the glass redox ratio.
  • increasing the air firing ratio (the oxygen firing ratio) while bubbling oxygen through the molten glass increases the amount of oxygen to the molten glass to oxidize the ferrous iron (Fe ++) to ferric iron (Fe +++ ) and can be used to avoid excessive increases of the air firing ratio (the oxygen firing ratio) thereby reducing environmental concerns.
  • the invention can be practiced to make a glass for solar control cover plates and for solar mirrors, e.g. low iron glass having the components in the range shown in Table 6, and the properties discussed below.
  • total iron equal to or less than 0.01 wt. %
  • Redox ratio less than 0.400, or less than 0.350, or less than 0.200, or less than 0.150
  • the glasses of Table 6 at a glass thickness of 5.5 millimeters have an LTA equal to or greater than 85%, or equal to or greater than 87%, or equal to or greater than 90%; a TSIR equal to or greater than 85%, or equal to or greater than 87%, or equal to or greater than 90%, or equal to or greater than 91 %, and a TSET equal to or greater than 89%, or equal to or greater than 90%, or equal to or greater than 91 %.
  • the spectral properties of the glass vary as the redox ratio and/or the Fe 2 O 3 (total iron) vary as was discussed above.
  • the invention can be practiced to make a glass for commercial and residential buildings, furniture and appliances, and for land, above and below water, and aerospace, e.g. high iron glass having the components in the range shown in Table 7, and the properties discussed below. TABLE 7
  • CeO 2 less than 0.080 wt. %, or less than
  • Fe 2 O 3 total iron greater than 0.01 wt. % to 0.12 wt. %
  • Redox ratio less than 0.550, or less than 0.400, or less than 0.350, or less than 0.200, or less than 0.150
  • the glasses of Table 7 at a glass thickness of 5.5 millimeters have an LTA equal to or greater than 85%, or equal to or greater than 87%, or equal to or greater than 90%; a TSIR equal to or greater than 85%, or equal to or greater than 87%, or equal to or greater than 89%, or equal to or greater than 90%, and a TSET equal to or greater than 88%, or equal to or greater than 89%, or equal to or greater than 90%.
  • the spectral properties of the glass vary as the redox ratio and/or the Fe 2 O 3 (total iron) vary as was discussed above.
  • the above glasses are preferably, but not limited to the invention, made in glass making equipment similar to, but not limited to the type shown in Figs. 1 and 2.
  • the above glass can be made in glass making equipment having a vacuum refiner, e.g. similar to, but not limited to the type shown in Fig. 3 by reducing the SO 3 to less than 0.010 wt% as discussed above.

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Abstract

Selon l’invention, un verre silico-sodo-calcique pour des plaques de revêtement de capteurs solaires et des miroirs solaires possède moins de 0,010 pour cent en poids de fer total en tant que Fe2O3, un rapport redox de moins de 0,350, moins de 0,0025 pour cent en poids de CeO2 et des propriétés spectrales qui incluent une transmission dans le visible, et une transmittance infrarouge solaire totale, de plus de 90 % à une épaisseur de 5,5 millimètres, et une solarisation réduite. Dans un mode de réalisation non limitatif de l'invention, le verre est obtenu par chauffage d'une masse silico-sodo-calcique fondue avec un mélange d'air de combustion et de gaz combustible ayant un rapport de cuisson dans l'air supérieur à 11, ou un rapport de cuisson dans l'oxygène supérieur à 2,31. Dans un autre mode de réalisation non limitatif de l'invention, des courants de bulles d'oxygène sont déplacés à travers une masse de verre fondu. Dans les deux modes de réalisation, l'oxygène oxyde le fer ferreux en fer ferrique pour réduire le rapport redox.
PCT/US2009/064557 2008-11-21 2009-11-16 Procédé de réduction du rapport redox de verre fondu et verre ultra transparent obtenu par ce procédé Ceased WO2010059559A1 (fr)

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ES09756894.3T ES2577527T3 (es) 2008-11-21 2009-11-16 Método de reducción de la relación redox de un vidrio fundido para la fabricación de vidrio ultra transparente
RU2011125304/03A RU2536526C2 (ru) 2008-11-21 2009-11-16 Способ снижения редокс-отношения стекломассы и получаемое этим способом сверхпрозрачное стекло
KR1020117014146A KR101304664B1 (ko) 2008-11-21 2009-11-16 용융 유리의 산화/환원 비를 감소시키는 방법 및 이로부터 제조된 초투명 유리
BRPI0921419A BRPI0921419A2 (pt) 2008-11-21 2009-11-16 método de redução da razão de redox de molde de vidro e vidro ultra-limpo feito desse modo
MX2011005385A MX343670B (es) 2008-11-21 2009-11-16 Metodo para disminuir la proporcion redox de vidrio fundido y vidrio fabricado de este modo.
CN2009801540729A CN102272062A (zh) 2008-11-21 2009-11-16 降低熔融玻璃的氧化还原比的方法和由该方法制造的超透明玻璃
CA2744380A CA2744380A1 (fr) 2008-11-21 2009-11-16 Procede de reduction du rapport redox de verre fondu et verre ultra transparent obtenu par ce procede
EP09756894.3A EP2396284B1 (fr) 2008-11-21 2009-11-16 Procédé de diminution du redox du verre fondu pour obtenir un verre extra clair
JP2011537534A JP5785092B2 (ja) 2008-11-21 2009-11-16 溶融ガラス及びそれから作製される超透明ガラスのレドックス比を低減する方法

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US8304358B2 (en) 2012-11-06

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